Rapid dendrite growth in quaternary Ni-based alloys

Dendritic growth is one of the most common micro-structural formation mechanisms during crystal growth. Its morphology provides the kinetics information of crystal growth. Therefore, it is valuable to perform the research on rapid dendrite growth in order…     

High undercooling and rapid dendritic growth of Cu-Sb alloy in drop tube

Droplets of Cu-20%Sb hypoeutectic alloy has been rapidly solidified in drop tube within the containerless condition. With the decrease of droplet diameter, undercooling increases and the microstructures of primary copper dendrite refines. Undercooling up to 207 K (0.17 T _L) is obtained in experiment. Theoretic analysis indicated that because of the broad temperature range of solidification, the rapid growth of primary copper dendrite is controlled by the solutal diffusion. Judging from the calculation of T₀ curve in the phase diagram, it is shown that the critical undercooling of segregationless solidification is δT ₀ = 474 K. At the maximum undercooling of 207 K, the growth velocity of primary copper phase exceeds to 37 mm/s, and the distinct solute trapping occurs.     

Primary dendrite growth of Ni<Subscript>3</Subscript>Sn intermetallic compound during rapid solidification of undercooled Ni-Sn-Ge alloy

Liquid Ni-31.7%Sn-2.5%Ge alloy was highly undercooled by up to 238 K(0.17TL) with glass fluxing and drop tube techniques.The dendritic growth velocity of primary Ni3Sn compound shows a power-law relation to undercooling and achieves a maximum velocity of 380 mm/s.The addition of Ge reduces its growth velocity as compared with the binary Ni75Sn25 alloy.A structural transition from coarse dendrites into equiaxed grains occurs once undercooling exceeds a critical value of about 125 K,which is accompanied by both grain refinement and solute trapping.The Ni3Sn intermetallic compound behaves like a normal solid solution phase showing nonfaceted growth during rapid solidification.     

Rapid eutectic growth during free fall

Rapid eutectic growth of Sb-24%Cu alloy is realized in the drop tube during the free fall under the containerless condition. Based on the analysis of crystal nucleation and eutectic growth in the free fall condition, it is indicated that, with the increase of undercooling, microstructural transition of Sb-24%Cu eutectic alloy proceeds from lamellar to anomalous eutectic structure. Undercoolings of 0 –154 K have been obtained in experiment. The maximum undercooling exceeds to 0.19T_e. Calculated results exhibit that Cu₂Sb compound is the primary nucleation phase, and that the primary Sb dendrite will grow more rapidly than the eutectic structure when undercooling is larger than 40 K. The eutectic coupled zone around Sb-24%Cu eutectic alloy leads strongly to the Cu-rich side and covers a composition range from 23.0% to 32.7%Sb.     

Rapid solidification of undercooled Al-Cu-Si eutectic alloys

Under the conventional solidification condition, a liquid aluminium alloy can be hardly undercooled because of oxidation. In this work, rapid solidification of an undercooled liquid Al_80.4Cu_13.6Si₆ ternary eutectic alloy was realized by the glass fluxing method combined with recycled superheating. The relationship between superheating and undercooling was investigated at a certain cooling rate of the alloy melt. The maximum undercooling is 147 K (0.18T _E). The undercooled ternary eutectic is composed of α(Al) solid solution, (Si) semiconductor and θ(CuAl₂) intermetallic compound. In the (Al+Si+θ) ternary eutectic, (Si) faceted phase grows independently, while (Al) and θ non-faceted phases grow cooperatively in the lamellar mode. When undercooling is small, only (Al) solid solution forms as the leading phase. Once undercooling exceeds 73 K, (Si) phase nucleates firstly and grows as the primary phase. The alloy microstructure consists of primary (Al) dendrite, (Al+θ) pseudobinary eutectic and (Al+Si+θ) ternary eutectic at small undercooling, while at large undercooling primary (Si) block, (Al+θ) pseudobinary eutectic and (Al+Si+θ) ternary eutectic coexist. As undercooling increases, the volume fraction of primary (Al) dendrite decreases and that of primary (Si) block increases. Supported by the National Natural Science Foundation of China (Grant Nos. 50121101, 50395105) and the Doctorate Foundation of Northwestern Polytechnical University (Grant No. CX200419)     

Phase separation and microstructural characteristics of undercooled Cu-Pb immiscible alloy

Bulk samples of Cu-80%Pb hypermonotectic alloy were undercooled by up to 270 K (0.21 TL) with glass fluxing technique. The undercooling behavior and the final microstructure were investigated experimentally. It was found that the macrosegregation decreased with the increase of undercooling exponentially. When undercooling reached 270 K, the volume fraction of macrosegregation was reduced by one order of magnitude. Meanwhile, high undercooling brought about significant changes to the microstructural morphology of S(Cu) phase. At small undercoolings, S(Cu) phase grew in dendritic manner. As undercooling increased, S(Cu) dendrite transformed gradually to spherical shell. This morphology transition was ascribed to the concurrent action of the phase separation within miscibility gap and the subsequent solidification process of L2 (Pb) matrix. As an essential step to model the final microstructure, theoretical calculations related to the nucleation of L1 (Cu) droplets were carried out.     

