Influences of the Powder Size and Process Parameters on the Quasi-Stability of Molten Pool Shape in Powder Bed Fusion-Laser Beam of Molybdenum

Influences of the Powder Size and Process Parameters on the Quasi-Stability of Molten Pool Shape in Powder Bed Fusion-Laser Beam of Molybdenum

몰리브덴 분말층 융합-레이저 빔의 용융 풀 형태의 준안정성에 대한 분말 크기 및 공정 매개변수의 영향

Abstract

Formation of a quasi-steady molten pool is one of the necessary conditions for achieving excellent quality in many laser processes. The influences of distribution characteristics of powder sizes on quasi-stability of the molten pool shape during single-track powder bed fusion-laser beam (PBF-LB) of molybdenum and the underlying mechanism were investigated.

The feasibility of improving quasi-stability of the molten pool shape by increasing the laser energy conduction effect and preheating was explored. Results show that an increase in the range of powder sizes does not significantly influence the average laser energy conduction effect in PBF-LB process. Whereas, it intensifies fluctuations of the transient laser energy conduction effect.

It also leads to fluctuations of the replenishment rate of metals, difficulty in formation of the quasi-steady molten pool, and increased probability of incomplete fusion and pores defects. As the laser power rises, the laser energy conduction effect increases, which improves the quasi-stability of the molten pool shape. When increasing the laser scanning speed, the laser energy conduction effect grows.

However, because the molten pool size reduces due to the decreased heat input, the replenishment rate of metals of the molten pool fluctuates more obviously and the quasi-stability of the molten pool shape gets worse. On the whole, the laser energy conduction effect in the PBF-LB process of Mo is low (20-40%). The main factor that affects quasi-stability of the molten pool shape is the amount of energy input per unit length of the scanning path, rather than the laser energy conduction effect.

Moreover, substrate preheating can not only enlarge the molten pool size, particularly the length, but also reduce non-uniformity and discontinuity of surface morphologies of clad metals and inhibit incomplete fusion and pores defects.

준안정 용융 풀의 형성은 많은 레이저 공정에서 우수한 품질을 달성하는 데 필요한 조건 중 하나입니다. 몰리브덴의 단일 트랙 분말층 융합 레이저 빔(PBF-LB) 동안 용융 풀 형태의 준안정성에 대한 분말 크기 분포 특성의 영향과 그 기본 메커니즘을 조사했습니다.

레이저 에너지 전도 효과와 예열을 증가시켜 용융 풀 형태의 준안정성을 향상시키는 타당성을 조사했습니다. 결과는 분말 크기 범위의 증가가 PBF-LB 공정의 평균 레이저 에너지 전도 효과에 큰 영향을 미치지 않음을 보여줍니다. 반면, 과도 레이저 에너지 전도 효과의 변동이 강화됩니다.

이는 또한 금속 보충 속도의 변동, 준안정 용융 풀 형성의 어려움, 불완전 융합 및 기공 결함 가능성 증가로 이어집니다. 레이저 출력이 증가함에 따라 레이저 에너지 전도 효과가 증가하여 용융 풀 모양의 준 안정성이 향상됩니다. 레이저 스캐닝 속도를 높이면 레이저 에너지 전도 효과가 커집니다.

그러나 열 입력 감소로 인해 용융 풀 크기가 줄어들기 때문에 용융 풀의 금속 보충 속도의 변동이 더욱 뚜렷해지고 용융 풀 형태의 준안정성이 악화됩니다.

전체적으로 Mo의 PBF-LB 공정에서 레이저 에너지 전도 효과는 낮다(20~40%). 용융 풀 형상의 준안정성에 영향을 미치는 주요 요인은 레이저 에너지 전도 효과보다는 스캐닝 경로의 단위 길이당 입력되는 에너지의 양입니다.

또한 기판 예열은 용융 풀 크기, 특히 길이를 확대할 수 있을 뿐만 아니라 클래드 금속 표면 형태의 불균일성과 불연속성을 줄이고 불완전한 융합 및 기공 결함을 억제합니다.

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Figure 3. The simulated temperature distribution and single-layer multi-track isothermograms of LPBF Hastelloy X, located at the bottom of the powder bed, are presented for various laser energy densities. (a) depicts the single-point temperature distribution at the bottom of the powder bed, followed by the isothermograms corresponding to laser energy densities of (b) 31 J/mm3 , (c) 43 J/mm3 , (d) 53 J/mm3 , (e) 67 J/mm3 , and (f) 91 J/mm3 .

An integrated multiscale simulation guiding the processing optimisation for additively manufactured nickel-based superalloys

적층 가공된 니켈 기반 초합금의 가공 최적화를 안내하는 통합 멀티스케일 시뮬레이션

Xing He, Bing Yang, Decheng Kong, Kunjie Dai, Xiaoqing Ni, Zhanghua Chen
& Chaofang Dong

ABSTRACT

Microstructural defects in laser powder bed fusion (LPBF) metallic materials are correlated with processing parameters. A multi-physics model and a crystal plasticity framework are employed to predict microstructure growth in molten pools and assess the impact of manufacturing defects on plastic damage parameters. Criteria for optimising the LPBF process are identified, addressing microstructural defects and tensile properties of LPBF Hastelloy X at various volumetric energy densities (VED). The results show that higher VED levels foster a specific Goss texture {110} <001>, with irregular lack of fusion defects significantly affecting plastic damage, especially near the material surface. A critical threshold emerges between manufacturing defects and grain sizes in plastic strain accumulation. The optimal processing window for superior Hastelloy X mechanical properties ranges from 43 to 53 J/mm3 . This work accelerates the development of superior strengthductility alloys via LPBF, streamlining the trial-and-error process and reducing associated costs.

Figure 3. The simulated temperature distribution and single-layer multi-track isothermograms of LPBF Hastelloy X, located at the bottom of the powder bed, are presented for various laser energy densities. (a) depicts the single-point temperature distribution at the bottom of the powder bed, followed by the isothermograms corresponding to laser energy densities of (b) 31 J/mm3 , (c) 43 J/mm3 , (d) 53 J/mm3 , (e) 67 J/mm3 , and (f) 91 J/mm3 .
Figure 3. The simulated temperature distribution and single-layer multi-track isothermograms of LPBF Hastelloy X, located at the bottom of the powder bed, are presented for various laser energy densities. (a) depicts the single-point temperature distribution at the bottom of the powder bed, followed by the isothermograms corresponding to laser energy densities of (b) 31 J/mm3 , (c) 43 J/mm3 , (d) 53 J/mm3 , (e) 67 J/mm3 , and (f) 91 J/mm3 .

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Lab-on-a-Chip 시스템의 혈류 역학에 대한 검토: 엔지니어링 관점

Review on Blood Flow Dynamics in Lab-on-a-Chip Systems: An Engineering Perspective

  • Bin-Jie Lai
  • Li-Tao Zhu
  • Zhe Chen*
  • Bo Ouyang*
  • , and 
  • Zheng-Hong Luo*

Abstract

다양한 수송 메커니즘 하에서, “LOC(lab-on-a-chip)” 시스템에서 유동 전단 속도 조건과 밀접한 관련이 있는 혈류 역학은 다양한 수송 현상을 초래하는 것으로 밝혀졌습니다.

본 연구는 적혈구의 동적 혈액 점도 및 탄성 거동과 같은 점탄성 특성의 역할을 통해 LOC 시스템의 혈류 패턴을 조사합니다. 모세관 및 전기삼투압의 주요 매개변수를 통해 LOC 시스템의 혈액 수송 현상에 대한 연구는 실험적, 이론적 및 수많은 수치적 접근 방식을 통해 제공됩니다.

전기 삼투압 점탄성 흐름에 의해 유발되는 교란은 특히 향후 연구 기회를 위해 혈액 및 기타 점탄성 유체를 취급하는 LOC 장치의 혼합 및 분리 기능 향상에 논의되고 적용됩니다. 또한, 본 연구는 보다 정확하고 단순화된 혈류 모델에 대한 요구와 전기역학 효과 하에서 점탄성 유체 흐름에 대한 수치 연구에 대한 강조와 같은 LOC 시스템 하에서 혈류 역학의 수치 모델링의 문제를 식별합니다.

전기역학 현상을 연구하는 동안 제타 전위 조건에 대한 보다 실용적인 가정도 강조됩니다. 본 연구는 모세관 및 전기삼투압에 의해 구동되는 미세유체 시스템의 혈류 역학에 대한 포괄적이고 학제적인 관점을 제공하는 것을 목표로 한다.

KEYWORDS: 

1. Introduction

1.1. Microfluidic Flow in Lab-on-a-Chip (LOC) Systems

Over the past several decades, the ability to control and utilize fluid flow patterns at microscales has gained considerable interest across a myriad of scientific and engineering disciplines, leading to growing interest in scientific research of microfluidics. 

(1) Microfluidics, an interdisciplinary field that straddles physics, engineering, and biotechnology, is dedicated to the behavior, precise control, and manipulation of fluids geometrically constrained to a small, typically submillimeter, scale. 

(2) The engineering community has increasingly focused on microfluidics, exploring different driving forces to enhance working fluid transport, with the aim of accurately and efficiently describing, controlling, designing, and applying microfluidic flow principles and transport phenomena, particularly for miniaturized applications. 

(3) This attention has chiefly been fueled by the potential to revolutionize diagnostic and therapeutic techniques in the biomedical and pharmaceutical sectorsUnder various driving forces in microfluidic flows, intriguing transport phenomena have bolstered confidence in sustainable and efficient applications in fields such as pharmaceutical, biochemical, and environmental science. The “lab-on-a-chip” (LOC) system harnesses microfluidic flow to enable fluid processing and the execution of laboratory tasks on a chip-sized scale. LOC systems have played a vital role in the miniaturization of laboratory operations such as mixing, chemical reaction, separation, flow control, and detection on small devices, where a wide variety of fluids is adapted. Biological fluid flow like blood and other viscoelastic fluids are notably studied among the many working fluids commonly utilized by LOC systems, owing to the optimization in small fluid sample volumed, rapid response times, precise control, and easy manipulation of flow patterns offered by the system under various driving forces. 

(4)The driving forces in blood flow can be categorized as passive or active transport mechanisms and, in some cases, both. Under various transport mechanisms, the unique design of microchannels enables different functionalities in driving, mixing, separating, and diagnosing blood and drug delivery in the blood. 

(5) Understanding and manipulating these driving forces are crucial for optimizing the performance of a LOC system. Such knowledge presents the opportunity to achieve higher efficiency and reliability in addressing cellular level challenges in medical diagnostics, forensic studies, cancer detection, and other fundamental research areas, for applications of point-of-care (POC) devices. 

(6)

1.2. Engineering Approach of Microfluidic Transport Phenomena in LOC Systems

Different transport mechanisms exhibit unique properties at submillimeter length scales in microfluidic devices, leading to significant transport phenomena that differ from those of macroscale flows. An in-depth understanding of these unique transport phenomena under microfluidic systems is often required in fluidic mechanics to fully harness the potential functionality of a LOC system to obtain systematically designed and precisely controlled transport of microfluids under their respective driving force. Fluid mechanics is considered a vital component in chemical engineering, enabling the analysis of fluid behaviors in various unit designs, ranging from large-scale reactors to separation units. Transport phenomena in fluid mechanics provide a conceptual framework for analytically and descriptively explaining why and how experimental results and physiological phenomena occur. The Navier–Stokes (N–S) equation, along with other governing equations, is often adapted to accurately describe fluid dynamics by accounting for pressure, surface properties, velocity, and temperature variations over space and time. In addition, limiting factors and nonidealities for these governing equations should be considered to impose corrections for empirical consistency before physical models are assembled for more accurate controls and efficiency. Microfluidic flow systems often deviate from ideal conditions, requiring adjustments to the standard governing equations. These deviations could arise from factors such as viscous effects, surface interactions, and non-Newtonian fluid properties from different microfluid types and geometrical layouts of microchannels. Addressing these nonidealities supports the refining of theoretical models and prediction accuracy for microfluidic flow behaviors.

The analytical calculation of coupled nonlinear governing equations, which describes the material and energy balances of systems under ideal conditions, often requires considerable computational efforts. However, advancements in computation capabilities, cost reduction, and improved accuracy have made numerical simulations using different numerical and modeling methods a powerful tool for effectively solving these complex coupled equations and modeling various transport phenomena. Computational fluid dynamics (CFD) is a numerical technique used to investigate the spatial and temporal distribution of various flow parameters. It serves as a critical approach to provide insights and reasoning for decision-making regarding the optimal designs involving fluid dynamics, even prior to complex physical model prototyping and experimental procedures. The integration of experimental data, theoretical analysis, and reliable numerical simulations from CFD enables systematic variation of analytical parameters through quantitative analysis, where adjustment to delivery of blood flow and other working fluids in LOC systems can be achieved.

Numerical methods such as the Finite-Difference Method (FDM), Finite-Element-Method (FEM), and Finite-Volume Method (FVM) are heavily employed in CFD and offer diverse approaches to achieve discretization of Eulerian flow equations through filling a mesh of the flow domain. A more in-depth review of numerical methods in CFD and its application for blood flow simulation is provided in Section 2.2.2.

1.3. Scope of the Review

In this Review, we explore and characterize the blood flow phenomena within the LOC systems, utilizing both physiological and engineering modeling approaches. Similar approaches will be taken to discuss capillary-driven flow and electric-osmotic flow (EOF) under electrokinetic phenomena as a passive and active transport scheme, respectively, for blood transport in LOC systems. Such an analysis aims to bridge the gap between physical (experimental) and engineering (analytical) perspectives in studying and manipulating blood flow delivery by different driving forces in LOC systems. Moreover, the Review hopes to benefit the interests of not only blood flow control in LOC devices but also the transport of viscoelastic fluids, which are less studied in the literature compared to that of Newtonian fluids, in LOC systems.

Section 2 examines the complex interplay between viscoelastic properties of blood and blood flow patterns under shear flow in LOC systems, while engineering numerical modeling approaches for blood flow are presented for assistance. Sections 3 and 4 look into the theoretical principles, numerical governing equations, and modeling methodologies for capillary driven flow and EOF in LOC systems as well as their impact on blood flow dynamics through the quantification of key parameters of the two driving forces. Section 5 concludes the characterized blood flow transport processes in LOC systems under these two forces. Additionally, prospective areas of research in improving the functionality of LOC devices employing blood and other viscoelastic fluids and potentially justifying mechanisms underlying microfluidic flow patterns outside of LOC systems are presented. Finally, the challenges encountered in the numerical studies of blood flow under LOC systems are acknowledged, paving the way for further research.

2. Blood Flow Phenomena

ARTICLE SECTIONS

Jump To


2.1. Physiological Blood Flow Behavior

Blood, an essential physiological fluid in the human body, serves the vital role of transporting oxygen and nutrients throughout the body. Additionally, blood is responsible for suspending various blood cells including erythrocytes (red blood cells or RBCs), leukocytes (white blood cells), and thrombocytes (blood platelets) in a plasma medium.Among the cells mentioned above, red blood cells (RBCs) comprise approximately 40–45% of the volume of healthy blood. 

(7) An RBC possesses an inherent elastic property with a biconcave shape of an average diameter of 8 μm and a thickness of 2 μm. This biconcave shape maximizes the surface-to-volume ratio, allowing RBCs to endure significant distortion while maintaining their functionality. 

(8,9) Additionally, the biconcave shape optimizes gas exchange, facilitating efficient uptake of oxygen due to the increased surface area. The inherent elasticity of RBCs allows them to undergo substantial distortion from their original biconcave shape and exhibits high flexibility, particularly in narrow channels.RBC deformability enables the cell to deform from a biconcave shape to a parachute-like configuration, despite minor differences in RBC shape dynamics under shear flow between initial cell locations. As shown in Figure 1(a), RBCs initiating with different resting shapes and orientations displaying display a similar deformation pattern 

(10) in terms of its shape. Shear flow induces an inward bending of the cell at the rear position of the rim to the final bending position, 

(11) resulting in an alignment toward the same position of the flow direction.

Figure 1. Images of varying deformation of RBCs and different dynamic blood flow behaviors. (a) The deforming shape behavior of RBCs at four different initiating positions under the same experimental conditions of a flow from left to right, (10) (b) RBC aggregation, (13) (c) CFL region. (18) Reproduced with permission from ref (10). Copyright 2011 Elsevier. Reproduced with permission from ref (13). Copyright 2022 The Authors, under the terms of the Creative Commons (CC BY 4.0) License https://creativecommons.org/licenses/by/4.0/. Reproduced with permission from ref (18). Copyright 2019 Elsevier.

The flexible property of RBCs enables them to navigate through narrow capillaries and traverse a complex network of blood vessels. The deformability of RBCs depends on various factors, including the channel geometry, RBC concentration, and the elastic properties of the RBC membrane. 

(12) Both flexibility and deformability are vital in the process of oxygen exchange among blood and tissues throughout the body, allowing cells to flow in vessels even smaller than the original cell size prior to deforming.As RBCs serve as major components in blood, their collective dynamics also hugely affect blood rheology. RBCs exhibit an aggregation phenomenon due to cell to cell interactions, such as adhesion forces, among populated cells, inducing unique blood flow patterns and rheological behaviors in microfluidic systems. For blood flow in large vessels between a diameter of 1 and 3 cm, where shear rates are not high, a constant viscosity and Newtonian behavior for blood can be assumed. However, under low shear rate conditions (0.1 s

–1) in smaller vessels such as the arteries and venules, which are within a diameter of 0.2 mm to 1 cm, blood exhibits non-Newtonian properties, such as shear-thinning viscosity and viscoelasticity due to RBC aggregation and deformability. The nonlinear viscoelastic property of blood gives rise to a complex relationship between viscosity and shear rate, primarily influenced by the highly elastic behavior of RBCs. A wide range of research on the transient behavior of the RBC shape and aggregation characteristics under varied flow circumstances has been conducted, aiming to obtain a better understanding of the interaction between blood flow shear forces from confined flows.

For a better understanding of the unique blood flow structures and rheological behaviors in microfluidic systems, some blood flow patterns are introduced in the following section.

2.1.1. RBC Aggregation

RBC aggregation is a vital phenomenon to be considered when designing LOC devices due to its impact on the viscosity of the bulk flow. Under conditions of low shear rate, such as in stagnant or low flow rate regions, RBCs tend to aggregate, forming structures known as rouleaux, resembling stacks of coins as shown in Figure 1(b). 

(13) The aggregation of RBCs increases the viscosity at the aggregated region, 

(14) hence slowing down the overall blood flow. However, when exposed to high shear rates, RBC aggregates disaggregate. As shear rates continue to increase, RBCs tend to deform, elongating and aligning themselves with the direction of the flow. 

(15) Such a dynamic shift in behavior from the cells in response to the shear rate forms the basis of the viscoelastic properties observed in whole blood. In essence, the viscosity of the blood varies according to the shear rate conditions, which are related to the velocity gradient of the system. It is significant to take the intricate relationship between shear rate conditions and the change of blood viscosity due to RBC aggregation into account since various flow driving conditions may induce varied effects on the degree of aggregation.

2.1.2. Fåhræus-Lindqvist Effect

The Fåhræus–Lindqvist (FL) effect describes the gradual decrease in the apparent viscosity of blood as the channel diameter decreases. 

(16) This effect is attributed to the migration of RBCs toward the central region in the microchannel, where the flow rate is higher, due to the presence of higher pressure and asymmetric distribution of shear forces. This migration of RBCs, typically observed at blood vessels less than 0.3 mm, toward the higher flow rate region contributes to the change in blood viscosity, which becomes dependent on the channel size. Simultaneously, the increase of the RBC concentration in the central region of the microchannel results in the formation of a less viscous region close to the microchannel wall. This region called the Cell-Free Layer (CFL), is primarily composed of plasma. 

(17) The combination of the FL effect and the following CFL formation provides a unique phenomenon that is often utilized in passive and active plasma separation mechanisms, involving branched and constriction channels for various applications in plasma separation using microfluidic systems.

2.1.3. Cell-Free Layer Formation

In microfluidic blood flow, RBCs form aggregates at the microchannel core and result in a region that is mostly devoid of RBCs near the microchannel walls, as shown in Figure 1(c). 

(18) The region is known as the cell-free layer (CFL). The CFL region is often known to possess a lower viscosity compared to other regions within the blood flow due to the lower viscosity value of plasma when compared to that of the aggregated RBCs. Therefore, a thicker CFL region composed of plasma correlates to a reduced apparent whole blood viscosity. 

(19) A thicker CFL region is often established following the RBC aggregation at the microchannel core under conditions of decreasing the tube diameter. Apart from the dependence on the RBC concentration in the microchannel core, the CFL thickness is also affected by the volume concentration of RBCs, or hematocrit, in whole blood, as well as the deformability of RBCs. Given the influence CFL thickness has on blood flow rheological parameters such as blood flow rate, which is strongly dependent on whole blood viscosity, investigating CFL thickness under shear flow is crucial for LOC systems accounting for blood flow.

2.1.4. Plasma Skimming in Bifurcation Networks

The uneven arrangement of RBCs in bifurcating microchannels, commonly termed skimming bifurcation, arises from the axial migration of RBCs within flowing streams. This uneven distribution contributes to variations in viscosity across differing sizes of bifurcating channels but offers a stabilizing effect. Notably, higher flow rates in microchannels are associated with increased hematocrit levels, resulting in higher viscosity compared with those with lower flow rates. Parametric investigations on bifurcation angle, 

(20) thickness of the CFL, 

(21) and RBC dynamics, including aggregation and deformation, 

(22) may alter the varying viscosity of blood and its flow behavior within microchannels.

2.2. Modeling on Blood Flow Dynamics

2.2.1. Blood Properties and Mathematical Models of Blood Rheology

Under different shear rate conditions in blood flow, the elastic characteristics and dynamic changes of the RBC induce a complex velocity and stress relationship, resulting in the incompatibility of blood flow characterization through standard presumptions of constant viscosity used for Newtonian fluid flow. Blood flow is categorized as a viscoelastic non-Newtonian fluid flow where constitutive equations governing this type of flow take into consideration the nonlinear viscometric properties of blood. To mathematically characterize the evolving blood viscosity and the relationship between the elasticity of RBC and the shear blood flow, respectively, across space and time of the system, a stress tensor (τ) defined by constitutive models is often coupled in the Navier–Stokes equation to account for the collective impact of the constant dynamic viscosity (η) and the elasticity from RBCs on blood flow.The dynamic viscosity of blood is heavily dependent on the shear stress applied to the cell and various parameters from the blood such as hematocrit value, plasma viscosity, mechanical properties of the RBC membrane, and red blood cell aggregation rate. The apparent blood viscosity is considered convenient for the characterization of the relationship between the evolving blood viscosity and shear rate, which can be defined by Casson’s law, as shown in eq 1.

𝜇=𝜏0𝛾˙+2𝜂𝜏0𝛾˙⎯⎯⎯⎯⎯⎯⎯√+𝜂�=�0�˙+2��0�˙+�

(1)where τ

0 is the yield stress–stress required to initiate blood flow motion, η is the Casson rheological constant, and γ̇ is the shear rate. The value of Casson’s law parameters under blood with normal hematocrit level can be defined as τ

0 = 0.0056 Pa and η = 0.0035 Pa·s. 

(23) With the known property of blood and Casson’s law parameters, an approximation can be made to the dynamic viscosity under various flow condition domains. The Power Law model is often employed to characterize the dynamic viscosity in relation to the shear rate, since precise solutions exist for specific geometries and flow circumstances, acting as a fundamental standard for definition. The Carreau and Carreau–Yasuda models can be advantageous over the Power Law model due to their ability to evaluate the dynamic viscosity at low to zero shear rate conditions. However, none of the above-mentioned models consider the memory or other elastic behavior of blood and its RBCs. Some other commonly used mathematical models and their constants for the non-Newtonian viscosity property characterization of blood are listed in Table 1 below. 

(24−26)Table 1. Comparison of Various Non-Newtonian Models for Blood Viscosity 

(24−26)

ModelNon-Newtonian ViscosityParameters
Power Law(2)n = 0.61, k = 0.42
Carreau(3)μ0 = 0.056 Pa·s, μ = 0.00345 Pa·s, λ = 3.1736 s, m = 2.406, a = 0.254
Walburn–Schneck(4)C1 = 0.000797 Pa·s, C2 = 0.0608 Pa·s, C3 = 0.00499, C4 = 14.585 g–1, TPMA = 25 g/L
Carreau–Yasuda(5)μ0 = 0.056 Pa·s, μ = 0.00345 Pa·s, λ = 1.902 s, n = 0.22, a = 1.25
Quemada(6)μp = 0.0012 Pa·s, k = 2.07, k0 = 4.33, γ̇c = 1.88 s–1

The blood rheology is commonly known to be influenced by two key physiological factors, namely, the hematocrit value (H

t) and the fibrinogen concentration (c

f), with an average value of 42% and 0.252 gd·L

–1, respectively. Particularly in low shear conditions, the presence of varying fibrinogen concentrations affects the tendency for aggregation and rouleaux formation, while the occurrence of aggregation is contingent upon specific levels of hematocrit. 

(27) The study from Apostolidis et al. 

(28) modifies the Casson model through emphasizing its reliance on hematocrit and fibrinogen concentration parameter values, owing to the extensive knowledge of the two physiological blood parameters.The viscoelastic response of blood is heavily dependent on the elasticity of the RBC, which is defined by the relationship between the deformation and stress relaxation from RBCs under a specific location of shear flow as a function of the velocity field. The stress tensor is usually characterized by constitutive equations such as the Upper-Convected Maxwell Model 

(29) and the Oldroyd-B model 

(30) to track the molecule effects under shear from different driving forces. The prominent non-Newtonian features, such as shear thinning and yield stress, have played a vital role in the characterization of blood rheology, particularly with respect to the evaluation of yield stress under low shear conditions. The nature of stress measurement in blood, typically on the order of 1 mPa, is challenging due to its low magnitude. The occurrence of the CFL complicates the measurement further due to the significant decrease in apparent viscosity near the wall over time and a consequential disparity in viscosity compared to the bulk region.In addition to shear thinning viscosity and yield stress, the formation of aggregation (rouleaux) from RBCs under low shear rates also contributes to the viscoelasticity under transient flow 

(31) and thixotropy 

(32) of whole blood. Given the difficulty in evaluating viscoelastic behavior of blood under low strain magnitudes and limitations in generalized Newtonian models, the utilization of viscoelastic models is advocated to encompass elasticity and delineate non-shear components within the stress tensor. Extending from the Oldroyd-B model, Anand et al. 

(33) developed a viscoelastic model framework for adapting elasticity within blood samples and predicting non-shear stress components. However, to also address the thixotropic effects, the model developed by Horner et al. 

(34) serves as a more comprehensive approach than the viscoelastic model from Anand et al. Thixotropy 

(32) typically occurs from the structural change of the rouleaux, where low shear rate conditions induce rouleaux formation. Correspondingly, elasticity increases, while elasticity is more representative of the isolated RBCs, under high shear rate conditions. The model of Horner et al. 

(34) considers the contribution of rouleaux to shear stress, taking into account factors such as the characteristic time for Brownian aggregation, shear-induced aggregation, and shear-induced breakage. Subsequent advancements in the model from Horner et al. often revolve around refining the three aforementioned key terms for a more substantial characterization of rouleaux dynamics. Notably, this has led to the recently developed mHAWB model 

(35) and other model iterations to enhance the accuracy of elastic and viscoelastic contributions to blood rheology, including the recently improved model suggested by Armstrong et al. 

(36)

2.2.2. Numerical Methods (FDM, FEM, FVM)

Numerical simulation has become increasingly more significant in analyzing the geometry, boundary layers of flow, and nonlinearity of hyperbolic viscoelastic flow constitutive equations. CFD is a powerful and efficient tool utilizing numerical methods to solve the governing hydrodynamic equations, such as the Navier–Stokes (N–S) equation, continuity equation, and energy conservation equation, for qualitative evaluation of fluid motion dynamics under different parameters. CFD overcomes the challenge of analytically solving nonlinear forms of differential equations by employing numerical methods such as the Finite-Difference Method (FDM), Finite-Element Method (FEM), and Finite-Volume Method (FVM) to discretize and solve the partial differential equations (PDEs), allowing for qualitative reproduction of transport phenomena and experimental observations. Different numerical methods are chosen to cope with various transport systems for optimization of the accuracy of the result and control of error during the discretization process.FDM is a straightforward approach to discretizing PDEs, replacing the continuum representation of equations with a set of finite-difference equations, which is typically applied to structured grids for efficient implementation in CFD programs. 

(37) However, FDM is often limited to simple geometries such as rectangular or block-shaped geometries and struggles with curved boundaries. In contrast, FEM divides the fluid domain into small finite grids or elements, approximating PDEs through a local description of physics. 

(38) All elements contribute to a large, sparse matrix solver. However, FEM may not always provide accurate results for systems involving significant deformation and aggregation of particles like RBCs due to large distortion of grids. 

(39) FVM evaluates PDEs following the conservation laws and discretizes the selected flow domain into small but finite size control volumes, with each grid at the center of a finite volume. 

(40) The divergence theorem allows the conversion of volume integrals of PDEs with divergence terms into surface integrals of surface fluxes across cell boundaries. Due to its conservation property, FVM offers efficient outcomes when dealing with PDEs that embody mass, momentum, and energy conservation principles. Furthermore, widely accessible software packages like the OpenFOAM toolbox 

(41) include a viscoelastic solver, making it an attractive option for viscoelastic fluid flow modeling. 

(42)

2.2.3. Modeling Methods of Blood Flow Dynamics

The complexity in the blood flow simulation arises from deformability and aggregation that RBCs exhibit during their interaction with neighboring cells under different shear rate conditions induced by blood flow. Numerical models coupled with simulation programs have been applied as a groundbreaking method to predict such unique rheological behavior exhibited by RBCs and whole blood. The conventional approach of a single-phase flow simulation is often applied to blood flow simulations within large vessels possessing a moderate shear rate. However, such a method assumes the properties of plasma, RBCs and other cellular components to be evenly distributed as average density and viscosity in blood, resulting in the inability to simulate the mechanical dynamics, such as RBC aggregation under high-shear flow field, inherent in RBCs. To accurately describe the asymmetric distribution of RBC and blood flow, multiphase flow simulation, where numerical simulations of blood flows are often modeled as two immiscible phases, RBCs and blood plasma, is proposed. A common assumption is that RBCs exhibit non-Newtonian behavior while the plasma is treated as a continuous Newtonian phase.Numerous multiphase numerical models have been proposed to simulate the influence of RBCs on blood flow dynamics by different assumptions. In large-scale simulations (above the millimeter range), continuum-based methods are wildly used due to their lower computational demands. 

(43) Eulerian multiphase flow simulations offer the solution of a set of conservation equations for each separate phase and couple the phases through common pressure and interphase exchange coefficients. Xu et al. 

(44) utilized the combined finite-discrete element method (FDEM) to replicate the dynamic behavior and distortion of RBCs subjected to fluidic forces, utilizing the Johnson–Kendall–Roberts model 

(45) to define the adhesive forces of cell-to-cell interactions. The iterative direct-forcing immersed boundary method (IBM) is commonly employed in simulations of the fluid–cell interface of blood. This method effectively captures the intricacies of the thin and flexible RBC membranes within various external flow fields. 

(46) The study by Xu et al. 

(44) also adopts this approach to bridge the fluid dynamics and RBC deformation through IBM. Yoon and You utilized the Maxwell model to define the viscosity of the RBC membrane. 

(47) It was discovered that the Maxwell model could represent the stress relaxation and unloading processes of the cell. Furthermore, the reduced flexibility of an RBC under particular situations such as infection is specified, which was unattainable by the Kelvin–Voigt model 

(48) when compared to the Maxwell model in the literature. The Yeoh hyperplastic material model was also adapted to predict the nonlinear elasticity property of RBCs with FEM employed to discretize the RBC membrane using shell-type elements. Gracka et al. 

(49) developed a numerical CFD model with a finite-volume parallel solver for multiphase blood flow simulation, where an updated Maxwell viscoelasticity model and a Discrete Phase Model are adopted. In the study, the adapted IBM, based on unstructured grids, simulates the flow behavior and shape change of the RBCs through fluid-structure coupling. It was found that the hybrid Euler–Lagrange (E–L) approach 

(50) for the development of the multiphase model offered better results in the simulated CFL region in the microchannels.To study the dynamics of individual behaviors of RBCs and the consequent non-Newtonian blood flow, cell-shape-resolved computational models are often adapted. The use of the boundary integral method has become prevalent in minimizing computational expenses, particularly in the exclusive determination of fluid velocity on the surfaces of RBCs, incorporating the option of employing IBM or particle-based techniques. The cell-shaped-resolved method has enabled an examination of cell to cell interactions within complex ambient or pulsatile flow conditions 

(51) surrounding RBC membranes. Recently, Rydquist et al. 

(52) have looked to integrate statistical information from macroscale simulations to obtain a comprehensive overview of RBC behavior within the immediate proximity of the flow through introduction of respective models characterizing membrane shape definition, tension, bending stresses of RBC membranes.At a macroscopic scale, continuum models have conventionally been adapted for assessing blood flow dynamics through the application of elasticity theory and fluid dynamics. However, particle-based methods are known for their simplicity and adaptability in modeling complex multiscale fluid structures. Meshless methods, such as the boundary element method (BEM), smoothed particle hydrodynamics (SPH), and dissipative particle dynamics (DPD), are often used in particle-based characterization of RBCs and the surrounding fluid. By representing the fluid as discrete particles, meshless methods provide insights into the status and movement of the multiphase fluid. These methods allow for the investigation of cellular structures and microscopic interactions that affect blood rheology. Non-confronting mesh methods like IBM can also be used to couple a fluid solver such as FEM, FVM, or the Lattice Boltzmann Method (LBM) through membrane representation of RBCs. In comparison to conventional CFD methods, LBM has been viewed as a favorable numerical approach for solving the N–S equations and the simulation of multiphase flows. LBM exhibits the notable advantage of being amenable to high-performance parallel computing environments due to its inherently local dynamics. In contrast to DPD and SPH where RBC membranes are modeled as physically interconnected particles, LBM employs the IBM to account for the deformation dynamics of RBCs 

(53,54) under shear flows in complex channel geometries. 

(54,55) However, it is essential to acknowledge that the utilization of LBM in simulating RBC flows often entails a significant computational overhead, being a primary challenge in this context. Krüger et al. 

(56) proposed utilizing LBM as a fluid solver, IBM to couple the fluid and FEM to compute the response of membranes to deformation under immersed fluids. This approach decouples the fluid and membranes but necessitates significant computational effort due to the requirements of both meshes and particles.Despite the accuracy of current blood flow models, simulating complex conditions remains challenging because of the high computational load and cost. Balachandran Nair et al. 

(57) suggested a reduced order model of RBC under the framework of DEM, where the RBC is represented by overlapping constituent rigid spheres. The Morse potential force is adapted to account for the RBC aggregation exhibited by cell to cell interactions among RBCs at different distances. Based upon the IBM, the reduced-order RBC model is adapted to simulate blood flow transport for validation under both single and multiple RBCs with a resolved CFD-DEM solver. 

(58) In the resolved CFD-DEM model, particle sizes are larger than the grid size for a more accurate computation of the surrounding flow field. A continuous forcing approach is taken to describe the momentum source of the governing equation prior to discretization, which is different from a Direct Forcing Method (DFM). 

(59) As no body-conforming moving mesh is required, the continuous forcing approach offers lower complexity and reduced cost when compared to the DFM. Piquet et al. 

(60) highlighted the high complexity of the DFM due to its reliance on calculating an additional immersed boundary flux for the velocity field to ensure its divergence-free condition.The fluid–structure interaction (FSI) method has been advocated to connect the dynamic interplay of RBC membranes and fluid plasma within blood flow such as the coupling of continuum–particle interactions. However, such methodology is generally adapted for anatomical configurations such as arteries 

(61,62) and capillaries, 

(63) where both the structural components and the fluid domain undergo substantial deformation due to the moving boundaries. Due to the scope of the Review being blood flow simulation within microchannels of LOC devices without deformable boundaries, the Review of the FSI method will not be further carried out.In general, three numerical methods are broadly used: mesh-based, particle-based, and hybrid mesh–particle techniques, based on the spatial scale and the fundamental numerical approach, mesh-based methods tend to neglect the effects of individual particles, assuming a continuum and being efficient in terms of time and cost. However, the particle-based approach highlights more of the microscopic and mesoscopic level, where the influence of individual RBCs is considered. A review from Freund et al. 

(64) addressed the three numerical methodologies and their respective modeling approaches of RBC dynamics. Given the complex mechanics and the diverse levels of study concerning numerical simulations of blood and cellular flow, a broad spectrum of numerical methods for blood has been subjected to extensive review. 

(64−70) Ye at al. 

(65) offered an extensive review of the application of the DPD, SPH, and LBM for numerical simulations of RBC, while Rathnayaka et al. 

(67) conducted a review of the particle-based numerical modeling for liquid marbles through drawing parallels to the transport of RBCs in microchannels. A comparative analysis between conventional CFD methods and particle-based approaches for cellular and blood flow dynamic simulation can be found under the review by Arabghahestani et al. 

(66) Literature by Li et al. 

(68) and Beris et al. 

(69) offer an overview of both continuum-based models at micro/macroscales and multiscale particle-based models encompassing various length and temporal dimensions. Furthermore, these reviews deliberate upon the potential of coupling continuum-particle methods for blood plasma and RBC modeling. Arciero et al. 

(70) investigated various modeling approaches encompassing cellular interactions, such as cell to cell or plasma interactions and the individual cellular phases. A concise overview of the reviews is provided in Table 2 for reference.

Table 2. List of Reviews for Numerical Approaches Employed in Blood Flow Simulation

ReferenceNumerical methods
Li et al. (2013) (68)Continuum-based modeling (BIM), particle-based modeling (LBM, LB-FE, SPH, DPD)
Freund (2014) (64)RBC dynamic modeling (continuum-based modeling, complementary discrete microstructure modeling), blood flow dynamic modeling (FDM, IBM, LBM, particle-mesh methods, coupled boundary integral and mesh-based methods, DPD)
Ye et al. (2016) (65)DPD, SPH, LBM, coupled IBM-Smoothed DPD
Arciero et al. (2017) (70)LBM, IBM, DPD, conventional CFD Methods (FDM, FVM, FEM)
Arabghahestani et al. (2019) (66)Particle-based methods (LBM, DPD, direct simulation Monte Carlo, molecular dynamics), SPH, conventional CFD methods (FDM, FVM, FEM)
Beris et al. (2021) (69)DPD, smoothed DPD, IBM, LBM, BIM
Rathnayaka (2022) (67)SPH, CG, LBM

3. Capillary Driven Blood Flow in LOC Systems

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3.1. Capillary Driven Flow Phenomena

Capillary driven (CD) flow is a pivotal mechanism in passive microfluidic flow systems 

(9) such as the blood circulation system and LOC systems. 

(71) CD flow is essentially the movement of a liquid to flow against drag forces, where the capillary effect exerts a force on the liquid at the borders, causing a liquid–air meniscus to flow despite gravity or other drag forces. A capillary pressure drops across the liquid–air interface with surface tension in the capillary radius and contact angle. The capillary effect depends heavily on the interaction between the different properties of surface materials. Different values of contact angles can be manipulated and obtained under varying levels of surface wettability treatments to manipulate the surface properties, resulting in different CD blood delivery rates for medical diagnostic device microchannels. CD flow techniques are appealing for many LOC devices, because they require no external energy. However, due to the passive property of liquid propulsion by capillary forces and the long-term instability of surface treatments on channel walls, the adaptability of CD flow in geometrically complex LOC devices may be limited.

3.2. Theoretical and Numerical Modeling of Capillary Driven Blood Flow

3.2.1. Theoretical Basis and Assumptions of Microfluidic Flow

The study of transport phenomena regarding either blood flow driven by capillary forces or externally applied forces under microfluid systems all demands a comprehensive recognition of the significant differences in flow dynamics between microscale and macroscale. The fundamental assumptions and principles behind fluid transport at the microscale are discussed in this section. Such a comprehension will lay the groundwork for the following analysis of the theoretical basis of capillary forces and their role in blood transport in LOC systems.

At the macroscale, fluid dynamics are often strongly influenced by gravity due to considerable fluid mass. However, the high surface to volume ratio at the microscale shifts the balance toward surface forces (e.g., surface tension and viscous forces), much larger than the inertial force. This difference gives rise to transport phenomena unique to microscale fluid transport, such as the prevalence of laminar flow due to a very low Reynolds number (generally lower than 1). Moreover, the fluid in a microfluidic system is often assumed to be incompressible due to the small flow velocity, indicating constant fluid density in both space and time.Microfluidic flow behaviors are governed by the fundamental principles of mass and momentum conservation, which are encapsulated in the continuity equation and the Navier–Stokes (N–S) equation. The continuity equation describes the conservation of mass, while the N–S equation captures the spatial and temporal variations in velocity, pressure, and other physical parameters. Under the assumption of the negligible influence of gravity in microfluidic systems, the continuity equation and the Eulerian representation of the incompressible N–S equation can be expressed as follows:

∇·𝐮⇀=0∇·�⇀=0

(7)

−∇𝑝+𝜇∇2𝐮⇀+∇·𝝉⇀−𝐅⇀=0−∇�+�∇2�⇀+∇·�⇀−�⇀=0

(8)Here, p is the pressure, u is the fluid viscosity, 

𝝉⇀�⇀ represents the stress tensor, and F is the body force exerted by external forces if present.

3.2.2. Theoretical Basis and Modeling of Capillary Force in LOC Systems

The capillary force is often the major driving force to manipulate and transport blood without an externally applied force in LOC systems. Forces induced by the capillary effect impact the free surface of fluids and are represented not directly in the Navier–Stokes equations but through the pressure boundary conditions of the pressure term p. For hydrophilic surfaces, the liquid generally induces a contact angle between 0° and 30°, encouraging the spread and attraction of fluid under a positive cos θ condition. For this condition, the pressure drop becomes positive and generates a spontaneous flow forward. A hydrophobic solid surface repels the fluid, inducing minimal contact. Generally, hydrophobic solids exhibit a contact angle larger than 90°, inducing a negative value of cos θ. Such a value will result in a negative pressure drop and a flow in the opposite direction. The induced contact angle is often utilized to measure the wall exposure of various surface treatments on channel walls where different wettability gradients and surface tension effects for CD flows are established. Contact angles between different interfaces are obtainable through standard values or experimental methods for reference. 

(72)For the characterization of the induced force by the capillary effect, the Young–Laplace (Y–L) equation 

(73) is widely employed. In the equation, the capillary is considered a pressure boundary condition between the two interphases. Through the Y–L equation, the capillary pressure force can be determined, and subsequently, the continuity and momentum balance equations can be solved to obtain the blood filling rate. Kim et al. 

(74) studied the effects of concentration and exposure time of a nonionic surfactant, Silwet L-77, on the performance of a polydimethylsiloxane (PDMS) microchannel in terms of plasma and blood self-separation. The study characterized the capillary pressure force by incorporating the Y–L equation and further evaluated the effects of the changing contact angle due to different levels of applied channel wall surface treatments. The expression of the Y–L equation utilized by Kim et al. 

(74) is as follows:

𝑃=−𝜎(cos𝜃b+cos𝜃tℎ+cos𝜃l+cos𝜃r𝑤)�=−�(cos⁡�b+cos⁡�tℎ+cos⁡�l+cos⁡�r�)

(9)where σ is the surface tension of the liquid and θ

bθ

tθ

l, and θ

r are the contact angle values between the liquid and the bottom, top, left, and right walls, respectively. A numerical simulation through Coventor software is performed to evaluate the dynamic changes in the filling rate within the microchannel. The simulation results for the blood filling rate in the microchannel are expressed at a specific time stamp, shown in Figure 2. The results portray an increasing instantaneous filling rate of blood in the microchannel following the decrease in contact angle induced by a higher concentration of the nonionic surfactant treated to the microchannel wall.

Figure 2. Numerical simulation of filling rate of capillary driven blood flow under various contact angle conditions at a specific timestamp. (74) Reproduced with permission from ref (74). Copyright 2010 Elsevier.

When in contact with hydrophilic or hydrophobic surfaces, blood forms a meniscus with a contact angle due to surface tension. The Lucas–Washburn (L–W) equation 

(75) is one of the pioneering theoretical definitions for the position of the meniscus over time. In addition, the L–W equation provides the possibility for research to obtain the velocity of the blood formed meniscus through the derivation of the meniscus position. The L–W equation 

(75) can be shown below:

𝐿(𝑡)=𝑅𝜎cos(𝜃)𝑡2𝜇⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯√�(�)=��⁡cos(�)�2�

(10)Here L(t) represents the distance of the liquid driven by the capillary forces. However, the generalized L–W equation solely assumes the constant physical properties from a Newtonian fluid rather than considering the non-Newtonian fluid behavior of blood. Cito et al. 

(76) constructed an enhanced version of the L–W equation incorporating the power law to consider the RBC aggregation and the FL effect. The non-Newtonian fluid apparent viscosity under the Power Law model is defined as

𝜇=𝑘·(𝛾˙)𝑛−1�=�·(�˙)�−1

(11)where γ̇ is the strain rate tensor defined as 

𝛾˙=12𝛾˙𝑖𝑗𝛾˙𝑗𝑖⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯√�˙=12�˙���˙��. The stress tensor term τ is computed as τ = μγ̇

ij. The updated L–W equation by Cito 

(76) is expressed as

𝐿(𝑡)=𝑅[(𝑛+13𝑛+1)(𝜎cos(𝜃)𝑅𝑘)1/𝑛𝑡]𝑛/𝑛+1�(�)=�[(�+13�+1)(�⁡cos(�)��)1/��]�/�+1

(12)where k is the flow consistency index and n is the power law index, respectively. The power law index, from the Power Law model, characterizes the extent of the non-Newtonian behavior of blood. Both the consistency and power law index rely on blood properties such as hematocrit, the appearance of the FL effect, the formation of RBC aggregates, etc. The updated L–W equation computes the location and velocity of blood flow caused by capillary forces at specified time points within the LOC devices, taking into account the effects of blood flow characteristics such as RBC aggregation and the FL effect on dynamic blood viscosity.Apart from the blood flow behaviors triggered by inherent blood properties, unique flow conditions driven by capillary forces that are portrayed under different microchannel geometries also hold crucial implications for CD blood delivery. Berthier et al. 

(77) studied the spontaneous Concus–Finn condition, the condition to initiate the spontaneous capillary flow within a V-groove microchannel, as shown in Figure 3(a) both experimentally and numerically. Through experimental studies, the spontaneous Concus–Finn filament development of capillary driven blood flow is observed, as shown in Figure 3(b), while the dynamic development of blood flow is numerically simulated through CFD simulation.

Figure 3. (a) Sketch of the cross-section of Berthier’s V-groove microchannel, (b) experimental view of blood in the V-groove microchannel, (78) (c) illustration of the dynamic change of the extension of filament from FLOW 3D under capillary flow at three increasing time intervals. (78) Reproduced with permission from ref (78). Copyright 2014 Elsevier.

Berthier et al. 

(77) characterized the contact angle needed for the initiation of the capillary driving force at a zero-inlet pressure, through the half-angle (α) of the V-groove geometry layout, and its relation to the Concus–Finn filament as shown below:

𝜃<𝜋2−𝛼sin𝛼1+2(ℎ2/𝑤)sin𝛼<cos𝜃{�<�2−�sin⁡�1+2(ℎ2/�)⁡sin⁡�<cos⁡�

(13)Three possible regimes were concluded based on the contact angle value for the initiation of flow and development of Concus–Finn filament:

𝜃>𝜃1𝜃1>𝜃>𝜃0𝜃0no SCFSCF without a Concus−Finn filamentSCF without a Concus−Finn filament{�>�1no SCF�1>�>�0SCF without a Concus−Finn filament�0SCF without a Concus−Finn filament

(14)Under Newton’s Law, the force balance with low Reynolds and Capillary numbers results in the neglect of inertial terms. The force balance between the capillary forces and the viscous force induced by the channel wall is proposed to derive the analytical fluid velocity. This relation between the two forces offers insights into the average flow velocity and the penetration distance function dependent on time. The apparent blood viscosity is defined by Berthier et al. 

(78) through Casson’s law, 

(23) given in eq 1. The research used the FLOW-3D program from Flow Science Inc. software, which solves transient, free-surface problems using the FDM in multiple dimensions. The Volume of Fluid (VOF) method 

(79) is utilized to locate and track the dynamic extension of filament throughout the advancing interface within the channel ahead of the main flow at three progressing time stamps, as depicted in Figure 3(c).

4. Electro-osmotic Flow (EOF) in LOC Systems

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The utilization of external forces, such as electric fields, has significantly broadened the possibility of manipulating microfluidic flow in LOC systems. 

(80) Externally applied electric field forces induce a fluid flow from the movement of ions in fluid terms as the “electro-osmotic flow” (EOF).Unique transport phenomena, such as enhanced flow velocity and flow instability, induced by non-Newtonian fluids, particularly viscoelastic fluids, under EOF, have sparked considerable interest in microfluidic devices with simple or complicated geometries within channels. 

(81) However, compared to the study of Newtonian fluids and even other electro-osmotic viscoelastic fluid flows, the literature focusing on the theoretical and numerical modeling of electro-osmotic blood flow is limited due to the complexity of blood properties. Consequently, to obtain a more comprehensive understanding of the complex blood flow behavior under EOF, theoretical and numerical studies of the transport phenomena in the EOF section will be based on the studies of different viscoelastic fluids under EOF rather than that of blood specifically. Despite this limitation, we believe these studies offer valuable insights that can help understand the complex behavior of blood flow under EOF.

4.1. EOF Phenomena

Electro-osmotic flow occurs at the interface between the microchannel wall and bulk phase solution. When in contact with the bulk phase, solution ions are absorbed or dissociated at the solid–liquid interface, resulting in the formation of a charge layer, as shown in Figure 4. This charged channel surface wall interacts with both negative and positive ions in the bulk sample, causing repulsion and attraction forces to create a thin layer of immobilized counterions, known as the Stern layer. The induced electric potential from the wall gradually decreases with an increase in the distance from the wall. The Stern layer potential, commonly termed the zeta potential, controls the intensity of the electrostatic interactions between mobile counterions and, consequently, the drag force from the applied electric field. Next to the Stern layer is the diffuse mobile layer, mainly composed of a mobile counterion. These two layers constitute the “electrical double layer” (EDL), the thickness of which is directly proportional to the ionic strength (concentration) of the bulk fluid. The relationship between the two parameters is characterized by a Debye length (λ

D), expressed as

𝜆𝐷=𝜖𝑘B𝑇2(𝑍𝑒)2𝑐0⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯√��=��B�2(��)2�0

(15)where ϵ is the permittivity of the electrolyte solution, k

B is the Boltzmann constant, T is the electron temperature, Z is the integer valence number, e is the elementary charge, and c

0 is the ionic density.

Figure 4. Schematic diagram of an electro-osmotic flow in a microchannel with negative surface charge. (82) Reproduced with permission from ref (82). Copyright 2012 Woodhead Publishing.

When an electric field is applied perpendicular to the EDL, viscous drag is generated due to the movement of excess ions in the EDL. Electro-osmotic forces can be attributed to the externally applied electric potential (ϕ) and the zeta potential, the system wall induced potential by charged walls (ψ). As illustrated in Figure 4, the majority of ions in the bulk phase have a uniform velocity profile, except for a shear rate condition confined within an extremely thin Stern layer. Therefore, EOF displays a unique characteristic of a “near flat” or plug flow velocity profile, different from the parabolic flow typically induced by pressure-driven microfluidic flow (Hagen–Poiseuille flow). The plug-shaped velocity profile of the EOF possesses a high shear rate above the Stern layer.Overall, the EOF velocity magnitude is typically proportional to the Debye Length (λ

D), zeta potential, and magnitude of the externally applied electric field, while a more viscous liquid reduces the EOF velocity.

4.2. Modeling on Electro-osmotic Viscoelastic Fluid Flow

4.2.1. Theoretical Basis of EOF Mechanisms

The EOF of an incompressible viscoelastic fluid is commonly governed by the continuity and incompressible N–S equations, as shown in eqs 7 and 8, where the stress tensor and the electrostatic force term are coupled. The electro-osmotic body force term F, representing the body force exerted by the externally applied electric force, is defined as 

𝐹⇀=𝑝𝐸𝐸⇀�⇀=���⇀, where ρ

E and 

𝐸⇀�⇀ are the net electric charge density and the applied external electric field, respectively.Numerous models are established to theoretically study the externally applied electric potential and the system wall induced potential by charged walls. The following Laplace equation, expressed as eq 16, is generally adapted and solved to calculate the externally applied potential (ϕ).

∇2𝜙=0∇2�=0

(16)Ion diffusion under applied electric fields, together with mass transport resulting from convection and diffusion, transports ionic solutions in bulk flow under electrokinetic processes. The Nernst–Planck equation can describe these transport methods, including convection, diffusion, and electro-diffusion. Therefore, the Nernst–Planck equation is used to determine the distribution of the ions within the electrolyte. The electric potential induced by the charged channel walls follows the Poisson–Nernst–Plank (PNP) equation, which can be written as eq 17.

∇·[𝐷𝑖∇𝑛𝑖−𝑢⇀𝑛𝑖+𝑛𝑖𝐷𝑖𝑧𝑖𝑒𝑘𝑏𝑇∇(𝜙+𝜓)]=0∇·[��∇��−�⇀��+����������∇(�+�)]=0

(17)where D

in

i, and z

i are the diffusion coefficient, ionic concentration, and ionic valence of the ionic species I, respectively. However, due to the high nonlinearity and numerical stiffness introduced by different lengths and time scales from the PNP equations, the Poisson–Boltzmann (PB) model is often considered the major simplified method of the PNP equation to characterize the potential distribution of the EDL region in microchannels. In the PB model, it is assumed that the ionic species in the fluid follow the Boltzmann distribution. This model is typically valid for steady-state problems where charge transport can be considered negligible, the EDLs do not overlap with each other, and the intrinsic potentials are low. It provides a simplified representation of the potential distribution in the EDL region. The PB equation governing the EDL electric potential distribution is described as

∇2𝜓=(2𝑒𝑧𝑛0𝜀𝜀0)sinh(𝑧𝑒𝜓𝑘b𝑇)∇2�=(2���0��0)⁡sinh(����b�)

(18)where n

0 is the ion bulk concentration, z is the ionic valence, and ε

0 is the electric permittivity in the vacuum. Under low electric potential conditions, an even further simplified model to illustrate the EOF phenomena is the Debye–Hückel (DH) model. The DH model is derived by obtaining a charge density term by expanding the exponential term of the Boltzmann equation in a Taylor series.

4.2.2. EOF Modeling for Viscoelastic Fluids

Many studies through numerical modeling were performed to obtain a deeper understanding of the effect exhibited by externally applied electric fields on viscoelastic flow in microchannels under various geometrical designs. Bello et al. 

(83) found that methylcellulose solution, a non-Newtonian polymer solution, resulted in stronger electro-osmotic mobility in experiments when compared to the predictions by the Helmholtz–Smoluchowski equation, which is commonly used to define the velocity of EOF of a Newtonian fluid. Being one of the pioneers to identify the discrepancies between the EOF of Newtonian and non-Newtonian fluids, Bello et al. attributed such discrepancies to the presence of a very high shear rate in the EDL, resulting in a change in the orientation of the polymer molecules. Park and Lee 

(84) utilized the FVM to solve the PB equation for the characterization of the electric field induced force. In the study, the concept of fractional calculus for the Oldroyd-B model was adapted to illustrate the elastic and memory effects of viscoelastic fluids in a straight microchannel They observed that fluid elasticity and increased ratio of viscoelastic fluid contribution to overall fluid viscosity had a significant impact on the volumetric flow rate and sensitivity of velocity to electric field strength compared to Newtonian fluids. Afonso et al. 

(85) derived an analytical expression for EOF of viscoelastic fluid between parallel plates using the DH model to account for a zeta potential condition below 25 mV. The study established the understanding of the electro-osmotic viscoelastic fluid flow under low zeta potential conditions. Apart from the electrokinetic forces, pressure forces can also be coupled with EOF to generate a unique fluid flow behavior within the microchannel. Sousa et al. 

(86) analytically studied the flow of a standard viscoelastic solution by combining the pressure gradient force with an externally applied electric force. It was found that, at a near wall skimming layer and the outer layer away from the wall, macromolecules migrating away from surface walls in viscoelastic fluids are observed. In the study, the Phan-Thien Tanner (PTT) constitutive model is utilized to characterize the viscoelastic properties of the solution. The approach is found to be valid when the EDL is much thinner than the skimming layer under an enhanced flow rate. Zhao and Yang 

(87) solved the PB equation and Carreau model for the characterization of the EOF mechanism and non-Newtonian fluid respectively through the FEM. The numerical results depict that, different from the EOF of Newtonian fluids, non-Newtonian fluids led to an increase of electro-osmotic mobility for shear thinning fluids but the opposite for shear thickening fluids.Like other fluid transport driving forces, EOF within unique geometrical layouts also portrays unique transport phenomena. Pimenta and Alves 

(88) utilized the FVM to perform numerical simulations of the EOF of viscoelastic fluids considering the PB equation and the Oldroyd-B model, in a cross-slot and flow-focusing microdevices. It was found that electroelastic instabilities are formed due to the development of large stresses inside the EDL with streamlined curvature at geometry corners. Bezerra et al. 

(89) used the FDM to numerically analyze the vortex formation and flow instability from an electro-osmotic non-Newtonian fluid flow in a microchannel with a nozzle geometry and parallel wall geometry setting. The PNP equation is utilized to characterize the charge motion in the EOF and the PTT model for non-Newtonian flow characterization. A constriction geometry is commonly utilized in blood flow adapted in LOC systems due to the change in blood flow behavior under narrow dimensions in a microchannel. Ji et al. 

(90) recently studied the EOF of viscoelastic fluid in a constriction microchannel connected by two relatively big reservoirs on both ends (as seen in Figure 5) filled with the polyacrylamide polymer solution, a viscoelastic fluid, and an incompressible monovalent binary electrolyte solution KCl.

Figure 5. Schematic diagram of a negatively charged constriction microchannel connected to two reservoirs at both ends. An electro-osmotic flow is induced in the system by the induced potential difference between the anode and cathode. (90) Reproduced with permission from ref (90). Copyright 2021 The Authors, under the terms of the Creative Commons (CC BY 4.0) License https://creativecommons.org/licenses/by/4.0/.

In studying the EOF of viscoelastic fluids, the Oldroyd-B model is often utilized to characterize the polymeric stress tensor and the deformation rate of the fluid. The Oldroyd-B model is expressed as follows:

𝜏=𝜂p𝜆(𝐜−𝐈)�=�p�(�−�)

(19)where η

p, λ, c, and I represent the polymer dynamic viscosity, polymer relaxation time, symmetric conformation tensor of the polymer molecules, and the identity matrix, respectively.A log-conformation tensor approach is taken to prevent convergence difficulty induced by the viscoelastic properties. The conformation tensor (c) in the polymeric stress tensor term is redefined by a new tensor (Θ) based on the natural logarithm of the c. The new tensor is defined as

Θ=ln(𝐜)=𝐑ln(𝚲)𝐑Θ=ln(�)=�⁡ln(�)�

(20)in which Λ is the diagonal matrix and R is the orthogonal matrix.Under the new conformation tensor, the induced EOF of a viscoelastic fluid is governed by the continuity and N–S equations adapting the Oldroyd-B model, which is expressed as

∂𝚯∂𝑡+𝐮·∇𝚯=𝛀Θ−ΘΩ+2𝐁+1𝜆(eΘ−𝐈)∂�∂�+�·∇�=�Θ−ΘΩ+2�+1�(eΘ−�)

(21)where Ω and B represent the anti-symmetric matrix and the symmetric traceless matrix of the decomposition of the velocity gradient tensor ∇u, respectively. The conformation tensor can be recovered by c = exp(Θ). The PB model and Laplace equation are utilized to characterize the charged channel wall induced potential and the externally applied potential.The governing equations are numerically solved through the FVM by RheoTool, 

(42) an open-source viscoelastic EOF solver on the OpenFOAM platform. A SIMPLEC (Semi-Implicit Method for Pressure Linked Equations-Consistent) algorithm was applied to solve the velocity-pressure coupling. The pressure field and velocity field were computed by the PCG (Preconditioned Conjugate Gradient) solver and the PBiCG (Preconditioned Biconjugate Gradient) solver, respectively.Ranging magnitudes of an applied electric field or fluid concentration induce both different streamlines and velocity magnitudes at various locations and times of the microchannel. In the study performed by Ji et al., 

(90) notable fluctuation of streamlines and vortex formation is formed at the upper stream entrance of the constriction as shown in Figure 6(a) and (b), respectively, due to the increase of electrokinetic effect, which is seen as a result of the increase in polymeric stress (τ

xx). 

(90) The contraction geometry enhances the EOF velocity within the constriction channel under high E

app condition (600 V/cm). Such phenomena can be attributed to the dependence of electro-osmotic viscoelastic fluid flow on the system wall surface and bulk fluid properties. 

(91)

Figure 6. Schematic diagram of vortex formation and streamlines of EOF depicting flow instability at (a) 1.71 s and (b) 1.75 s. Spatial distribution of the elastic normal stress at (c) high Eapp condition. Streamline of an electro-osmotic flow under Eapp of 600 V/cm (90) for (d) non-Newtonian and (e) Newtonian fluid through a constriction geometry. Reproduced with permission from ref (90). Copyright 2021 The Authors, under the terms of the Creative Commons (CC BY 4.0) License https://creativecommons.org/licenses/by/4.0/.

As elastic normal stress exceeds the local shear stress, flow instability and vortex formation occur. The induced elastic stress under EOF not only enhances the instability of the flow but often generates an irregular secondary flow leading to strong disturbance. 

(92) It is also vital to consider the effect of the constriction layout of microchannels on the alteration of the field strength within the system. The contraction geometry enhances a larger electric field strength compared with other locations of the channel outside the constriction region, resulting in a higher velocity gradient and stronger extension on the polymer within the viscoelastic solution. Following the high shear flow condition, a higher magnitude of stretch for polymer molecules in viscoelastic fluids exhibits larger elastic stresses and enhancement of vortex formation at the region. 

(93)As shown in Figure 6(c), significant elastic normal stress occurs at the inlet of the constriction microchannel. Such occurrence of a polymeric flow can be attributed to the dominating elongational flow, giving rise to high deformation of the polymers within the viscoelastic fluid flow, resulting in higher elastic stress from the polymers. Such phenomena at the entrance result in the difference in velocity streamline as circled in Figure 6(d) compared to that of the Newtonian fluid at the constriction entrance in Figure 6(e). 

(90) The difference between the Newtonian and polymer solution at the exit, as circled in Figure 6(d) and (e), can be attributed to the extrudate swell effect of polymers 

(94) within the viscoelastic fluid flow. The extrudate swell effect illustrates that, as polymers emerge from the constriction exit, they tend to contract in the flow direction and grow in the normal direction, resulting in an extrudate diameter greater than the channel size. The deformation of polymers within the polymeric flow at both the entrance and exit of the contraction channel facilitates the change in shear stress conditions of the flow, leading to the alteration in streamlines of flows for each region.

4.3. EOF Applications in LOC Systems

4.3.1. Mixing in LOC Systems

Rather than relying on the micromixing controlled by molecular diffusion under low Reynolds number conditions, active mixers actively leverage convective instability and vortex formation induced by electro-osmotic flows from alternating current (AC) or direct current (DC) electric fields. Such adaptation is recognized as significant breakthroughs for promotion of fluid mixing in chemical and biological applications such as drug delivery, medical diagnostics, chemical synthesis, and so on. 

(95)Many researchers proposed novel designs of electro-osmosis micromixers coupled with numerical simulations in conjunction with experimental findings to increase their understanding of the role of flow instability and vortex formation in the mixing process under electrokinetic phenomena. Matsubara and Narumi 

(96) numerically modeled the mixing process in a microchannel with four electrodes on each side of the microchannel wall, which generated a disruption through unstable electro-osmotic vortices. It was found that particle mixing was sensitive to both the convection effect induced by the main and secondary vortex within the micromixer and the change in oscillation frequency caused by the supplied AC voltage when the Reynolds number was varied. Qaderi et al. 

(97) adapted the PNP equation to numerically study the effect of the geometry and zeta potential configuration of the microchannel on the mixing process with a combined electro-osmotic pressure driven flow. It was reported that the application of heterogeneous zeta potential configuration enhances the mixing efficiency by around 23% while the height of the hurdles increases the mixing efficiency at most 48.1%. Cho et al. 

(98) utilized the PB model and Laplace equation to numerically simulate the electro-osmotic non-Newtonian fluid mixing process within a wavy and block layout of microchannel walls. The Power Law model is adapted to describe the fluid rheological characteristic. It was found that shear-thinning fluids possess a higher volumetric flow rate, which could result in poorer mixing efficiency compared to that of Newtonian fluids. Numerous studies have revealed that flow instability and vortex generation, in particular secondary vortices produced by barriers or greater magnitudes of heterogeneous zeta potential distribution, enhance mixing by increasing bulk flow velocity and reducing flow distance.To better understand the mechanism of disturbance formed in the system due to externally applied forces, known as electrokinetic instability, literature often utilize the Rayleigh (Ra) number, 

(1) as described below:

𝑅𝑎𝑣=𝑢ev𝑢eo=(𝛾−1𝛾+1)2𝑊𝛿2𝐸el2𝐻2𝜁𝛿Ra�=�ev�eo=(�−1�+1)2��2�el2�2��

(22)where γ is the conductivity ratio of the two streams and can be written as 

𝛾=𝜎el,H𝜎el,L�=�el,H�el,L. The Ra number characterizes the ratio between electroviscous and electro-osmotic flow. A high Ra

v value often results in good mixing. It is evident that fluid properties such as the conductivity (σ) of the two streams play a key role in the formation of disturbances to enhance mixing in microsystems. At the same time, electrokinetic parameters like the zeta potential (ζ) in the Ra number is critical in the characterization of electro-osmotic velocity and a slip boundary condition at the microchannel wall.To understand the mixing result along the channel, the concentration field can be defined and simulated under the assumption of steady state conditions and constant diffusion coefficient for each of the working fluid within the system through the convection–diffusion equation as below:

∂𝑐𝒊∂𝑡+∇⇀(𝑐𝑖𝑢⇀−𝐷𝑖∇⇀𝑐𝒊)=0∂��∂�+∇⇀(���⇀−��∇⇀��)=0

(23)where c

i is the species concentration of species i and D

i is the diffusion coefficient of the corresponding species.The standard deviation of concentration (σ

sd) can be adapted to evaluate the mixing quality of the system. 

(97) The standard deviation for concentration at a specific portion of the channel may be calculated using the equation below:

𝜎sd=∫10(𝐶∗(𝑦∗)−𝐶m)2d𝑦∗∫10d𝑦∗⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯⎯�sd=∫01(�*(�*)−�m)2d�*∫01d�*

(24)where C*(y*) and C

m are the non-dimensional concentration profile and the mean concentration at the portion, respectively. C* is the non-dimensional concentration and can be calculated as 

𝐶∗=𝐶𝐶ref�*=��ref, where C

ref is the reference concentration defined as the bulk solution concentration. The mean concentration profile can be calculated as 

𝐶m=∫10(𝐶∗(𝑦∗)d𝑦∗∫10d𝑦∗�m=∫01(�*(�*)d�*∫01d�*. With the standard deviation of concentration, the mixing efficiency 

(97) can then be calculated as below:

𝜀𝑥=1−𝜎sd𝜎sd,0��=1−�sd�sd,0

(25)where σ

sd,0 is the standard derivation of the case of no mixing. The value of the mixing efficiency is typically utilized in conjunction with the simulated flow field and concentration field to explore the effect of geometrical and electrokinetic parameters on the optimization of the mixing results.

5. Summary

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5.1. Conclusion

Viscoelastic fluids such as blood flow in LOC systems are an essential topic to proceed with diagnostic analysis and research through microdevices in the biomedical and pharmaceutical industries. The complex blood flow behavior is tightly controlled by the viscoelastic characteristics of blood such as the dynamic viscosity and the elastic property of RBCs under various shear rate conditions. Furthermore, the flow behaviors under varied driving forces promote an array of microfluidic transport phenomena that are critical to the management of blood flow and other adapted viscoelastic fluids in LOC systems. This review addressed the blood flow phenomena, the complicated interplay between shear rate and blood flow behaviors, and their numerical modeling under LOC systems through the lens of the viscoelasticity characteristic. Furthermore, a theoretical understanding of capillary forces and externally applied electric forces leads to an in-depth investigation of the relationship between blood flow patterns and the key parameters of the two driving forces, the latter of which is introduced through the lens of viscoelastic fluids, coupling numerical modeling to improve the knowledge of blood flow manipulation in LOC systems. The flow disturbances triggered by the EOF of viscoelastic fluids and their impact on blood flow patterns have been deeply investigated due to their important role and applications in LOC devices. Continuous advancements of various numerical modeling methods with experimental findings through more efficient and less computationally heavy methods have served as an encouraging sign of establishing more accurate illustrations of the mechanisms for multiphase blood and other viscoelastic fluid flow transport phenomena driven by various forces. Such progress is fundamental for the manipulation of unique transport phenomena, such as the generated disturbances, to optimize functionalities offered by microdevices in LOC systems.

The following section will provide further insights into the employment of studied blood transport phenomena to improve the functionality of micro devices adapting LOC technology. A discussion of the novel roles that external driving forces play in microfluidic flow behaviors is also provided. Limitations in the computational modeling of blood flow and electrokinetic phenomena in LOC systems will also be emphasized, which may provide valuable insights for future research endeavors. These discussions aim to provide guidance and opportunities for new paths in the ongoing development of LOC devices that adapt blood flow.

5.2. Future Directions

5.2.1. Electro-osmosis Mixing in LOC Systems

Despite substantial research, mixing results through flow instability and vortex formation phenomena induced by electro-osmotic mixing still deviate from the effective mixing results offered by chaotic mixing results such as those seen in turbulent flows. However, recent discoveries of a mixing phenomenon that is generally observed under turbulent flows are found within electro-osmosis micromixers under low Reynolds number conditions. Zhao 

(99) experimentally discovered a rapid mixing process in an AC applied micromixer, where the power spectrum of concentration under an applied voltage of 20 V

p-p induces a −5/3 slope within a frequency range. This value of the slope is considered as the O–C spectrum in macroflows, which is often visible under relatively high Re conditions, such as the Taylor microscale Reynolds number Re > 500 in turbulent flows. 

(100) However, the Re value in the studied system is less than 1 at the specific location and applied voltage. A secondary flow is also suggested to occur close to microchannel walls, being attributed to the increase of convective instability within the system.Despite the experimental phenomenon proposed by Zhao et al., 

(99) the range of effects induced by vital parameters of an EOF mixing system on the enhanced mixing results and mechanisms of disturbance generated by the turbulent-like flow instability is not further characterized. Such a gap in knowledge may hinder the adaptability and commercialization of the discovery of micromixers. One of the parameters for further evaluation is the conductivity gradient of the fluid flow. A relatively strong conductivity gradient (5000:1) was adopted in the system due to the conductive properties of the two fluids. The high conductivity gradients may contribute to the relatively large Rayleigh number and differences in EDL layer thickness, resulting in an unusual disturbance in laminar flow conditions and enhanced mixing results. However, high conductivity gradients are not always achievable by the working fluids due to diverse fluid properties. The reliance on turbulent-like phenomena and rapid mixing results in a large conductivity gradient should be established to prevent the limited application of fluids for the mixing system. In addition, the proposed system utilizes distinct zeta potential distributions at the top and bottom walls due to their difference in material choices, which may be attributed to the flow instability phenomena. Further studies should be made on varying zeta potential magnitude and distribution to evaluate their effect on the slip boundary conditions of the flow and the large shear rate condition close to the channel wall of EOF. Such a study can potentially offer an optimized condition in zeta potential magnitude through material choices and geometrical layout of the zeta potential for better mixing results and manipulation of mixing fluid dynamics. The two vital parameters mentioned above can be varied with the aid of numerical simulation to understand the effect of parameters on the interaction between electro-osmotic forces and electroviscous forces. At the same time, the relationship of developed streamlines of the simulated velocity and concentration field, following their relationship with the mixing results, under the impact of these key parameters can foster more insight into the range of impact that the two parameters have on the proposed phenomena and the microfluidic dynamic principles of disturbances.

In addition, many of the current investigations of electrokinetic mixers commonly emphasize the fluid dynamics of mixing for Newtonian fluids, while the utilization of biofluids, primarily viscoelastic fluids such as blood, and their distinctive response under shear forces in these novel mixing processes of LOC systems are significantly less studied. To develop more compatible microdevice designs and efficient mixing outcomes for the biomedical industry, it is necessary to fill the knowledge gaps in the literature on electro-osmotic mixing for biofluids, where properties of elasticity, dynamic viscosity, and intricate relationship with shear flow from the fluid are further considered.

5.2.2. Electro-osmosis Separation in LOC Systems

Particle separation in LOC devices, particularly in biological research and diagnostics, is another area where disturbances may play a significant role in optimization. 

(101) Plasma analysis in LOC systems under precise control of blood flow phenomena and blood/plasma separation procedures can detect vital information about infectious diseases from particular antibodies and foreign nucleic acids for medical treatments, diagnostics, and research, 

(102) offering more efficient results and simple operating procedures compared to that of the traditional centrifugation method for blood and plasma separation. However, the adaptability of LOC devices for blood and plasma separation is often hindered by microchannel clogging, where flow velocity and plasma yield from LOC devices is reduced due to occasional RBC migration and aggregation at the filtration entrance of microdevices. 

(103)It is important to note that the EOF induces flow instability close to microchannel walls, which may provide further solutions to clogging for the separation process of the LOC systems. Mohammadi et al. 

(104) offered an anti-clogging effect of RBCs at the blood and plasma separating device filtration entry, adjacent to the surface wall, through RBC disaggregation under high shear rate conditions generated by a forward and reverse EOF direction.

Further theoretical and numerical research can be conducted to characterize the effect of high shear rate conditions near microchannel walls toward the detachment of binding blood cells on surfaces and the reversibility of aggregation. Through numerical modeling with varying electrokinetic parameters to induce different degrees of disturbances or shear conditions at channel walls, it may be possible to optimize and better understand the process of disrupting the forces that bind cells to surface walls and aggregated cells at filtration pores. RBCs that migrate close to microchannel walls are often attracted by the adhesion force between the RBC and the solid surface originating from the van der Waals forces. Following RBC migration and attachment by adhesive forces adjacent to the microchannel walls as shown in Figure 7, the increase in viscosity at the region causes a lower shear condition and encourages RBC aggregation (cell–cell interaction), which clogs filtering pores or microchannels and reduces flow velocity at filtration region. Both the impact that shear forces and disturbances may induce on cell binding forces with surface walls and other cells leading to aggregation may suggest further characterization. Kinetic parameters such as activation energy and the rate-determining step for cell binding composition attachment and detachment should be considered for modeling the dynamics of RBCs and blood flows under external forces in LOC separation devices.

Figure 7. Schematic representations of clogging at a microchannel pore following the sequence of RBC migration, cell attachment to channel walls, and aggregation. (105) Reproduced with permission from ref (105). Copyright 2018 The Authors under the terms of the Creative Commons (CC BY 4.0) License https://creativecommons.org/licenses/by/4.0/.

5.2.3. Relationship between External Forces and Microfluidic Systems

In blood flow, a thicker CFL suggests a lower blood viscosity, suggesting a complex relationship between shear stress and shear rate, affecting the blood viscosity and blood flow. Despite some experimental and numerical studies on electro-osmotic non-Newtonian fluid flow, limited literature has performed an in-depth investigation of the role that applied electric forces and other external forces could play in the process of CFL formation. Additional studies on how shear rates from external forces affect CFL formation and microfluidic flow dynamics can shed light on the mechanism of the contribution induced by external driving forces to the development of a separate phase of layer, similar to CFL, close to the microchannel walls and distinct from the surrounding fluid within the system, then influencing microfluidic flow dynamics.One of the mechanisms of phenomena to be explored is the formation of the Exclusion Zone (EZ) region following a “Self-Induced Flow” (SIF) phenomenon discovered by Li and Pollack, 

(106) as shown in Figure 8(a) and (b), respectively. A spontaneous sustained axial flow is observed when hydrophilic materials are immersed in water, resulting in the buildup of a negative layer of charges, defined as the EZ, after water molecules absorb infrared radiation (IR) energy and break down into H and OH

+.

Figure 8. Schematic representations of (a) the Exclusion Zone region and (b) the Self Induced Flow through visualization of microsphere movement within a microchannel. (106) Reproduced with permission from ref (106). Copyright 2020 The Authors under the terms of the Creative Commons (CC BY 4.0) License https://creativecommons.org/licenses/by/4.0/.

Despite the finding of such a phenomenon, the specific mechanism and role of IR energy have yet to be defined for the process of EZ development. To further develop an understanding of the role of IR energy in such phenomena, a feasible study may be seen through the lens of the relationships between external forces and microfluidic flow. In the phenomena, the increase of SIF velocity under a rise of IR radiation resonant characteristics is shown in the participation of the external electric field near the microchannel walls under electro-osmotic viscoelastic fluid flow systems. The buildup of negative charges at the hydrophilic surfaces in EZ is analogous to the mechanism of electrical double layer formation. Indeed, research has initiated the exploration of the core mechanisms for EZ formation through the lens of the electrokinetic phenomena. 

(107) Such a similarity of the role of IR energy and the transport phenomena of SIF with electrokinetic phenomena paves the way for the definition of the unknown SIF phenomena and EZ formation. Furthermore, Li and Pollack 

(106) suggest whether CFL formation might contribute to a SIF of blood using solely IR radiation, a commonly available source of energy in nature, as an external driving force. The proposition may be proven feasible with the presence of the CFL region next to the negatively charged hydrophilic endothelial glycocalyx layer, coating the luminal side of blood vessels. 

(108) Further research can dive into the resonating characteristics between the formation of the CFL region next to the hydrophilic endothelial glycocalyx layer and that of the EZ formation close to hydrophilic microchannel walls. Indeed, an increase in IR energy is known to rapidly accelerate EZ formation and SIF velocity, depicting similarity to the increase in the magnitude of electric field forces and greater shear rates at microchannel walls affecting CFL formation and EOF velocity. Such correlation depicts a future direction in whether SIF blood flow can be observed and characterized theoretically further through the lens of the relationship between blood flow and shear forces exhibited by external energy.

The intricate link between the CFL and external forces, more specifically the externally applied electric field, can receive further attention to provide a more complete framework for the mechanisms between IR radiation and EZ formation. Such characterization may also contribute to a greater comprehension of the role IR can play in CFL formation next to the endothelial glycocalyx layer as well as its role as a driving force to propel blood flow, similar to the SIF, but without the commonly assumed pressure force from heart contraction as a source of driving force.

5.3. Challenges

Although there have been significant improvements in blood flow modeling under LOC systems over the past decade, there are still notable constraints that may require special attention for numerical simulation applications to benefit the adaptability of the designs and functionalities of LOC devices. Several points that require special attention are mentioned below:

1.The majority of CFD models operate under the relationship between the viscoelasticity of blood and the shear rate conditions of flow. The relative effect exhibited by the presence of highly populated RBCs in whole blood and their forces amongst the cells themselves under complex flows often remains unclearly defined. Furthermore, the full range of cell populations in whole blood requires a much more computational load for numerical modeling. Therefore, a vital goal for future research is to evaluate a reduced modeling method where the impact of cell–cell interaction on the viscoelastic property of blood is considered.
2.Current computational methods on hemodynamics rely on continuum models based upon non-Newtonian rheology at the macroscale rather than at molecular and cellular levels. Careful considerations should be made for the development of a constructive framework for the physical and temporal scales of micro/nanoscale systems to evaluate the intricate relationship between fluid driving forces, dynamic viscosity, and elasticity.
3.Viscoelastic fluids under the impact of externally applied electric forces often deviate from the assumptions of no-slip boundary conditions due to the unique flow conditions induced by externally applied forces. Furthermore, the mechanism of vortex formation and viscoelastic flow instability at laminar flow conditions should be better defined through the lens of the microfluidic flow phenomenon to optimize the prediction of viscoelastic flow across different geometrical layouts. Mathematical models and numerical methods are needed to better predict such disturbance caused by external forces and the viscoelasticity of fluids at such a small scale.
4.Under practical situations, zeta potential distribution at channel walls frequently deviates from the common assumption of a constant distribution because of manufacturing faults or inherent surface charges prior to the introduction of electrokinetic influence. These discrepancies frequently lead to inconsistent surface potential distribution, such as excess positive ions at relatively more negatively charged walls. Accordingly, unpredicted vortex formation and flow instability may occur. Therefore, careful consideration should be given to these discrepancies and how they could trigger the transport process and unexpected results of a microdevice.

Author Information

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  • Corresponding Authors
    • Zhe Chen – Department of Chemical Engineering, School of Chemistry and Chemical Engineering, State Key Laboratory of Metal Matrix Composites, Shanghai Jiao Tong University, Shanghai 200240, P. R. China;  Email: zaccooky@sjtu.edu.cn
    • Bo Ouyang – Department of Chemical Engineering, School of Chemistry and Chemical Engineering, State Key Laboratory of Metal Matrix Composites, Shanghai Jiao Tong University, Shanghai 200240, P. R. China;  Email: bouy93@sjtu.edu.cn
    • Zheng-Hong Luo – Department of Chemical Engineering, School of Chemistry and Chemical Engineering, State Key Laboratory of Metal Matrix Composites, Shanghai Jiao Tong University, Shanghai 200240, P. R. China;  Orcidhttps://orcid.org/0000-0001-9011-6020; Email: luozh@sjtu.edu.cn
  • Authors
    • Bin-Jie Lai – Department of Chemical Engineering, School of Chemistry and Chemical Engineering, State Key Laboratory of Metal Matrix Composites, Shanghai Jiao Tong University, Shanghai 200240, P. R. China;  Orcidhttps://orcid.org/0009-0002-8133-5381
    • Li-Tao Zhu – Department of Chemical Engineering, School of Chemistry and Chemical Engineering, State Key Laboratory of Metal Matrix Composites, Shanghai Jiao Tong University, Shanghai 200240, P. R. China;  Orcidhttps://orcid.org/0000-0001-6514-8864
  • NotesThe authors declare no competing financial interest.

Acknowledgments

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This work was supported by the National Natural Science Foundation of China (No. 22238005) and the Postdoctoral Research Foundation of China (No. GZC20231576).

Vocabulary

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Microfluidicsthe field of technological and scientific study that investigates fluid flow in channels with dimensions between 1 and 1000 μm
Lab-on-a-Chip Technologythe field of research and technological development aimed at integrating the micro/nanofluidic characteristics to conduct laboratory processes on handheld devices
Computational Fluid Dynamics (CFD)the method utilizing computational abilities to predict physical fluid flow behaviors mathematically through solving the governing equations of corresponding fluid flows
Shear Ratethe rate of change in velocity where one layer of fluid moves past the adjacent layer
Viscoelasticitythe property holding both elasticity and viscosity characteristics relying on the magnitude of applied shear stress and time-dependent strain
Electro-osmosisthe flow of fluid under an applied electric field when charged solid surface is in contact with the bulk fluid
Vortexthe rotating motion of a fluid revolving an axis line

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Figure 4. Field gate discharge experiment.

FLOW-3D Model Development for the Analysis of the Flow Characteristics of Downstream Hydraulic Structures

하류 유압 구조물의 유동 특성 분석을 위한 FLOW-3D 모델 개발

Beom-Jin Kim 1, Jae-Hong Hwang 2 and Byunghyun Kim 3,*
1 Advanced Structures and Seismic Safety Research Division, Korea Atomic Energy Research Institute,
Daejeon 34057, Korea
2 Korea Water Resources Corporation (K-Water), Daejeon 34350, Korea
3 Department of Civil Engineering, Kyungpook National University, Daegu 41566, Korea

  • Correspondence: bhkimc@knu.ac.kr; Tel.: +82-53-950-7819

Abstract

Hydraulic structures installed in rivers inevitably create a water level difference between upstream and downstream regions. The potential energy due to this difference in water level is converted into kinetic energy, causing high-velocity flow and hydraulic jumps in the river. As a result, problems such as scouring and sloping downstream may occur around the hydraulic structures. In this study, a FLOW-3D model was constructed to perform a numerical analysis of the ChangnyeongHaman weir in the Republic of Korea. The constructed model was verified based on surface velocity measurements from a field gate operation experiment. In the simulation results, the flow discharge differed from the measured value by 9–15 m3/s, from which the accuracy was evaluated to be 82–87%. The flow velocity was evaluated with an accuracy of 92% from a difference of 0.01 to 0.16 m/s. Following this verification, a flow analysis of the hydraulic structures was performed according to boundary conditions and operation conditions for numerous scenarios. Since 2018, the ChangnyeongHaman weir gate has been fully opened due to the implementation of Korea’s eco-environmental policy; therefore, in this study, the actual gate operation history data prior to 2018 was applied and evaluated. The evaluation conditions were a 50% open gate condition and the flow discharge of two cases with a large difference in water level. As a result of the analysis, the actual operating conditions showed that the velocity and the Froude number were lower than the optimal conditions, confirming that the selected design was appropriate. It was also found that in the bed protection section, the average flow velocity was high when the water level difference was large, whereas the bottom velocity was high when the gate opening was large. Ultimately, through the reviewed status survey data in this study, the downstream flow characteristics of hydraulic structures along with adequacy verification techniques, optimal design techniques such as procedures for design, and important considerations were derived. Based on the current results, the constructed FLOW-3D-based model can be applied to creating or updating flow analysis guidelines for future repair and reinforcement measures as well as hydraulic structure design.

하천에 설치되는 수력구조물은 필연적으로 상류와 하류의 수위차를 발생시킨다. 이러한 수위차로 인한 위치에너지는 운동에너지로 변환되어 하천의 고속유동과 수압점프를 일으킨다. 그 결과 수력구조물 주변에서 하류의 세굴, 경사 등의 문제가 발생할 수 있다.

본 연구에서는 대한민국 창녕함안보의 수치해석을 위해 FLOW-3D 모델을 구축하였다. 구축된 모델은 현장 게이트 작동 실험에서 표면 속도 측정을 기반으로 검증되었습니다.

시뮬레이션 결과에서 유량은 측정값과 9~15 m3/s 차이가 나고 정확도는 82~87%로 평가되었다. 유속은 0.01~0.16m/s의 차이에서 92%의 정확도로 평가되었습니다.

검증 후 다양한 시나리오에 대한 경계조건 및 운전조건에 따른 수리구조물의 유동해석을 수행하였다. 2018년부터 창녕함안보 문은 한국의 친환경 정책 시행으로 전면 개방되었습니다.

따라서 본 연구에서는 2018년 이전의 실제 게이트 운영 이력 데이터를 적용하여 평가하였다. 평가조건은 50% open gate 조건과 수위차가 큰 2가지 경우의 유수방류로 하였다. 해석 결과 실제 운전조건은 속도와 Froude수가 최적조건보다 낮아 선정된 설계가 적합함을 확인하였다.

또한 베드보호구간에서는 수위차가 크면 평균유속이 높고, 수문개구가 크면 저저유속이 높은 것으로 나타났다. 최종적으로 본 연구에서 검토한 실태조사 자료를 통해 적정성 검증기법과 함께 수력구조물의 하류 유동특성, 설계절차 등 최적 설계기법 및 중요 고려사항을 도출하였다.

현재의 결과를 바탕으로 구축된 FLOW-3D 기반 모델은 수력구조 설계뿐만 아니라 향후 보수 및 보강 조치를 위한 유동해석 가이드라인 생성 또는 업데이트에 적용할 수 있습니다.

Figure 1. Effect of downstream riverbed erosion according to the type of weir foundation.
Figure 1. Effect of downstream riverbed erosion according to the type of weir foundation.
Figure 2. Changnyeong-Haman weir depth survey results (June 2015)
Figure 2. Changnyeong-Haman weir depth survey results (June 2015)
Figure 4. Field gate discharge experiment.
Figure 4. Field gate discharge experiment.
Figure 16. Analysis results for Case 7 and Case 8
Figure 16. Analysis results for Case 7 and Case 8

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Fig. 1. (a) Dimensions of the casting with runners (unit: mm), (b) a melt flow simulation using Flow-3D software together with Reilly's model[44], predicted that a large amount of bifilms (denoted by the black particles) would be contained in the final casting. (c) A solidification simulation using Pro-cast software showed that no shrinkage defect was contained in the final casting.

AZ91 합금 주물 내 연행 결함에 대한 캐리어 가스의 영향

TianLiabJ.M.T.DaviesaXiangzhenZhuc
aUniversity of Birmingham, Birmingham B15 2TT, United Kingdom
bGrainger and Worrall Ltd, Bridgnorth WV15 5HP, United Kingdom
cBrunel Centre for Advanced Solidification Technology, Brunel University London, Kingston Ln, London, Uxbridge UB8 3PH, United Kingdom

Abstract

An entrainment defect (also known as a double oxide film defect or bifilm) acts a void containing an entrapped gas when submerged into a light-alloy melt, thus reducing the quality and reproducibility of the final castings. Previous publications, carried out with Al-alloy castings, reported that this trapped gas could be subsequently consumed by the reaction with the surrounding melt, thus reducing the void volume and negative effect of entrainment defects. Compared with Al-alloys, the entrapped gas within Mg-alloy might be more efficiently consumed due to the relatively high reactivity of magnesium. However, research into the entrainment defects within Mg alloys has been significantly limited. In the present work, AZ91 alloy castings were produced under different carrier gas atmospheres (i.e., SF6/CO2, SF6/air). The evolution processes of the entrainment defects contained in AZ91 alloy were suggested according to the microstructure inspections and thermodynamic calculations. The defects formed in the different atmospheres have a similar sandwich-like structure, but their oxide films contained different combinations of compounds. The use of carrier gases, which were associated with different entrained-gas consumption rates, affected the reproducibility of AZ91 castings.

연행 결함(이중 산화막 결함 또는 이중막이라고도 함)은 경합금 용융물에 잠길 때 갇힌 가스를 포함하는 공극으로 작용하여 최종 주물의 품질과 재현성을 저하시킵니다. Al-합금 주물을 사용하여 수행된 이전 간행물에서는 이 갇힌 가스가 주변 용융물과의 반응에 의해 후속적으로 소모되어 공극 부피와 연행 결함의 부정적인 영향을 줄일 수 있다고 보고했습니다. Al-합금에 비해 마그네슘의 상대적으로 높은 반응성으로 인해 Mg-합금 내에 포집된 가스가 더 효율적으로 소모될 수 있습니다. 그러나 Mg 합금 내 연행 결함에 대한 연구는 상당히 제한적이었습니다. 현재 작업에서 AZ91 합금 주물은 다양한 캐리어 가스 분위기(즉, SF6/CO2, SF6/공기)에서 생산되었습니다. AZ91 합금에 포함된 연행 결함의 진화 과정은 미세 조직 검사 및 열역학 계산에 따라 제안되었습니다. 서로 다른 분위기에서 형성된 결함은 유사한 샌드위치 구조를 갖지만 산화막에는 서로 다른 화합물 조합이 포함되어 있습니다. 다른 동반 가스 소비율과 관련된 운반 가스의 사용은 AZ91 주물의 재현성에 영향을 미쳤습니다.

Keywords

Magnesium alloy, Casting, Oxide film, Bifilm, Entrainment defect, Reproducibility

1. Introduction

As the lightest structural metal available on Earth, magnesium became one of the most attractive light metals over the last few decades. The magnesium industry has consequently experienced a rapid development in the last 20 years [1,2], indicating a large growth in demand for Mg alloys all over the world. Nowadays, the use of Mg alloys can be found in the fields of automobiles, aerospace, electronics and etc.[3,4]. It has been predicted that the global consumption of Mg metals will further increase in the future, especially in the automotive industry, as the energy efficiency requirement of both traditional and electric vehicles further push manufactures lightweight their design [3,5,6].

The sustained growth in demand for Mg alloys motivated a wide interest in the improvement of the quality and mechanical properties of Mg-alloy castings. During a Mg-alloy casting process, surface turbulence of the melt can lead to the entrapment of a doubled-over surface film containing a small quantity of the surrounding atmosphere, thus forming an entrainment defect (also known as a double oxide film defect or bifilm) [7][8][9][10]. The random size, quantity, orientation, and placement of entrainment defects are widely accepted to be significant factors linked to the variation of casting properties [7]. In addition, Peng et al. [11] found that entrained oxides films in AZ91 alloy melt acted as filters to Al8Mn5 particles, trapping them as they settle. Mackie et al. [12] further suggested that entrained oxide films can act to trawl the intermetallic particles, causing them to cluster and form extremely large defects. The clustering of intermetallic compounds made the entrainment defects more detrimental for the casting properties.

Most of the previous studies regarding entrainment defects were carried out on Al-alloys [7,[13][14][15][16][17][18], and a few potential methods have been suggested for diminishing their negative effect on the quality of Al-alloy castings. Nyahumwa et al.,[16] shows that the void volume within entrainment defects could be reduced by a hot isostatic pressing (HIP) process. Campbell [7] suggested the entrained gas within the defects could be consumed due to reaction with the surrounding melt, which was further verified by Raiszedeh and Griffiths [19].The effect of the entrained gas consumption on the mechanical properties of Al-alloy castings has been investigated by [8,9], suggesting that the consumption of the entrained gas promoted the improvement of the casting reproducibility.

Compared with the investigation concerning the defects within Al-alloys, research into the entrainment defects within Mg-alloys has been significantly limited. The existence of entrainment defects has been demonstrated in Mg-alloy castings [20,21], but their behaviour, evolution, as well as entrained gas consumption are still not clear.

In a Mg-alloy casting process, the melt is usually protected by a cover gas to avoid magnesium ignition. The cavities of sand or investment moulds are accordingly required to be flushed with the cover gas prior to the melt pouring [22]. Therefore, the entrained gas within Mg-alloy castings should contain the cover gas used in the casting process, rather than air only, which may complicate the structure and evolution of the corresponding entrainment defects.

SF6 is a typical cover gas widely used for Mg-alloy casting processes [23][24][25]. Although this cover gas has been restricted to use in European Mg-alloy foundries, a commercial report has pointed out that this cover is still popular in global Mg-alloy industry, especially in the countries which dominated the global Mg-alloy production, such as China, Brazil, India, etc. [26]. In addition, a survey in academic publications also showed that this cover gas was widely used in recent Mg-alloy studies [27]. The protective mechanism of SF6 cover gas (i.e., the reaction between liquid Mg-alloy and SF6 cover gas) has been investigated by several previous researchers, but the formation process of the surface oxide film is still not clearly understood, and even some published results are conflicting with each other. In early 1970s, Fruehling [28] found that the surface film formed under SF6 was MgO mainly with traces of fluorides, and suggested that SF6 was absorbed in the Mg-alloy surface film. Couling [29] further noticed that the absorbed SF6 reacted with the Mg-alloy melt to form MgF2. In last 20 years, different structures of the Mg-alloy surface films have been reported, as detailed below.(1)

Single-layered film. Cashion [30,31] used X-ray Photoelectron Spectroscopy (XPS) and Auger Spectroscopy (AES) to identify the surface film as MgO and MgF2. He also found that composition of the film was constant throughout the thickness and the whole experimental holding time. The film observed by Cashion had a single-layered structure created from a holding time from 10 min to 100 min.(2)

Double-layered film. Aarstad et. al [32] reported a doubled-layered surface oxide film in 2003. They observed several well-distributed MgF2 particles attached to the preliminary MgO film and grew until they covered 25–50% of the total surface area. The inward diffusion of F through the outer MgO film was the driving force for the evolution process. This double-layered structure was also supported by Xiong’s group [25,33] and Shih et al. [34].(3)

Triple-layered film. The triple-layered film and its evolution process were reported in 2002 by Pettersen [35]. Pettersen found that the initial surface film was a MgO phase and then gradually evolved to the stable MgF2 phase by the inward diffusion of F. In the final stage, the film has a triple-layered structure with a thin O-rich interlayer between the thick top and bottom MgF2 layers.(4)

Oxide film consisted of discrete particles. Wang et al [36] stirred the Mg-alloy surface film into the melt under a SF6 cover gas, and then inspect the entrained surface film after the solidification. They found that the entrained surface films were not continues as the protective surface films reported by other researchers but composed of discrete particles. The young oxide film was composed of MgO nano-sized oxide particles, while the old oxide films consist of coarse particles (about 1  µm in average size) on one side that contained fluorides and nitrides.

The oxide films of a Mg-alloy melt surface or an entrained gas are both formed due to the reaction between liquid Mg-alloy and the cover gas, thus the above-mentioned research regarding the Mg-alloy surface film gives valuable insights into the evolution of entrainment defects. The protective mechanism of SF6 cover gas (i.e., formation of a Mg-alloy surface film) therefore indicated a potential complicated evolution process of the corresponding entrainment defects.

However, it should be noted that the formation of a surface film on a Mg-alloy melt is in a different situation to the consumption of an entrained gas that is submerged into the melt. For example, a sufficient amount of cover gas was supported during the surface film formation in the studies previously mentioned, which suppressed the depletion of the cover gas. In contrast, the amount of entrained gas within a Mg-alloy melt is finite, and the entrained gas may become fully depleted. Mirak [37] introduced 3.5%SF6/air bubbles into a pure Mg-alloy melt solidifying in a specially designed permanent mould. It was found that the gas bubbles were entirely consumed, and the corresponding oxide film was a mixture of MgO and MgF2. However, the nucleation sites (such as the MgF2 spots observed by Aarstad [32] and Xiong [25,33]) were not observed. Mirak also speculated that the MgF2 formed prior to MgO in the oxide film based on the composition analysis, which was opposite to the surface film formation process reported in previous literatures (i.e., MgO formed prior to MgF2). Mirak’s work indicated that the oxide-film formation of an entrained gas may be quite different from that of surface films, but he did not reveal the structure and evolution of the oxide films.

In addition, the use of carrier gas in the cover gases also influenced the reaction between the cover gas and the liquid Mg-alloy. SF6/air required a higher content of SF6 than did a SF6/CO2 carrier gas [38], to avoid the ignition of molten magnesium, revealing different gas-consumption rates. Liang et.al [39] suggested that carbon was formed in the surface film when CO2 was used as a carrier gas, which was different from the films formed in SF6/air. An investigation into Mg combustion [40] reported a detection of Mg2C3 in the Mg-alloy sample after burning in CO2, which not only supported Liang’s results, but also indicated a potential formation of Mg carbides in double oxide film defects.

The work reported here is an investigation into the behaviour and evolution of entrainment defects formed in AZ91 Mg-alloy castings, protected by different cover gases (i.e., SF6/air and SF6/CO2). These carrier gases have different protectability for liquid Mg alloy, which may be therefore associated with different consumption rates and evolution processes of the corresponding entrained gases. The effect of the entrained-gas consumption on the reproducibility of AZ91 castings was also studied.

2. Experiment

2.1. Melting and casting

Three kilograms AZ91 alloy was melted in a mild steel crucible at 700 ± 5 °C. The composition of the AZ91 alloy has been shown in Table 1. Prior to heating, all oxide scale on the ingot surface was removed by machining. The cover gases used were 0.5%SF6/air or 0.5%SF6/CO2 (vol.%) at a flow rate of 6 L/min for different castings. The melt was degassed by argon with a flow rate of 0.3 L/min for 15 min [41,42], and then poured into sand moulds. Prior to pouring, the sand mould cavity was flushed with the cover gas for 20 min [22]. The residual melt (around 1 kg) was solidified in the crucible.

Table 1. Composition (wt.%) of the AZ91 alloy used in this study.

AlZnMnSiFeNiMg
9.40.610.150.020.0050.0017Residual

Fig. 1(a) shows the dimensions of the casting with runners. A top-filling system was deliberately used to generate entrainment defects in the final castings. Green and Campbell [7,43] suggested that a top-filling system caused more entrainment events (i.e., bifilms) during a casting process, compared with a bottom-filling system. A melt flow simulation (Flow-3D software) of this mould, using Reilly’s model [44] regarding the entrainment events, also predicted that a large amount of bifilms would be contained in the final casting (denoted by the black particles in Fig. 1b).

Fig. 1. (a) Dimensions of the casting with runners (unit: mm), (b) a melt flow simulation using Flow-3D software together with Reilly's model[44], predicted that a large amount of bifilms (denoted by the black particles) would be contained in the final casting. (c) A solidification simulation using Pro-cast software showed that no shrinkage defect was contained in the final casting.

Shrinkage defects also affect the mechanical properties and reproducibility of castings. Since this study focused on the effect of bifilms on the casting quality, the mould has been deliberately designed to avoid generating shrinkage defects. A solidification simulation using ProCAST software showed that no shrinkage defect would be contained in the final casting, as shown in Fig. 1c. The casting soundness has also been confirmed using a real time X-ray prior to the test bar machining.

The sand moulds were made from resin-bonded silica sand, containing 1wt. % PEPSET 5230 resin and 1wt. % PEPSET 5112 catalyst. The sand also contained 2 wt.% Na2SiF6 to act as an inhibitor [45]. The pouring temperature was 700 ± 5 °C. After the solidification, a section of the runner bars was sent to the Sci-Lab Analytical Ltd for a H-content analysis (LECO analysis), and all the H-content measurements were carried out on the 5th day after the casting process. Each of the castings was machined into 40 test bars for a tensile strength test, using a Zwick 1484 tensile test machine with a clip extensometer. The fracture surfaces of the broken test bars were examined using Scanning Electron Microscope (SEM, Philips JEOL7000) with an accelerating voltage of 5–15 kV. The fractured test bars, residual Mg-alloy solidified in the crucible, and the casting runners were then sectioned, polished and also inspected using the same SEM. The cross-section of the oxide film found on the test-bar fracture surface was exposed by the Focused Ion Beam milling technique (FIB), using a CFEI Quanta 3D FEG FIB-SEM. The oxide film required to be analysed was coated with a platinum layer. Then, a gallium ion beam, accelerated to 30 kV, milled the material substrate surrounding the platinum coated area to expose the cross section of the oxide film. EDS analysis of the oxide film’s cross section was carried out using the FIB equipment at accelerating voltage of 30 kV.

2.2. Oxidation cell

As previously mentioned, several past researchers investigated the protective film formed on a Mg-alloy melt surface [38,39,[46][47][48][49][50][51][52]. During these experiments, the amount of cover gas used was sufficient, thus suppressing the depletion of fluorides in the cover gas. The experiment described in this section used a sealed oxidation cell, which limited the supply of cover gas, to study the evolution of the oxide films of entrainment defects. The cover gas contained in the oxidation cell was regarded as large-size “entrained bubble”.

As shown in Fig. 2, the main body of the oxidation cell was a closed-end mild steel tube which had an inner length of 400 mm, and an inner diameter of 32 mm. A water-cooled copper tube was wrapped around the upper section of the cell. When the tube was heated, the cooling system created a temperature difference between the upper and lower sections, causing the interior gas to convect within the tube. The temperature was monitored by a type-K thermocouple located at the top of the crucible. Nie et al. [53] suggested that the SF6 cover gas would react with the steel wall of the holding furnace when they investigated the surface film of a Mg-alloy melt. To avoid this reaction, the interior surface of the steel oxidation cell (shown in Fig. 2) and the upper half section of the thermocouple were coated with boron nitride (the Mg-alloy was not in contact with boron nitride).

Fig. 2. Schematic of the oxidation cell used to study the evolution of the oxide films of the entrainment defects (unit mm).

During the experiment, a block of solid AZ91 alloy was placed in a magnesia crucible located at the bottom of the oxidation cell. The cell was heated to 100 °C in an electric resistance furnace under a gas flow rate of 1 L/min. The cell was held at this temperature for 20 min, to replace the original trapped atmosphere (i.e. air). Then, the oxidation cell was further heated to 700 °C, melting the AZ91 sample. The gas inlet and exit valves were then closed, creating a sealed environment for oxidation under a limited supply of cover gas. The oxidation cell was then held at 700 ± 10 °C for periods of time from 5 min to 30 min in 5-min intervals. At the end of each holding time, the cell was quenched in water. After cooling to room temperature, the oxidised sample was sectioned, polished, and subsequently examined by SEM.

3. Results

3.1. Structure and composition of the entrainment defects formed in SF6/air

The structure and composition of the entrainment defect formed in the AZ91 castings under a cover gas of 0.5%SF6/air was observed by SEM and EDS. The results indicate that there exist two types of entrainment defects which are sketched in Fig. 3: (1) Type A defect whose oxide film has a traditional single-layered structure and (2) Type B defect, whose oxide film has two layers. The details of these defects were introduced in the following. Here it should be noticed that, as the entrainment defects are also known as biofilms or double oxide film, the oxide films of Type B defect were referred to as “multi-layered oxide film” or “multi-layered structure” in the present work to avoid a confusing description such as “the double-layered oxide film of a double oxide film defect”.

Fig. 3. Schematic of the different types of entrainment defects found in AZ91 castings. (a) Type A defect with a single-layered oxide film and (b) Type B defect with two-layered oxide film.

Fig. 4(a-b) shows a Type A defect having a compact single-layered oxide film with about 0.4 µm thickness. Oxygen, fluorine, magnesium and aluminium were detected in this film (Fig. 4c). It is speculated that oxide film is the mixture of fluoride and oxide of magnesium and aluminium. The detection of fluorine revealed that an entrained cover gas was contained in the formation of this defect. That is to say that the pores shown in Fig. 4(a) were not shrinkage defects or hydrogen porosity, but entrainment defects. The detection of aluminium was different with Xiong and Wang’s previous study [47,48], which showed that no aluminium was contained in their surface film of an AZ91 melt protected by a SF6 cover gas. Sulphur could not be clearly recognized in the element map, but there was a S-peak in the corresponding ESD spectrum.

Fig. 4. (a) A Type A entrainment defect formed in SF6/air and having a single-layered oxide film, (b) the oxide film of this defect, (c) SEM-EDS element maps (using Philips JEOL7000) corresponding to the area highlighted in (b).

Fig. 5(a-b) shows a Type B entrainment defect having a multi-layered oxide film. The compact outer layers of the oxide films were enriched with fluorine and oxygen (Fig. 5c), while their relatively porous inner layers were only enriched with oxygen (i.e., poor in fluorine) and partly grew together, thus forming a sandwich-like structure. Therefore, it is speculated that the outer layer is the mixture of fluoride and oxide, while the inner layer is mainly oxide. Sulphur could only be recognized in the EDX spectrum and could not be clearly identified in the element map, which might be due to the small S-content in the cover gas (i.e., 0.5% volume content of SF6 in the cover gas). In this oxide film, aluminium was contained in the outer layer of this oxide film but could not be clearly detected in the inner layer. Moreover, the distribution of Al seems to be uneven. It can be found that, in the right side of the defect, aluminium exists in the film but its concentration can not be identified to be higher than the matrix. However, there is a small area with much higher aluminium concentration in the left side of the defect. Such an uneven distribution of aluminium was also observed in other defects (shown in the following), and it is the result of the formation of some oxide particles in or under the film.

Fig. 5. (a) A Type B entrainment defect formed in SF6/air and having a multi-layered oxide film, (b) the oxide films of this defect have grown together, (c) SEM-EDS element maps (using Philips JEOL7000) corresponding to the area shown in (b).

Figs. 4 and 5 show cross sectional observations of the entrainment defects formed in the AZ91 alloy sample cast under a cover gas of SF6/air. It is not sufficient to characterize the entrainment defects only by the figures observed from the two-dimensional section. To have a further understanding, the surface of the entrainment defects (i.e. the oxide film) was further studied by observing the fracture surface of the test bars.

Fig. 6(a) shows fracture surfaces of an AZ91 alloy tensile test bar produced in SF6/air. Symmetrical dark regions can be seen on both sides of the fracture surfaces. Fig. 6(b) shows boundaries between the dark and bright regions. The bright region consisted of jagged and broken features, while the surface of the dark region was relatively smooth and flat. In addition, the EDS results (Fig. 6c-d and Table 2) show that fluorine, oxygen, sulphur, and nitrogen were only detected in the dark regions, indicating that the dark regions were surface protective films entrained into the melt. Therefore, it could be suggested that the dark regions were an entrainment defect with consideration of their symmetrical nature. Similar defects on fracture surfaces of Al-alloy castings have been previously reported [7]Nitrides were only found in the oxide films on the test-bar fracture surfaces but never detected in the cross-sectional samples shown in Figs. 4 and 5. An underlying reason is that the nitrides contained in these samples may have hydrolysed during the sample polishing process [54].

Fig. 6. (a) A pair of the fracture surfaces of a AZ91 alloy tensile test bar produced under a cover gas of SF6/air. The dimension of the fracture surface is 5 mm × 6 mm, (b) a section of the boundary between the dark and bright regions shown in (a), (c-d) EDS spectrum of the (c) bright regions and (d) dark regions, (e) schematic of an entrainment defect contained in a test bar.

Table 2. EDS results (wt.%) corresponding to the regions shown in Fig. 6 (cover gas: SF6/air).

Empty CellCOMgFAlZnSN
Dark region in Fig. 6(b)3.481.3279.130.4713.630.570.080.73
Bright region in Fig. 6(b)3.5884.4811.250.68

In conjunction with the cross-sectional observation of the defects shown in Figs. 4 and 5, the structure of an entrainment defect contained in a tensile test bar was sketched as shown in Fig. 6(e). The defect contained an entrained gas enclosed by its oxide film, creating a void section inside the test bar. When the tensile force applied on the defect during the fracture process, the crack was initiated at the void section and propagated along the entrainment defect, since cracks would be propagated along the weakest path [55]. Therefore, when the test bar was finally fractured, the oxide films of entrainment defect appeared on both fracture surfaces of the test bar, as shown in Fig. 6(a).

3.2. Structure and composition of the entrainment defects formed in SF6/CO2

Similar to the entrainment defect formed in SF6/air, the defects formed under a cover gas of 0.5%SF6/CO2 also had two types of oxide films (i.e., single-layered and multi-layered types). Fig. 7(a) shows an example of the entrainment defects containing a multi-layered oxide film. A magnified observation to the defect (Fig. 7b) shows that the inner layers of the oxide films had grown together, presenting a sandwich-like structure, which was similar to the defects formed in an atmosphere of SF6/air (Fig. 5b). An EDS spectrum (Fig. 7c) revealed that the joint area (inner layer) of this sandwich-like structure mainly contained magnesium oxides. Peaks of fluorine, sulphur, and aluminium were recognized in this EDS spectrum, but their amount was relatively small. In contrast, the outer layers of the oxide films were compact and composed of a mixture of fluorides and oxides (Fig. 7d-e).

Fig. 7. (a) An example of entrainment defects formed in SF6/CO2 and having a multi-layered oxide film, (b) magnified observation of the defect, showing the inner layer of the oxide films has grown together, (c) EDS spectrum of the point denoted in (b), (d) outer layer of the oxide film, (e) SEM-EDS element maps (using Philips JEOL7000) corresponding to the area shown in (d).

Fig. 8(a) shows an entrainment defect on the fracture surfaces of an AZ91 alloy tensile test bar, which was produced in an atmosphere of 0.5%SF6/CO2. The corresponding EDS results (Table 3) showed that oxide film contained fluorides and oxides. Sulphur and nitrogen were not detected. Besides, a magnified observation (Fig. 8b) indicated spots on the oxide film surface. The diameter of the spots ranged from hundreds of nanometres to a few micron meters.

Fig. 8. (a) A pair of the fracture surfaces of a AZ91 alloy tensile test bar, produced in an atmosphere of SF6/CO2. The dimension of the fracture surface is 5 mm × 6 mm, (b) surface appearance of the oxide films on the fracture surfaces, showing spots on the film surface.

To further reveal the structure and composition of the oxide film clearly, the cross-section of the oxide film on a test-bar fracture surface was onsite exposed using the FIB technique (Fig. 9). As shown in Fig. 9a, a continuous oxide film was found between the platinum coating layer and the Mg-Al alloy substrate. Fig. 9 (b-c) shows a magnified observation to oxide films, indicating a multi-layered structure (denoted by the red box in Fig. 9c). The bottom layer was enriched with fluorine and oxygen and should be the mixture of fluoride and oxide, which was similar to the “outer layer” shown in Figs. 5 and 7, while the only-oxygen-enriched top layer was similar to the “inner layer” shown in Figs. 5 and 7.

Fig. 9. (a) A cross-sectional observation of the oxide film on the fracture surface of the AZ91 casting produced in SF6/CO2, exposed by FIB, (b) a magnified observation of area highlighted in (a), and (c) SEM-EDS elements map of the area shown in (b), obtained by CFEI Quanta 3D FEG FIB-SEM.

Except the continuous film, some individual particles were also observed in or below the continuous film, as shown in Fig. 9. An Al-enriched particle was detected in the left side of the oxide film shown in Fig. 9b and might be speculated to be spinel Mg2AlO4 because it also contains abundant magnesium and oxygen elements. The existing of such Mg2AlO4 particles is responsible for the high concentration of aluminium in small areas of the observed film and the uneven distribution of aluminium, as shown in Fig. 5(c). Here it should be emphasized that, although the other part of the bottom layer of the continuous oxide film contains less aluminium than this Al-enriched particle, the Fig. 9c indicated that the amount of aluminium in this bottom layer was still non-negligible, especially when comparing with the outer layer of the film. Below the right side of the oxide film shown in Fig. 9b, a particle was detected and speculated to be MgO because it is rich in Mg and O. According to Wang’s result [56], lots of discrete MgO particles can be formed on the surface of the Mg melt by the oxidation of Mg melt and Mg vapor. The MgO particles observed in our present work may be formed due to the same reasons. While, due to the differences in experimental conditions, less Mg melt can be vapored or react with O2, thus only a few of MgO particles formed in our work. An enrichment of carbon was also found in the film, revealing that CO2 was able to react with the melt, thus forming carbon or carbides. This carbon concentration was consistent with the relatively high carbon content of the oxide film shown in Table 3 (i.e., the dark region). In the area next to the oxide film.

Table 3. EDS results (wt.%) corresponding to the regions shown in Fig. 8 (cover gas: SF6/ CO2).

Empty CellCOMgFAlZnSN
Dark region in Fig. 8(a)7.253.6469.823.827.030.86
Bright region in Fig. 8(a)2.100.4482.8313.261.36

This cross-sectional observation of the oxide film on a test bar fracture surface (Fig. 9) further verified the schematic of the entrainment defect shown in Fig. 6(e). The entrainment defects formed in different atmospheres of SF6/CO2 and SF6/air had similar structures, but their compositions were different.

3.3. Evolution of the oxide films in the oxidation cell

The results in Section 3.1 and 3.2 have shown the structures and compositions of entrainment defects formed in AZ91 castings under cover gases of SF6/air and SF6/CO2. Different stages of the oxidation reaction may lead to the different structures and compositions of entrainment defects. Although Campbell has conjectured that an entrained gas may react with the surrounding melt, it is rarely reported that the reaction occurring between the Mg-alloy melt and entrapped cover gas. Previous researchers normally focus on the reaction between a Mg-alloy melt and the cover gas in an open environment [38,39,[46][47][48][49][50][51][52], which was different from the situation of a cover gas trapped into the melt. To further understand the formation of the entrainment defect in an AZ91 alloy, the evolution process of oxide films of the entrainment defect was further studied using an oxidation cell.

Fig. 10 (a and d) shows a surface film held for 5 min in the oxidation cell, protected by 0.5%SF6/air. There was only one single layer consisting of fluoride and oxide (MgF2 and MgO). In this surface film. Sulphur was detected in the EDS spectrum, but its amount was too small to be recognized in the element map. The structure and composition of this oxide film was similar to the single-layered films of entrainment defects shown in Fig. 4.

Fig. 10. Oxide films formed in the oxidation cell under a cover gas of 0.5%SF6/air and held at 700 °C for (a) 5 min; (b) 10 min; (c) 30 min, and (d-f) the SEM-EDS element maps (using Philips JEOL7000) corresponding to the oxide film shown in (a-c) respectively, (d) 5 min; (e) 10 min; (f) 30 min. The red points in (c and f) are the location references, denoting the boundary of the F-enriched layer in different element maps.

After a holding time of 10 min, a thin (O, S)-enriched top layer (around 700 nm) appeared upon the preliminary F-enriched film, forming a multi-layered structure, as shown in Fig. 10(b and e). The thickness of the (O, S)-enriched top layer increased with increased holding time. As shown in Fig. 10(c and f), the oxide film held for 30 min also had a multi-layered structure, but the thickness of its (O, S)-enriched top layer (around 2.5 µm) was higher than the that of the 10-min oxide film. The multi-layered oxide films shown in Fig. 10(b-c) presented a similar appearance to the films of the sandwich-like defect shown in Fig. 5.

The different structures of the oxide films shown in Fig. 10 indicated that fluorides in the cover gas would be preferentially consumed due to the reaction with the AZ91 alloy melt. After the depletion of fluorides, the residual cover gas reacted further with the liquid AZ91 alloy, forming the top (O, S)-enriched layer in the oxide film. Therefore, the different structures and compositions of entrainment defects shown in Figs. 4 and 5 may be due to an ongoing oxidation reaction between melt and entrapped cover gas.

This multi-layered structure has not been reported in previous publications concerning the protective surface film formed on a Mg-alloy melt [38,[46][47][48][49][50][51]. This may be due to the fact that previous researchers carried out their experiments with an un-limited amount of cover gas, creating a situation where the fluorides in the cover gas were not able to become depleted. Therefore, the oxide film of an entrainment defect had behaviour traits similar to the oxide films shown in Fig. 10, but different from the oxide films formed on the Mg-alloy melt surface reported in [38,[46][47][48][49][50][51].

Similar with the oxide films held in SF6/air, the oxide films formed in SF6/CO2 also had different structures with different holding times in the oxidation cell. Fig. 11(a) shows an oxide film, held on an AZ91 melt surface under a cover gas of 0.5%SF6/CO2 for 5 min. This film had a single-layered structure consisting of MgF2. The existence of MgO could not be confirmed in this film. After the holding time of 30 min, the film had a multi-layered structure; the inner layer was of a compact and uniform appearance and composed of MgF2, while the outer layer is the mixture of MgF2 and MgO. Sulphur was not detected in this film, which was different from the surface film formed in 0.5%SF6/air. Therefore, fluorides in the cover gas of 0.5%SF6/CO2 were also preferentially consumed at an early stage of the film growth process. Compared with the film formed in SF6/air, the MgO in film formed in SF6/CO2 appeared later and sulphide did not appear within 30 min. It may mean that the formation and evolution of film in SF6/air is faster than SF6/CO2. CO2 may have subsequently reacted with the melt to form MgO, while sulphur-containing compounds accumulated in the cover gas and reacted to form sulphide in very late stage (may after 30 min in oxidation cell).

Fig. 11. Oxide films formed in the oxidation cell under a cover gas of 0.5%SF6/CO2, and their SEM-EDS element maps (using Philips JEOL7000). They were held at 700 °C for (a) 5 min; (b) 30 min. The red points in (b) are the location references, denoting the boundary between the top and bottom layers in the oxide film.

4. Discussion

4.1. Evolution of entrainment defects formed in SF6/air

HSC software from Outokumpu HSC Chemistry for Windows (http://www.hsc-chemistry.net/) was used to carry out thermodynamic calculations needed to explore the reactions which might occur between the trapped gases and liquid AZ91 alloy. The solutions to the calculations suggest which products are most likely to form in the reaction process between a small amount of cover gas (i.e., the amount within a trapped bubble) and the AZ91-alloy melt.

In the trials, the pressure was set to 1 atm, and the temperature set to 700 °C. The amount of the cover gas was assumed to be 7 × 10−7 kg, with a volume of approximately 0.57 cm3 (3.14 × 10−8 kmol) for 0.5%SF6/air, and 0.35 cm3 (3.12 × 10−8 kmol) for 0.5%SF6/CO2. The amount of the AZ91 alloy melt in contact with the trapped gas was assumed to be sufficient to complete all reactions. The decomposition products of SF6 were SF5, SF4, SF3, SF2, F2, S(g), S2(g) and F(g) [57][58][59][60].

Fig. 12 shows the equilibrium diagram of the thermodynamic calculation of the reaction between the AZ91 alloy and 0.5%SF6/air. In the diagram, the reactants and products with less than 10−15 kmol have not been shown, as this was 5 orders of magnitude less than the amount of SF6 present (≈ 1.57 × 10−10 kmol) and therefore would not affect the observed process in a practical way.

Fig. 12. An equilibrium diagram for the reaction between 7e-7 kg 0.5%SF6/air and a sufficient amount of AZ91 alloy. The X axis is the amount of AZ91 alloy melt having reacted with the entrained gas, and the vertical Y-axis is the amount of the reactants and products.

This reaction process could be divided into 3 stages.

Stage 1: The formation of fluorides. the AZ91 melt preferentially reacted with SF6 and its decomposition products, producing MgF2, AlF3, and ZnF2. However, the amount of ZnF2 may have been too small to be detected practically (1.25 × 10−12 kmol of ZnF2 compared with 3 × 10−10 kmol of MgF2), which may be the reason why Zn was not detected in any the oxide films shown in Sections 3.13.3. Meanwhile, sulphur accumulated in the residual gas as SO2.

Stage 2: The formation of oxides. After the liquid AZ91 alloy had depleted all the available fluorides in the entrapped gas, the amount of AlF3 and ZnF2 quickly reduced due to a reaction with Mg. O2(g) and SO2 reacted with the AZ91 melt, forming MgO, Al2O3, MgAl2O4, ZnO, ZnSO4 and MgSO4. However, the amount of ZnO and ZnSO4 would have been too small to be found practically by EDS (e.g. 9.5 × 10−12 kmol of ZnO,1.38 × 10−14 kmol of ZnSO4, in contrast to 4.68 × 10−10 kmol of MgF2, when the amount of AZ91 on the X-axis is 2.5 × 10−9 kmol). In the experimental cases, the concentration of F in the cover gas is very low, whole the concentration f O is much higher. Therefore, the stage 1 and 2, i.e, the formation of fluoride and oxide may happen simultaneously at the beginning of the reaction, resulting in the formation of a singer-layered mixture of fluoride and oxide, as shown in Figs. 4 and 10(a). While an inner layer consisted of oxides but fluorides could form after the complete depletion of F element in the cover gas.

Stages 1- 2 theoretically verified the formation process of the multi-layered structure shown in Fig. 10.

The amount of MgAl2O4 and Al2O3 in the oxide film was of a sufficient amount to be detected, which was consistent with the oxide films shown in Fig. 4. However, the existence of aluminium could not be recognized in the oxide films grown in the oxidation cell, as shown in Fig. 10. This absence of Al may be due to the following reactions between the surface film and AZ91 alloy melt:(1)

Al2O3 + 3Mg + = 3MgO + 2Al, △G(700 °C) = -119.82 kJ/mol(2)

Mg + MgAl2O4 = MgO + Al, △G(700 °C) =-106.34 kJ/molwhich could not be simulated by the HSC software since the thermodynamic calculation was carried out under an assumption that the reactants were in full contact with each other. However, in a practical process, the AZ91 melt and the cover gas would not be able to be in contact with each other completely, due to the existence of the protective surface film.

Stage 3: The formation of Sulphide and nitride. After a holding time of 30 min, the gas-phase fluorides and oxides in the oxidation cell had become depleted, allowing the melt reaction with the residual gas, forming an additional sulphur-enriched layer upon the initial F-enriched or (F, O)-enriched surface film, thus resulting in the observed multi-layered structure shown in Fig. 10 (b and c). Besides, nitrogen reacted with the AZ91 melt until all reactions were completed. The oxide film shown in Fig. 6 may correspond to this reaction stage due to its nitride content. However, the results shows that the nitrides were not detected in the polished samples shown in Figs. 4 and 5, but only found on the test bar fracture surfaces. The nitrides may have hydrolysed during the sample preparation process, as follows [54]:(3)

Mg3N2 + 6H2O =3Mg(OH)2 + 2NH3↑(4)

AlN+ 3H2O =Al(OH)3 + NH3

In addition, Schmidt et al. [61] found that Mg3N2 and AlN could react to form ternary nitrides (Mg3AlnNn+2, n= 1, 2, 3…). HSC software did not contain the database of ternary nitrides, and it could not be added into the calculation. The oxide films in this stage may also contain ternary nitrides.

4.2. Evolution of entrainment defects formed in SF6/CO2

Fig. 13 shows the results of the thermodynamic calculation between AZ91 alloy and 0.5%SF6/CO2. This reaction processes can also be divided into three stages.

Fig. 13. An equilibrium diagram for the reaction between 7e-7 kg 0.5%SF6/CO2 and a sufficient amount of AZ91 alloy. The X axis denotes the amount of Mg alloy melt having reacted with the entrained gas, and the vertical Y-axis denotes the amounts of the reactants and products.

Stage 1: The formation of fluorides. SF6 and its decomposition products were consumed by the AZ91 melt, forming MgF2, AlF3, and ZnF2. As in the reaction of AZ91 in 0.5%SF6/air, the amount of ZnF2 was too small to be detected practically (1.51 × 10−13 kmol of ZnF2 compared with 2.67 × 10−10 kmol of MgF2). Sulphur accumulated in the residual trapped gas as S2(g) and a portion of the S2(g) reacted with CO2, to form SO2 and CO. The products in this reaction stage were consistent with the film shown in Fig. 11(a), which had a single layer structure that contained fluorides only.

Stage 2: The formation of oxides. AlF3 and ZnF2 reacted with the Mg in the AZ91 melt, forming MgF2, Al and Zn. The SO2 began to be consumed, producing oxides in the surface film and S2(g) in the cover gas. Meanwhile, the CO2 directly reacted with the AZ91 melt, forming CO, MgO, ZnO, and Al2O3. The oxide films shown in Figs. 9 and 11(b) may correspond to this reaction stage due to their oxygen-enriched layer and multi-layered structure.

The CO in the cover gas could further react with the AZ91 melt, producing C. This carbon may further react with Mg to form Mg carbides, when the temperature reduced (during solidification period) [62]. This may be the reason for the high carbon content in the oxide film shown in Figs. 89. Liang et al. [39] also reported carbon-detection in an AZ91 alloy surface film protected by SO2/CO2. The produced Al2O3 may be further combined with MgO, forming MgAl2O4 [63]. As discussed in Section 4.1, the alumina and spinel can react with Mg, causing an absence of aluminium in the surface films, as shown in Fig. 11.

Stage 3: The formation of Sulphide. the AZ91 melt began to consume S2(g) in the residual entrapped gas, forming ZnS and MgS. These reactions did not occur until the last stage of the reaction process, which could be the reason why the S-content in the defect shown Fig. 7(c) was small.

In summary, thermodynamic calculations indicate that the AZ91 melt will react with the cover gas to form fluorides firstly, then oxides and sulphides in the last. The oxide film in the different reaction stages would have different structures and compositions.

4.3. Effect of the carrier gases on consumption of the entrained gas and the reproducibility of AZ91 castings

The evolution processes of entrainment defects, formed in SF6/air and SF6/CO2, have been suggested in Sections 4.1 and 4.2. The theoretical calculations were verified with respect to the corresponding oxide films found in practical samples. The atmosphere within an entrainment defect could be efficiently consumed due to the reaction with liquid Mg-alloy, in a scenario dissimilar to the Al-alloy system (i.e., nitrogen in an entrained air bubble would not efficiently react with Al-alloy melt [64,65], however, nitrogen would be more readily consumed in liquid Mg alloys, commonly referred to as “nitrogen burning” [66]).

The reaction between the entrained gas and the surrounding liquid Mg-alloy converted the entrained gas into solid compounds (e.g. MgO) within the oxide film, thus reducing the void volume of the entrainment defect and hence probably causing a collapse of the defect (e.g., if an entrained gas of air was depleted by the surrounding liquid Mg-alloy, under an assumption that the melt temperature is 700 °C and the depth of liquid Mg-alloy is 10 cm, the total volume of the final solid products would be 0.044% of the initial volume taken by the entrapped air).

The relationship between the void volume reduction of entrainment defects and the corresponding casting properties has been widely studied in Al-alloy castings. Nyahumwa and Campbell [16] reported that the Hot Isostatic Pressing (HIP) process caused the entrainment defects in Al-alloy castings to collapse and their oxide surfaces forced into contact. The fatigue lives of their castings were improved after HIP. Nyahumwa and Campbell [16] also suggested a potential bonding of the double oxide films that were in contact with each other, but there was no direct evidence to support this. This binding phenomenon was further investigated by Aryafar et.al.[8], who re-melted two Al-alloy bars with oxide skins in a steel tube and then carried out a tensile strength test on the solidified sample. They found that the oxide skins of the Al-alloy bars strongly bonded with each other and became even stronger with an extension of the melt holding time, indicating a potential “healing” phenomenon due to the consumption of the entrained gas within the double oxide film structure. In addition, Raidszadeh and Griffiths [9,19] successfully reduced the negative effect of entrainment defects on the reproducibility of Al-alloy castings, by extending the melt holding time before solidification, which allowed the entrained gas to have a longer time to react with the surrounding melt.

With consideration of the previous work mentioned, the consumption of the entrained gas in Mg-alloy castings may diminish the negative effect of entrainment defects in the following two ways.

(1) Bonding phenomenon of the double oxide films. The sandwich-like structure shown in Fig. 5 and 7 indicated a potential bonding of the double oxide film structure. However, more evidence is required to quantify the increase in strength due to the bonding of the oxide films.

(2) Void volume reduction of entrainment defects. The positive effect of void-volume reduction on the quality of castings has been widely demonstrated by the HIP process [67]. As the evolution processes discussed in Section 4.14.2, the oxide films of entrainment defects can grow together due to an ongoing reaction between the entrained gas and surrounding AZ91 alloy melt. The volume of the final solid products was significant small compared with the entrained gas (i.e., 0.044% as previously mentioned).

Therefore, the consumption rate of the entrained gas (i.e., the growth rate of oxide films) may be a critical parameter for improving the quality of AZ91 alloy castings. The oxide film growth rate in the oxidization cell was accordingly further investigated.

Fig. 14 shows a comparison of the surface film growth rates in different cover gases (i.e., 0.5%SF6/air and 0.5%SF6/CO2). 15 random points on each sample were selected for film thickness measurements. The 95% confidence interval (95%CI) was computed under an assumption that the variation of the film thickness followed a Gaussian distribution. It can be seen that all the surface films formed in 0.5%SF6/air grew faster than those formed in 0.5%SF6/CO2. The different growth rates suggested that the entrained-gas consumption rate of 0.5%SF6/air was higher than that of 0.5%SF6/CO2, which was more beneficial for the consumption of the entrained gas.

Fig. 14. A comparison of the AZ91 alloy oxide film growth rates in 0.5%SF6/air and 0.5%SF6/CO2

It should be noted that, in the oxidation cell, the contact area of liquid AZ91 alloy and cover gas (i.e. the size of the crucible) was relatively small with consideration of the large volume of melt and gas. Consequently, the holding time for the oxide film growth within the oxidation cell was comparatively long (i.e., 5–30 min). However, the entrainment defects contained in a real casting are comparatively very small (i.e., a few microns size as shown in Figs. 36, and [7]), and the entrained gas is fully enclosed by the surrounding melt, creating a relatively large contact area. Hence the reaction time for cover gas and the AZ91 alloy melt may be comparatively short. In addition, the solidification time of real Mg-alloy sand castings can be a few minutes (e.g. Guo [68] reported that a Mg-alloy sand casting with 60 mm diameter required 4 min to be solidified). Therefore, it can be expected that an entrained gas trapped during an Mg-alloy melt pouring process will be readily consumed by the surrounding melt, especially for sand castings and large-size castings, where solidification times are long.

Therefore, the different cover gases (0.5%SF6/air and 0.5%SF6/CO2) associated with different consumption rates of the entrained gases may affect the reproducibility of the final castings. To verify this assumption, the AZ91 castings produced in 0.5%SF6/air and 0.5%SF6/CO2 were machined into test bars for mechanical evaluation. A Weibull analysis was carried out using both linear least square (LLS) method and non-linear least square (non-LLS) method [69].

Fig. 15(a-b) shows a traditional 2-p linearized Weibull plot of the UTS and elongation of the AZ91 alloy castings, obtained by the LLS method. The estimator used is P= (i-0.5)/N, which was suggested to cause the lowest bias among all the popular estimators [69,70]. The casting produced in SF6/air has an UTS Weibull moduli of 16.9, and an elongation Weibull moduli of 5.0. In contrast, the UTS and elongation Weibull modulus of the casting produced in SF6/CO2 are 7.7 and 2.7 respectively, suggesting that the reproducibility of the casting protected by SF6/CO2 were much lower than that produced in SF6/air.

Fig. 15. The Weibull modulus of AZ91 castings produced in different atmospheres, estimated by (a-b) the linear least square method, (c-d) the non-linear least square method, where SSR is the sum of residual squares.

In addition, the author’s previous publication [69] demonstrated a shortcoming of the linearized Weibull plots, which may cause a higher bias and incorrect R2 interruption of the Weibull estimation. A Non-LLS Weibull estimation was therefore carried out, as shown in Fig. 15 (c-d). The UTS Weibull modulus of the SF6/air casting was 20.8, while the casting produced under SF6/CO2 had a lower UTS Weibull modulus of 11.4, showing a clear difference in their reproducibility. In addition, the SF6/air elongation (El%) dataset also had a Weibull modulus (shape = 5.8) higher than the elongation dataset of SF6/CO2 (shape = 3.1). Therefore, both the LLS and Non-LLS estimations suggested that the SF6/air casting has a higher reproducibility than the SF6/CO2 casting. It supports the method that the use of air instead of CO2 contributes to a quicker consumption of the entrained gas, which may reduce the void volume within the defects. Therefore, the use of 0.5%SF6/air instead of 0.5%SF6/CO2 (which increased the consumption rate of the entrained gas) improved the reproducibility of the AZ91 castings.

However, it should be noted that not all the Mg-alloy foundries followed the casting process used in present work. The Mg-alloy melt in present work was degassed, thus reducing the effect of hydrogen on the consumption of the entrained gas (i.e., hydrogen could diffuse into the entrained gas, potentially suppressing the depletion of the entrained gas [7,71,72]). In contrast, in Mg-alloy foundries, the Mg-alloy melt is not normally degassed, since it was widely believed that there is not a ‘gas problem’ when casting magnesium and hence no significant change in tensile properties [73]. Although studies have shown the negative effect of hydrogen on the mechanical properties of Mg-alloy castings [41,42,73], a degassing process is still not very popular in Mg-alloy foundries.

Moreover, in present work, the sand mould cavity was flushed with the SF6 cover gas prior to pouring [22]. However, not all the Mg-alloy foundries flushed the mould cavity in this way. For example, the Stone Foundry Ltd (UK) used sulphur powder instead of the cover-gas flushing. The entrained gas within their castings may be SO2/air, rather than the protective gas.

Therefore, although the results in present work have shown that using air instead of CO2 improved the reproducibility of the final casting, it still requires further investigations to confirm the effect of carrier gases with respect to different industrial Mg-alloy casting processes.

7. Conclusion

Entrainment defects formed in an AZ91 alloy were observed. Their oxide films had two types of structure: single-layered and multi-layered. The multi-layered oxide film can grow together forming a sandwich-like structure in the final casting.2.

Both the experimental results and the theoretical thermodynamic calculations demonstrated that fluorides in the trapped gas were depleted prior to the consumption of sulphur. A three-stage evolution process of the double oxide film defects has been suggested. The oxide films contained different combinations of compounds, depending on the evolution stage. The defects formed in SF6/air had a similar structure to those formed in SF6/CO2, but the compositions of their oxide films were different. The oxide-film formation and evolution process of the entrainment defects were different from that of the Mg-alloy surface films previous reported (i.e., MgO formed prior to MgF2).3.

The growth rate of the oxide film was demonstrated to be greater under SF6/air than SF6/CO2, contributing to a quicker consumption of the damaging entrapped gas. The reproducibility of an AZ91 alloy casting improved when using SF6/air instead of SF6/CO2.

Acknowledgements

The authors acknowledge funding from the EPSRC LiME grant EP/H026177/1, and the help from Dr W.D. Griffiths and Mr. Adrian Carden (University of Birmingham). The casting work was carried out in University of Birmingham.

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Fig 3. Front view of the ejected powder particles due to the plume movement. Powder particles are colored by their respective temperature while trajectory colors show their magnitude at 0.007 seconds.

316-L 스테인리스강의 레이저 분말 베드 융합 중 콜드 스패터 형성의 충실도 높은 수치 모델링

316-L 스테인리스강의 레이저 분말 베드 융합 중 콜드 스패터 형성의 충실도 높은 수치 모델링

M. BAYAT1,* , AND J. H. HATTEL1

  • Corresponding author
    1 Technical University of Denmark (DTU), Building 425, Kgs. 2800 Lyngby, Denmark

ABSTRACT

Spatter and denudation are two very well-known phenomena occurring mainly during the laser powder bed fusion process and are defined as ejection and displacement of powder particles, respectively. The main driver of this phenomenon is the formation of a vapor plume jet that is caused by the vaporization of the melt pool which is subjected to the laser beam. In this work, a 3-dimensional transient turbulent computational fluid dynamics model coupled with a discrete element model is developed in the finite volume-based commercial software package Flow-3D AM to simulate the spatter phenomenon. The numerical results show that a localized low-pressure zone forms at the bottom side of the plume jet and this leads to a pseudo-Bernoulli effect that drags nearby powder particles into the area of influence of the vapor plume jet. As a result, the vapor plume acts like a momentum sink and therefore all nearby particles point are dragged towards this region. Furthermore, it is noted that due to the jet’s attenuation, powder particles start diverging from the central core region of the vapor plume as they move vertically upwards. It is moreover observed that only particles which are in the very central core region of the plume jet get sufficiently accelerated to depart the computational domain, while the rest of the dragged particles, especially those which undergo an early divergence from the jet axis, get stalled pretty fast as they come in contact with the resting fluid. In the last part of the work, two simulations with two different scanning speeds are carried out, where it is clearly observed that the angle between the departing powder particles and the vertical axis of the plume jet increases with increasing scanning speed.

스패터와 denudation은 주로 레이저 분말 베드 융합 과정에서 발생하는 매우 잘 알려진 두 가지 현상으로 각각 분말 입자의 배출 및 변위로 정의됩니다.

이 현상의 주요 동인은 레이저 빔을 받는 용융 풀의 기화로 인해 발생하는 증기 기둥 제트의 형성입니다. 이 작업에서 이산 요소 모델과 결합된 3차원 과도 난류 ​​전산 유체 역학 모델은 스패터 현상을 시뮬레이션하기 위해 유한 체적 기반 상용 소프트웨어 패키지 Flow-3D AM에서 개발되었습니다.

수치적 결과는 플룸 제트의 바닥면에 국부적인 저압 영역이 형성되고, 이는 근처의 분말 입자를 증기 플룸 제트의 영향 영역으로 끌어들이는 의사-베르누이 효과로 이어진다는 것을 보여줍니다.

결과적으로 증기 기둥은 운동량 흡수원처럼 작용하므로 근처의 모든 입자 지점이 이 영역으로 끌립니다. 또한 제트의 감쇠로 인해 분말 입자가 수직으로 위쪽으로 이동할 때 증기 기둥의 중심 코어 영역에서 발산하기 시작합니다.

더욱이 플룸 제트의 가장 중심 코어 영역에 있는 입자만 계산 영역을 벗어날 만큼 충분히 가속되는 반면, 드래그된 나머지 입자, 특히 제트 축에서 초기 발산을 겪는 입자는 정체되는 것으로 관찰됩니다. 그들은 휴식 유체와 접촉하기 때문에 꽤 빠릅니다.

작업의 마지막 부분에서 두 가지 다른 스캔 속도를 가진 두 가지 시뮬레이션이 수행되었으며, 여기서 출발하는 분말 입자와 연기 제트의 수직 축 사이의 각도가 스캔 속도가 증가함에 따라 증가하는 것이 명확하게 관찰되었습니다.

Fig 1. Two different views of the computational domain for the fluid domain. The vapor plume is simulated by a moving momentum source with a prescribed temperature of 3000 K.
Fig 1. Two different views of the computational domain for the fluid domain. The vapor plume is simulated by a moving momentum source with a prescribed temperature of 3000 K.
Fig 2. (a) and (b) are two snapshots taken at an x-y plane parallel to the powder layer plane before and 0.008 seconds after the start of the scanning process. (c) Shows a magnified view of (b) where detailed powder particles' movement along with their velocity magnitude and directions are shown.
Fig 2. (a) and (b) are two snapshots taken at an x-y plane parallel to the powder layer plane before and 0.008 seconds after the start of the scanning process. (c) Shows a magnified view of (b) where detailed powder particles’ movement along with their velocity magnitude and directions are shown.
Fig 3. Front view of the ejected powder particles due to the plume movement. Powder particles are colored by their respective temperature while trajectory colors show their magnitude at 0.007 seconds.
Fig 3. Front view of the ejected powder particles due to the plume movement. Powder particles are colored by their respective temperature while trajectory colors show their magnitude at 0.007 seconds.

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Figure 2. Schematic diagram for pilot-scale cooling-water circulation system (a) along with a real picture of the system (b).

Application of Computational Fluid Dynamics in Chlorine-Dynamics Modeling of In-Situ Chlorination Systems for Cooling Systems

Jongchan Yi 1, Jonghun Lee 1, Mohd Amiruddin Fikri 2,3, Byoung-In Sang 4 and Hyunook Kim 1,*

Abstract

염소화는 상대적인 효율성과 저렴한 비용으로 인해 발전소 냉각 시스템에서 생물학적 오염을 제어하는​​데 선호되는 방법입니다. 해안 지역에 발전소가 있는 경우 바닷물을 사용하여 현장에서 염소를 전기화학적으로 생성할 수 있습니다. 이를 현장 전기염소화라고 합니다. 이 접근 방식은 유해한 염소화 부산물이 적고 염소를 저장할 필요가 없다는 점을 포함하여 몇 가지 장점이 있습니다. 그럼에도 불구하고, 이 전기화학적 공정은 실제로는 아직 초기 단계에 있습니다. 이 연구에서는 파일럿 규모 냉각 시스템에서 염소 붕괴를 시뮬레이션하기 위해 병렬 1차 동역학을 적용했습니다. 붕괴가 취수관을 따라 발생하기 때문에 동역학은 전산유체역학(CFD) 코드에 통합되었으며, 이후에 파이프의 염소 거동을 시뮬레이션하는데 적용되었습니다. 실험과 시뮬레이션 데이터는 강한 난류가 형성되는 조건하에서도 파이프 벽을 따라 염소 농도가 점진적인 것으로 나타났습니다. 염소가 중간보다 파이프 표면을 따라 훨씬 더 집중적으로 남아 있다는 사실은 전기 염소화를 기반으로 하는 시스템의 전체 염소 요구량을 감소시킬 수 있었습니다. 현장 전기 염소화 방식의 냉각 시스템은 직접 주입 방식에 필요한 염소 사용량의 1/3만 소비했습니다. 따라서 현장 전기염소화는 해안 지역의 발전소에서 바이오파울링 제어를 위한 비용 효율적이고 환경 친화적인 접근 방식으로 사용될 수 있다고 결론지었습니다.

Chlorination is the preferred method to control biofouling in a power plant cooling system due to its comparative effectiveness and low cost. If a power plant is located in a coastal area, chlorine can be electrochemically generated in-situ using seawater, which is called in-situ electrochlorination; this approach has several advantages including fewer harmful chlorination byproducts and no need for chlorine storage. Nonetheless, this electrochemical process is still in its infancy in practice. In this study, a parallel first-order kinetics was applied to simulate chlorine decay in a pilot-scale cooling system. Since the decay occurs along the water-intake pipe, the kinetics was incorporated into computational fluid dynamics (CFD) codes, which were subsequently applied to simulate chlorine behavior in the pipe. The experiment and the simulation data indicated that chlorine concentrations along the pipe wall were incremental, even under the condition where a strong turbulent flow was formed. The fact that chlorine remained much more concentrated along the pipe surface than in the middle allowed for the reduction of the overall chlorine demand of the system based on the electro-chlorination. The cooling system, with an in-situ electro-chlorination, consumed only 1/3 of the chlorine dose demanded by the direct injection method. Therefore, it was concluded that in-situ electro-chlorination could serve as a cost-effective and environmentally friendly approach for biofouling control at power plants on coastal areas.

Keywords

computational fluid dynamics; power plant; cooling system; electro-chlorination; insitu chlorination

Figure 1. Electrodes and batch experiment set-up. (a) Two cylindrical electrodes used in this study. (b) Batch experiment set-up for kinetic tests.
Figure 1. Electrodes and batch experiment set-up. (a) Two cylindrical electrodes used in this study. (b) Batch experiment set-up for kinetic tests.
Figure 2. Schematic diagram for pilot-scale cooling-water circulation system (a) along with a real picture of the system (b).
Figure 2. Schematic diagram for pilot-scale cooling-water circulation system (a) along with a real picture of the system (b).
Figure 3. Free chlorine decay curves in seawater with different TOC and initial chlorine concentration. Each line represents the predicted concentration of chlorine under a given condition. (a) Artificial seawater solution with 1 mg L−1 of TOC; (b) artificial seawater solution with 2 mg L−1 of TOC; (c) artificial seawater solution with 3 mg L−1 of TOC; (d) West Sea water (1.3 mg L−1 of TOC).
Figure 3. Free chlorine decay curves in seawater with different TOC and initial chlorine concentration. Each line represents the predicted concentration of chlorine under a given condition. (a) Artificial seawater solution with 1 mg L−1 of TOC; (b) artificial seawater solution with 2 mg L−1 of TOC; (c) artificial seawater solution with 3 mg L−1 of TOC; (d) West Sea water (1.3 mg L−1 of TOC).
Figure 4. Correlation between model and experimental data in the chlorine kinetics using seawater.
Figure 4. Correlation between model and experimental data in the chlorine kinetics using seawater.
Figure 5. Free chlorine concentrations in West Sea water under different current conditions in an insitu electro-chlorination system.
Figure 5. Free chlorine concentrations in West Sea water under different current conditions in an insitu electro-chlorination system.
Figure 6. Free chlorine distribution along the sampling ports under different flow rates. Each dot represents experimental data, and each point on the black line is the expected chlorine concentration obtained from computational fluid dynamics (CFD) simulation with a parallel first-order decay model. The red-dotted line is the desirable concentration at the given flow rate: (a) 600 L min−1 of flow rate, (b) 700 L min−1 of flow rate, (c) 800 L min−1 of flow rate, (d) 900 L min−1 of flow rate.
Figure 6. Free chlorine distribution along the sampling ports under different flow rates. Each dot represents experimental data, and each point on the black line is the expected chlorine concentration obtained from computational fluid dynamics (CFD) simulation with a parallel first-order decay model. The red-dotted line is the desirable concentration at the given flow rate: (a) 600 L min−1 of flow rate, (b) 700 L min−1 of flow rate, (c) 800 L min−1 of flow rate, (d) 900 L min−1 of flow rate.
Figure 7. Fluid contour images from CFD simulation of the electro-chlorination experiment. Inlet flow rate is 800 L min−1. Outlet pressure was set to 10.8 kPa. (a) Chlorine concentration; (b) expanded view of electrode side in image (a); (c) velocity magnitude; (d) pressure.
Figure 7. Fluid contour images from CFD simulation of the electro-chlorination experiment. Inlet flow rate is 800 L min−1. Outlet pressure was set to 10.8 kPa. (a) Chlorine concentration; (b) expanded view of electrode side in image (a); (c) velocity magnitude; (d) pressure.
Figure 8. Chlorine concentration contour in the simulation of full-scale in-situ electro-chlorination with different cathode positions. The pipe diameter is 2 m and the flow rate is 14 m3 s−1. The figure shows 10 m of the pipeline. (a) The simulation result when the cathode is placed on the surface of the pipe wall. (b) The simulation result when the cathode is placed on the inside of the pipe with 100 mm of distance from the pipe wall.
Figure 8. Chlorine concentration contour in the simulation of full-scale in-situ electro-chlorination with different cathode positions. The pipe diameter is 2 m and the flow rate is 14 m3 s−1. The figure shows 10 m of the pipeline. (a) The simulation result when the cathode is placed on the surface of the pipe wall. (b) The simulation result when the cathode is placed on the inside of the pipe with 100 mm of distance from the pipe wall.
Figure 9. Comparison of in-situ electro-chlorination and direct chlorine injection in full-scale applications. (a) Estimated chlorine concentrations along the pipe surface. (b) Relative chlorine demands.
Figure 9. Comparison of in-situ electro-chlorination and direct chlorine injection in full-scale applications. (a) Estimated chlorine concentrations along the pipe surface. (b) Relative chlorine demands.

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Fig. 3. Experimental angled top-view setup for laser welding of zinc-coated steel with a laser illumination.

Effect of zinc vapor forces on spattering in partial penetration laser welding of zinc-coated steels

Yu Hao a, Nannan Chen a,b, Hui-Ping Wang c,*, Blair E. Carlson c, Fenggui Lu a,*
a Shanghai Key Laboratory of Materials Laser Processing and Modification, School of Materials Science and Engineering, Shanghai Jiao Tong University, Shanghai,
200240, PR China b Department of Industrial and Manufacturing Eng

ABSTRACT

A three-dimensional thermal-fluid numerical model considering zinc vapor interaction with the molten pool was developed to study the occurrence of zinc vapor-induced spatter in partial penetration laser overlap welding of zinc-coated steels. The zinc vapor effect was represented by two forces: a jet pressure force acting on the keyhole rear wall as the vapor bursts into the keyhole and a drag force on the upper keyhole wall as the vapor escapes upwards. The numerical model was calibrated by comparing the predicted keyhole shape with the keyhole shape observed by high-speed X-ray imaging and applied for various weld schedules. The study showed that large jet pressure forces induced violent fluctuations of the keyhole rear wall, resulting in an unstable keyhole and turbulent melt flow. A large drag force pushed the melt adjacent to the keyhole surface upward and accelerated the movement of the melt whose velocities reached 1 m/s or even higher, potentially inducing spatter. Increased heat input facilitated the occurrence of large droplets of spatter, which agreed with experimental observations captured by high-speed camera.

아연도금강의 부분용입 레이저 겹침용접에서 아연증기유도 스패터의 발생을 연구하기 위하여 용융풀과의 아연증기 상호작용을 고려한 3차원 열유체 수치모델을 개발하였습니다.

아연 증기 효과는 증기가 열쇠 구멍으로 폭발할 때 키홀 뒤쪽 벽에 작용하는 제트 압력력과 증기가 위쪽으로 빠져나갈 때 위쪽 키홀 벽에 작용하는 항력의 두 가지 힘으로 표시됩니다.

수치 모델은 예측된 열쇠 구멍 모양과 고속 X선 영상으로 관찰된 키홀 모양을 비교하여 보정하고 다양한 용접 일정에 적용했습니다.

이 연구는 큰 제트 압력이 키홀 뒷벽의 격렬한 변동을 유발하여 불안정한 열쇠 구멍과 난류 용융 흐름을 초래한다는 것을 보여주었습니다. 큰 항력은 키홀 표면에 인접한 용융물을 위로 밀어올리고 속도가 1m/s 이상에 도달한 용융물의 이동을 가속화하여 잠재적으로 스패터를 유발할 수 있습니다.

증가된 열 입력은 고속 카메라로 포착한 실험적 관찰과 일치하는 큰 방울의 스패터 발생을 촉진했습니다.

Fig. 1. Schematic of zero-gap laser welding of zinc-coated steel.
Fig. 1. Schematic of zero-gap laser welding of zinc-coated steel.
Fig. 2. Experimental setup for capturing a side view of the laser welding of zinc-coated steel enabled by use of high-temperature glass.
Fig. 2. Experimental setup for capturing a side view of the laser welding of zinc-coated steel enabled by use of high-temperature glass.
Fig. 3. Experimental angled top-view setup for laser welding of zinc-coated steel with a laser illumination.
Fig. 3. Experimental angled top-view setup for laser welding of zinc-coated steel with a laser illumination.
Fig. 4. Schematic of the rotating Gaussian body heat source.
Fig. 4. Schematic of the rotating Gaussian body heat source.
Fig. 5. Schematic of jet pressure force caused by zinc vapor: (a) locating the outlet of zinc vapor (point A), (b) schematic of assigning the jet pressure force.
Fig. 5. Schematic of jet pressure force caused by zinc vapor: (a) locating the outlet of zinc vapor (point A), (b) schematic of assigning the jet pressure force.
Fig. 6. Schematic of drag force caused by zinc vapor.
Fig. 6. Schematic of drag force caused by zinc vapor.
Fig. 7. Procedure for calculating the outgassing velocity of zinc vapor.
Fig. 7. Procedure for calculating the outgassing velocity of zinc vapor.
Fig. 8. Schematic related to calculating the zone of vaporized zinc.
Fig. 8. Schematic related to calculating the zone of vaporized zinc.
Fig. 9. The meshed domains for the thermal-fluid simulation of laser welding.
Fig. 9. The meshed domains for the thermal-fluid simulation of laser welding.
Fig. 10. The calculated temperature field and validation: (a) 3-D temperature field; (b)-(f) Comparison of experimental and simulated weld cross section: (b) P = 2000 W, v = 50 mm/s; (c) P = 2500 W, v = 50 mm/s; (d) P = 3000 W, v = 50 mm/s; (e) P = 3000 W, v = 60 mm/s; (f) P = 3000 W, v = 70 mm/s.
Fig. 10. The calculated temperature field and validation: (a) 3-D temperature field; (b)-(f) Comparison of experimental and simulated weld cross section: (b) P = 2000 W, v = 50 mm/s; (c) P = 2500 W, v = 50 mm/s; (d) P = 3000 W, v = 50 mm/s; (e) P = 3000 W, v = 60 mm/s; (f) P = 3000 W, v = 70 mm/s.
Fig. 11. Comparison of X-Ray images of in-process keyhole profiles and the numerical predictions: (a) Single sheet penetration (P = 480 W, v = 150 mm/s); (b) Two sheet penetration (P = 532 W, v = 150 mm/s).
Fig. 11. Comparison of X-Ray images of in-process keyhole profiles and the numerical predictions: (a) Single sheet penetration (P = 480 W, v = 150 mm/s); (b) Two sheet penetration (P = 532 W, v = 150 mm/s).
Fig. 12. High-speed images of dynamic keyhole in laser welding of steels: (a) without zinc coating (b) with zinc coating.
Fig. 12. High-speed images of dynamic keyhole in laser welding of steels: (a) without zinc coating (b) with zinc coating.
Fig. 13. Mass loss and molten pool observation under different laser power and welding velocity for 1.2 mm + 1.2 mm HDG 420LA stack-up
Fig. 13. Mass loss and molten pool observation under different laser power and welding velocity for 1.2 mm + 1.2 mm HDG 420LA stack-up
Fig. 14. Numerical results of keyhole and flow field in molten pool: (a) without zinc vapor forces, (b) with zinc vapor forces.
Fig. 14. Numerical results of keyhole and flow field in molten pool: (a) without zinc vapor forces, (b) with zinc vapor forces.
Fig. 18. Calculated velocity fields for different welding parameters: (a) P = 2 kW, v = 50 mm/s, (b) P = 2.5 kW, v = 50 mm/s, (c) P = 3 kW, v = 50 mm/s, (d) P = 3 kW, v = 60 mm/s, (e) P = 3 kW, v = 70 mm/s.
Fig. 18. Calculated velocity fields for different welding parameters: (a) P = 2 kW, v = 50 mm/s, (b) P = 2.5 kW, v = 50 mm/s, (c) P = 3 kW, v = 50 mm/s, (d) P = 3 kW, v = 60 mm/s, (e) P = 3 kW, v = 70 mm/s.
Fig. 19. Schematic of the generation of spatter in different sizes: (a) small size, (b) large size.
Fig. 19. Schematic of the generation of spatter in different sizes: (a) small size, (b) large size.

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Figure 1. (a) Top view of the microfluidic-magnetophoretic device, (b) Schematic representation of the channel cross-sections studied in this work, and (c) the magnet position relative to the channel location (Sepy and Sepz are the magnet separation distances in y and z, respectively).

Continuous-Flow Separation of Magnetic Particles from Biofluids: How Does the Microdevice Geometry Determine the Separation Performance?

1Department of Chemical and Biomolecular Engineering, ETSIIT, University of Cantabria, Avda. Los Castros s/n, 39005 Santander, Spain
2William G. Lowrie Department of Chemical and Biomolecular Engineering, The Ohio State University, 151 W. Woodruff Ave., Columbus, OH 43210, USA
*Author to whom correspondence should be addressed.
Sensors 202020(11), 3030; https://doi.org/10.3390/s20113030
Received: 16 April 2020 / Revised: 21 May 2020 / Accepted: 25 May 2020 / Published: 27 May 2020
(This article belongs to the Special Issue Lab-on-a-Chip and Microfluidic Sensors)

Abstract

The use of functionalized magnetic particles for the detection or separation of multiple chemicals and biomolecules from biofluids continues to attract significant attention. After their incubation with the targeted substances, the beads can be magnetically recovered to perform analysis or diagnostic tests. Particle recovery with permanent magnets in continuous-flow microdevices has gathered great attention in the last decade due to the multiple advantages of microfluidics. As such, great efforts have been made to determine the magnetic and fluidic conditions for achieving complete particle capture; however, less attention has been paid to the effect of the channel geometry on the system performance, although it is key for designing systems that simultaneously provide high particle recovery and flow rates. Herein, we address the optimization of Y-Y-shaped microchannels, where magnetic beads are separated from blood and collected into a buffer stream by applying an external magnetic field. The influence of several geometrical features (namely cross section shape, thickness, length, and volume) on both bead recovery and system throughput is studied. For that purpose, we employ an experimentally validated Computational Fluid Dynamics (CFD) numerical model that considers the dominant forces acting on the beads during separation. Our results indicate that rectangular, long devices display the best performance as they deliver high particle recovery and high throughput. Thus, this methodology could be applied to the rational design of lab-on-a-chip devices for any magnetically driven purification, enrichment or isolation.

Keywords: particle magnetophoresisCFDcross sectionchip fabrication

Korea Abstract

생체 유체에서 여러 화학 물질과 생체 분자의 검출 또는 분리를위한 기능화 된 자성 입자의 사용은 계속해서 상당한 관심을 받고 있습니다. 표적 물질과 함께 배양 한 후 비드를 자기 적으로 회수하여 분석 또는 진단 테스트를 수행 할 수 있습니다. 연속 흐름 마이크로 장치에서 영구 자석을 사용한 입자 회수는 마이크로 유체의 여러 장점으로 인해 지난 10 년 동안 큰 관심을 모았습니다. 

따라서 완전한 입자 포획을 달성하기 위한 자기 및 유체 조건을 결정하기 위해 많은 노력을 기울였습니다. 그러나 높은 입자 회수율과 유속을 동시에 제공하는 시스템을 설계하는 데있어 핵심이기는 하지만 시스템 성능에 대한 채널 형상의 영향에 대해서는 덜주의를 기울였습니다. 

여기에서 우리는 자기 비드가 혈액에서 분리되고 외부 자기장을 적용하여 버퍼 스트림으로 수집되는 YY 모양의 마이크로 채널의 최적화를 다룹니다. 비드 회수 및 시스템 처리량에 대한 여러 기하학적 특징 (즉, 단면 형상, 두께, 길이 및 부피)의 영향을 연구합니다. 

이를 위해 분리 중에 비드에 작용하는 지배적인 힘을 고려하는 실험적으로 검증 된 CFD (Computational Fluid Dynamics) 수치 모델을 사용합니다. 우리의 결과는 직사각형의 긴 장치가 높은 입자 회수율과 높은 처리량을 제공하기 때문에 최고의 성능을 보여줍니다. 

따라서 이 방법론은 자기 구동 정제, 농축 또는 분리를 위한 랩온어 칩 장치의 합리적인 설계에 적용될 수 있습니다.

Figure 1. (a) Top view of the microfluidic-magnetophoretic device, (b) Schematic representation of the channel cross-sections studied in this work, and (c) the magnet position relative to the channel location (Sepy and Sepz are the magnet separation distances in y and z, respectively).
Figure 1. (a) Top view of the microfluidic-magnetophoretic device, (b) Schematic representation of the channel cross-sections studied in this work, and (c) the magnet position relative to the channel location (Sepy and Sepz are the magnet separation distances in y and z, respectively).
Figure 2. (a) Channel-magnet configuration and (b–d) magnetic force distribution in the channel midplane for 2 mm, 5 mm and 10 mm long rectangular (left) and U-shaped (right) devices.
Figure 2. (a) Channel-magnet configuration and (b–d) magnetic force distribution in the channel midplane for 2 mm, 5 mm and 10 mm long rectangular (left) and U-shaped (right) devices.
Figure 3. (a) Velocity distribution in a section perpendicular to the flow for rectangular (left) and U-shaped (right) cross section channels, and (b) particle location in these cross sections.
Figure 3. (a) Velocity distribution in a section perpendicular to the flow for rectangular (left) and U-shaped (right) cross section channels, and (b) particle location in these cross sections.
Figure 4. Influence of fluid flow rate on particle recovery when the applied magnetic force is (a) different and (b) equal in U-shaped and rectangular cross section microdevices.
Figure 4. Influence of fluid flow rate on particle recovery when the applied magnetic force is (a) different and (b) equal in U-shaped and rectangular cross section microdevices.
Figure 5. Magnetic bead capture as a function of fluid flow rate for all of the studied geometries.
Figure 5. Magnetic bead capture as a function of fluid flow rate for all of the studied geometries.
Figure 6. Influence of (a) magnetic and fluidic forces (J parameter) and (b) channel geometry (θ parameter) on particle recovery. Note that U-2mm does not accurately fit a line.
Figure 6. Influence of (a) magnetic and fluidic forces (J parameter) and (b) channel geometry (θ parameter) on particle recovery. Note that U-2mm does not accurately fit a line.
Figure 7. Dependence of bead capture on the (a) functional channel volume and (b) particle residence time (tres). Note that in the curve fitting expressions V represents the functional channel volume and that U-2mm does not accurately fit a line.
Figure 7. Dependence of bead capture on the (a) functional channel volume and (b) particle residence time (tres). Note that in the curve fitting expressions V represents the functional channel volume and that U-2mm does not accurately fit a line.

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Fluid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 3: (a,b) Magnet distance d = 0; (c,d) Magnet distance d = 1 mm.

Numerical Analysis of Bead Magnetophoresis from Flowing Blood in a Continuous-Flow Microchannel: Implications to the Bead-Fluid Interactions

Scientific Reports volume 9, Article number: 7265 (2019) Cite this article

Abstract

이 연구에서는 비드 운동과 유체 흐름에 미치는 영향에 대한 자세한 분석을 제공하기 위해 연속 흐름 마이크로 채널 내부의 비드 자기 영동에 대한 수치 흐름 중심 연구를 보고합니다.

수치 모델은 Lagrangian 접근 방식을 포함하며 영구 자석에 의해 생성 된 자기장의 적용에 의해 혈액에서 비드 분리 및 유동 버퍼로의 수집을 예측합니다.

다음 시나리오가 모델링됩니다. (i) 운동량이 유체에서 점 입자로 처리되는 비드로 전달되는 단방향 커플 링, (ii) 비드가 점 입자로 처리되고 운동량이 다음으로부터 전달되는 양방향 결합 비드를 유체로 또는 그 반대로, (iii) 유체 변위에서 비드 체적의 영향을 고려한 양방향 커플 링.

결과는 세 가지 시나리오에서 비드 궤적에 약간의 차이가 있지만 특히 높은 자기력이 비드에 적용될 때 유동장에 상당한 변화가 있음을 나타냅니다.

따라서 높은 자기력을 사용할 때 비드 운동과 유동장의 체적 효과를 고려한 정확한 전체 유동 중심 모델을 해결해야 합니다. 그럼에도 불구하고 비드가 중간 또는 낮은 자기력을 받을 때 계산적으로 저렴한 모델을 안전하게 사용하여 자기 영동을 모델링 할 수 있습니다.

Sketch of the magnetophoresis process in the continuous-flow microdevice.
Sketch of the magnetophoresis process in the continuous-flow microdevice.
Schematic view of the microdevice showing the working conditions set in the simulations.
Schematic view of the microdevice showing the working conditions set in the simulations.
Bead trajectories for different magnetic field conditions, magnet placed at different distances “d” from the channel: (a) d = 0; (b) d = 1 mm; (c) d = 1.5 mm; (d) d = 2 mm
Bead trajectories for different magnetic field conditions, magnet placed at different distances “d” from the channel: (a) d = 0; (b) d = 1 mm; (c) d = 1.5 mm; (d) d = 2 mm
Separation efficacy as a function of the magnet distance. Comparison between one-way and two-way coupling.
Separation efficacy as a function of the magnet distance. Comparison between one-way and two-way coupling.
(a) Fluid velocity magnitude including velocity vectors and (b) blood volumetric fraction contours with magnet distance d = 0 mm for scenario 1 (t = 0.25 s).
(a) Fluid velocity magnitude including velocity vectors and (b) blood volumetric fraction contours with magnet distance d = 0 mm for scenario 1 (t = 0.25 s).
luid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 2: (a,b) Magnet distance d = 0 mm at t = 0.4 s; (c,d) Magnet distance d = 1 mm at t = 0.4 s.
luid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 2: (a,b) Magnet distance d = 0 mm at t = 0.4 s; (c,d) Magnet distance d = 1 mm at t = 0.4 s.
Fluid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 3: (a,b) Magnet distance d = 0; (c,d) Magnet distance d = 1 mm.
Fluid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 3: (a,b) Magnet distance d = 0; (c,d) Magnet distance d = 1 mm.
Blood volumetric fraction contours. Scenario 1: (a) Magnet distance d = 0 and (b) Magnet distance d = 1 mm; Scenario 2: (c) Magnet distance d = 0 and (d) Magnet distance d = 1 mm; and Scenario 3: (e) Magnet distance d = 0 and (f) Magnet distance d = 1 mm.
Blood volumetric fraction contours. Scenario 1: (a) Magnet distance d = 0 and (b) Magnet distance d = 1 mm; Scenario 2: (c) Magnet distance d = 0 and (d) Magnet distance d = 1 mm; and Scenario 3: (e) Magnet distance d = 0 and (f) Magnet distance d = 1 mm.

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Author information

  1. Edward P. Furlani is deceased.

Affiliations

  1. Department of Chemical and Biomolecular Engineering, ETSIIT, University of Cantabria, Avda. Los Castros s/n, 39005, Santander, SpainJenifer Gómez-Pastora, Eugenio Bringas & Inmaculada Ortiz
  2. Flow Science, Inc, Santa Fe, New Mexico, 87505, USAIoannis H. Karampelas
  3. Department of Chemical and Biological Engineering, University at Buffalo (SUNY), Buffalo, New York, 14260, USAEdward P. Furlani
  4. Department of Electrical Engineering, University at Buffalo (SUNY), Buffalo, New York, 14260, USAEdward P. Furlani
The Simulation of Droplet Impact on the Super-Hydrophobic Surface with Micro-Pillar Arrays Fabricated by Laser Irradiation and Silanization Processes

The simulation of droplet impact on the super-hydrophobic surface with micro-pillar arrays fabricated by laser irradiation and silanization processes

레이저 조사 및 silanization 공정으로 제작된 micro-pillar arrays를 사용하여 초 소수성 표면에 대한 액적 영향 시뮬레이션

ZhenyanXiaa YangZhaoa ZhenYangabc ChengjuanYangab LinanLia ShibinWanga MengWangab
aSchool of Mechanical Engineering, Tianjin University, Tianjin, 300054, China
bKey Laboratory of Mechanism Theory and Equipment Design of Ministry of Education, Tianjin, 300072, Chinac
School of Engineering, University of Warwick, Coventry, CV4 7AL, UK

Received 23 September 2020, Revised 17 November 2020, Accepted 26 November 2020, Available online 11 December 2020.

Abstract

Super-hydrophobicity is one of the significant natural phenomena, which has inspired researchers to fabricate artificial smart materials using advanced manufacturing techniques. In this study, a super-hydrophobic aluminum surface was prepared by nanosecond laser texturing and FAS modification in sequence. The surface wettability turned from original hydrophilicity to super-hydrophilicity immediately after laser treatment. Then it changed to super-hydrophobicity showing a WCA of 157.6 ± 1.2° with a SA of 1.7 ± 0.7° when the laser-induced rough surface being coated with a layer of FAS molecules. The transforming mechanism was further explored from physical and chemical aspects based on the analyses of surface morphology and surface chemistry. Besides, the motion process of droplet impacting super-hydrophobic surface was systematically analyzed via the optimization of simulation calculation grid and the simulation method of volume of fluid (VOF). Based on this simulation method, the morphological changes, the inside pressure distribution and velocity of the droplet were further investigated. And the motion mechanism of the droplet on super-hydrophobic surface was clearly revealed in this paper. The simulation results and the images captured by high-speed camera were highly consistent, which indicated that the computational fluid dynamics (CFD) is an effective method to predict the droplet motion on super- hydrophobic surfaces. This paper can provide an explicit guidance for the selection of suitable methods for functional surfaces with different requirements in the industry.

Korea Abstract

초 소수성은 연구원들이 첨단 제조 기술을 사용하여 인공 스마트 재료를 제작하도록 영감을 준 중요한 자연 현상 중 하나 입니다. 이 연구에서 초 소수성 알루미늄 표면은 나노초 레이저 텍스처링과 FAS 수정에 의해 순서대로 준비되었습니다.

레이저 처리 직후 표면 습윤성은 원래의 친수성에서 초 친수성으로 바뀌 었습니다. 그런 다음 레이저 유도 거친 표면을 FAS 분자 층으로 코팅했을 때 WCA가 157.6 ± 1.2 °이고 SA가 1.7 ± 0.7 ° 인 초 소수성으로 변경되었습니다.

변형 메커니즘은 표면 형태 및 표면 화학 분석을 기반으로 물리적 및 화학적 측면에서 추가로 탐구 되었습니다. 또한, 초 소수성 표면에 영향을 미치는 물방울의 운동 과정은 시뮬레이션 계산 그리드의 최적화와 유체 부피 (VOF) 시뮬레이션 방법을 통해 체계적으로 분석되었습니다.

이 시뮬레이션 방법을 바탕으로 형태학적 변화, 내부 압력 분포 및 액 적의 속도를 추가로 조사했습니다. 그리고 초 소수성 표면에 있는 물방울의 운동 메커니즘이 이 논문에서 분명하게 드러났습니다.

시뮬레이션 결과와 고속 카메라로 캡처한 이미지는 매우 일관적 이었습니다. 이는 전산 유체 역학 (CFD)이 초 소수성 표면에서 액적 움직임을 예측하는 효과적인 방법임을 나타냅니다.

이 백서는 업계의 다양한 요구 사항을 가진 기능 표면에 적합한 방법을 선택하기 위한 명시적인 지침을 제공 할 수 있습니다.

Keywords: Laser irradiation; Wettability; Droplet impact; Simulation; VOF

Introduction

서식지에 적응하기 위해 많은 자연 식물과 동물에서 특별한 습윤 표면이 진화되었습니다 [1-3]. 연잎은 먼지에 의한 오염으로부터 스스로를 보호하기 위해 우수한 자가 청소 특성을 나타냅니다 [4]. 사막 딱정벌레는 공기에서 물을 수확할 수 있는 기능적 표면 때문에 건조한 사막에서 생존 할 수 있습니다 [5].

자연 세계에서 영감을 받아 고체 기질의 표면 습윤성을 수정하는데 더 많은 관심이 집중되었습니다 [6-7]. 기능성 표면의 우수한 성능은 고유 한 표면 습윤성에 기인하며, 이는 고체 표면에서 액체의 확산 능력을 반영하는 중요한 특성 중 하나입니다 [8].

일반적으로 물 접촉각 (WCA) 값에 따라 90 °는 친수성과 소수성의 경계로 간주됩니다. WCA가 90 ° 이상인 소수성 표면, WCA가 90 ° 미만인 친수성 표면 [9 ]. 특히 고체 표면은 WCA가 10 ° 미만의 슬라이딩 각도 (SA)에서 150 °를 초과 할 때 특별한 초 소수성을 나타냅니다 [10-11].

<내용 중략> ……

 The Simulation of Droplet Impact on the Super-Hydrophobic Surface with Micro-Pillar Arrays Fabricated by Laser Irradiation and Silanization Processes
The Simulation of Droplet Impact on the Super-Hydrophobic Surface with Micro-Pillar Arrays Fabricated by Laser Irradiation and Silanization Processes

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A new dynamic masking technique for time resolved PIV analysis

A new dynamic masking technique for time resolved PIV analysis

시간 분해 PIV 분석을위한 새로운 동적 마스킹 기술

물체 가시성을 허용하기 위해 형광 코팅과 결합 된 새로운 프리웨어 레이 캐스팅 도구

Journal of Visualization ( 2021 ) 이 기사 인용

Abstract

Time resolved PIV encompassing moving and/or deformable objects interfering with the light source requires the employment of dynamic masking (DM). A few DM techniques have been recently developed, mainly in microfluidics and multiphase flows fields. Most of them require ad-hoc design of the experimental setup, and may spoil the accuracy of the resulting PIV analysis. A new DM technique is here presented which envisages, along with a dedicated masking algorithm, the employment of fluorescent coating to allow for accurate tracking of the object. We show results from measurements obtained through a validated PIV setup demonstrating the need to include a DM step even for objects featuring limited displacements. We compare the proposed algorithm with both a no-masking and a static masking solution. In the framework of developing low cost, flexible and accurate PIV setups, the proposed algorithm is made available through a freeware application able to generate masks to be used by an existing, freeware PIV analysis package.

광원을 방해하는 이동 또는 변형 가능한 물체를 포함하는 시간 해결 PIV는 동적 마스킹 (DM)을 사용해야 합니다. 주로 미세 유체 및 다상 흐름 분야에서 몇 가지 DM 기술이 최근 개발되었습니다. 대부분은 실험 설정의 임시 설계가 필요하며 결과 PIV 분석의 정확도를 떨어 뜨릴 수 있습니다. 여기에는 전용 마스킹 알고리즘과 함께 형광 코팅을 사용하여 물체를 정확하게 추적 할 수있는 새로운 DM 기술이 제시되어 있습니다. 제한된 변위를 특징으로 하는 물체에 대해서도 DM 단계를 포함해야 하는 필요성을 보여주는 검증 된 PIV 설정을 통해 얻은 측정 결과를 보여줍니다. 제안 된 알고리즘을 no-masking 및 static masking 솔루션과 비교합니다. 저비용, 유연하고 정확한 PIV 설정 개발 프레임 워크에서 제안 된 알고리즘은 기존 프리웨어 PIV 분석 패키지에서 사용할 마스크를 생성 할 수 있는 프리웨어 애플리케이션을 통해 사용할 수 있습니다.

Keywords

  • Time resolved PIV, Dynamics masking, Image processing, Vibration inducers, Fluorescent coating

그래픽 개요

소개

PIV (입자 영상 속도계)의 사용은 70 년대 후반 (Archbold 및 Ennos 1972 )이 반점 계측의 확장 (Barker and Fourney 1977 ) 으로 도입된 이래 실험 유체 역학에서 중심적인 역할을 했습니다 . PIV 기술의 기본 아이디어는 유체에 주입된 입자의 속도를 측정하여 유동장을 재구성하는 것입니다. 입자의 크기와 밀도는 확실하게 선택되고 유동을 만족스럽게 따르게 됩니다.

흐름은 레이저 / LED 소스를 통해 조명되고 입자에 의해 산란 된 빛은 추적을 허용합니다. 독자는 리뷰 작품 Grant ( 1997 ), Westerweel et al. ( 2013 년)에 대한 자세한 설명을 참조하십시오. 기본 2D 기술은 고유한 설정으로 발전했으며, 가장 진보 된 것은 단일 / 다중 평면 입체 PIV (Prasad 2000 ) 및 체적 / 단층 PIV (Scarano 2013 )입니다. 광범위한 유동장의 비 침습적 측정이 필요한 산업 및 연구 응용 분야에서 광범위하게 사용되었습니다.

조사된 유동장이 단단한 서있는 경계의 영향을 받는 경우 정적 마스킹 (SM) 접근 방식을 사용하여 PIV 분석을 수행하는 영역에서 솔리드 객체와 그림자가 차지하는 영역을 빼기 위해 주의를 기울여야 합니다. 실제로 이러한 영역에서는 파종 입자를 식별 할 수 없으므로 유속 재구성을 수행 할 수 없습니다. 제대로 처리되지 않으면 이 마스킹 단계는 잘못된 예측으로 이어질 수 있으며, 불행히도 그림자 영역 경계의 근접성에 국한되지 않습니다.

PIV 기술은 획득 프레임 속도를 관심있는 시간 척도로 조정하여 정상 상태 또는 시간 변화 흐름에 적용 할 수 있습니다. 시간의 가변성이 고체 물체의 위치 / 모양과 관련된 경우 이미지를 동적으로 마스킹하기 위해 추가 노력이 필요합니다. 고체 물체뿐만 아니라 다른 유체 단계도 가려야한다는 점에 유의해야합니다 (Foeth et al. 2006). 

이 프로세스는 고체 물체의 움직임이 선험적으로 알려진 경우 비교적 쉬우므로 SM 알고리즘에 대한 최소한의 수정이 목적에 부합 할 수 있습니다. 그러나 고체 물체의 위치 및 / 또는 모양이 알려지지 않은 방식으로 시간에 따라 변할 경우 물체를 동적으로 추적 할 수 있는 마스킹 기술이 필요합니다. PIV 분석을위한 동적 마스킹 (DM) 접근 방식은 현재 상당한 주목을 받고 있습니다 (Sanchis and Jensen 2011 , Masullo 및 Theunissen 2017 , Anders et al. 2019 ) . 시간 분해 PIV 시스템의 확산 덕분에 고속 카메라의 가용성이 높아집니다. 

DM 기술의 주요 발전은 마이크로 PIV 분야에서 비롯됩니다 (Lindken et al. 2009) 마이크로 및 나노 스위 머 (Ergin et al. 2015 ) 및 다상 흐름 (Brücker 2000 , Khalitov 및 Longmire 2002 ) 주변의 유동장을 조사 하려면 정확하고 유연한 알고리즘이 필요합니다. DM 기술은 상용 PIV 분석 소프트웨어 패키지 (TSI Instruments 2014 , DantecDynamics 2018 )에 포함되어 있습니다. 최근 개발 (Vennemann 및 Rösgen 2020 )은 신경망 자동 마스킹 기술의 적용을 예상하지만, 네트워크를 훈련하려면 합성 데이터 세트를 생성해야합니다.

많은 알고리즘은 이미지 처리 기술을 사용하여 개체를 추적하며, 대부분 사용자는 획득 한 이미지에서 추적 할 개체를 강조 표시 할 수있는 임시 실험 설정을 개발해야합니다. 따라서 실험 설정의 설계는 알고리즘의 최종 정확도에 영향을줍니다.

몇 가지 해결책을 구상 할 수 있습니다. 다음에서는 간단한 2D PIV 설정을 참조하지만 대부분의 고려 사항은 더 복잡한 설정으로 확장 할 수 있습니다. PIV 설정에서 객체를 쉽고 정확하게 추적 할 수 있도록 렌더링하는 가장 간단한 방법은 일반적으로 PIV 레이저 시트에 대략 수직 인 카메라를 향한 반사를 최대화하는 방향을 가리키는 추가 광원을 사용하여 조명하는 것입니다. 이 순진한 솔루션과 관련된 주요 문제는 PIV의 ROI (관심 영역)를 비추 지 않고는 광원을 움직이는 물체에만 겨냥하는 것이 사실상 불가능하여 시딩에 의해 산란 된 레이저 광 사이의 명암비를 감소 시킨다는 것입니다. 입자와 어두운 배경.

카메라의 프레임 속도가 높을수록 센서에 닿는 빛의 양이 적다는 사실로 인해 상황이 가혹 해집니다. 고체 물체의 움직임과 유동 입자가 모두 사용 된 설정의 획득 속도에 비해 충분히 느리다면, 가능한 해결책은 레이저 펄스 쌍 사이에 단일 확산 광 샷을 삽입하는 것입니다 (반드시 대칭 삽입은 아님). 그리고 카메라 샷을 둘 모두에 동기화합니다. 각 레이저 커플에서 물체의 위치는 확산 광에 의해 생성 된 이전 샷과 다음 샷의 두 위치를 보간하여 결정될 수 있습니다. 이 접근 방식에는 레이저, 카메라 및 빛을 제어 할 수있는 동기화 장치가 필요합니다.

이 문제에 대한 해결책이 제안되었으며 유체 인터페이스 (Foeth et al. 2006 ; Dussol et al. 2016 ) 의 밝은 반사를 활용 하여 이미지에서 많은 양의 산란 레이저 광을 획득 할 수 있습니다. 고체 표면에는 효과를 높이기 위해 반사 코팅이 제공 될 수 있습니다. 그런 다음 물체는 비정상적으로 큰 입자로 식별되고 경계를 쉽게 추적 할 수 있습니다. 이 솔루션의 단점은 물체 표면에서 산란 된 빛이 레이저 시트에 있지 않은 많은 시딩 입자를 비추어 PIV 분석의 정확도를 점진적으로 저하 시킨다는 것입니다.

위의 접근 방식의 개선은 다른 파장 의 두 번째 동일 평면 레이저 시트 (Driscoll et al. 2003 )를 사용합니다. 첫 번째 레이저 파장을 중심으로 한 좁은 반사 대역. 전체 설정은 매우 비쌀 수 있습니다. 파장 방출의 차이를 이용하여 설정을 저렴하게 만들 수 있습니다. 서로 다른 필터가 장착 된 두 대의 카메라를 적용하면 인터페이스로부터의 반사와 독립적으로 형광 시드 입자를 식별 할 수 있습니다 (Pedocchi et al. 2008 ).

객체의 변위가 작을 때 기본 솔루션은 실제 시간에 따라 변하는 음영 영역에 가장 근접한 하나의 정적 마스크를 추출하는 것입니다. 일반적인 경험 법칙은 예상되는 음영 영역보다 약간 더 크게 마스크를 그려 분석에 포함 된 조명 영역의 양을 단순화하고 최소화하는 것 사이의 최상의 균형을 찾는 것입니다.

본 논문에서는 PIV 분석을위한 DM 문제에 대한 새로운 실험적 접근법을 제안합니다. 우리의 방법은 형광 페인팅을 사용하여 물체를 쉽게 추적 할 수 있도록 하는 기술과 시변 마스크를 생성 할 수있는 특정 오픈 소스 알고리즘을 포함합니다. 이 접근법은 레이저 광에 불투명 한 물체의 큰 변위를 허용함으로써 효과적인 것으로 입증되었습니다. 

우리의 방법인 NM (no-masking)과 SM (static masking) 접근 방식을 비교합니다. 우리의 접근 방식의 타당성을 입증하는 것 외에도 이 백서는 마스킹 단계가 정확한 결과를 얻기 위해 가장 중요하다는 것을 확인합니다. 실제로 물체의 변위가 무시할 수 없는 경우 DM에 대한 리조트는 필수이며 SM 접근 방식은 음영 처리 된 영역의 주변 환경에 국한되지 않는 부정확성을 유발합니다. 

논문의 구조는 다음과 같습니다. 먼저 형광 코팅 기술과 마스킹 소프트웨어를 설명하는 제안된 접근법의 근거를 소개합니다. 그런 다음 PIV 설정에 대한 설명 후 두 벤치 마크 사례를 통해 전체 PIV 체인 분석의 신뢰성을 평가합니다. 그런 다음 제안 된 DM 방법의 결과를 NM 및 SM 솔루션과 비교합니다. 마지막으로 몇 가지 결론이 도출됩니다.

행동 양식

제안 된 DM 기술은 PIV 분석을 위해 캡처 한 동일한 이미지에서 쉽고 정확한 추적 성을 허용하기 위해 움직이는 물체 표면의 형광 코팅을 구상합니다. 물체가 가시화되면 특정 알고리즘이 물체 추적을 수행하고 레이저 위치가 알려지면 (그림 1 참조  ) 음영 영역의 마스킹을 수행합니다.

형광 코팅

코팅은 구조적 매트릭스 에 시판되는 형광 분말 (fluorescein (Taniguchi and Lindsey 2018 ; Taniguchi et al. 2018 )) 의 분산액으로 구성됩니다 . 단단한 물체의 경우 매트릭스는 폴리 에스터 / 에폭시 (대상 재료와의 화학적 호환성에 따라) 투명 수지 일 수 있습니다. 변형 가능한 물체의 경우 매트릭스는 투명한 실리콘 고무로 만들 수 있습니다. 형광 코팅 된 물체는 실행 중에 지속적으로 빛을 방출하기 위해 실험 전에 충분히 오랫동안 조명을 비춰 야합니다. 우리는 4W LED 소스 (그림 2 에서 볼 수 있음)에 20 초 긴 노출이  실험 실행 (몇 초)의 짧은 기간 동안 일관된 형광 방출을 제공하기에 충분하다는 것을 발견했습니다.

우리 실험에서 물체와 입자 크기 사이의 상당한 차이를 감안할 때 전자를 식별하는 것은 간단합니다. 그림  3 은 씨 뿌리기 입자와 물체 모양이 서로 다른 세 번에 겹쳐진 모습을 보여줍니다 (색상은 다른 순간을 나타냄).

대신, 이러한 크기 기반 분류가 가능하지 않은 경우 입자와 물체의 파장을 분리해야합니다. 이러한 분리는 시드 입자에 의해 산란 된 빛과 현저하게 다른 파장에서 방출되는 형광 코팅을 선택하여 달성 할 수 있습니다. 또는 레이저에서 멀리 떨어진 대역에서 방출되는 형광 입자를 이용하는 것 (Pedocchi et al. 2008 ). 두 경우 모두 컬러 이미지 획득의 채널 분리 또는 멀티 카메라 설정의 애드혹 필터링은 물체 식별을 크게 촉진 할 수 있습니다. 우리의 경우에는 그러한 파장 분리를 달성 할 필요가 없습니다. 실제로 형광 코팅의 방출 스펙트럼의 피크는 540nm입니다 (Taniguchi and Lindsey 2018 ; Taniguchi et al. 2018), 사용 된 레이저의 532 nm에 매우 가깝습니다.

마스킹 소프트웨어

DM 용으로 개발 된 알고리즘 은 무료 PIV 분석 패키지 PIVlab (Thielicke 2020 , Thielicke 및 Stamhuis 2014 ) 과 함께 작동하도록 고안된 오픈 소스 프리웨어 GUI 기반 도구 (Prestininzi 및 Lombardi 2021 )입니다. 이것은 세 단계의 순차적 실행으로 구성됩니다 (그림 1 에서 a–b–c라고 함 ). 첫 번째 단계 (a)는 장면에서 레이저 위치를 찾는 데 사용됩니다 (즉, 소스의 좌표를 계산합니다. 장애물에 부딪히는 빛); 두 번째 항목 (b)은 개체 위치를 추적하고 각 프레임의 음영 영역을 계산합니다. 세 번째 항목 (c)은 추적 된 개체 영역과 음영 처리 된 개체 영역을 PIV 알고리즘을위한 단일 마스크로 병합합니다.

각 단계에 대한 자세한 내용은 다음과 같습니다.

  1. (ㅏ)레이저 위치는 프레임 (즉, 획득 한 프레임의 시야 (FOV)) 내에서 가시적 일 수도 있고 아닐 수도 있습니다. 전자의 경우 사용자는 GUI에서 레이저 소스를 클릭하여 찾기 만하면됩니다. 후자의 경우, 사용자는 음영 영역의 경계에 속하는 두 개의 세그먼트 (두 쌍의 점)를 그리도록 요청받습니다. 그러면 FOV 외부에있는 레이저 위치가 두 선의 교차점으로 계산됩니다. 세그먼트로 구성됩니다. 개체 그림자는 ROI 프레임 상자에 도달하는 것으로 간주됩니다.
  2. (비)레이저 위치가 알려지면 물체 추적은 다음과 같이 수행됩니다. 각 프레임의 하나의 채널 (이 경우 RGB 색상 공간이 사용되기 때문에 녹색 채널이지만 GUI는 선호하는 채널을 지정할 수 있음)은 다음과 같습니다. 로컬 적응 임계 값을 사용하여 이진화 됨 (Bradley and Roth 2007), 후자는 이웃 주변의 로컬 평균 강도를 사용하여 각 픽셀에 대해 계산됩니다. 그런 다음 입자와 물체로 구성된 이진 이미지가 영역으로 변환됩니다. 우리 실험에 존재하는 유일한 장애물은 모든 입자에 비해 더 큰 크기를 기준으로 식별됩니다. 다른 전략은 이전에 논의되었습니다. 그런 다음 장애물 영역의 경계 다각형은 사용자 정의 포인트 밀도로 결정됩니다. 여기에서는 그림자 결정을 위해 광선 투사 (RC) 접근 방식을 채택했습니다. RC는 컴퓨터 그래픽을 기반으로하는 “경 운송 모델링”의 틀에 속합니다. 수치 적으로 정확한 그림자를 제공하기 때문에 여기에서 선택됩니다. 정확도는 떨어지지 만 주로 RC의 계산 부하를 줄이는 것을 목표로하는 몇 가지 다른 방법이 개발되었습니다.2015 ), 여기서 간략히 회상합니다. 각 프레임 (명확성을 위해 여기에 색인화되지 않음)에 대해 광선아르 자형나는 j아르 자형나는제이레이저 위치 L 에서 i 번째 정점 으로 캐스트됩니다.피나는 j피나는제이의 J 오브젝트의 경계 다각형 일; 목표는피나는 j피나는제이 하위 집합에 속 ㅏ제이ㅏ제이 레이저에 의해 직접 조명되는 경계 정점의 피나는 j피나는제이 에 추가됩니다 ㅏ제이ㅏ제이 만약 아르 자형나는 j아르 자형나는제이 적어도 한쪽을 교차 에스k j에스케이제이( j 번째 개체 경계 다각형 의 모든면에 걸쳐있는 k )피나는 j피나는제이 (그것이 교차로 큐나는 j k큐나는제이케이 레이저 위치와 정점 사이에 있지 않습니다. 피나는 j피나는제이). 두 개의 광선, 즉ρ1ρ1 과 ρ2ρ2추가면을 가로 지르지 않는는 저장됩니다.
  3. (씨)일단 정점 세트, 즉 ㅏ제이ㅏ제이 레이저에 의해 직접 비춰지고 식별되었으며 ROI 프레임 상자의 음영 부분은 후자와 교차하여 결정됩니다. ρ1ρ1 과 ρ2ρ2. 두 교차점은 다음에 추가됩니다.ㅏ제이ㅏ제이. 점으로 둘러싸인 영역ㅏ제이ㅏ제이 마침내 마스크로 변환됩니다.

레이저 소스가 여러 개인 경우 각각에 RC 알고리즘을 적용해야하며 음영 영역의 결합이 수행됩니다. 레이 캐스팅 절차의 의사 코드는 Alg에보고됩니다. 1.

그림
그림 1
그림 1

DM 검증

이 섹션에서는 제안 된 DM으로 수행 된 PIV 측정과 두 가지 다른 접근 방식, 즉 no-masking (NM)과 static masking (SM) 간의 비교를 제시합니다.

그림 2
그림 2
그림 3
그림 3

실험 설정

진동 유도기 (VI)의 성능을 분석하기 위해 PIV 설정을 설계하고 현재 DM 기술을 개발했습니다 (Curatolo et al. 2019 , 2020 ). 후자는 비 맥동 ​​유체 흐름에서 역류에 배치 된 캔틸레버의 규칙적이고 넓은 진동을 유도 할 수있는 윙렛입니다. 이러한 VI는 캔틸레버의 끝에 장착되며 (그림 2 참조   ) 진동 운동의 어느 지점에서든 캔틸레버의 중립 구성을 향해 양력을 생성 할 수있는 두 개의 오목한 날개가 있습니다.

VI는 캔틸레버 표면에 장착 된 압전 패치를 사용하여 고정 유체 흐름에서 기계적 에너지 추출을 향상시킬 수 있습니다. 그림 2 에서 강조된 날개의 전체 측면 가장자리는  Sect에 설명 된 사양에 따라 형광 페인트로 코팅되어 있습니다. 2.1 . 실험은 Roma Tre University 공학부 수력 학 실험실의 자유 표면 채널에서 수행됩니다. 10.8cm 길이의 캔틸레버는 채널의 중심선에 배치되고 상류로 향하며 수직-세로 평면에서 진동합니다. 세라믹 페 로브 스카이 트 (PZT) 압전 패치 (7××캔틸레버의 윗면에는 Physik Instrumente (PI)에서 만든 3cm)가 부착되어 있습니다. 흐름 유도 진동 하에서 변형으로 인해 AC 전압 차이를 제공합니다. VI 왼쪽 날개의 수직 중앙면에있는 2D 속도 필드는 수제 수중 PIV 장비를 통해 얻었습니다.각주1 연속파, 저비용, 저전력 (150mW), 녹색 (532nm) 레이저 빔이 2mm 두께의 부채꼴 시트에 퍼집니다.120∘120∘그림 2 와 같이 VI의 한쪽 날개를 절반으로 교차 합니다. 물은 평균 직경이 100 인 폴리 아미드 입자로 시드됩니다.μμm 및 1016 Kg / m의 밀도삼삼. 레이저 소스는 VI의 15cm 위쪽 (자유 표면 아래 약 4cm)과 VI의 하류 5cm에 경사지게 배치됩니다.5∘5∘상류. 위의 설정은 주로 날개의 후류를 조사하기 위해 고안되었습니다. 날개의 상류면과 하류 부분의 일부는 레이저 시트에 직접 맞지 않습니다. 레이저 시트에 수직으로 촬영하는 고속 상용 카메라 (Sony RX100 M5)를 사용하여 동영상을 촬영합니다. 후자는 1920의 프레임 크기로 500fps의 높은 프레임 속도 모드로 기록됩니다.×× 1080px, 나중에 더 작은 655로 잘림 ××이미지 분석 중에 분석 할 850px ROI. 시간 해결, 프리웨어, 오픈 소스, MatLab 용 PIV 분석 도구가 사용됩니다 (Thielicke and Stamhuis 2014 ). 이 도구는 질의 영역 (IA) 변형 (우리의 경우 64×× 64, 32 ×× 32 및 26 ××26). 각 패스에서 각 IA의 경계와 모서리에서 추가 변위 정보를 얻기 위해 인접한 IA 사이에 50 %의 중첩이 허용됩니다. 첫 번째 통과 후, 입자 변위 정보가 보간되어 IA의 모든 픽셀의 변위를 도출하고 그에 따라 변형됩니다.

시딩 입자 수 밀도는 첫 번째 패스에서 IA 당 약 5입니다. Keane과 Adrian ( 1992 )에 따르면 이러한 밀도 값은 95 % 유효한 탐지 확률을 보장합니다. IA는 프레임 커플 내에서 입자의 충분한 영구성을 보장하기 위해 크기가 조정됩니다. 분석 된 유동 역학은 0.4 ~ 0.7m / s 범위의 유동 속도를 특징으로합니다. 따라서 입자는 권장 최소값 인 2 프레임 (Keane and Adrian 1992 ) 보다 큰 약 3-4 프레임의 세 번째 패스 IA에 나타납니다 .

PIV 체인 분석 평가

사용 된 PIV 알고리즘의 정확성은 이전에 문헌에서 광범위하게 평가되었습니다 (예 : Guérin et al. ( 2020 ), Vennemann and Rösgen ( 2020 ), Mohammadshahi et al. ( 2020 ), Narayan et al. ( 2020 )). 그러나 PIV 측정의 물리적 일관성을 보장하기 위해 두 가지 벤치 마크 사례가 여기에 나와 있습니다.

첫 번째는 Sect에 설명 된 동일한 PIV 설정을 통해 측정 된 세로 유속의 수직 프로파일을 비교합니다. 3.1 분석 기준 용액이있는 실험 채널에서. 후자는 플로팅 트레이서로 수행되는 PTV (입자 추적 속도계) 측정을 통해 보정되었습니다. 분석 속도 프로파일은 Eq. 1 (Keulegan 1938 ).u ( z) =유∗[5.75 로그(지δ) +8.5];유(지)=유∗[5.75로그⁡(지δ)+8.5];(1)

여기서 u 는 수평 유속 성분, z 는 수직 좌표,δδ 침대 거칠기 및 V∗V∗ 균일 한 흐름 공식에 의해 주어진 것으로 가정되는 마찰 속도, 즉 유∗= U/ C유∗=유/씨; U 는 깊이 평균 유속이고 C 는 다음 과 같이 주어진 마찰 계수입니다.씨= 5.75로그( 13.3에프R / δ)씨=5.75로그⁡(13.3에프아르 자형/δ), R = 0.2아르 자형=0.2 m은 유압 반경이고 에프= 0.92에프=0.92유한 폭 채널의 형상 계수. 그림  4 는 4 초의 시간 창에 걸쳐 순간 값을 평균화하여 얻은 분석 프로필과 PIV 측정 간의 비교를 보여줍니다. 국부적 인 변동은 대략 0.5 초의 시간 척도에서 진화하는 것으로 밝혀졌습니다. PTV 결과에 가장 적합하면 다음과 같은 값이 산출됩니다.δ= 1δ=1cm, 베드 거칠기의 경우 Eq. 1 , 실험 채널 침대 표면의 실제 조건과 호환됩니다. VI의 휴지 구성 위치에서 유속의 분석 값은 그림에서 검은 색 십자가로 표시됩니다. 비교는 놀라운 일치를 보여 주므로 실험 설정과 PIV 알고리즘의 조합이 분석 된 설정에 대해 신뢰할 수있는 것으로 간주 될 수 있음을 증명합니다.

두 번째 벤치 마크는 VI 뒷면에 재 부착 된 흐름의 양을 비교합니다. 실제로 이러한 장치의 높은 캠버를 고려할 때 흐름은 하류 표면에서 분리되어 결국 다시 연결됩니다. 첨부 흐름을 나타내는 표면의 양 (Curatolo 외. 발견 2020 ) 흥미로운 압전 패치 (즉, 효율이 큰 경우에 더 빠르게 진동이 유발되는 것이다)에서 VI의 효율과 상관된다. 여기에서는 PIV 분석을 통해 측정 된 진동의 상사 점에서 재 부착 된 흐름의 길이를 CFD (전산 유체 역학) 상용 코드 FLOW-3D® (Flow Science 2019 )로 예측 한 길이와 비교하여 RANS를 해결합니다. 결합 식 (비어 스톡스 레이놀즈 평균) 케이 -ϵϵ구조화 된 그리드의 난류 폐쇄 (시뮬레이션을 위해 1mm 간격이 선택됨). 다운 스트림 측면의 흐름은 이러한 높은 캠버 VI를 위해 여러 위치에서 분리 및 재 부착됩니다. 이 벤치 마크에서 비교 된 양은 VI의 앞쪽 가장자리와 가장 가까운 흐름 재 부착 위치 사이의 호 길이입니다. 그림 5를 참조  하면 CFD 모델에 의해 예측 된 호의 길이는 측정 된 호의 길이보다 10 % 더 큽니다. 이 작업에 제시된 DM 기술을 사용하는 PIV 분석은 물리적으로 건전한 측정을 제공하는 것으로 입증됩니다. 후류의 유체 역학에 대한 자세한 분석과 VI의 전반적인 효율성과의 상관 관계는 현재 진행 중이며 향후 작업의 대상이 될 것입니다.

그림 4
그림 4
그림 5
그림 5

결과

그림 6을 참조하여  순간 유속 장의 관점에서 세 가지 접근법의 결과를 비교합니다. 선택한 순간은 진동의 상사 점에 해당합니다.

제안 된 DM (그림 6 의 패널 a  )은 부드러운 유동장을 생성하여 후류에서 일관된 소용돌이 구조를 나타냅니다.

NM 접근법 (그림 6 의 패널 b1  )도 후류의 와류 구조를 정확하게 예측하지만 음영 영역에서 대부분 부정확 한 값을 산출합니다. 또한 비교에서 합리적인 기준을 추론 할 수 없기 때문에 획득 한 유동장 의 사후 필터링이 실현 가능하지 않다는 것이 분명합니다 . 실제로 유속은 그림 6 의 패널 c1에서 볼 수 있듯이 가장 큰 오류가 생성되는 위치에서도 “합리적인”크기를 갖습니다. , DM 및 NM 접근 방식으로 얻은 속도 필드 간의 차이가 표시됩니다. 더욱이 후류에서 발생하는 매우 불안정한 소용돌이 운동이 이러한 위치에 가깝게 이동하기 때문에 그럴듯한 흐름 방향을 가정하더라도 필터링 기준을 공식화 할 수 없습니다. 모델러가 그러한 부정확성을 알고 있었다하더라도 NM 접근법은 “합리적”이지만 여전히 날개의 내부 현과 그 바로 아래에있는 유동장의 대부분은 부정확합니다. 이러한 행동은 매우 오해의 소지가 있습니다.

그림 6 의 패널 b2는  SM 접근법으로 얻은 유속 장을 보여주고 패널 c2는 SM과 DM 접근법으로 얻은 결과 간의 차이를 보여줍니다. SM 접근법은 NM 대응 물에 비해 전반적으로 더 나은 정확도를 명확하게 보여 주지만, 이는 레이저 소스의 위치가 진동 중에 음영 영역이 많이 움직이지 않기 때문입니다 (그림 3 참조). 한 번의 진동 동안 VI가 경험 한 최대 변위를 육안으로 검사합니다. 즉, 분석 된 사례의 경우 정적 마스크를 그리기위한 중립 구성을 선택하면 NM 접근 방식보다 낮은 오류를 얻을 수 있습니다. 더 큰 물체 변위를 포함하는 실험 설정은 NM이 일관되게 더 정확해질 수 있기 때문에 NM보다 SM의 우월성은 일반화 될 수 없음을 강조하고 싶습니다.

그림  6 은 분석 된 접근법에 의해 생성 된 차이를 철저히 보여 주지만 결과에 대한보다 정량적 인 평가를 제공하기 위해 오류의 빈도 분포를 계산했습니다. 그림 7 에서 이러한 분포를  살펴보면 SM 접근법이 NM보다 전체적인 예측이 더 우수하고 SM 분포가 더 정점에 있음을 확인합니다. 그럼에도 불구하고 SM은 여전히 ​​비정상적인 강도의 스파이크를 생성합니다. 분포의 꼬리로 표시되는 이러한 값은 정적 마스크 범위의 과대 평가 (왼쪽 꼬리) 및 과소 평가 (오른쪽 꼬리)에 연결됩니다. 그러나 주파수의 크기는 고려되는 경우에 SM과 NM의 적용 가능성을 배제하여 DM에 대한 리조트를 의무적으로 만듭니다.

그림 6
그림 6
그림 7
그림 7

결론

이 작업에서는 PIV 분석 도구에 DM (Dynamic Masking) 모듈을 제공하기위한 새로운 실험 기법을 제시합니다. 동적 마스킹은 유체 흐름에 잠긴 불투명 이동 / 변형 가능한 물체를 포함하는 시간 해결 PIV 설정에서 필요한 단계입니다. 마스킹 알고리즘과 함께 형광 코팅을 사용하여 물체를 정확하게 추적 할 수 있습니다. 우리는 제안 된 DM과 두 가지 다른 접근 방식, 즉 no-masking (NM)과 static masking (SM)을 비교하여 자체적으로 설계된 저비용 PIV 설정을 통해 수행 된 측정을 제시합니다. 분석 된 유동 역학은 고체 물체의 제한된 변위를 포함하지만 정량적 비교는 DM 기술을 채택해야하는 필수 필요성을 보여줍니다. 여기에서 정확성이 입증 된 현재의 실험적 접근 방식은

메모

  1. 1.실험 데이터 세트는 PIV 분석의 복제를 허용하기 위해 요청시 제공됩니다.

참고 문헌

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  1. 이탈리아 Roma, Università Roma Tre 공학과Valentina Lombardi, Michele La Rocca, Pietro Prestininzi

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Valentina Lombardi에 대한 서신 .

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Lombardi, V., Rocca, ML & Prestininzi, P. 시간 분해 PIV 분석을위한 새로운 동적 마스킹 기술. J Vis (2021). https://doi.org/10.1007/s12650-021-00756-0

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키워드

  • 시간 해결 PIV
  • 역학 마스킹
  • 이미지 처리
  • 진동 유도제
  • 형광 코팅
Fig. 9 (a) Velocity field, keyhole profile, and breakage of the keyhole to form bubble and (b) 2D temperature and velocity field along the longitudinal section

A Numerical Study on the Keyhole Formation During Laser Powder Bed Fusion Process

Keyhole에 대한 수치적 연구 : 레이저 분말 중 형성 베드 퓨전 공정

Subin Shrestha1
J.B. Speed School of Engineering,University of Louisville,Louisville, KY 40292
e-mail: subin.shrestha@louisville.edu

Y. Kevin Chou
J.B. Speed School of Engineering,University of Louisville,Louisville, KY 40292
e-mail: kevin.chou@louisville.edu

LPBF (Laser Powder Bed fusion) 공정 중 용융 풀의 동적 현상은 복잡하고 공정 매개 변수에 민감합니다. 에너지 밀도 입력이 특정 임계 값을 초과하면 키홀이라고 하는 거대한 증기 함몰이 형성 될 수 있습니다.

이 연구는 수치 분석을 통해 LPBF 과정에서 키홀 거동 및 관련 기공 형성을 이해하는 데 중점을 둡니다. 이를 위해 이산 분말 입자가 있는 열 유동 모델이 개발되었습니다.

이산 요소 방법 (DEM)에서 얻은 분말 분포는 계산 영역에 통합되어 FLOW-3D를 사용하는 3D 프로세스 물리학 모델을 개발합니다.

전도 모드 중 용융 풀 형성과 용융의 키홀 모드가 식별되고 설명되었습니다. 높은 에너지 밀도는 증기 기둥의 형성으로 이어지고 결과적으로 레이저 스캔 트랙 아래에 구멍이 생깁니다.

또한 다양한 레이저 출력과 스캔 속도로 인한 Keyhole 모양을 조사합니다. 수치 결과는 동일한 에너지 밀도에서도 레이저 출력이 증가함에 따라 Keyhole크기가 증가 함을 나타냅니다. Keyhole은 더 높은 출력에서 ​​안정되어 레이저 스캔 중 Keyhole 발생을 줄일 수 있습니다.

The dynamic phenomenon of a melt pool during the laser powder bed fusion (LPBF) process is complex and sensitive to process parameters. As the energy density input exceeds a certain threshold, a huge vapor depression may form, known as the keyhole. This study focuses on understanding the keyhole behavior and related pore formation during the LPBF process through numerical analysis. For this purpose, a thermo-fluid model with discrete powder particles is developed. The powder distribution, obtained from a discrete element method (DEM), is incorporated into the computational domain to develop a 3D process physics model using flow-3d. The melt pool formation during the conduction mode and the keyhole mode of melting has been discerned and explained. The high energy density leads to the formation of a vapor column and consequently pores under the laser scan track. Further, the keyhole shape resulted from different laser powers and scan speeds is investigated. The numerical results indicated that the keyhole size increases with the increase in the laser power even with the same energy density. The keyhole becomes stable at a higher power, which may reduce the occurrence of pores during laser scanning.

Keywords: additive manufacturing, keyhole, laser powder bed fusion, porosity

Fig. 1 (a) Powder added to the dispenser platform and (b) powder particles settled over build plate after the recoating process
Fig. 1 (a) Powder added to the dispenser platform and (b) powder particles settled over build plate after the recoating process
Fig. 2 3D computational domain used for single-track simulation
Fig. 2 3D computational domain used for single-track simulation
Fig. 3 Temperature-dependent material properties of Ti-6Al-4V
Fig. 3 Temperature-dependent material properties of Ti-6Al-4V
Fig. 4 Powder and substrate melting during laser application
Fig. 4 Powder and substrate melting during laser application
Fig. 5 Melt region formed after complete melting and solidification
Fig. 5 Melt region formed after complete melting and solidification
Fig. 6 Melt pool boundary comparison between the experiment [25] and the simulation
Fig. 6 Melt pool boundary comparison between the experiment [25] and the simulation
Fig. 7 Equilibrium points during the formation of vapor column [27]
Fig. 7 Equilibrium points during the formation of vapor column [27]
Fig. 8 Multiple reflection vectors from the keyhole wall
Fig. 8 Multiple reflection vectors from the keyhole wall
Fig. 9 (a) Velocity field, keyhole profile, and breakage of the keyhole to form bubble and (b) 2D temperature and velocity field along the longitudinal section
Fig. 9 (a) Velocity field, keyhole profile, and breakage of the keyhole to form bubble and (b) 2D temperature and velocity field along the longitudinal section
Fig. 10 Fluid flow in the transverse direction during keyhole melting
Fig. 10 Fluid flow in the transverse direction during keyhole melting
Fig. 11 Melt pool boundary compared with the experiment [21] for 195 W laser power and 400 mm/s scan speed
Fig. 11 Melt pool boundary compared with the experiment [21] for 195 W laser power and 400 mm/s scan speed
Fig. 12 Melt region formed after complete melting and solidification
Fig. 12 Melt region formed after complete melting and solidification
Fig. 13 2D images of the pores formed at the beginning of the single track and their 3D-rendered morphology
Fig. 13 2D images of the pores formed at the beginning of the single track and their 3D-rendered morphology
Fig. 14 Pore number and volume from a different level of power with LED = 0.4 J/mm [29]
Fig. 14 Pore number and volume from a different level of power with LED = 0.4 J/mm [29]
Fig. 15 Keyhole shape at different time steps from different parameters: (a) P = 100 W, v = 250 mm/s, (b) P = 200 W, v = 500 mm/s, (c) P = 300 W, v = 750 mm/s, and (d) P = 400 W, v = 1000 mm/s
Fig. 15 Keyhole shape at different time steps from different parameters: (a) P = 100 W, v = 250 mm/s, (b) P = 200 W, v = 500 mm/s, (c) P = 300 W, v = 750 mm/s, and (d) P = 400 W, v = 1000 mm/s
Fig. 16 Intensity dependence in the relationship between vapor column and evaporation pressure [27]
Fig. 16 Intensity dependence in the relationship between vapor column and evaporation pressure [27]
Fig. 17 Temperature distribution when laser has moved 0.8 mm with P = 300 W, v = 750 mm/s and P = 400 W, v = 1000 mm/s
Fig. 17 Temperature distribution when laser has moved 0.8 mm with P = 300 W, v = 750 mm/s and P = 400 W, v = 1000 mm/s
Fig. 18 Melt region with different level of power with LED of 0.4 J/mm
Fig. 18 Melt region with different level of power with LED of 0.4 J/mm

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Figure 3. (a) Velocity distribution in a section perpendicular to the flow for rectangular (left) and Ushaped (right) cross section channels, and (b) particle location in these cross sections.

Continuous-Flow Separation of Magnetic Particles from Biofluids: How Does the Microdevice Geometry Determine the Separation Performance?

Cristina González Fernández,1 Jenifer Gómez Pastora,2 Arantza Basauri,1 Marcos Fallanza,1 Eugenio Bringas,1 Jeffrey J. Chalmers,2 and Inmaculada Ortiz1,*
Author information Article notes Copyright and License information Disclaimer

생체 유체에서 자성 입자의 연속 흐름 분리 : 마이크로 장치 형상이 분리 성능을 어떻게 결정합니까?

Abstract

The use of functionalized magnetic particles for the detection or separation of multiple chemicals and biomolecules from biofluids continues to attract significant attention. After their incubation with the targeted substances, the beads can be magnetically recovered to perform analysis or diagnostic tests. Particle recovery with permanent magnets in continuous-flow microdevices has gathered great attention in the last decade due to the multiple advantages of microfluidics. As such, great efforts have been made to determine the magnetic and fluidic conditions for achieving complete particle capture; however, less attention has been paid to the effect of the channel geometry on the system performance, although it is key for designing systems that simultaneously provide high particle recovery and flow rates. Herein, we address the optimization of Y-Y-shaped microchannels, where magnetic beads are separated from blood and collected into a buffer stream by applying an external magnetic field. The influence of several geometrical features (namely cross section shape, thickness, length, and volume) on both bead recovery and system throughput is studied. For that purpose, we employ an experimentally validated Computational Fluid Dynamics (CFD) numerical model that considers the dominant forces acting on the beads during separation. Our results indicate that rectangular, long devices display the best performance as they deliver high particle recovery and high throughput. Thus, this methodology could be applied to the rational design of lab-on-a-chip devices for any magnetically driven purification, enrichment or isolation.

생체 유체에서 여러 화학 물질과 생체 분자의 검출 또는 분리를 위한 기능화된 자성 입자의 사용은 계속해서 상당한 관심을 받고 있습니다. 표적 물질과 함께 배양 한 후 비드는 자기적으로 회수되어 분석 또는 진단 테스트를 수행 할 수 있습니다.

연속 흐름 마이크로 장치에서 영구 자석을 사용한 입자 회수는 마이크로 유체의 여러 장점으로 인해 지난 10 년 동안 큰 관심을 모았습니다. 따라서 완전한 입자 포획을 달성하기 위한 자기 및 유체 조건을 결정하기 위해 많은 노력을 기울였습니다.

그러나 높은 입자 회수율과 유속을 동시에 제공하는 시스템을 설계하는데 있어 핵심이기는 하지만 시스템 성능에 대한 채널 형상의 영향에 대해서는 덜 주의를 기울였습니다.

여기에서 우리는 자기 비드가 혈액에서 분리되어 외부 자기장을 적용하여 버퍼 스트림으로 수집되는 Y-Y 모양의 마이크로 채널의 최적화를 다룹니다. 비드 회수 및 시스템 처리량에 대한 여러 기하학적 특징 (즉, 단면 형상, 두께, 길이 및 부피)의 영향을 연구합니다.

이를 위해 분리 중에 비드에 작용하는 지배적인 힘을 고려하는 실험적으로 검증된 CFD (Computational Fluid Dynamics) 수치 모델을 사용합니다.

우리의 결과는 직사각형의 긴 장치가 높은 입자 회수율과 높은 처리량을 제공하기 때문에 최고의 성능을 보여줍니다. 따라서 이 방법론은 자기 구동 정제, 농축 또는 분리를 위한 랩 온어 칩 장치의 합리적인 설계에 적용될 수 있습니다.

Keywords: particle magnetophoresis, CFD, cross section, chip fabrication

Figure 1 (a) Top view of the microfluidic-magnetophoretic device, (b) Schematic representation of the channel cross-sections studied in this work, and (c) the magnet position relative to the channel location (Sepy and Sepz are the magnet separation distances in y and z, respectively).
Figure 1 (a) Top view of the microfluidic-magnetophoretic device, (b) Schematic representation of the channel cross-sections studied in this work, and (c) the magnet position relative to the channel location (Sepy and Sepz are the magnet separation distances in y and z, respectively).
Figure 2. (a) Channel-magnet configuration and (b–d) magnetic force distribution in the channel midplane for 2 mm, 5 mm and 10 mm long rectangular (left) and U-shaped (right) devices.
Figure 2. (a) Channel-magnet configuration and (b–d) magnetic force distribution in the channel midplane for 2 mm, 5 mm and 10 mm long rectangular (left) and U-shaped (right) devices.
Figure 3. (a) Velocity distribution in a section perpendicular to the flow for rectangular (left) and Ushaped (right) cross section channels, and (b) particle location in these cross sections.
Figure 3. (a) Velocity distribution in a section perpendicular to the flow for rectangular (left) and Ushaped (right) cross section channels, and (b) particle location in these cross sections.
Figure 4. Influence of fluid flow rate on particle recovery when the applied magnetic force is (a) different and (b) equal in U-shaped and rectangular cross section microdevices.
Figure 4. Influence of fluid flow rate on particle recovery when the applied magnetic force is (a) different and (b) equal in U-shaped and rectangular cross section microdevices.
Figure 5. Magnetic bead capture as a function of fluid flow rate for all of the studied geometries.
Figure 5. Magnetic bead capture as a function of fluid flow rate for all of the studied geometries.
Figure 6. Influence of (a) magnetic and fluidic forces (J parameter) and (b) channel geometry (θ parameter) on particle recovery. Note that U-2mm does not accurately fit a line.
Figure 6. Influence of (a) magnetic and fluidic forces (J parameter) and (b) channel geometry (θ parameter) on particle recovery. Note that U-2mm does not accurately fit a line.
Figure 7. Dependence of bead capture on the (a) functional channel volume, and (b) particle residence time (tres). Note that in the curve fitting expressions V represents the functional channel volume and that U-2mm does not accurately fit a line.
Figure 7. Dependence of bead capture on the (a) functional channel volume, and (b) particle residence time (tres). Note that in the curve fitting expressions V represents the functional channel volume and that U-2mm does not accurately fit a line.

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Effect of Substrate Roughness on Splatting Behavior of HVOF Sprayed Polymer Particles: Modeling and Experiments

International Thermal Spray Conference – ITSC-2006
Seattle, Washington, U.S.A., May 2006

M. Ivosevic, V. Gupta, R. A. Cairncross, T. E. Twardowski, R. Knight,
Drexel University, Philadelphia, Pennsylvania, USA
J. A. Baldoni
Duke University, North Carolina, USA

Abstract

거친 표면에 대한 입자 충격 및 변형의 3 차원 모델이 HVOF 스프레이 폴리머 입자에 대해 개발되었습니다. 유체 흐름 및 입자 변형은 FLOW-3D® 소프트웨어를 사용하는 유체 부피 (VoF) 방법으로 예측되었습니다. 스플래팅(splatting) 및 최종 스플랫 모양(splat shapes)의 역학에 대한 거칠기의 영향은 몇 가지 프로토타입 거친 표면을 사용하여 탐색 되었습니다 (예: 단계와 그루브)

또한 실제 그릿 블라스팅(grit blasted)된 강철 표면의 광학 간섭 측정에 의해 생성된 보다 사실적인 거친 표면의 수치 표현도 모델에 통합되었습니다. 예측된 스플랫 모양을 그릿 블라스팅 된 강철 기판에 증착된 나일론 11 스플랫의 SEM 이미지와 비교했습니다. 거친 기판은 부드러운 기판의 스플래팅 시뮬레이션에서 거의 관찰되지 않는 손가락 및 기타 비대칭 3 차원 불안정성을 생성했습니다.

Introduction

기판 거칠기가 용사 코팅의 접착력과 접착력을 향상 시킨다는 사실은 잘 알려져 있으며 일반적으로 받아 들여지고 있습니다 [1]. 스프레이하기 전에 기판 표면은 일반적으로 알루미나 또는 SiC와 같은 50 – 300 µm 각 세라믹 입자로 그릿 블라스팅으로 거칠게 처리됩니다.

기판 표면에 증착된 초기 스플랫의 형태는 코팅 / 기판 인터페이스의 무결성과 결과 코팅의 접착 강도에 중요한 역할을합니다. 단단하고 불규칙한 표면에 대한 열 스프레이 액적의 충격 및 변형은 액적 표면의 복잡한 대규모 3 차원 변형이 특징입니다.

충돌하는 물방울의 “스플래싱”이 발생하는 경우, 운지법 또는 위성 입자 생성 및 분리 중 새로운 표면 생성은 일반적으로 축 대칭이 아니므로 사실적인 splat 예측을 위해 3 차원 모델이 필요합니다. 이것은 정확한 3 차원 스플래팅 모델의 개발에 많은 수치적 도전을 야기합니다.

Fauchais et al. [2]는 스플랫 형성 과정과 관련하여 발표 된 논문의 대부분 (~ 98 %)이 매끄러운 표면에 대한 정상적인 액적 충격을 설명한다고보고했습니다. 게시된 작업의 2 % 미만은 매끄러운 표면에 대한 비정상적인 입자 영향과 관련이 있으며 ~ 0.1 %만이 거친 기판과 관련됩니다.

여러 저자 [3, 4]는 2 차원 모델을 사용하여 비평면 표면과 물방울의 상호 작용을 연구했거나 평행 그루브가 있는 표면에 대한 3 차원 충격 [5]을 연구했습니다. 그러나 이 접근법의 주요 단점은 거친 표면에 스플래팅의 비축 대칭 측면을 연구합니다.

최근 Raessi et al. [6] 이전에 개발된 VoF 모델 [7]을 확장하여 평평한 기판에 액적 스플래팅을 프로토 타입 거친 표면과 액적 상호 작용으로 확장했습니다. 표면 거칠기는 규칙적으로 정렬 된 정사각형 블록으로 근사화 되었습니다. Feng et al. [8]은 평평한 표면의 마찰 조건에 의해 표면 거칠기가 근사된 3 차원 Lagrangian 유한 요소 모델을 사용했습니다.

이 접근 방식은 소규모 점성 및 축 대칭 자유 표면 흐름과 관련하여 매우 정확할 수 있지만 fingering 생성 또는 satellites 생성 및 breakups 중 새로운 표면 생성과 관련된 물방울이 튀기는 경계 맞춤 기술에 적합하지 않습니다.

또한, 열 분무에 사용되는 그릿 블라스팅 표면의 평균 표면 거칠기 (Ra)는 일반적으로 50μm의 평균 액적 크기에 비해 ~ 5 ~ 30 % (~ 2 ~ 15μm)입니다. 평평한 표면에 간단한 마찰 흐름.

본 연구의 목표는 임의의 거친 기질에 영향을 미치는 HVOF 분무 중합체 입자의 모델을 개발하는 것이다. 매끄럽지 않은 표면에 대한 입자 분할 모델은 표면의 기하학적 불규칙성이 분할 거동과 최종 분할 형태에 어떻게 영향을 미치는지 더 잘 이해할 수 있게 해줄 것입니다.

HVOF 제트에서 미크론 크기의 공급 원료 입자로의 강제 대류는 높은 대류 열 전달 계수 (h ~ 5000 – 17,000 W / (m2 K))를 특징으로 합니다. 이로 인해 입자 표면 온도가 급격히 증가하지만 폴리머 입자의 높은 내부 열 저항 (높은 Bi 수)은 입자 내부가 동일한 속도로 가열되는 것을 방지합니다. 결과적으로 더 큰 (예 : 90 µm 직경) 나일론 11 입자는 기판에 충격을 주기 전에 코어와 표면 사이에 급격한 온도 구배를 나타냅니다 (그림 1) [9, 10, 11].

Figure 1: Temperature of a 90 µm diameter Nylon 11 particle with respect to normalized particle radius (r/R) [10].
Figure 1: Temperature of a 90 µm diameter Nylon 11 particle with respect to normalized particle radius (r/R) [10].
Figure 2: (a) Velocity field within a spreading 90 µm diameter particle; (Left): velocity magnitude, (Right): velocity vectors, (b) example Nylon 11 splat deposited via swipe test onto a room temperature glass slide.
Figure 2: (a) Velocity field within a spreading 90 µm diameter particle; (Left): velocity magnitude, (Right): velocity vectors, (b) example Nylon 11 splat deposited via swipe test onto a room temperature glass slide.

또한 가파른 내부 온도 구배를 가진 HVOF 스프레이 폴리머 입자가 얇은 디스크 중앙에 크고 거의 반구형 인 코어가있는 특징적인 “튀김 달걀”모양으로 퍼졌다고 보고되었습니다 [10]. 이 모양은 저온, 고점도 코어와 고온, 저점도 표면의 유동 특성 간에 큰 방사형 차이가 있음을 나타냅니다.

변형된 입자의 예측 된 모양 (그림 2a)은 유리 슬라이드에 증착된 실험적으로 관찰 된 스플랫과 좋은 질적 일치를 나타 냈습니다 (그림 2b). 액적의 오른쪽에 표시된 속도 장 벡터 (그림 2a)는 저점도 “피부”가 고점도 코어 주위를 흐르면서 특징적인 “튀김 달걀” splat 모양이 형성되었음을 나타냅니다.

이 작업에서 보고된 실험 중에 사용된 HVOF 스프레이 매개 변수는 나일론 11을 증착하는데 사용할 수 있는 일반적인 HVOF 스프레이 매개 변수를 나타냅니다. 그러나 실험 기준 매개 변수를 중심으로 개발된 수치 모델은 개별 스플랫의 흐름 거동을 더 잘 이해하는 데 사용할 수 있습니다. 증착 효율 향상을 위한 공정 최적화를 지원합니다.

Figure 3: Boundary conditions, initial conditions and crosssection of a typical mesh used in Flow-3D
Figure 3: Boundary conditions, initial conditions and crosssection of a typical mesh used in Flow-3D
Figure 5: Cross section of four steel substrates: (a) polished with ~1 Pm alumina suspension, (b) grit blasted with #120 grit, (c) grit blasted with #50 grit, (d) grit blasted with #12 grit. Top image shows optical interferometry scan of # 120 grit blasted surface.
Figure 5: Cross section of four steel substrates: (a) polished with ~1 Pm alumina suspension, (b) grit blasted with #120 grit, (c) grit blasted with #50 grit, (d) grit blasted with #12 grit. Top image shows optical interferometry scan of # 120 grit blasted surface.
Figure 6: Nylon-11 splats deposited during a single run over steel substrates with roughnesses as per Figure 5.
Figure 6: Nylon-11 splats deposited during a single run over steel substrates with roughnesses as per Figure 5.
Figure 7: Nylon-11 splat on a grit blasted steel substrate, (a) close up of a peripheral splat finger.
Figure 7: Nylon-11 splat on a grit blasted steel substrate, (a) close up of a peripheral splat finger.
Figure 8: Cross-sections of predicted three-dimensional spreading splats for a 90 µm diameter Nylon-11 particle on four different surface roughnesses (dimensionless time t* = t/(D/v o (p))).
Figure 8: Cross-sections of predicted three-dimensional spreading splats for a 90 µm diameter Nylon-11 particle on four different surface roughnesses (dimensionless time t* = t/(D/v o (p))).
Figure 9: Predicted three-dimensional spreading splats for a 90 µm diameter Nylon-11 droplet.
Figure 9: Predicted three-dimensional spreading splats for a 90 µm diameter Nylon-11 droplet.

중략…….

References

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Figure 20. Top: image of electrospray, bottom: cone-jet profile using the CF emitter. Distance between the carbon fiber tip and the counter electrode is 4.0 mm, potential difference is 3500 V, flow rate is 300 nL min−1 .

Modeling and characterization of a carbon fiber emitter for electrospray ionization

A K Sen1, J Darabi1, D R Knapp2 and J Liu2
1 MEMS and Microsystems Laboratory, Department of Mechanical Engineering,
University of South Carolina, 300 Main Street, Columbia, SC 29208, USA
2 Department of Pharmacology, Medical University of South Carolina, 173 Ashley Avenue,
Charleston, SC 29425, USA
E-mail: darabi@engr.sc.edu

뾰족한 탄소 섬유(CF)를 사용하는 새로운 마이크로 스케일 이미터는 질량 분석 (MS) 분석에서 전기 분무에 사용할 수 있습니다. 탄소 섬유는 360 µm OD 및 75 µm ID의 용융 실리카 모세관과 동축에 위치하며 날카로운 팁은 튜브 말단에서 30 µm 연장됩니다.

Abstract

전기 분무 이온화 (ESI) 프로세스는 전기 유체 역학을 해결하기 위한 Taylor–Melcher 누설 유전체 유체 모델 및 액체-가스 인터페이스 추적을 위한 유체 부피 (VOF) 접근 방식을 기반으로 하는 전산 유체 역학 (CFD) 코드를 사용하여 시뮬레이션 됩니다. CFD 코드는 먼저 기존 지오메트리에 대해 검증한 다음 CF 이미터 기반 ESI 모델을 시뮬레이션하는데 사용됩니다.

시뮬레이션된 전류 흐름 및 전류 전압 결과는 CF 이미터의 실험 결과와 잘 일치합니다. 이미터 형상, 전위차, 유속 및 액체의 물리적 특성이 CF 이미터의 전기 분무 거동에 미치는 영향을 철저히 조사합니다.

스프레이 전류와 제트 직경은 액체의 유속, 전위차 및 물리적 특성과 상관 관계가 있으며 상관 결과는 문헌에 보고된 결과와 정량적으로 비교됩니다. (이 기사의 일부 그림은 전자 버전에서만 색상입니다)

Introduction

1980 년대 후반부터 매트릭스 보조 레이저 탈착 이온화 (MALDI)와 전기 분무 이온화 (ESI)의 두 가지 이온화 기술을 구현하여 감도, 속도 및 구조 정보 수준 측면에서 MS 분석이 엄청나게 성장했습니다. 1980 년대 초까지 전자 충격 (EI) 또는 화학 이온화 (CI) 방법은 가스 크로마토 그래피에 적합한 작은 생체 분자를 이온화 하는 데 사용되었습니다.

그러나 크고 열에 민감한 비 휘발성 샘플은 적절한 사전 처리 없이 EI 또는 CI-MS 기술로 분석 할 수 없습니다 [1]. ESI 기술을 사용하면 액체상에서 직접 이러한 큰 분자를 분석 할 수 있습니다 [2]. Zeleny [3, 4]는 출구에 높은 전위를 적용하여 모세관에서 액체 용액을 분사 할 수 있음을 보여주었습니다.

Dole [5, 6] 및 Fenn [7]의 선구적인 연구는 ESI를 고분자 및 생체 분자와 같은 대형 화합물의 이온화 방법으로 표시했습니다. 이에 이어이 기술에 의한 기상 이온 발생에 관련된 과정과 메커니즘이 널리 조사되고 있습니다.

ESI 방법에서 기체 이온화 된 분자는 강한 전계가 있는 상태에서 미세한 물방울을 생성하여 액체 용액에서 생성됩니다. ESI 프로세스의 이러한 능력은 단백질 및 기타 생체 분자 연구에 자연적으로 적용됨을 발견했습니다. ESI 방법과 관련된 다양한 프로세스가 그림 1에 나와 있습니다.

Figure 1. Schematic of an ESI process.
Figure 1. Schematic of an ESI process.

ESI 전위는 일반적으로 전도성 물질로 코팅 된 이미 터 튜브를 통해 외부에서 샘플 액체에 적용되지만 액체 샘플 내부에 적용될 수도 있습니다. Herring과 Qin [8]은 이미 터 팁에 삽입된 팔라듐 와이어를 통해 전기 분무 전위가 적용되는 모세관 전기 영동 (CE)을위한 ESI 인터페이스를 보여주었습니다.

Chiou의 설계 [9]에서는 작은 PDMS 칩에 있는 샘플 저장소, 마이크로 채널 및 실리카 모세관 노즐과 통합 된 내장 전극을 통해 전기 분무를 위한 고전압이 적용되었습니다.

Cao and Moini [10]는 ESI 전압이 모세관 내부에 위치한 전극을 통해인가되고 전기적 접촉이 출구 근처 모세관 벽의 작은 구멍을 통해 유지되는 전기 분무 방출기를 설계했습니다. 작은 모세관 직경 (~ 10 µm)을 가진 이미 터를 사용하여 낮은 전압에서 전기 분무가 가능하지만, 더 작은 구멍은 과도한 배압으로 인해 쉽게 막힐 수 있습니다.

직경이 더 큰 (> 50µm) 이미 터를 처리하는 것이 더 쉽습니다. 그러나 그들은 더 작은 직경의 이미 터만큼 효율적이지 않습니다 [11]. 일반적으로 ESI 전압을 적용하기 위해 유리 또는 용융 실리카와 같은 절연 재료로 제작 된 저 유량 이미 터의 외주에 전도성 코팅이 적용됩니다.

용융 실리카 모세관의 끝 부분에있는 스퍼터 코팅 된 귀금속 층은 내구성에 빠르게 영향을 미치는 것으로 관찰되었습니다. 코팅의 빠른 열화는 방전, 전기 화학적 반응 및 층과 용융 실리카 표면 사이의 불량한 기계적 결합으로 인해 발생할 수 있습니다.

이러한 에미 터의 수명은 스퍼터 코팅 후에 금을 전기 도금하거나 [12] 스퍼터 코팅 된 금 위에 SiOx를 코팅하여 증가시킬 수 있습니다 [13]. 크롬 또는 니켈 합금의 접착층 위에 금으로 코팅 된 이미 터는 우수한 결합력을 제공 할 수 있으며 음극으로 작동 할 때 내구성이 있습니다.

그러나 양극으로 작동하는 동안 접착층은 금 막을 통해 화학적으로 용해됩니다. 이미 터의 안정성과 내구성을 향상시키기 위해 대체 전도성 코팅이 평가되었습니다.

안정적인 ESI 작동을 위해 콜로이드 흑연 코팅 이미 터가 사용되었으며 수명이 길었습니다 [14]. 폴리아닐린 (PANI) 코팅 이미 터는 두꺼운 코팅으로 인해 높은 내구성을 보여주고 방전에 강합니다. PANIcoated와 gold-coated nanospray emitter의 electrospray ionization 거동을 비교 한 결과 PANIcoated emitter는 goldcoated emitter와 비슷한 향상된 감도를 제공합니다 [15].

그라파이트-폴리이 미드 혼합물은 또한 무 접착 전기 분무 방출기의 경우 전도성 코팅으로 사용되었습니다. 전도성 코팅의 안정성은 산화 스트레스 동안 좋은 성능을 나타내는 전기 화학적 방법에 의해 조사되었습니다 [16].

탄소 코팅 이미 터의 기능은 마이크로 스프레이 및 시스리스 CE 및 ESI 응용 분야에서 입증되었습니다. 이 이미 터는 견고하지는 않지만 방수가 되지 않는 CE 또는 ESI 애플리케이션에 충분히 내구성이있었습니다 [17].

우리는 막힘 문제를 제거하고 시료 액체와 금층 사이의 접촉 문제를 피할 수있는 뾰족한 탄소 섬유 기반의 새로운 ESI 방출기를 도입하여 ESI 시스템의 적용 성, 신뢰성 및 내구성을 향상 시켰습니다 [18]. 이 작업에서 탄소 섬유 기반 ESI 이미 터는 전산 유체 역학 (CFD) 소프트웨어 패키지 FLOW-3D [19]를 사용하여 시뮬레이션됩니다.

실험은 새로운 CF 이미 터를 사용하여 수행됩니다. 모델 예측은 실험 결과와 비교됩니다. 새로운 이미 터의 ESI 성능은 이미 터의 기하학적 구조, 유속, 액체의 물리적 특성과 같은 다양한 매개 변수에 대한 반응을 연구하여 평가됩니다.

스프레이 전류 및 제트 직경은 유량 및 액체의 특성과 상관 관계가 있으며 상관 결과는 문헌에보고 된 결과와 정량적으로 비교됩니다. 다음 섹션에서 ESI 공정을 지배하는 전기 유체 역학 이론은 Taylor–Melcher 누설 유전체 모델 [20]을 참조하여 설명됩니다.

그런 다음 Hartman 등이 사용하는 ESI 구성을 고려하여 CFD 코드의 유효성을 확인합니다 [21]. 또한 CF 기반 ESI 모델에 대한 시뮬레이션 및 실험 결과가 제시되고 논의됩니다. 마지막으로 모수 연구 결과와 상관 관계를 제시하고 논의합니다.

Figure 2. Forces in the liquid cone.
Figure 2. Forces in the liquid cone.
Figure 3. Schematic of the ESI model studied by Hartman et al [21].
Figure 3. Schematic of the ESI model studied by Hartman et al [21].
Figure 6. Cone-Jet profile and the electric potential contours at 19 kV; cone length is 4.3 mm.
Figure 6. Cone-Jet profile and the electric potential contours at 19 kV; cone length is 4.3 mm.
Figure 7. A photograph of the experimental cone shape; cone length is 4.2 ± 0.2 mm [21].
Figure 7. A photograph of the experimental cone shape; cone length is 4.2 ± 0.2 mm [21].
Figure 15. Electric field contours at various time steps
Figure 15. Electric field contours at various time steps
Figure 20. Top: image of electrospray, bottom: cone-jet profile using the CF emitter. Distance between the carbon fiber tip and the counter electrode is 4.0 mm, potential difference is 3500 V, flow rate is 300 nL min−1 .
Figure 20. Top: image of electrospray, bottom: cone-jet profile using the CF emitter. Distance between the carbon fiber tip and the counter electrode is 4.0 mm, potential difference is 3500 V, flow rate is 300 nL min−1 .

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Fig. 7. Simulation results of temperature distribution between Ni stamps and PBO-SAM/PMMA substrate in NIL process: (A) stamp cross-sectional, (B) PMMA substrate cross-sectional, (C) 3-dimensional and (D) intrinsic 3-dimensional views, respectively. The study of computed condition in nanoimprint process is at 150 o C and 50 bar during 10 min. Note that for NIL experimental parameters, the simulated results have already decided before doing nanoimprint experiment.

A non-fluorine mold release agent for Ni stamp in nanoimprint process

Tien-Li Chang a,*, Jung-Chang Wang b
, Chun-Chi Chen c
, Ya-Wei Lee d
, Ta-Hsin Chou a
a Mechanical and Systems Research Laboratories, Industrial Technology Research Institute, Rm. 125, Building 22, 195 Section 4, Chung Hsing Road, Chutung, Hsinchu 310, Taiwan, ROC bDepartment of Manufacturing Research and Development, ADDA Corporation, Taiwan
cNational Nano Device Laboratories, Taiwan
d Research and Development Division, Ordnance Readiness Development Center, Taiwan

Abstract

이 연구는 나노 임프린트 공정에서 Ni 몰드 스탬프와 PMMA (폴리 메틸 메타 크릴 레이트) 기판 사이의 접착 방지 층으로서 새로운 재료를 제시합니다. 폴리 벤족 사진 ((6,6′-bis (2,3-dihydro3-methyl-4H-1,3-benzoxazinyl))) 분자 자기 조립 단층 (PBO-SAM)은 점착 방지 코팅제로 간주되어 불소 함유 화합물은 Ni / PMMA 기판의 나노 임프린트 공정을 개선 할 수 있습니다. 이 작업에서 나노 구조 기반 Ni 스탬프와 각인 된 PMMA 몰드는 각각 전자빔 석판화 (EBL)와 수제 나노 임프린트 장비에 의해 수행됩니다. 제작 된 나노 패턴의 형성을 제어하기 위해 시뮬레이션은 HEL (hot embossing lithography) 공정 동안 PBO-SAM / PMMA 기판의 변형에 대한 온도 분포의 영향을 분석 할 수 있습니다. 여기서 기둥 패턴의 직경은 Ni 스탬프 표면에 200nm 및 400nm 피치입니다. 이 적합성 조건에서 소수성 PBO-SAM 표면을 기반으로하여 Ni 몰드 스탬프의 결과는 품질 및 수량 제어에서 90 % 이상의 개선을 추론합니다.

Introduction

나노 임프린트 리소그래피 (NIL)는 초 미세 패터닝 기판 기술을 대량 생산할 수있는 가장 큰 잠재력입니다 [1,2]. 최근에는 광전자 장치 [3], 양자 컴퓨팅 장치 [4], 바이오 센서 [5] 및 전자 장치 [6]에 요구 될 수있는 NEMS / MEMS 기술의 빠른 개발이 이루어지고 있습니다.

따라서 기존의 포토 리소 그래프는 할당에 적합한 방법이 아닐 수 있습니다 [7]. X 선, 이온빔, 전자빔 리소그래피의 경우 LCD의 도광판 초박막 판과 같은 대 면적 패턴 제작에 적합하지 않습니다. 제어하기 어렵습니다. 일부 제작된 문제를 기반으로 NIL 프로세스는 재료, 패턴 크기, 구조 및 기판 지형면에서 유연성을 제공합니다 [8].

오늘날 NIL 제조 방법은 낮은 비용과 높은 처리량의 높은 패터닝 해상도의 조합으로 학제 간 나노 스케일 연구 및 상용 제품의 새로운 문을 열 수 있는 큰 관심을 받고 있습니다. 그러나 이 나노 임프린트 기술이 산업 규모 공정을 위해 충분히 성숙하기 전에 몇 가지 응용 문제를 해결해야 합니다.

각인된 몰드 공정은 종종 고온 (폴리머의 유리 전이 온도에 대해> 100oC)과 고압 (> 100bar)에서 수행되기 때문에 분명히 바람직하지 않습니다. 가열 및 냉각 공정의 열주기는 금형 및 각인 된 기판의 왜곡을 유발할 수 있습니다. 한 가지 특별한 문제는 스탬프와 폴리머 사이의 접착 방지 층 처리를 제어하여 기계적 결함이 임프린트 품질과 스탬프 수명에 영향을 미칠 수있는 중요한 패턴 결함이되는 것을 방지하는 것입니다.

Schift et al. 플루오르화 트리클로로 실란을 마이크로 미터 체제에서 실리콘에 대한 접착 방지 코팅으로 사용하는 것으로 입증되었습니다 [9]. 또한 Park et al. Ni 몰드 스탬프에 더 나은 접착 방지 코팅 공정을 달성하기 위해 불소화 실란제를 사용했습니다 [10].

그러나 지금까지 Ni 스탬프에 대한 접착 방지 코팅 처리의 NIL 공정에서 비 불소 물질에 대한 시도는 거의 이루어지지 않았습니다. 우리의 생활 환경은 그것을 유지하기 위해 불소가 아닌 물질이 필요합니다. 또한 Ni 계 소재의 부드러운 특성을 바탕으로 가장 중요한 롤러 나노 임프린트 기술을 개발할 수 있습니다.

본 연구의 목적은 Ni 스탬프와 PMMA 기판 사이의 점착 방지 코팅제로 PBO-SAM을 개발하여 나노 제조 기술, 즉 NIL을 향상시키는 것입니다.

Experiment

먼저 4,4′- 이소 프로필 리 덴디 페놀 (비스페놀 -A, BA-m), 포름 알데히드 및 ​​메틸 아민을 반응시켜 폴리 벤족 사진을 제조 하였다. 미국 Aldrich Chemical company, Inc.에서 구입 한 모든 화학 물질. 합성 과정에서 포름 알데히드/디 옥산 및 메틸 아민 / 디 옥산 물질을 10 o C에서 항아리에서 10분 동안 측정하는 벤족 사진 단량체가 필요했습니다.

디 에틸 에테르를 기화시킨 후, 벤족 사진 전구체가 완성되었다. benzoxazine 전구체를 140 o C에서 1 시간 동안 가열하면 BA-m 폴리 벤족 사진을 얻을 수 있습니다. 다음으로 4 인치입니다.

이 연구에서는 p 형 Si (10 0) 웨이퍼를 사용할 수 있습니다. SiO2 기반 Ni (원자량 5.87g / mole) 기판의 제조를 위해 Ti (5nm) 및 SiO2 (20nm)를 순차적으로 증착 한 후 O2- 플라즈마 처리를 수행했습니다. Ni 기판과 SiO2 층 사이의 접착력을 높이기 위해 Ti 중간층이 사용되었습니다. 아세톤, 이소프로판올 및 탈 이온수를 사용하여 세척 한 후 샘플을 포토 레지스트 (ZEP520A-7, Nippon Zeon Co., Ltd.)로 스핀 코팅했습니다.

Fig. 1. Schematic diagram of nanostructures using NIL process: (A) EBL equipment for fabricated mold stamp. (B) HEL equipment for nanoimprint pattern with computer controlled electronics. (C) A nickel-based pillar mold can imprint into a PBO-SAM polymer resist layer; afterward, the mold removal and pattern transfer are based on anisotropic etching to remove reside.
Fig. 1. Schematic diagram of nanostructures using NIL process: (A) EBL equipment for fabricated mold stamp. (B) HEL equipment for nanoimprint pattern with computer controlled electronics. (C) A nickel-based pillar mold can imprint into a PBO-SAM polymer resist layer; afterward, the mold removal and pattern transfer are based on anisotropic etching to remove reside.

마스터 몰드는 그림 1 (A)에서 Ni 필름의 반응성 이온 에칭 (RIE)과 함께 Crestec CABL8210 전자 빔 직접 쓰기 도구 (30 keV, 100 pA)를 사용하여 제작되었습니다. 그런 다음 시뮬레이션된 결과는 NIL 프로세스에서 엠보싱 압력으로 기계적 고장의 효과를 제공할 수 있으며, 이는 우리가 원하는 나노 패턴 설계 및 연구에 도움이 될 수 있습니다.

PBOSAM / PMMA 기판 모델의 변형은 3 차원 접근법에 기반한 유한 체적 방법 (FVM)을 통해 예측할 수 있습니다. Navier-Stokes 방정식 [11]에서 압력과 속도 사이의 결합은 SIMPLE 알고리즘을 사용하여 이루어집니다. 2 차 상향 이산화 방식은 대류 플럭스 및 운동량의 확산 플럭스, 유체의 질량 분율에 대한 중심 차이 방식에 대해 구현됩니다. 완화 부족 요인의 일반적인 값은 0.5입니다.

수렴 기준이 1105로 설정된 연속성을 제외한 모든 변수에 대해 잔차가 1103 미만인 경우 솔루션이 수렴된 것으로 간주됩니다. 여기서 각인된 나노 패턴은 그림 1 (B)와 같이 수제 장비에서 수행한 HEL 공정을 통해 사용할 수 있습니다. PBO-SAM 코팅 방법으로 HEL 절차를 활용 한 나노 패턴의 제작은 그림 1 (C)에 개략적으로 표시되었습니다.

200nm의 얇은 PMMA 필름 (분자량 15kg / mole)을 SiO2 기판에 스핀 코팅 한 후 160oC에서 30 분 동안 핫 플레이트에서 베이킹했습니다. 또한 PBO-SAM 코팅은 접착 방지제입니다. CVD 공정에 의해 증착되었습니다. 마스터는 150oC 및 50bar에서 10 분 동안 PBO-SAM / PMMA 기판 필름에 엠보싱하여 복제되었습니다.

마지막으로, 엠보싱 된 나노 구조물의 바닥에 남아 있던 PBO-SAM / PMMA 층은 RIE 처리로 제거되었습니다. 각 임프린트 후 스탬프 및 기판의 품질이 제작 된 후 현미경을 사용하여 관찰하고 물 접촉각 (CA) 측정을 사용하여 습윤 및 접착 특성을 알아낼 수 있습니다.

Fig. 2. FTIR absorption spectrum of polybenzoxazines indicates the vibrational modes of molecular bonds.
Fig. 2. FTIR absorption spectrum of polybenzoxazines indicates the vibrational modes of molecular bonds.
Fig. 3. FE-SEM micrograph of Ni stamps before imprinted PMMA substrate. The pillar diameter is 200 nm, and its period is 400 nm.
Fig. 3. FE-SEM micrograph of Ni stamps before imprinted PMMA substrate. The pillar diameter is 200 nm, and its period is 400 nm.
Fig. 5. Contact angles of water drops on (A) a PMMA polymer film surface, and (B) a smooth PBO-SAM coating film surfaceFig. 6. Simulation of Ni stamps and PBO-SAM/PMMA substrate in NIL process: (A) A nanoimprint system geometry, and (B) its grid plot.
Fig. 5. Contact angles of water drops on (A) a PMMA polymer film surface, and (B) a smooth PBO-SAM coating film surfaceFig. 6. Simulation of Ni stamps and PBO-SAM/PMMA substrate in NIL process: (A) A nanoimprint system geometry, and (B) its grid plot.
Fig. 7. Simulation results of temperature distribution between Ni stamps and PBO-SAM/PMMA substrate in NIL process: (A) stamp cross-sectional, (B) PMMA substrate cross-sectional, (C) 3-dimensional and (D) intrinsic 3-dimensional views, respectively. The study of computed condition in nanoimprint process is at 150 o C and 50 bar during 10 min. Note that for NIL experimental parameters, the simulated results have already decided before doing nanoimprint experiment.
Fig. 7. Simulation results of temperature distribution between Ni stamps and PBO-SAM/PMMA substrate in NIL process: (A) stamp cross-sectional, (B) PMMA substrate cross-sectional, (C) 3-dimensional and (D) intrinsic 3-dimensional views, respectively. The study of computed condition in nanoimprint process is at 150 o C and 50 bar during 10 min. Note that for NIL experimental parameters, the simulated results have already decided before doing nanoimprint experiment.

References

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Simulation of EPS foam decomposition in the lost foam casting process

X.J. Liu a,∗, S.H. Bhavnani b,1, R.A. Overfelt c,2
a United States Steel Corporation, Great Lakes Works, #1 Quality Drive, Ecorse, MI 48229, United States b 213 Ross Hall, Department of Mechanical Engineering, Auburn University, Auburn, AL 36849-5341, United States c 202 Ross Hall, Department of Mechanical Engineering, Materials Engineering Program, Auburn University, Auburn, AL 36849-5341, United States
Received 17 April 2006; received in revised form 14 July 2006; accepted 21 August 2006

Keywords: Lost foam casting; Heat transfer coefficient; Gas pressure; VOF-FAVOR

LFC (Loss Foam Casting) 공정에서 부드러운 몰드 충진의 중요성은 오랫동안 인식되어 왔습니다. 충진 공정이 균일할수록 생산되는 주조 제품의 품질이 향상됩니다. 성공적인 컴퓨터 시뮬레이션은 금형 충전 공정에서 복잡한 메커니즘과 다양한 공정 매개 변수의 상호 작용을 더 잘 이해함으로써 새로운 주조 제품 설계의 시도 횟수를 줄이고 리드 타임을 줄이는데 도움이 될 수 있습니다.

이 연구에서는 용융 알루미늄의 유체 흐름과 금속과 발포 폴리스티렌 (EPS) 폼 패턴 사이의 계면 갭에 관련된 열 전달을 시뮬레이션하기 위해 전산 유체 역학 (CFD) 모델이 개발되었습니다.

상업용 코드 FLOW-3D는 VOF (Volume of Fluid) 방법으로 용융 금속의 전면을 추적 할 수 있고 FAVOR (Fractional Area / Volume Ratios) 방법으로 복잡한 부품을 모델링 할 수 있기 때문에 사용되었습니다. 이 코드는 폼 열화 및 코팅 투과성과 관련된 기체 갭 압력을 기반으로 다양한 계면 열 전달 계수 (VHTC)의 효과를 포함하도록 수정되었습니다.

수정은 실험 연구에 대해 검증되었으며 비교는 FLOW-3D의 기본 상수 열 전달 (CHTC) 모델보다 더 나은 일치를 보여주었습니다. 금속 전면 온도는 VHTC 모델에 의해 실험적 불확실성 내에서 예측되었습니다. 몰드 충전 패턴과 1-4 초의 충전 시간 차이는 여러 형상에 대해 CHTC 모델보다 VHTC 모델에 의해 더 정확하게 포착되었습니다. 이 연구는 전통적으로 매우 경험적인 분야에서 중요한 프로세스 및 설계 변수의 효과에 대한 추가 통찰력을 제공했습니다.

지난 20 년 동안 LFC (Loss Foam Casting) 공정은 코어가 필요없는 복잡한 부품을 제조하기 위해 널리 채택되었습니다. 이는 자동차 제조업체가 현재 LFC 기술을 사용하여 광범위한 엔진 블록과 실린더 헤드를 생산하기 때문에 알루미늄 주조 산업에서 특히 그렇습니다.

기본 절차, 적용 및 장점은 [1]에서 찾을 수 있습니다. LFC 프로세스는 주로 숙련 된 실무자의 경험적 지식을 기반으로 개발되었습니다. 발포 폴리스티렌 (EPS) 발포 분해의 수치 모델링은 최근에야 설계 및 공정 변수를 최적화하는 데 유용한 통찰력을 제공 할 수있는 지점에 도달했습니다. LFC 공정에서 원하는 모양의 발포 폴리스티렌 폼 패턴을 적절한 게이팅 시스템이있는 모래 주형에 배치합니다.

폼 패턴은 용융 금속 전면이 패턴으로 진행될 때 붕괴, 용융, 기화 및 열화를 겪습니다. 전진하는 금속 전면과 후퇴하는 폼 패턴 사이의 간격 인 운동 영역은 Warner et al. [2] LFC 프로세스를 모델링합니다. 금형 충진 과정에서 분해 산물은 운동 영역에서 코팅층을 통해 모래로 빠져 나갑니다.

용융 금속과 폼 패턴 사이의 복잡한 반응은 LFC 공정의 시뮬레이션을 극도로 어렵게 만듭니다. SOLA-VOF (SOLution AlgorithmVolume of Fluid) 방법이 Hirt와 Nichols [3]에 의해 처음 공식화 되었기 때문에 빈 금형을 사용한 전통적인 모래 주조 시뮬레이션은 광범위하게 연구되었습니다.

Lost foam 주조 공정은 기존의 모래 주조와 많은 특성을 공유하기 때문에이 새로운 공정을 모델링하는 데 적용된 이론과 기술은 대부분 기존의 모래 주조를 위해 개발 된 시뮬레이션 방법에서 비롯되었습니다. 패턴 분해 속도가 금속성 헤드와 금속 전면 온도의 선형 함수라고 가정함으로써 Wang et al. [4]는 기존의 모래 주조의 기존 컴퓨터 프로그램을 기반으로 복잡한 3D 형상에서 Lost foam 주조 공정을 시뮬레이션했습니다.

Liu et al. [5]는 금속 앞쪽 속도를 예측하기 위한 간단한 1D 수학적 모델과 함께 운동 영역의 배압을 포함했습니다. Mirbagheri et al. [6]은 SOLA-VOF 기술을 기반으로 금속 전면의 자유 표면에 대한 압력 보정 방식을 사용하는 Foam 열화 모델을 개발했습니다.

Kuo et al.에 의해 유사한 배압 방식이 채택되었습니다. [7] 운동량 방정식에서이 힘의 값은 실험 결과에 따라 패턴의 충전 순서를 연구하기 위해 조정되었습니다.

이러한 시뮬레이션의 대부분은 LFC 공정의 충전 속도가 기존의 모래 주조 공정보다 훨씬 느린 것으로 성공적으로 예측합니다. 그러나 Foam 분해의 역할은 대부분 모델의 일부가 아니며 시뮬레이션을 수행하려면 실험 데이터 또는 경험적 함수가 필요합니다.

현재 연구는 일정한 열전달 계수 (CHTC)를 사용하는 상용 코드 FLOW-3D의 기본 LFC 모델을 수정하여 Foam 열화와 관련된 기체 갭 압력에 따라 다양한 열전달 계수 (VHTC)의 영향을 포함합니다. 코팅 투과성. 수정은 여러 공정 변수에 대한 실험 연구에 대해 검증되었습니다.

또한, 손실 된 폼 주조에서 가장 중요한 문제인 결함 형성은 문헌에서 인용 된 수치 작업에서 모델링되지 않았습니다. 접힘, 내부 기공 및 표면 기포와 같은 열분해 결함은 LFC 작업에서 많은 양의 스크랩을 설명합니다. FLOW-3D의 결함 예측 기능은 프로세스를 이해하고 최적화하는데 매우 중요합니다.

Fig. 7. Comparison of mold filling times for a plate pattern with three ingates: (a) measured values by thermometric technique [18]; (b) predicted filling times based on basic CHTC model with gravity effect; and (c) predicted filing times based on the VHTC model with heat transfer coefficient changing with gas pressure; (d) mold filling time at the right-and wall of the mold for the plate pattern with three ingates.
Fig. 7. Comparison of mold filling times for a plate pattern with three ingates: (a) measured values by thermometric technique [18]; (b) predicted filling times based on basic CHTC model with gravity effect; and (c) predicted filing times based on the VHTC model with heat transfer coefficient changing with gas pressure; (d) mold filling time at the right-and wall of the mold for the plate pattern with three ingates.
Fig. 10. Defects formation predicted by (a) basic CHTC model with gravity effect; (b) VHTC model with heat transfer coefficient based on both gas pressure and coating thickness; and (c) improved model for two ingates. Color represents probability for defects (blue is the lowest and red highest).
Fig. 10. Defects formation predicted by (a) basic CHTC model with gravity effect; (b) VHTC model with heat transfer coefficient based on both gas pressure and coating thickness; and (c) improved model for two ingates. Color represents probability for defects (blue is the lowest and red highest).

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Figure 8 Evaluation test of thermal sprayed coatings

Development of Advanced Materials and Manufacturing Technologies for High-efficiency Gas Turbines

고효율 가스 터빈용 신소재 및 제조 기술 개발

Mitsubishi Heavy Industries Technical Review Vol. 52 No. 4 (December 2015)

가스 터빈 복합 화력 (GTCC) 발전 시장은 재생 에너지와 공존 할 수 있는 가장 깨끗하고 경제적인 화력 발전 시스템으로 장기적으로 성장할 것으로 예상됩니다. 효율성을 더욱 높이려면 터빈 부품 재료의 특성을 개선하고 첨단 블레이드 설계에 필요한 복잡한 구조를 구축하기 위한 제조 기술 개발이 필수적입니다.

이 보고서는 가스 터빈의 고온 적용을 위한 재료 및 제조 기술로서 합금 설계 및 주조, 코팅, 용접 수리 및 냉각 구멍 드릴링 공정을 포함한 기술 개발을 제시합니다.

최근 몇 년 동안 세계 에너지 수요는 특히 중국과 인도와 같은 아시아 국가에서 현저하게 증가하고 있습니다. 2035 년 글로벌 에너지 소비량은 2010 년 대비 약 1.5 배 수준에이를 것으로 예상됩니다. 일본에서는 에너지 자급률이 10 % 미만이며 에너지 사용 효율을 높이고 환경 부하를 줄이는 것이 시급한 문제입니다. . 특히 현재 일본 전기 생산량의 거의 90 %를 차지하고있는 화력 발전의 효율화가 필요하다. 발전 효율은 가스 터빈 (시스템의 주요 구성 요소)의 연소 온도에 크게 영향을받습니다. 온도가 상승함에 따라 열 순환 효율이 향상 될 수 있기 때문에 Mitsubishi Hitachi Power Systems, Ltd.

(MHPS)는 1980 년대 초부터 더 높은 온도 / 더 나은 효율성 및 더 큰 용량을 가진 고급 시스템을 개발했습니다.
그림 11에서 보듯이 터빈 입구 온도는 1984 년 (Type D) 1,100 ° C 등급에서 시작하여 1989 년 1,350 ° C 등급 (Type F), 1997 년 1,500 ° C 등급 (Type 지).

또한 2011 년에는 1,600 ° C 급 가스 터빈 (J 형)이 출범했습니다 .2 2004 회계 연도부터 국가 프로젝트 “1,700 ° C 급 가스 터빈을위한 원소 기술 개발”이 시작되었습니다. J 형 가스 터빈 개발 프로젝트는 첨단 열 차단 코팅 (TBC) 및 냉각 / 공기 역학 기술과 같은 결과도 활용되었습니다 (그림 2).

가스 터빈 온도를 더욱 높이려면 이러한 고온을 견딜 수있는 신소재를 설계하고 터빈 부품의 특성을 개선하며 고급 블레이드 설계에 필요한 복잡한 구조를 구축하기 위한 제조 기술을 발명하는 것이 중요합니다.
이 보고서는 MHPS가 Mitsubishi Heavy Industries, Ltd. (MHI) 연구 및 혁신 센터와 함께 개발하고 있는 이러한 기술을 소개합니다.

 Figure 1    Increase in the turbine inlet temperature and transition of applied materials and technologies
Figure 1 Increase in the turbine inlet temperature and transition of applied materials and technologies
Characteristics of the M501J gas turbine
Characteristics of the M501J gas turbine

MHPS와 MHI는 MGA1400, MGA1400DS, MGA2400을 고온 환경에서 사용할 수 있을 만큼 내구성이 있는 고강도 Ni 계 초합금으로 개발하여 자사 제품에 적용하고 있습니다. 일반적으로 인터 빈 블레이드에 사용되는 초합금은 주조 방법에 따라 기존 주조 합금, 방향 응고 합금, 단결정 합금 중 하나로 분류됩니다.

이 세 가지 유형 중 MGA1400 및 MGA2400은 기존 주조 합금의 범주에 해당하는 반면 MGA1400DS는 방향성 응고 합금입니다 . 단결정 합금은 입자 경계가 없기 때문에 가장 강하고 (그 존재는 재료 강도 측면에서 불리 함) 입자 경계 강화를 고려하지 않고 합금 조성을 최적화 할 수 있습니다.

그러나 주조 공정에서 발생하는 주조 결함은 강도를 크게 저하시킬 수 있으므로 제조 기술의 확립이 중요합니다. 산업용 가스 터빈 블레이드는 크기가 크기 때문에 항공기 엔진보다 제조하기가 더 어렵습니다.

MHI 연구 혁신 센터는 1700 ° C 급 가스 터빈을 건설하기 위해 NIMS (National Institute for Materials Science)와 공동 연구를 수행하여 단결정 블레이드용 고내열 소재를 개발했습니다. 고온에서 재료의 강도를 검증하는 것 뿐만 아니라 결함이 없는 좋은 단결정 구조를 얻기 위한 주조 기술 개발도 필수적입니다.

신소재는 원재료 및 주조 비용 등 경제성 측면에서도 만족스러워야 한다. 또한 고온에서 필요한 모든 재료 특성 (예 : 크리프 강도, 열 피로 강도 및 내 산화성)을 나타내야 합니다. 특히 크리프 강도와 열 피로 강도의 공존을 실현하기 위한 기술 개발이 어려웠습니다.

NIMS 합금 설계 프로그램에 의해 결정된 조성으로 테스트 합금을 조사하는 동안 MHI와 NIMS는 속성 예측을 위한 데이터베이스를 확장하기 위해 주로 열 피로 강도에 대한 데이터를 수집했습니다. 이러한 노력으로 인해 크리프 강도와 열 피로 강도 모두에서 우수한 특성을 가진 단결정 합금 인 MGA1700이 개발되었습니다 (그림 3).

일반적으로 레늄과 같은 고가의 희귀 금속을 포함하는 고강도의 다른 단결정 합금과 달리 MGA1700은 콘없이 고강도를 실현하는 획기적인 합금입니다.

 Figure 3    Micro structure and high-temperature strength property of the designed alloy
Figure 3 Micro structure and high-temperature strength property of the designed alloy
   Figure 8    Evaluation test of thermal sprayed coatings
Figure 8 Evaluation test of thermal sprayed coatings
 Figure 11    Schematic diagram of LMD Figure 13    Cross-sectional comparison of weld beads between analysis results and LMD application      Figure 12    Analytical model and a typical result of the analysis
Figure 11 Schematic diagram of LMD Figure
Figure 12 Analytical model and a typical result of the analysis
13 Cross-sectional comparison of weld beads between analysis results and LMD application

중략 ……

References

1. Komori, T. et al., the 41th GTSJ Seminar material (2013) pp. 57-64 2. Yuri, M. et al., Development of 1600°C-Class High-efficiency Gas Turbine for Power Generation Applying J-Type Technology, Mitsubishi Heavy Industries Technical Review Vol. 50 No. 3 (2013) pp.1-10. 3. Okada, I. et al., Development of Ni base Superalloy for Industrial Gas Turbine, Superalloy2004,(2004),p707-712. 4. Kishi, K. et al., Welding Repair Technology for Single Crystal Blade and Vane,Proceedings of the International Gas Turbine Congress, (2014), IGTC07-116S. 5. KREUTZ, E.W. et al., Process Development and Control of Laser Drilled and Shaped Holes in TurbineComponents, JLMN-Journal of Laser Micro/Nanoengineering, Vol.2 No.2 (2007), p123. 6. Sezer, H.K. et al., Mechanisms of Acute Angle Laser Drilling induced Thermal Barrier CoatingDelamination,Journal of Manufacturing Science and Engineering, vol.131 (2009), p.051014-1 7. Goya, S. et al., High-Speed & High-Quality Laser Drilling Technology Using a Prism Rotator, MitsubishiHeavy Industries Technical Review Vol. 52 No. 1 (2015) pp. 106-109

Figure 2: Computational domain and boundary conditions for the two-dimensional flow problem

3-D transient simulation of viscoelastic coating flows

점탄성 코팅 흐름의 3-D 과도 시뮬레이션

James M. Brethour
Flow Science, Inc.
Santa Fe, New Mexico USA 87505
Presented at the 13th International Coating Science and Technology Symposium, September 10-
13, 2006, Denver, Colorado1

일시적인 프로세스의 3 차원 시뮬레이션은 자유 표면 이동 중에 왜곡을 방지하기 위해 시뮬레이션 중에 업데이트 해야 하는 복잡한 메시를 생성하기 때문에 일반적으로 사용자와 컴퓨터 모두에게 매우 어렵고 지루합니다.

고정된 규칙적인 메시를 통해 유체 운동을 추적하는 Eulerian 기술을 사용하면 이러한 어려움이 제거됩니다. 이러한 방식으로, 큰 유체 변형과 심지어 분열을 계산할 수 있습니다.

이 작업에 사용된 계산 소프트웨어인 FLOW-3D® [1]는 지속적으로 변화하는 유체 영역의 자유 표면을 추적하기 위해 Volume-of-Fluid 기반 기술의 독창적이고 진정한 형태 인 TruVOF®를 사용합니다.

이 모델에 추가 된 것은 점탄성 흐름의 시뮬레이션을 가능하게 하는 사용자 정의입니다. 점탄성 모델은 형태 텐서 [2]를 사용하여 각 유체 요소의 변형 및 회전 이력을 추적합니다. 이러한 계산은 이미 흐름 모델에 존재하는 질량 보존 및 운동량 방정식과 함께 해결됩니다. 필요한 추가 매개 변수는 탄성 계수와 이완 시간입니다.

계산 결과는 슬롯 코팅 [3]에서 하류 접촉 라인이 불안정해질 때까지 코팅액의 공급이 점차 감소하는 저 유량 한계의 실험 결과와 비교됩니다. 계산 결과는 모세관 수의 변화와 유체의 탄성 모두에 대한 실험과 잘 연관되어 있습니다.

Figure 1: Two-dimensional slice of slot coating process; in the experiments, the coating gap was maintained at 100 μm, the slot gap was 125 μm, and the vacuum pressure and web speed were continously varied.
Figure 1: Two-dimensional slice of slot coating process; in the experiments, the coating gap was maintained at 100 μm, the slot gap was 125 μm, and the vacuum pressure and web speed were continously varied.
Figure 2: Computational domain and boundary conditions for the two-dimensional flow problem
Figure 2: Computational domain and boundary conditions for the two-dimensional flow problem
Figure 3: Plot of low flow limits in slot coating as a function of capillary number and fluid elasticity. The solid markers indicate simulation results while the open markers indicate experimental results [3]. The lines represent best-fit power-law curves.
Figure 3: Plot of low flow limits in slot coating as a function of capillary number and fluid elasticity. The solid markers indicate simulation results while the open markers indicate experimental results [3]. The lines represent best-fit power-law curves.
Deep 코팅 검증계산

The Coating Application Using the Excellent Flow Modeling Software FLOW-3D

우수한 플로우 모델링 소프트웨어 FLOW-3D를 이용한 코팅 적용 연구

FLOW-3D는 미국 Flow Science Inc.에 의해 개발된 고유한 계산 유체 동적 프로그램입니다. FORE-3D는 FORDR(장애물 표현의 단편 영역 볼륨) 유한 차이 체계를 기반으로 Navier-Stokes 전체 솔버를 가지고 있습니다.

실제 VOF(Volume of Fluid) 알고리즘은 FLOW-3D에 통합되어 신뢰할 수 있는 자유 표면 흐름 분석을 제공합니다. FLOW-3D에는 다양한 물리적 모델이 있습니다. 따라서 FLOW-3D는 잉크젯 또는 코팅 등 광범위한 산업 영역에 사용됩니다.

본 논문에서는 FLOW-3D의 특징과 동적 접촉선의 직접 연산, 코팅 적용 예제를 설명합니다.

확대한 구형 방울
확대한 구형 방울
표면 파를 수반하는 세류의 시트 모양 흐름/세류가 축퇴하여 액적을 형성하는 예
표면 파를 수반하는 세류의 시트 모양 흐름/세류가 축퇴하여 액적을 형성하는 예
Deep 코팅 검증계산
Deep 코팅 검증계산
롤 코팅 검증계산
롤 코팅 검증계산
2層 コー テ ィング計算 例/ゆ っ くりした ウェ ブ接 近
2層 コー テ ィング計算 例/ゆ っ くりした ウェ ブ接 近
カー テ ン塗 布 のエ ッジ近 傍 にお け る塗 液流 れ解 析
カー テ ン塗 布 のエ ッジ近 傍 にお け る塗 液流 れ解 析
Laser Welding and Additive Manufacturing

Melt Pool Modeling: Innovation in Laser Welding & Additive Manufacturing

Melt Pool Modeling - Innovation in Laser Welding & Additive Manufacturing Webinar

Additive Manufacturing 기술이 새로운 제조 방식을 계속 발전시키면서 CFD 모델링은 공정 개발 및 최적화와, 재료의 변화를 이해하고, 설계 및 연구를 수행하는 매우 유용한 도구가 되었습니다. 이 웨비나에서는 최첨단 CFD 소프트웨어 FLOW-3D AM이 레이저 파우더 베드 융합 및 직접 에너지 증착 공정에서 용융 풀 역학을 모델링하는데 어떻게 사용되는지 살펴볼 것입니다. 그런 다음 유용한 정보를 얻기 위해 모델 데이터의 추출 및 분석에 집중하고 FLOW-3D AM에서 최근에 구현된 기능에 대해 논의합니다. 마지막으로 레이저 용접 및 적층 제조 응용 분야 모두에 적용할 수 있는 관련 산업 사례 연구를 검토하여 산업 응용 분야에 소프트웨어 사용을 보여줍니다.

https://www.facebook.com/FLOW3D.CFD.Software/videos/359103388813376/

Laser Metal Deposition Simulation | FLOW-3D AM | Facebook
Laser Metal Deposition Simulation | FLOW-3D AM | Facebook
FLOW-3D - We'll be presenting and exhibiting at the 2021
FLOW-3D – We’ll be presenting and exhibiting at the 2021

등록 링크https://zoom.us/webinar/register/7516034917241/WN_tik88gXJRzult2_HDNIzPA
산지 표준시(미국 및 캐나다)의 2021년 5월 5일 11:00 오전 (현지 시간)
이벤트 주최: FLOW-3D

발표자

photo of Paree Allu

Paree AlluSenior CFD Engineer @Flow Science, Inc.Paree Allu is a Senior CFD Engineer with Flow Science, where he leads the technical and business strategy for Flow Science’s additive manufacturing and laser welding software solutions. Paree holds a Master’s Degree in Mechanical Engineering from The Ohio State University.

photo of Allyce Jackman

Allyce JackmanCFD Engineer @Flow Science, Inc.Allyce Jackman is a CFD Engineer with Flow Science, where she specializes in laser welding, coating, and complex multiphysics applications. Allyce holds a Bachelor’s Degree in Mechanical Engineering from the University of New Mexico.

Rivulet Formation in Slide Coating

Simulation of Transient and Three-Dimensional Coating Flows Using a Volume-of-Fluid Technique

Volume-of-Fluid 기법을 사용한 과도 및 3 차원 코팅 흐름 시뮬레이션

슬라이드 코팅 흐름은 정밀 필름 코팅 제품의 제조에 널리 사용됩니다. 코팅 속도를 높이고 코팅 필름의 성능을 향상시키기 위해 슬라이드 코팅 공정을 더 잘 이해하기 위해 상당한 노력을 기울이고 있습니다. 예를 들어 Chen1과 같이 잘 정의 된 한계 이상으로 코팅 속도를 높이면 코팅 비드가 완전히 파손될 수 있음이 입증되었습니다.

이 논문에서는 유체 표면의 임의, 3 차원 및 시간에 따른 변형을 설명 할 수있는 계산 방법에서 얻은 슬라이드 코팅 흐름의 시뮬레이션 결과를 제시합니다. 상용 프로그램에서 사용할 수있는이 방법은 VOF (Volume-of-Fluid) 기술 3,4로 유체를 추적하는 고정 그리드를 사용합니다. 표면 장력, 벽 접착력, 유체 운동량 및 점성 응력은 분석에서 완전히 설명됩니다.

기본 방법은 딥 코팅 데이터와의 비교를 통해 설명됩니다 5. 그런 다음 접촉 선과 동적 접촉각이 우리의 방법에서 암시 적으로 처리되는 방법에 대한 논의를 제시합니다. VOF 기술을 사용하기 때문에 유체를 포함하는 각 제어 볼륨에 작용하는 힘의 합계 만 필요합니다. 그러면 접촉 선의 위치와 동적 접촉각이 계산 된 힘 균형에서 자동으로 발생합니다. 우리의 기술은 코팅 흐름에서 시작 및 비드 분해 현상의 예와 함께 설명됩니다.

그림에서 볼 수 있듯이 신속한 공정의 경우 당사의 접근 방식은 기존 분석 방법으로는 달성하기 어려운 코팅 공정 설계 및 최적화 시뮬레이션을위한 효율성과 견고성을 제공합니다.

Introduction

모든 코팅 공정에는 일정한 조건을 달성하기 전에 코팅 재료가 큰 변형을 겪는 일종의 시작 기간이 포함됩니다. 시작 프로세스의 우수한 특성화는 낭비를 줄이고 프로세스가 원하는 한계 내에서 작동하는지 확인하는 데 종종 중요합니다.

다양한 섭동에 대한 코팅 흐름의 과도 ​​응답에 대한 유사한 이해가 또한 바람직하여 코팅 비드의 파손 및 코팅의 불균일성을 피할 수 있습니다. 코팅 흐름의 역학은 일반적으로 비선형이고 다양한 경쟁 물리적 프로세스의 결합 된 상호 작용을 포함하기 때문에 이론적 조사를 수행하기 위해 특수한 계산 도구에 의존해야합니다.

이 작업을 위해 선택한 모델링 도구의 장점은 고정 그리드를 통해 임의의 유체 변형을 추적 할 수있는 강력한 수치 기법 인 VOF (Volume-of-Fluid) 방법을 사용한다는 것입니다. 코팅 흐름 분석에 중요한 프로그램의 다른 기능과 함께 이것이 수행되는 방식은 다음 섹션에서 설명합니다.

Overview of Numerical Method

여기에 사용 된 수치 프로그램 FLOW-3D®는 1960 년대 중반 Los Alamos National Laboratory에서 개발 된 Marker-and-Cell (MAC) 방법 6에서 유래되었습니다. 원래 MAC 방법에 대한 많은 개선이 수년에 걸쳐 이루어졌습니다.

본 출원에서 가장 흥미로운 것은 유체 영역을 찾기 위해 연속적인 유체 부피 함수에 의해 개별 마커 입자를 대체하는 것입니다. VOF 방법에서는 관심있는 계산 영역을 포함하는 사각형 제어 볼륨의 고정 그리드가 구성됩니다. 각 제어 볼륨에 대해 숫자 F는 액체가 차지하는 볼륨의 비율을 표시하기 위해 유지됩니다.

F 함수를 사용하는 것 외에도 VOF 방법은 날카로운 액체-가스 인터페이스를 유지하는 방식으로 직사각형 셀의 고정 그리드를 통해 F 함수를 전진시키기 위해 특수 수치 기법을 사용합니다. 마지막으로 VOF 방법은 경계면에서 적절한 법선 및 접선 응력 조건을 충족하기 위해 신중하게 구현 된 자유 표면 경계 조건 세트를 사용합니다. 접근 방식의 또 다른 특징은 복잡한 기하학적 영역을 정의하는 방식입니다.

장애물은 제어 볼륨의 일부를 차단할 수 있도록하여 고정 그리드에 포함됩니다. 각 제어 볼륨에서 흐름을 위해 열린 분수 영역 및 볼륨은 지오메트리 표현으로 저장됩니다. FAVOR 방법 7이라고하는이 방법은 형상을 질량, 운동량 및 에너지에 대한 이산화 된 방정식에 자동으로 통합합니다. VOF 및 FAVOR 방법을 사용하면 코팅 문제에 대한 지오메트리 및 초기 유체 구성을 정의하는 데 필요한 복잡한 그리드 생성 프로세스가 없기 때문에 시간과 노력이 절약됩니다.

다음 섹션에서는 플랫 시트에 코팅을 담그는 응용 프로그램과 함께 기본적인 수치 방법의 유용성을 설명합니다.

Dip Coating – A Validation Test

Lee와 Tallmadge는 액체 수조에서 수직으로 인출 된 평판에 딥 코팅하는 과정에 대해 광범위한 조사를 수행했습니다.

이 프로세스는 다양한 상업용 응용 프로그램에서 널리 사용됩니다. 그들의 연구는 2 차원 흐름 (즉, 가장자리 효과 없음)에 초점을 맞추고 실험 데이터에 맞는 경험적 매개 변수를 포함하는 분석 표면 프로파일로 구성되었습니다. 0.085에서 23.9 사이의 모세관 수에 대한 실험 데이터가 수집되었으며, 레이놀즈 수는 0.044에서 12.7 사이입니다. 필름 두께에 대한 실험 데이터는 약 10 % 이하로 추정되는 오류를 가졌습니다.

이 실험에 대한 계산 모델은 코팅 할 시트의 수직 (접선) 속도와 동일한 수직 (접선) 속도가 주어진 직사각형 욕조로 구성되어 매우 간단합니다. 처음에 코팅액은 수평면을 가지며 시트는 충동 적으로 시작됩니다 (그림 1c 참조). 다양한 모세관 수 사례가 시뮬레이션되었으며 모든 경우에 예측 된 필름 두께는 실험 오차 범위 내에있었습니다. 예를 들어 모세관 번호 1.17에 해당하는 경우를 고려하십시오. 시트를 3.31cm / s에서 수조 (밀도 0.885gm / cc, 표면 장력 32.7dynes / cm 및 점도 1159.4cp를 갖는 점성 윤활유)에서 꺼냈다. 우리는 2.5cm의 욕조 너비와 2.0cm의 깊이 (35 x 25 그리드 셀)를 사용했습니다.

필름 흐름을 캡처하기 위해 욕조 위의 2.0cm 영역이 모델에 포함되었습니다 (수직으로 추가 25 개 셀 필요). 수조의 오른쪽은 유체 높이가 일정하게 유지되고 압력이 수압이고 흐름이 계산 영역으로 들어갈 수있는 열린 경계 였지만 휴식에서 시작해야했습니다. 이른바 “정체”경계 조건은 움직이는 시트의 오른쪽으로 충분히 멀리 떨어져있는 경우 수평 무한 욕조에 대한 좋은 근사치입니다. 모델링이 필요한 수조의 폭을 설정하기 위해 여러 가지 계산이 수행되었으며, 필름 두께가이 폭에 크게 민감하지 않다는 것이 밝혀졌으며 그 결과는 실험에서도 발견되었습니다.

그림 1a는 초기 조건, 그림 1b는 계산 된 과도 상태의 스냅 샷, 그림 1c는 최종 정상 상태 결과를 보여줍니다. 처음에 시트에 의해 그려지는 액체 팁의 모양은 정적 접촉각 (즉, 시트와 액체 사이의 접착력)에 따라 달라지며 임의로 10 도로 취해졌습니다. 액체가 끌어 올려짐에 따라, 배출되는 액체 필름을 대체하기 위해 시트쪽으로 흐름이 시작되어야한다는 신호로서 함몰 파가 나머지 수조에 대한 신호로 오른쪽으로 이동합니다. 약 5.0 초만에 정상 상태에 도달합니다. 필름 두께는 0.145cm로 계산되었으며, 이는 0.142cm의 측정 값과 매우 일치합니다.

Rivulet Formation in Slide Coating
Rivulet Formation in Slide Coating

자세한 내용은 본문을 참고하시기 바랍니다.

Solution-Coating Technology for AMOLEDDisplays

전자 장치 응용 분야를위한 솔루션 기반 코팅 방법은 비용 절감, 성능 향상 및 새로운 기능과 같은 많은 설득력있는 이유에 대한 집중적인 연구 노력의 초점입니다.

수동 및 능동 요소 솔루션 기반 코팅에 대한 응용 범위는 디스플레이에 걸쳐 있습니다. 

조명, 태양 전지, 센서, 무선 주파수 식별 (RFID)을 위한 무선 장치 및 의료 장치, 여기서 활성이라는 용어는 재료의 반도체 특성을 장치의 주요 기능으로 사용하는 것을 의미합니다. 예를 들어 다이오드 및 트랜지스터에서. 대량 생산을 달성한 대부분의 용액 기반 코팅 제품은 용액 코팅층의 전기 전도성 및 / 또는 광학적 또는 기계적 특성이 기능의 핵심인 수동 소자에 국한됩니다. 일부 예는 패턴화된 버스 라인, 반사 방지 필름, 평탄화 층 및 인광체 층입니다.

용액 코팅된 능동 소자의 몇 가지 예가 대규모 상업 생산을 달성했습니다. 액티브 매트릭스 유기 발광 다이오드 (AMOLED) 디스플레이는 유기 물질을 사용하여 핵심 활성 전자 층을 형성하는 유망한 기술입니다. AMOLED 디스플레이의 기존 상업 기술은 현재 열 증착을 사용합니다.

그리고 미세 금속 마스크를 사용하여 작은 분자 물질을 증착하지만 대형 유리로 확장하는 데는 잘 알려진 어려움이 있습니다 . 용액 코팅은 재료 낭비를 줄이고 코팅을 통해 AMOLED 생산에서 상당한 비용 절감 잠재력을 제공합니다. AMLCD 기술보다 더 낮은 비용으로 AMOLED 기술을 사용할 수 있습니다. 상세한 비용 모델은 솔루션 코팅 된 AMOLED가 소형 디스플레이 용 AMLCD보다 약 20 % 더 저렴할 수 있으며, 3 AMOLEDTV와 같은 대형 생산 라인 및 디스플레이 크기에서 비용 절감이 증가 할 것으로 예측합니다.

Solution-coated OLED fabrication can be achieved using the above process flow

DuPont Displays는 높은 AMOLED 제조 비용을 해결하기 위해 고성능 재료 및 솔루션 처리 기술의 전체 세트를 개발했습니다. 우리는 기존의 상업용 증착 기술에 비해 비용과 성능 경쟁력을 갖도록 코팅 공정을 최적화했습니다.

평판 디스플레이의 밝기 및 색상 균일 성 사양은 솔루션 코팅 AMOLED 레이어에 대한 까다로운 두께 및 균일 성 요구 사항을 제시합니다. 다양한 맞춤형 모델링 및 분석 접근 방식을 사용하여 대형 유리 크기에서 상업적으로 실행 가능한 단거리 및 장거리 필름 두께 제어 및 단일성을 개발했습니다. 이러한 코팅 기술 향상은 다른 솔루션 기반 응용 프로그램으로도 확장되어야합니다.

자세한 내용은 첨부 문서를 참고하시기 바랍니다.

Coating field – Coating with Non-Newtonian fluids (비뉴턴 유체를 이용한 코팅)

Coating with Non-Newtonian fluids (비뉴튼 유체를 이용한 코팅)

  • 비뉴턴 유체는 뉴턴의 점성 법칙, 응력과 무관하여 일정한 점도를 가지지 않는 유체를 나타냄
  • FLOW-3D의 점성 모델
    – Carreau function
    – Power-law (멱법칙)
    – Herschel-Bulkley
    – 변형률에 의존
    – 온도에 의존

Carreau Function ?


FLOW-3D를 이용한 비뉴턴 유체의 코팅 해석


Coating field – Gravure Coating/Printing (그라비어 코팅/인쇄)

Gravure Coating/Printing (그라비어 코팅/인쇄)

  • 금속 실린더에 새겨진 요점에 액체가 묻어나고 금속 실린더가 회전하면서 필름 표면에 액체가 묻어나도록 하는 기법
  • 새겨진 패턴 안에서 유체가 놓임
  • 작동 속도를 증가할 수 있음
  • 상세 패턴 및 이미지 인쇄에도 사용

FLOW-3D를 이용한 깊이별 그라비어 코팅


Coating field – Curtain Coating (커튼 코팅)

Curtain Coating (커튼 코팅)

  • 기판에서 떨어지는 유체가 멈추지 않고 커튼처럼 나오면서 코팅을 함
  • 새겨진 패턴 안에서 유체가 놓임
  • 고르지 않은 표면도 코팅 가능
  • 다층의 코팅으로 생산량 증대

FLOW-3D를 이용한 커튼 코팅

  • 다층 기능
  • 가장자리 효과를 정확하게 캡처함

Coating field – Slot Die Coating (슬롯다이 코팅)

Slot Die Coating (슬롯다이 코팅)

  • 응용
    – 배터리 전극
    – 광학 코팅
    – 전도성 필름
  • 공정 파라미터
    – 유량
    – 롤 속도
    – 기질 속도
    – 유동학
  • 품질 관리
    – 코팅 두께
    – 결함 최소화

슬롯다이 모델링

  • 세밀한 형상
  • 큰 종횡비
  • 간단한 격자 설정

슬롯다이 내부


슬롯다이 외부


슬롯다이 비교

  • 진공 보조 장치가 없는 슬롯 코팅
  • 실험 결과와 매우 일치

Coating field – Roll Coating

Roll Coating (롤 코팅)

  • 응용
    – 접착제
    – 밀폐제
    – 섬유 산업
  • 공정 파라미터
    – 롤 속도
    – 기질 속도
    – 유동학
  • 품질 관리
    – 코팅 두께
    – 결함 최소화

  • 손쉬운 설정의 시뮬레이션
    – STL 가져 오기 또는 기본 요소로 생성
    – 간단한 직사각형 격자

롤의 속도가 코팅에 미치는 영향

  • 전형적으로 유입구에 코팅액이 적당하게 있는 상황
  • 롤의 회전이 역으로 작동하는 상황
  • 유입구에 코팅액이 적게 들어오는 상황

공기가 유입된 롤 코팅


Coating Application/코팅분야 응용

해석 조건

  • Viscosity(점도) = 0.204 Pa-s
  • Density(밀도) = 965 kg/m^3
  • Surface tension(표면 장력) = 0.035N/m
  • Roll coating

물리 모델

  • Surface tension(표면 장력) 모델
  • Viscosity(점도)
  • Moving Objects(운동)

Classic Inlet Flooded Regime

Revers Operating Regime

Inlet Starved Operating Regime

  • 2D 시뮬레이션은 작동 코팅 윈도우의 빠른 평가를 제공
  • 계단식, 공기 유입, 기아 및 런백을 식별
  • 리빙(Ribbing)은 3D 분석이 필요

해석 결과

FLOW-3D 교육 안내

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FLOW-3D 분야별 교육 과정 안내


  • 교육 과정명 : 수리 분야

댐, 하천의 여수로, 수문 등 구조물 설계 및 방류, 월류 등 흐름 검토를 하기 위한 유동 해석 방법을 소개하는 교육 과정입니다. 유입 조건(수위, 유량 등)과 유출 조건에 따른 방류량 및 유속, 압력 분포 등 유체의 흐름을 검토를 할 수 있도록 관련 예제를 통해 적절한 기능을 습득하실 수 있습니다.

  • 교육 과정명 : 수처리 분야

정수처리 및 하수처리 공정에서 각 시설물들의 특성에 맞는 최적 운영조건 검토 및 설계 검토을 위한 유동해석 방법을 소개하는 교육 과정입니다. 취수부터 시작하여 혼화지, 분배수로, 응집지, 침전지, 여과지, 정수지, 협기조, 호기조, 소독조 등 각 공정별 유동 특성을 검토하기 위한 해석 모델을 설정하는 방법에 대해 알려드립니다.

  • 교육 과정명 : 주조 분야

주조 분야 사용자들이 쉽게 접근할 수 있도록 각 공정별로 해석 절차 및 해석 방법을 소개하는 교육 과정입니다. 고압다이캐스팅, 저압다이캐스팅, 경동주조, 중력주조, 원심주조, 정밀주조 등 주조 공법 별 관련 예제를 통해 적절한 기능들을 습득할 수 있도록 도와 드립니다.

  • 교육 과정명 : Micro/Bio/Nano Fluidics 분야

점성력 및 모세관력 같은 유체 표면에 작용하는 힘이 지배적인 미세 유동의 특성을 정확하게 표현할 수 있는 해석 방법에 대해 소개하는 교육 과정입니다. 열적, 전기적 물리 현상을 구현할 수 있도록 관련 예제와 함께 해석 방법을 알려드립니다.

  • 교육 과정명 : 코팅 분야 과정

코팅 공정에 따른 코팅액의 두께, 균일도, 유동 특성 분석을 위한 해석 방법을 소개하는 교육 과정입니다. Slide coating, Dip coating, Spin coating, Curtain coating, Slot coating, Roll coating, Gravure coating 등 각 공정별 예제와 함께 적절한 기능을 습득하실 수 있도록 도와 드립니다.

  • 교육 과정명 : 레이저 용접 분야

레이저 용접 해석을 하기 위한 물리 모델과 용접 조건들을 설정하는 방법에 대해 소개하는 교육 과정입니다. 해석을 통해 용접 공정을 최적화할 수 있도록 관련 예제와 함께 적절한 기능들을 습득할 수 있도록 도와 드립니다.

  • 교육 과정명 : 3D프린팅 분야 과정

Powder Bed Fusion(PBF)와 Directed Energy Deposition(DED) 공정에 대한 해석 방법을 소개하는 교육 과정입니다. 파우더 적층 및 레이저 빔을 조사하면서 동시에 금속 파우더 용융지가 적층되는 공정을 해석하는 방법을 관련 예제와 함께 습득하실 수 있습니다.

  • 교육 과정명 : 해양/항만 분야

해안, 항만, 해양 구조물에 대한 파랑의 영향 및 유체의 수위, 유속, 압력의 영향을 예측할 수 있는 해석 방법을 소개하는 과정입니다. 항주파, 슬로싱, 계류 등 해안, 해양, 에너지, 플랜트 분야 구조물 설계 및 검토에 필요한 유동해석을 하실 수 있는 방법을 알려드립니다. 각 현상에 대한 적절한 예제를 통해 기능을 습득하실 수 있습니다.

  • 교육 과정명 : 우주/항공 분야

항공기 및 우주선의 연료 탱크와 추진체 관리장치의 내부 유동, 엔진 및 터빈 노즐 내부의 유동해석을 하실 수 있도록 관련 메뉴에 대한 설명, 설정 방법을 소개하는 과정입니다. 경계조건 설정, Mesh 방법 등 유동해석을 위한 기본적인 내용과 함께 관련 예제를 통해 기능들을 습득하실 수 있습니다.

고객 맞춤형 과정


상기 과정 이외의 경우 고객의 사업 업무 환경에 적합한 사례를 중심으로 맞춤형 교육을 실시합니다. 필요하신 부분이 있으시면 언제든지 교육 담당자에게 연락하여 협의해 주시기 바랍니다.

고객센터 및 교육 담당자

  • 전화 : 02)2026-0450, 02)2026-0455
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교육은 매월 정해진 일정에 시행되는 정기 교육과 고객의 요청에 의해 시행되는 비정기 교육이 있습니다. 비정기 교육은 별도문의 바랍니다.

1. 연간교육 일정


2. 교육 내용 : FLOW-3D Basic

  1. FLOW-3D 소개 및 이론
    • FLOW-3D 소개  – 연혁, 특징 등
    • FLOW-3D 기본 개념
      • VOF
      • FAVOR
    • 해석사례 리뷰
  2. GUI 소개 및 사용법
    • 해석 모델 작성법  – 물리 모델 설정
      • 모델 형상 정의
      • 격자 분할
      • 초기 유체 지정
      • 경계 조건 설정
    • 해석 결과 분석 방법  – 해석 모델 설명
  3. 해석 모델 작성 실습
    • 해석 모델 작성 실습  – 격자 분할
      • 물리 모델 설정
      • 모델 형상 및 초기 조건 정의
      • 경계 조건 설정
      • 해석 과정 모니터링
      • 해석 결과 분석
    • 질의 응답 및 토의

3. 교육 과정 : FLOW-3D Advanced

  1. Physics Ⅰ
    • Density evaluation
    • Drift flux
    • Scalars
    • Sediment scour
    • Shallow water
  2. Physics Ⅱ
    • Gravity and non-inertial reference frame
    • Heat transfer
    • Moving objects
    • Solidification
  3. FLOW-3D POST (Post-processor)
    • FLOW-3D POST 소개
    • Interface Basics
    • 예제 실습

FLOW-3D 교육 신청 방법 안내


  • 교육 신청은 홈페이지의 교육 신청 창에서 최소 3일 전에 신청합니다.
  • 모든 교육과정은 신청 인원이 2인 이상일때 개설되며, 선착순 마감입니다.
  • 교육 신청을 완료하시면, 신청시 입력하신 메일주소로 교육 담당자가 확인 메일을 보내드립니다.
  • 교육 시간은 Basic : 오전10시~오후5시, Advanced : 오후1시30분~오후5시30분까지입니다.
  • 교육비 안내
    • FLOW-3D, FLOW-3D CAST, FLOW-3D HYDRO Basic (2일) : 기업 66만원, 학생 55만원
    • FLOW-3D WELD/AM Basic 레이저용접, 3D 프린팅(2일) : 기업 88만원, 학생 66만원
    • FLOW-3D Advanced (1일) : 기업 33만원, 학생 25만원
    • 상기 가격은 부가세 포함 가격입니다.
  • 교육비는 현금(계좌이체)로 납부 가능하며, 교재 및 중식이 제공됩니다.
  • 세금계산서 발급을 위해 사업자등록증 또는 신분증 사본을 함께 첨부하여 신청해 주시기 바랍니다.
  • 교육 종료 후 이메일로 수료증이 발급됩니다.
고객센터 및 교육 담당자
  • 전화 : 02)2026-0450, 02)2026-0455
  • 이메일 : flow3d@stikorea.co.kr
교육 장소 안내
  • 지하철 1호선/가산디지털단지역 (8번출구), 지하철 7호선/가산디지털단지역 (5번출구)
  • 우림라이온스밸리 B동 302호 또는 교육장
  • 당사 건물에 주차할 경우 무료 주차 1시간만 지원되오니, 가능하면 대중교통을 이용해 주시기 바랍니다.
오시는 길

Additive Manufacturing & Welding Bibliography

Additive Manufacturing & Welding Bibliography

다음은 적층 제조 및 용접 참고 문헌의 기술 문서 모음입니다. 이 모든 논문에는 FLOW-3D AM 결과가 나와 있습니다. FLOW-3D AM을 사용하여 적층 제조, 레이저 용접 및 기타 용접 기술에서 발견되는 프로세스를 성공적으로 시뮬레이션하는 방법에 대해 자세히 알아보십시오.

2024년 3월 20일 update

3-24 Kunjie Dai, Xing He, Decheng Kong, Chaofang Dong, Multi-physical field simulation to yield defect-free IN718 alloy fabricated by laser powder bed fusion, Materials Letters, 355; 135437, 2024. doi.org/10.1016/j.matlet.2023.135437

2-24 You Wang, Yinkai Xie, Huaixue Li, Caiyou Zeng, Ming Xu, Hongqiang Zhang, In-situ monitoring plume, spattering behavior and revealing their relationship with melt flow in laser powder bed fusion of nickel-based superalloy, Journal of Materials Science & Technology, 177; pp. 44-58, 2024. doi.org/10.1016/j.jmst.2023.07.068

1-24 Yukai Chen, Hongtu Xu, Yu Lu, Yin Wang, Shuangyuzhou Wang, Ke Huang, Qi Zhang, Prediction of microstructure for Inconel 718 laser welding process using multi-scale model, Proceedings of the 14th International Conference on the Technology of Plasticity – Current Trends in the Technology of Plasticity, pp. 713-722, 2024. doi.org/10.1007/978-3-031-41341-4_75

211-23 Giovanni Chianese, Qamar Hayat, Sharhid Jabar, Pasquale Franciosa, Darek Ceglarek, Stanislao Patalano, A multi-physics CFD study to investigate the impact of laser beam shaping on metal mixing and molten pool dynamics during laser welding of copper to steel for battery terminal-to-casing connections, Journal of Materials Processing Technology, 322; 118202, 2023. doi.org/10.1016/j.jmatprotec.2023.118202

207-23 Dong Liu, Jiaqi Pei, Hua Hou, Xiaofeng Niu, Yuhong Zhao, Optimizing solidification dendrites and process parameters for laser powder bed fusion additive manufacturing of GH3536 superalloy by finite volume and phase-field method, Journal of Materials Research and Technology, 27; pp. 3323-3338, 2023. doi.org/10.1016/j.jmrt.2023.10.188

206-23 Houshang Yin, Jingfan Yang, Ralf D. Fischer, Zilong Zhang, Bart Prorok, Lang Yuan, Xiaoyuan Lou, Pulsed laser additive manufacturing for 316L stainless steel: a new approach to control subgrain cellular structure, JOM, 75; pp. 5027-5036, 2023. doi.org/10.1007/s11837-023-06177-8

205-23 Francis Ogoke, William Lee, Ning-Yu Kao, Alexander Myers, Jack Beuth, Jonathan Malen, Amir Barati Farimani, Convolutional neural networks for melt depth prediction and visualization in laser powder bed fusion, The International Journal of Advanced Manufacturing Technology, 129; pp. 3047-3062, 2023. doi.org/10.1007/s00170-023-12384-z

202-23 Habib Hamed Zargari, Kazuhiro Ito, Abhay Sharma, Effect of workpiece vibration frequency on heat distribution and material flow in the molten pool in tandem-pulsed gas metal arc welding, The International Journal of Advanced Manufacturing Technology, 129; pp. 2507-2522, 2023. doi.org/10.1007/s00170-023-12424-8

199-23 Yukai Chen, Yin Wang, Hao Li, Yu Lu, Bin Han, Qi Zhang, Effects of process parameters on the microstructure of Inconel 718 during powder bed fusion based on cellular automata approach, Virtual and Physical Prototyping, 18.1; e2251032, 2023. doi.org/10.1080/17452759.2023.2251032

197-23 Qiong Wu, Chuang Qiao, Yuhang Wu, Zhe Liu, Xiaodan Li, Ju Wang, Xizhong An, Aijun Huang, Chao Voon Samuel Lim, Numerical investigation on the reuse of recycled powders in powder bed fusion additive manufacturing, Additive Manufacturing, 77; 103821, 2023. doi.org/10.1016/j.addma.2023.103821

196-23 Daicong Zhang, Chunhui Jing, Wei Guo, Yuan Xiao, Jun Luo, Lehua Qi, Microchannels formed using metal microdroplets, Micromachines, 14.10; 1922, 2023. doi.org/10.3390/mi14101922

195-23 Trong-Nhan Le, Santosh Rauniyar, V.H. Nismath, Kevin Chou, An investigation into the effects of contouring process parameters on the up-skin surface characteristics in laser powder-bed fusion process, Manufacturing Letters, 35; Supplement, pp. 707-716, 2023. doi.org/10.1016/j.mfglet.2023.08.085

194-23 Kyubok Lee, Teresa J. Rinker, Masoud M. Pour, Wayne Cai, Wenkang Huang, Wenda Tan, Jennifer Bracey, Jingjing Li, A study on cracks and IMCs in laser welding of Al and Cu, Manufacturing Letters, 35; Supplement, pp. 221-231, 2023. doi.org/10.1016/j.mfglet.2023.08.026

192-23 Kunjie Dai, Xing He, Wei Zhang, Decheng Kong, Rong Guo, Minlei Hu, Ketai He, Chaofang Dong, Tailoring the microstructure and mechanical properties for Hastelloy X alloy by laser powder bed fusion via scanning strategy, Materials & Design, 235; 112386, 2023. doi.org/10.1016/j.matdes.2023.112386

191-23 Jun Du, Daqing Wang, Jimiao He, Yongheng Zhang, Zhike Peng, Influence of droplet size and ejection frequency on molten pool dynamics and deposition morphology in TIG-aided droplet deposition manufacturing, International Communications in Heat and Mass Transfer, 148; 107075, 2023. doi.org/10.1016/j.icheatmasstransfer.2023.107075

188-23 Jin-Hyeong Park, Du-Song Kim, Dae-Won Cho, Jaewoong Kim, Changmin Pyo, Influence of thermal flow and predicting phase transformation on various welding positions, Heat and Mass Transfer, 2023. doi.org/10.1007/s00231-023-03429-w

184-23 Lin Gao, Jishnu Bhattacharyya, Wenhao Lin, Zhongshu Ren, Andrew C. Chuang, Pavel D. Shevchenko, Viktor Nikitin, Ji Ma, Sean R. Agnew, Tao Sun, Tailoring material microstructure and property in wire-laser directed energy deposition through a wiggle deposition strategy, Additive Manufacturing, 77; 103801, 2023. doi.org/10.1016/j.addma.2023.103801

182-23 Liping Guo, Hanjie Liu, Hongze Wang, Qianglong Wei, Jiahui Zhang, Yingyan Chen, Chu Lun Alex Leung, Qing Lian, Yi Wu, Yu Zou, Haowei Wang, A high-fidelity comprehensive framework for the additive manufacturing printability assessment, Journal of Manufacturing Processes, 105; pp. 219-231, 2023. doi.org/10.1016/j.jmapro.2023.09.041

172-23 Liping Guo, Hanjie Liu, Hongze Wang, Qianglong Wei, Yakai Xiao, Zijue Tang, Yi Wu, Haowei Wang, Identifying the keyhole stability and pore formation mechanisms in laser powder bed fusion additive manufacturing, Journal of Materials Processing Technology, 321; 118153, 2023. doi.org/10.1016/j.jmatprotec.2023.118153

171-23 Yuhang Wu, Qiong Wu, Meng Li, Ju Wang, Dengzhi Yao, Hao Luo, Xizhong An, Haitao Fu, Hao Zhang, Xiaohong Yang, Qingchuan Zou, Shujun Li, Haibin Ji, Xing Zhang, Numerical investigation on effects of operating conditions and final dimension predictions in laser powder bed fusion of molybdenum, Additive Manufacturing, 76; 103783, 2023. doi.org/10.1016/j.addma.2023.103783

158-23 K. El Abbaoui, I. Al Korachi, M.T. Mollah, J. Spangenberg, Numerical modelling of planned corner deposition in 3D concrete printing, Archives of Materials Science and Engineering, 121.2; pp. 71-79, 2023. doi.org/10.5604/01.3001.0053.8488

156-23 Liping Guo, Hanjie Liu, Hongze Wang, Valentino A.M. Cristino, C.T. Kwok, Qianglong Wei, Zijue Tang, Yi Wu, Haowei Wang, Deepening the scientific understanding of different phenomenology in laser powder bed fusion by an integrated framework, International Journal of Heat and Mass Transfer, 216; 124596, 2023. doi.org/10.1016/j.ijheatmasstransfer.2023.124596

154-23 Zhiyong Li, Xiuli He, Shaoxia Li, Xinfeng Kan, Yanjun Yin, Gang Yu, Sulfur-induced transitions of thermal behavior and flow dynamics in laser powder bed fusion of 316L powders, Thermal Science and Engineering Progress, 45; 102072, 2023. doi.org/10.1016/j.tsep.2023.102072

149-23 Shardul Kamat, Wayne Cai, Teresa J. Rinker, Jennifer Bracey, Liang Xi, Wenda Tan, A novel integrated process-performance model for laser welding of multi-layer battery foils and tabs, Journal of Materials Processing Technology, 320; 118121, 2023. doi.org/10.1016/j.jmatprotec.2023.118121

148-23 Reza Ghomashchi, Shahrooz Nafisi, Solidification of Al12Si melt pool in laser powder bed fusion, Journal of Materials En gineering and Performance, 2023. doi.org/10.1007/s11665-023-08502-3

133-23 Hesam Moghadasi, Md Tusher Mollah, Deepak Marla, Hamid Saffari, Jon Spangenberg, Computational fluid dynamics modeling of top-down digital light processing additive manufacturing, Polymers, 15.11; 2459, 2023. doi.org/10.3390/polym15112459

131-23 Luca Santoro, Raffaella Sesana, Rosario Molica Nardo, Francesca Curà, In line defect detection in steel welding process by means of thermography, Experimental Mechanics in Engineering and Biomechanics – Proceedings ICEM20, 19981, 2023.

128-23 Md Tusher Mollah, Raphaël Comminal, Wilson Ricardo Leal da Silva, Berin Šeta, Jon Spangenberg, Computational fluid dynamics modelling and experimental analysis of reinforcement bar integration in 3D concrete printing, Cement and Concrete Research, 173; 107263, 2023. doi.org/10.1016/j.cemconres.2023.107263

123-23 Arash Samaei, Zhongsheng Sang, Jennifer A. Glerum, Jon-Erik Mogonye, Gregory J. Wagner, Multiphysics modeling of mixing and material transport in additive manufacturing with multicomponent powder beds, Additive Manufacturing, 67; 103481, 2023. doi.org/10.1016/j.addma.2023.103481

122-23 Chu Han, Ping Jiang, Shaoning Geng, Lingyu Guo, Kun Liu, Inhomogeneous microstructure distribution and its formation mechanism in deep penetration laser welding of medium-thick aluminum-lithium alloy plates, Optics & Laser Technology, 167; 109783, 2023. doi.org/10.1016/j.optlastec.2023.109783

111-23 Alexander J. Myers, Guadalupe Quirarte, Francis Ogoke, Brandon M. Lane, Syed Zia Uddin, Amir Barati Farimani, Jack L. Beuth, Jonathan A. Malen, High-resolution melt pool thermal imaging for metals additive manufacturing using the two-color method with a color camera, Additive Manufacturing, 73; 103663, 2023. doi.org/10.1016/j.addma.2023.103663

107-23 M. Mohsin Raza, Yu-Lung Lo, Hua-Bin Lee, Chang Yu-Tsung, Computational modeling of laser welding for aluminum–copper joints using a circular strategy, Journal of Materials Research and Technology, 25; pp. 3350-3364, 2023. doi.org/10.1016/j.jmrt.2023.06.122

106-23 H.Z. Lu, L.H. Liu, X. Luo, H.W. Ma, W.S. Cai, R. Lupoi, S. Yin, C. Yang, Formation mechanism of heterogeneous microstructures and shape memory effect in NiTi shape memory alloy fabricated via laser powder bed fusion, Materials & Design, 232; 112107, 2023. doi.org/10.1016/j.matdes.2023.112107

105-23 Harun Kahya, Hakan Gurun, Gokhan Kucukturk, Experimental and analytical investigation of the re-melting effect in the manufacturing of 316L by direct energy deposition (DED) method, Metals, 13.6; 1144, 2023. doi.org/10.3390/met13061144

100-23 Dongju Chen, Gang Li, Peng Wang, Zhiqiang Zeng, Yuhang Tang, Numerical simulation of melt pool size and flow evolution for laser powder bed fusion of powder grade Ti6Al4V, Finite Elements in Analysis and Design, 223; 103971, 2023. doi.org/10.1016/j.finel.2023.103971

97-23 Mahyar Khorasani, Martin Leary, David Downing, Jason Rogers, Amirhossein Ghasemi, Ian Gibson, Simon Brudler, Bernard Rolfe, Milan Brandt, Stuart Bateman, Numerical and experimental investigations on manufacturability of Al–Si–10Mg thin wall structures made by LB-PBF, Thin-Walled Structures, 188; 110814, 2023. doi.org/10.1016/j.tws.2023.110814

95-23 M.S. Serdeczny, Laser welding of dissimilar materials – simulation driven optimization of process parameters, IOP Conference Series: Materials Science and Engineering, 1281; 012018, 2023. doi.org/10.1088/1757-899X/1281/1/012018

90-23 Lin Liu, Tubin Liu, Xi Dong, Min Huang, Fusheng Cao, Mingli Qin, Numerical simulation of thermal dynamic behavior and morphology evolution of the molten pool of selective laser melting BN/316L stainless steel composite, Journal of Materials Engineering and Performance, 2023. doi.org/10.1007/s11665-023-08210-y

89-23 M. P. Serdeczny, A. Jackman, High fidelity modelling of bead geometry in directed energy deposition – simulation driven optimization, Journal of Physics: Conference Series, NOLAMP19, 2023.

88-23 Lu Wang, Shuhao Wang, Yanming Zhang, Wentao Yan, Multi-phase flow simulation of powder streaming in laser-based directed energy deposition, International Journal of Heat and Mass Transfer, 212; 124240, 2023. doi.org/10.1016/j.ijheatmasstransfer.2023.124240

80-23 Mahyar Khorasani, AmirHossein Ghasemi, Martin Leary, David Downing, Ian Gibson, Elmira G. Sharabian, Jithin Kozuthala Veetil, Milan Brandt, Stuart Batement, Bernard Rolfe, Benchmark models for conduction and keyhole modes in laser-based powder bed fusion of Inconel 718, Optics & Laser Technology, 164; 109509, 2023. doi.org/10.1016/j.optlastec.2023.109509

78-23   Md. Tusher Mollah, Raphaël Comminal, Marcin P. Serdeczny, Berin Šeta, Jon Spangenberg, Computational analysis of yield stress buildup and stability of deposited layers in material extrusion additive manufacturing, Additive Manufacturing, 71; 103605, 2023. doi.org/10.1016/j.addma.2023.103605

76-23   Asif Ur Rehman, Kashif Azher, Abid Ullah, Celal Sami Tüfekci, Metin Uymaz Salamci, Binder jetting of SS316L: a computational approach for droplet-powder interaction, Rapid Prototyping Journal, 2023. doi.org/10.1108/RPJ-08-2022-0264

75-23   Dengzhi Yao, Ju Wang, Hao Luo, Yuhang Wu, Xizhong An, Thermal behavior and control during multi-track laser powder bed fusion of 316 L stainless steel, Additive Manufacturing, 70; 103562, 2023. doi.org/10.1016/j.addma.2023.103562

61-23   Yaqing Hou, Hang Su, Hao Zhang, Fafa Li, Xuandong Wang, Yazhou He, Dupeng He, An integrated simulation model towards laser powder bed fusion in-situ alloying technology, Materials & Design, 228; 111795, 2023. doi.org/10.1016/j.matdes.2023.111795

56-23   Maohong Yang, Guiyi Wu, Xiangwei Li, Shuyan Zhang, Honghong Wang, Jiankang Huang, Influence of heat source model on the behavior of laser cladding pool, Journal of Laser Applications, 35.2; 2023. doi.org/10.2351/7.0000963

45-23   Daniel Martinez, Philip King, Santosh Reddy Sama, Jay Sim, Hakan Toykoc, Guha Manogharan, Effect of freezing range on reducing casting defects through 3D sand-printed mold designs, The International Journal of Advanced Manufacturing Technology, 2023. doi.org/10.1007/s00170-023-11112-x

39-23   Peter S. Cook, David J. Ritchie, Determining the laser absorptivity of Ti-6Al-4V during laser powder bed fusion by calibrated melt pool simulation, Optics & Laser Technology, 162; 109247. 2023. doi.org/10.1016/j.optlastec.2023.109247

36-23   Yixuan Chen, Weihao Wang, Yao Ou, Yingna Wu, Zirong Zhai, Rui Yang, Impact of laser power and scanning velocity on microstructure and mechanical properties of Inconel 738LC alloys fabricated by laser powder bed fusion, TMS 2023 152nd Annual Meeting & Exhibition Supplemental Proceedings, pp. 138-149, 2023. doi.org/10.1007/978-3-031-22524-6_15

34-23   Chao Kang, Ikki Ikeda, Motoki Sakaguchi, Recoil and solidification of a paraffin droplet impacted on a metal substrate: Numerical study and experimental verification, Journal of Fluids and Structures, 118; 103839, 2023. doi.org/10.1016/j.jfluidstructs.2023.103839

30-23   Fei Wang, Tiechui Yuan, Ruidi Li, Shiqi Lin, Zhonghao Xie, Lanbo Li, Valentino Cristino, Rong Xu, Bing liu, Comparative study on microstructures and mechanical properties of ultra ductility single-phase Nb40Ti40Ta20 refractory medium entropy alloy by selective laser melting and vacuum arc melting, Journal of Alloys and Compounds, 942; 169065, 2023. doi.org/10.1016/j.jallcom.2023.169065

29-23   Haejin Lee, Yeonghwan Song, Seungkyun Yim, Kenta Aoyagi, Akihiko Chiba, Byoungsoo Lee, Influence of linear energy on side surface roughness in powder bed fusion electron beam melting process: Coupled experimental and simulation study, Powder Technology, 418; 118292, 2023.

27-23   Yinan Chen, Bo Li, Double-phase refractory medium entropy alloy NbMoTi via selective laser melting (SLM) additive manufacturing, Journal of Physics: Conference Series, 2419; 012074, 2023. doi.org/10.1088/1742-6596/2419/1/012074

23-23   Yunwei Gui, Kenta Aoyagi, Akihiko Chiba, Development of macro-defect-free PBF-EB-processed Ti–6Al–4V alloys with superior plasticity using PREP-synthesized powder and machine learning-assisted process optimization, Materials Science and Engineering: A, 864; 144595, 2023. doi.org/10.1016/j.msea.2023.144595

21-23   Tatsuhiko Sakai, Yasuhiro Okamoto, Nozomi Taura, Riku Saito, Akira Okada, Effect of scanning speed on molten metal behaviour under angled irradiation with a continuous-wave laser, Journal of Materials Processing Technology, 313; 117866, 2023. doi.org/10.1016/j.jmatprotec.2023.117866

19-23   Gianna M. Valentino, Arunima Banerjee, Alexander lark, Christopher M. Barr, Seth H. Myers, Ian D. McCue, Influence of laser processing parameters on the density-ductility tradeoff in additively manufactured pure tantalum, Additive Manufacturing Letters, 4; 100117, 2023. doi.org/10.1016/j.addlet.2022.100117

15-23   Runbo Jiang, Zhongshu Ren, Joseph Aroh, Amir Mostafaei, Benjamin Gould, Tao Sun, Anthony D. Rollett, Quantifying equiaxed vs epitaxial solidification in laser melting of CMSX-4 single crystal superalloy, Metallurgical and Materials Transactions A, 54; pp. 808-822, 2023. doi.org/10.1007/s11661-022-06929-2

14-23   Nguyen Thi Tien, Yu-Lung Lo, M. Mohsin Raza, Cheng-Yen Chen, Chi-Pin Chiu, Optimization of processing parameters for pulsed laser welding of dissimilar metal interconnects, Optics & Laser Technology, 159; 109022, 2023. doi.org/10.1016/j.optlastec.2022.109022

9-23 Hou Yi Chia, Wentao Yan, High-fidelity modeling of metal additive manufacturing, Additive Manufacturing Technology: Design, Optimization, and Modeling, Ed. Kun Zhou, 2023.

8-23 Akash Aggarwal, Yung C. Shin, Arvind Kumar, Investigation of the transient coupling between the dynamic laser beam absorptance and the melt pool – vapor depression morphology in laser powder bed fusion process, International Journal of Heat and Mass Transfer, 201.2; 123663, 2023. doi.org/10.1016/j.ijheatmasstransfer.2022.123663

199-22 Md. Tusher Mollah, Raphaël Comminal, Marcin P. Serdeczny, David B. Pedersen, Jon Spangenberg, Numerical predictions of bottom layer stability in material extrusion additive manufacturing, JOM, 74; pp. 1096-1101, 2022. doi.org/10.1007/s11837-021-05035-9

198-22 Md. Tusher Mollah, Amirpasha Moetazedian, Andy Gleadall, Jiongyi Yan, Wayne Edgar Alphonso, Raphael Comminal, Berin Seta, Tony Lock, Jon Spangenberg, Investigation on corner precision at different corner angles in material extrusion additive manufacturing: An experimental and computational fluid dynamics analysis, Proceedings of the 33rd Annual Solid Freeform Fabrication Symposium, 2022.

197-22 Md. Tusher Mollah, Marcin P. Serdeczny, Raphaël Comminal, Berin Šeta, Marco Brander, David B. Pedersen, Jon Spangenberg, A numerical investigation of the inter-layer bond and surface roughness during the yield stress buildup in wet-on-wet material extrusion additive manufacturing, ASPE and euspen Summer Topical Meeting, 77, 2022.

182-22   Chan Kyu Kim, Dae-Won Cho, Seok Kim, Sang Woo Song, Kang Myung Seo, Young Tae Cho, High-throughput metal 3D printing pen enabled by a continuous molten droplet transfer, Advanced Science, 2205085, 2022. doi.org/10.1002/advs.202205085

180-22 Xu Kaikai, Gong Yadong, Zhang Qiang, Numerical simulation of dynamic analysis of molten pool in the process of direct energy deposition, The International Journal of Advanced Manufacturing Technology, 2022. doi.org/10.1007/s00170-022-10271-7

179-22 Yasuhiro Okamoto, Nozomi Taura, Akira Okada, Study on laser drilling process of solid metal on its liquid, International Journal of Electrical Machining, 27; 2022. doi.org/10.2526/ijem.27.35

175-22 Lu Min, Xhi Xiaojie, Lu Peipei, Wu Meiping, Forming quality and wettability of surface texture on CuSn10 fabricated by laser powder bed fusion, AIP Advances, 12.12; 125114, 2022. doi.org/10.1063/5.0122076

174-22 Thinus Van Rhijn, Willie Du Preez, Maina Maringa, Dean Kouprianoff, An investigation into the optimization of the selective laser melting process parameters for Ti6Al4V through numerical modelling, JOM, 2022. doi.org/10.1007/s11837-022-05608-2

171-22 Jonathan Yoshioka, Mohsen Eshraghi, Temporal evolution of temperature gradient and solidification rate in laser powder bed fusion additive manufacturing, Heat and Mass Transfer, 2022. doi.org/10.1007/s00231-022-03318-8

170-22 Subin Shrestha and Kevin Chou, Residual heat effect on the melt pool geometry during the laser powder bed fusion process, Journal of Manufacturing and Materials Processing, 6.6; 153, 2022. doi.org/10.3390/jmmp6060153

169-22 Aryan Aryan, Obinna Chukwubuzo, Desmond Bourgeois, Wei Zhang, Hardness prediction by incorporating heat transfer and molten pool fluid flow in a mult-pass, multi-layer weld for onsite repair of Grade 91 steel, U.S. Department of Energy Office of Scientific and Technical Information, DOE-OSU-0032067, 2022. doi.org/10.2172/1898594

158-22 Dafan Du, Lu Wang, Anping Dong, Wentao Yan, Guoliang Zhu, Baode Sun, Promoting the densification and grain refinement with assistance of static magnetic field in laser powder bed fusion, International Journal of Machine Tools and Manufacture, 183; 103965, 2022. doi.org/10.1016/j.ijmachtools.2022.103965

157-22 Han Chu, Jiang Ping, Geng Shaoning, Liu Kun, Nucleation mechanism in oscillating laser welds of 2024 aluminium alloy: A combined experimental and numerical study, Optics & Laser Technology, 158.A; 108812, 2022. doi.org/10.1016/j.optlastec.2022.108812

153-22 Zixiang Li, Yinan Cui, Baohua Chang, Guan Liu, Ze Pu, Haoyu Zhang, Zhiyue Liang, Changmeng Liu, Li Wang, Dong Du, Manipulating molten pool in in-situ additive manufacturing of Ti-22Al-25 Nb through alternating dual-electron beams, Additive Manufacturing, 60.A; 103230, 2022. doi.org/10.1016/j.addma.2022.103230

149-22   Qian Chen, Yao Fu, Albert C. To, Multiphysics modeling of particle spattering and induced defect formation mechanism in Inconel 718 laser powder bed fusion, The International Journal of Advanced Manufacturing Technology, 123; pp. 783-791, 2022. doi.org/10.1007/s00170-022-10201-7

146-22   Zixuan Wan, Hui-ping Wang, Jingjing Li, Baixuan Yang, Joshua Solomon, Blair Carlson, Effect of welding mode on remote laser stitch welding of zinc-coated steel with different sheet thickness combinations, Journal of Manufacturing Science and Engineering, MANU-21-1598, 2022. doi.org/10.1115/1.4055792

143-22   Du-Rim Eo, Seong-Gyu Chung, JeongHo Yang, Won Tae Cho, Sun-Hong Park, Jung-Wook Cho, Surface modification of high-Mn steel via laser-DED: Microstructural characterization and hot crack susceptibility of clad layer, Materials & Design, 223; 111188, 2022. doi.org/10.1016/j.matdes.2022.111188

142-22   Zichuan Fu, Xiangman Zhou, Bin Luo, Qihua Tian, Numerical simulation study of the effect of weld current on WAAM welding pool dynamic and weld bead morphology, International Conference on Mechanical Design and Simulation, Proceedings, 12261; 122614G, 2022. doi.org/10.1117/12.2639074

132-22   Yiyu Huang, Zhonghao Xie, Wenshu Li, Haoyu Chen, Bin Liu, Bingfeng Wang, Dynamic mechanical properties of the selective laser melting NiCrFeCoMo0.2 high entropy alloy and the microstructure of molten pool, Journal of Alloys and Compounds, 927; 167011, 2022. doi.org/10.1016/j.jallcom.2022.167011

126-22   Jingqi Zhang, Yingang Liu, Gang Sha, Shenbao Jin, Ziyong Hou, Mohamad Bayat, Nan Yang, Qiyang Tan, Yu Yin, Shiyang Liu, Jesper Henri Hattel, Matthew Dargusch, Xiaoxu Huang, Ming-Xing Zhang, Designing against phase and property heterogeneities in additively manufactured titanium alloys, Nature Communications, 13; 4660, 2022. doi.org/10.1038/s41467-022-32446-2

119-22   Xu Kaikai, Gong Yadong, Zhao Qiang, Numerical simulation on molten pool flow of Inconel718 alloy based on VOF during additive manufacturing, Materials Today Communications, 33; 104147, 2022. doi.org/10.1016/j.mtcomm.2022.104147

118-22   AmirPouya Hemmasian, Francis Ogoke, Parand Akbari, Jonathan Malen, Jack Beuth, Amir Barati Farimani, Surrogate modeling of melt pool thermal field using deep learning, SSRN, 2022. doi.org/10.2139/ssrn.4190835

117-22   Chiara Ransenigo, Marialaura Tocci, Filippo Palo, Paola Ginestra, Elisabetta Ceretti, Marcello Gelfi, Annalisa Pola, Evolution of melt pool and porosity during laser powder bed fusion of Ti6Al4V alloy: Numerical modelling and experimental validation, Lasers in Manufacturing and Materials Processing, 2022. doi.org/10.1007/s40516-022-00185-3

112-22   Chris Jasien, Alec Saville, Chandler Gus Becker, Jonah Klemm-Toole, Kamel Fezzaa, Tao Sun, Tresa Pollock, Amy J. Clarke, In situ x-ray radiography and computational modeling to predict grain morphology in β-titanium during simulated additive manufacturing, Metals, 12.7; 1217, 2022. doi.org/10.3390/met12071217

110-22   Haotian Zhou, Haijun Su, Yinuo Guo, Peixin Yang, Yuan Liu, Zhonglin Shen, Di Zhao, Haifang Liu, Taiwen Huang, Min Guo, Jun Zhang, Lin Liu, Hengzhi Fu, Formation and evolution mechanisms of pores in Inconel 718 during selective laser melting: Meso-scale modeling and experimental investigations, Journal of Manufacturing Processes, 81; pp. 202-213, 2022. doi.org/10.1016/j.jmapro.2022.06.072

109-22   Yufan Zhao, Huakang Bian, Hao Wang, Aoyagi Kenta, Yamanaka Kenta, Akihiko Chiba, Non-equilibrium solidification behavior associated with powder characteristics during electron beam additive manufacturing, Materials & Design, 221; 110915, 2022. doi.org/10.1016/j.matdes.2022.110915

107-22   Dan Lönn, David Spångberg, Study of process parameters in laser beam welding of copper hairpins, Thesis, University of Skövde, 2022.

106-22   Liping Guo, Hongze Wang, Qianglong Wei, Hanjie Liu, An Wang, Yi Wu, Haowei Wang, A comprehensive model to quantify the effects of additional nano-particles on the printability in laser powder bed fusion of aluminum alloy and composite, Additive Manufacturing, 58; 103011, 2022. doi.org/10.1016/j.addma.2022.103011

104-22   Hongjiang Pan, Thomas Dahmen, Mohamad Bayat, Kang Lin, Xiaodan Zhang, Independent effects of laser power and scanning speed on IN718’s precipitation and mechanical properties produced by LBPF plus heat treatment, Materials Science and Engineering: A, 849; 143530, 2022. doi.org/10.1016/j.msea.2022.143530

101-22   Yufan Zhao, Kenta Aoyagi, Kenta Yamanaka, Akihiko Chiba, A survey on basic influencing factors of solidified grain morphology during electron beam melting, Materials & Design, 221; 110927, 2022. doi.org/10.1016/j.matdes.2022.110927

98-22   Jon Spangenberg, Wilson Ricardo Leal da Silva, Md. Tusher Mollah, Raphaël Comminal, Thomas Juul Andersen, Henrik Stang, Integrating reinforcement with 3D concrete printing: Experiments and numerical modelling, Third RILEM International Conference on Concrete and Digital Fabrication, Eds. Ana Blanco, Peter Kinnell, Richard Buswell, Sergio Cavalaro, pp. 379-384, 2022.

93-22   Minglei Qu, Qilin Guo, Luis I. Escano, Samuel J. Clark Kamel Fezzaa, Lianyi Chen, Mitigating keyhole pore formation by nanoparticles during laser powder bed fusion additive manufacturing, Additive Manufacturing Letters, 100068, 2022. doi.org/10.1016/j.addlet.2022.100068

86-22   Patiparn Ninpetch, Prasert Chalermkarnnon, Pruet Kowitwarangkul, Multiphysics simulation of thermal-fluid behavior in laser powder bed fusion of H13 steel: Influence of layer thickness and energy input, Metals and Materials International, 2022. doi.org/10.1007/s12540-022-01239-z

85-22   Merve Biyikli, Taner Karagoz, Metin Calli, Talha Muslim, A. Alper Ozalp, Ali Bayram, Single track geometry prediction of laser metal deposited 316L-Si via multi-physics modelling and regression analysis with experimental validation, Metals and Materials International, 2022. doi.org/10.1007/s12540-022-01243-3

76-22   Zhichao Yang, Shuhao Wang, Lida Zhu, Jinsheng Ning, Bo Xin, Yichao Dun, Wentao Yan, Manipulating molten pool dynamics during metal 3D printing by ultrasound, Applied Physics Reviews, 9; 021416, 2022. doi.org/10.1063/5.0082461

73-22   Yu Sun, Liqun Li, Yu Hao, Sanbao Lin, Xinhua Tang, Fenggui Lu, Numerical modeling on formation of periodic chain-like pores in high power laser welding of thick steel plate, Journal of Materials Processing Technology, 306; 117638, 2022. doi.org/10.1016/j.jmatprotec.2022.117638

67-22   Yu Hao, Hiu-Ping Wang, Yu Sun, Liqun Li, Yihan Wu, Fenggui Lu, The evaporation behavior of zince and its effect on spattering in laser overlap welding of galvanized steels, Journal of Materials Processing Technology, 306; 117625, 2022. doi.org/10.1016/j.jmatprotec.2022.117625

65-22   Yanhua Zhao, Chuanbin Du, Peifu Wang, Wei Meng, Changming Li, The mechanism of in-situ laser polishing and its effect on the surface quality of nickel-based alloy fabricated by selective laser melting, Metals, 12.5; 778, 2022. doi.org/10.3390/met12050778

58-22   W.E. Alphonso, M. Bayat, M. Baier, S. Carmignato, J.H. Hattel, Multi-physics numerical modelling of 316L Austenitic stainless steel in laser powder bed fusion process at meso-scale, 17th UK Heat Transfer Conference (UKHTC2021), Manchester, UK, April 4-6, 2022.

57-22   Brandon Hayes, Travis Hainsworth, Robert MacCurdy, Liquid-solid co-printing of multi-material 3D fluidic devices via material jetting, Additive Manufacturing, in press, 102785, 2022. doi.org/10.1016/j.addma.2022.102785

55-22   Xiang Wang, Lin-Jie Zhang, Jie Ning, Suck-joo Na, Fluid thermodynamic simulation of Ti-6Al-4V alloy in laser wire deposition, 3D Printing and Additive Manufacturing, 2022. doi.org/10.1089/3dp.2021.0159

54-22   Junhao Zhao, Binbin Wang, Tong Liu, Liangshu Luo, Yanan Wang, Xiaonan Zheng, Liang Wang, Yanqing Su, Jingjie Guo, Hengzhi Fu, Dayong Chen, Study of in situ formed quasicrystals in Al-Mn based alloys fabricated by SLM, Journal of Alloys and Compounds, 909; 164847, 2022. doi.org/10.1016/j.jallcom.2022.164847

48-22   Yueming Sun, Jianxing Ma, Fei Peng, Konstantin G. Kornev, Making droplets from highly viscous liquids by pushing a wire through a tube, Physics of Fluids, 34; 032119, 2022. doi.org/10.1063/5.0082003

46-22   H.Z. Lu, T. Chen, H. Liu, H. Wang, X. Luo, C.H. Song, Constructing function domains in NiTi shape memory alloys by additive manufacturing, Virtual and Physical Prototyping, 17.3; 2022. doi.org/10.1080/17452759.2022.2053821

42-22   Islam Hassan, P. Ravi Selvaganapathy, Microfluidic printheads for highly switchable multimaterial 3D printing of soft materials, Advanced Materials Technologies, 2101709, 2022. doi.org/10.1002/admt.202101709

41-22   Nan Yang, Youping Gong, Honghao Chen, Wenxin Li, Chuanping Zhou, Rougang Zhou, Huifeng Shao, Personalized artificial tibia bone structure design and processing based on laser powder bed fusion, Machines, 10.3; 205, 2022. doi.org/10.3390/machines10030205

31-22   Bo Shen, Raghav Gnanasambandam, Rongxuan Wang, Zhenyu (James) Kong, Multi-Task Gaussian process upper confidence bound for hyperparameter tuning and its application for simulation studies of additive manufacturing, IISE Transactions, 2022. doi.org/10.1080/24725854.2022.2039813

27-22   Lida Zhu, Shuhao Wang, Hao Lu, Dongxing Qi, Dan Wang, Zhichao Yang, Investigation on synergism between additive and subtractive manufacturing for curved thin-walled structure, Virtual and Physical Prototyping, 17.2; 2022. doi.org/10.1080/17452759.2022.2029009

24-22   Hoon Sohn, Peipei Liu, Hansol Yoon, Kiyoon Yi, Liu Yang, Sangjun Kim, Real-time porosity reduction during metal directed energy deposition using a pulse laser, Journal of Materials Science & Technology, 116; pp. 214-223. doi.org/10.1016/j.jmst.2021.12.013

18-22   Yaohong Xiao, Zixuan Wan, Pengwei Liu, Zhuo Wang, Jingjing Li, Lei Chen, Quantitative simulations of grain nucleation and growth at additively manufactured bimetallic interfaces of SS316L and IN625, Journal of Materials Processing Technology, 302; 117506, 2022. doi.org/10.1016/j.jmatprotec.2022.117506

06-22   Amal Charles, Mohamad Bayat, Ahmed Elkaseer, Lore Thijs, Jesper Henri Hattel, Steffen Scholz, Elucidation of dross formation in laser powder bed fusion at down-facing surfaces: Phenomenon-oriented multiphysics simulation and experimental validation, Additive Manufacturing, 50; 102551, 2022. doi.org/10.1016/j.addma.2021.102551

05-22   Feilong Ji, Xunpeng Qin, Zeqi Hu, Xiaochen Xiong, Mao Ni, Mengwu Wu, Influence of ultrasonic vibration on molten pool behavior and deposition layer forming morphology for wire and arc additive manufacturing, International Communications in Heat and Mass Transfer, 130; 105789, 2022. doi.org/10.1016/j.icheatmasstransfer.2021.105789

150-21   Daniel Knüttel, Stefano Baraldo, Anna Valente, Konrad Wegener, Emanuele Carpanzano, Model based learning for efficient modelling of heat transfer dynamics, Procedia CIRP, 102; pp. 252-257, 2021. doi.org/10.1016/j.procir.2021.09.043

149-21   T. van Rhijn, W. du Preez, M. Maringa, D. Kouprianoff, Towards predicting process parameters for selective laser melting of titanium alloys through the modelling of melt pool characteristics, Suid-Afrikaanse Tydskrif vir Natuurwetenskap en Tegnologie, 40.1; 2021. 

148-21   Qian Chen, Multiscale process modeling of residual deformation and defect formation for laser powder bed fusion additive manufacturing, Thesis, University of Pittsburgh, Pittsburgh, PA USA, 2021. 

147-21   Pareekshith Allu, Developing process parameters through CFD simulations, Lasers in Manufacturing Conference, 2021.

143-21   Asif Ur Rehman, Muhammad Arif Mahmood, Fatih Pitir, Metin Uymaz Salamci, Andrei C. Popescu, Ion N. Mihailescu, Spatter formation and splashing induced defects in laser-based powder bed fusion of AlSi10Mg alloy: A novel hydrodynamics modelling with empirical testing, Metals, 11.12; 2023, 2021. doi.org/10.3390/met11122023

142-21   Islam Hassan, Ponnambalam Ravi Selvaganapathy, A microfluidic printhead with integrated hybrid mixing by sequential injection for multimaterial 3D printing, Additive Manufacturing, 102559, 2021. doi.org/10.1016/j.addma.2021.102559

137-21   Ting-Yu Cheng, Ying-Chih Liao, Enhancing drop mixing in powder bed by alternative particle arrangements with contradictory hydrophilicity, Journal of the Taiwan Institute of Chemical Engineers, 104160, 2021. doi.org/10.1016/j.jtice.2021.104160

134-21   Asif Ur Rehman, Muhammad Arif Mahmood, Fatih Pitir, Metin Uymaz Salamci, Andrei C. Popescu, Ion N. Mihailescu, Keyhole formation by laser drilling in laser powder bed fusion of Ti6Al4V biomedical alloy: Mesoscopic computational fluid dynamics simulation versus mathematical modelling using empirical validation, Nanomaterials, 11.2; 3284, 2021. doi.org/10.3390/nano11123284

128-21   Sang-Woo Han, Won-Ik Cho, Lin-Jie Zhang, Suck-Joo Na, Coupled simulation of thermal-metallurgical-mechanical behavior in laser keyhole welding of AH36 steel, Materials & Design, 212; 110275, 2021. doi.org/10.1016/j.matdes.2021.110275

127-21   Jiankang Huang, Zhuoxuan Li, Shurong Yu, Xiaoquan Yu, Ding Fan, Real-time observation and numerical simulation of the molten pool flow and mass transfer behavior during wire arc additive manufacturing, Welding in the World, 2021. doi.org/10.1007/s40194-021-01214-z

123-21   Boxue Song, Tianbiao Yu, Xingyu Jiang, Wenchao Xi, Xiaoli Lin, Zhelun Ma, ZhaoWang, Development of the molten pool and solidification characterization in single bead multilayer direct energy deposition, Additive Manufacturing, 102479, 2021. doi.org/10.1016/j.addma.2021.102479

112-21   Kathryn Small, Ian D. McCue, Katrina Johnston, Ian Donaldson, Mitra L. Taheri, Precision modification of microstructure and properties through laser engraving, JOM, 2021. doi.org/10.1007/s11837-021-04959-6

111-21   Yongki Lee, Jason Cheon, Byung-Kwon Min, Cheolhee Kim, Modelling of fume particle behaviour and coupling glass contamination during vacuum laser beam welding, Science and Technology of Welding and Joining, 2021. doi.org/10.1080/13621718.2021.1990658

110-21   Menglin Liu, Hao Yi, Huajun Cao, Rufeng Huang, Le Jia, Heat accumulation effect in metal droplet-based 3D printing: Evolution mechanism and elimination strategy, Additive Manufacturing, 48.A; 102413, 2021. doi.org/10.1016/j.addma.2021.102413

108-21   Nozomi Taura, Akiya Mitsunobu, Tatsuhiko Sakai, Yasuhiro Okamoto, Akira Okada, Formation and its mechanism of high-speed micro-grooving on metal surface by angled CW laser irradiation, Journal of Laser Micro/Nanoengineering, 16.2, 2021. doi.org/10.2961/jlmn.2021.02.2006

105-21   Jon Spangenberg, Wilson Ricardo Leal da Silva, Raphaël Comminal, Md. Tusher Mollah, Thomas Juul Andersen, Henrik Stang, Numerical simulation of multi-layer 3D concrete printing, RILEM Technical Letters, 6; pp. 119-123, 2021. doi.org/10.21809/rilemtechlett.2021.142

104-21   Lin Chen, Chunming Wang, Gaoyang Mi, Xiong Zhang, Effects of laser oscillating frequency on energy distribution, molten pool morphology and grain structure of AA6061/AA5182 aluminum alloys lap welding, Journal of Materials Research and Technology, 15; pp. 3133-3148, 2021. doi.org/10.1016/j.jmrt.2021.09.141

101-21   R.J.M. Wolfs, T.A.M. Salet, N. Roussel, Filament geometry control in extrusion-based additive manufacturing of concrete: The good, the bad and the ugly, Cement and Concrete Research, 150; 106615, 2021. doi.org/10.1016/j.cemconres.2021.106615

89-21   Wenlin Ye, Jin Bao, Jie Lei, Yichang Huang, Zhihao Li, Peisheng Li, Ying Zhang, Multiphysics modeling of thermal behavior of commercial pure titaniu