Phase-selection and metastable phase formation in highly undercooled eutectic Ni_(78.6)Si_(21.4)alloys

A large undercooling (250 K) was achieved in eutectic Ni78.6 Si21.4 melt by the combination of molten-glass denucleation and cyclic superheating. The metastable phase formation process in the bulk undercooled eutectic Ni78.6 Si21.4 melts was investigated. With the increase of undercooling, different metastable phases form in eutectic Ni78.6 Si21.4 melts and part of these metastable phases can be kept at room temperature through slow post-solidification. Under large undercooling, the metastable phases β2-Ni3Si, Ni31Si12 and Ni3Si2 were identified. Especially, the Ni3Si2 phase was obtained in eutectic Ni78.6 Si21.4 alloy for the first time. Based on the principle of free energy minimum and transient nucleation theory, the solidification behavior of melts was analyzed with regard to the metastable phase formation when the melts were in highly undercooled state.     

Pb-15%Sb过共晶合金的深过冷及快速凝固

采用熔剂净化深过冷和洁净容器快速凝固方法,研究了Pb-15%Sb过共晶合金在不同凝固条件下的组织演变.在熔剂净化条件下,随着凝固过冷度△T的增大,初生相Sb的组织形貌由尖角块状向树枝晶转变并不断细化,Sb的宏观偏析减弱,实验测得的最大过冷度为73K;在洁净容器快速凝固条件下,计算获得的最大过冷度为196.2K,初生相Sb的结晶被完全抑制,凝固组织发生了完全的共生生长,出现了快速凝固超细化组织.     

Rapid dendritic growth of Al-Ge hypoeutectic alloy in a drop tube

Abstract Dendritic growth in Al-45% Ge hypoeutectic alloy has been investigated during free fall in a 3 m drop tube. Calculationsindicate that the undercooling obtained for the falling Al-45% Ge droplets ranges from 13 K to 201 K. The maximum undercooling attains0. 27 T_L. With the increase of undercooling, the primary (Al) phase undergoes a "columnar dendrite to equiaxed dendrite" structural tran-sition. According to the current rapid dendritic growth theory, the growth of primary (Al) phase is always controlled by solute diffusion.     

Phase-selection and metastable phase formation in highly undercooled eutectic Ni78.6Si21.4 alloys

A large undercooling (250 K) was achieved in eutectic Ni_78.6Si_21.4 melt by the combination of molten-glass denucleation and cyclic superheating. The metastable phase formation process in the bulk undercooled eutectic Ni_78.6Si_21.4 melts was investigated. With the increase of undercooling, different metastable phases form in eutectic Ni_78.6Si_21.4 melts and part of these metastable phases can be kept at room temperature through slow post-solidification. Under large undercooling, the metastable phases β₂-Ni₃Si, Ni₃₁Si₁₂ and Ni₃Si₂ were identified. Especially, the Ni₃Si₂ phase was obtained in eutectic Ni_78.6Si_21.4 alloy for the first time. Based on the principle of free energy minimum and transient nucleation theory, the solidification behavior of melts was analyzed with regard to the metastable phase formation when the melts were in highly undercooled state.     

Phase-selection and metastable phase formation in highly undercooled eutectic Ni78.6Si21.4 alloys

A large undercooling (250 K) was achieved in eutectic Ni_78.6Si_21.4 melt by the combination of molten-glass denucleation and cyclic superheating. The metastable phase formation process in the bulk undercooled eutectic Ni_78.6Si_21.4 melts was investigated. With the increase of undercooling, different metastable phases form in eutectic Ni_78.6Si_21.4 melts and part of these metastable phases can be kept at room temperature through slow post-solidification. Under large undercooling, the metastable phases β₂-Ni₃Si, Ni₃₁Si₁₂ and Ni₃Si₂ were identified. Especially, the Ni₃Si₂ phase was obtained in eutectic Ni_78.6Si_21.4 alloy for the first time. Based on the principle of free energy minimum and transient nucleation theory, the solidification behavior of melts was analyzed with regard to the metastable phase formation when the melts were in highly undercooled state.     

Determination of interface width value in phase-field simulation of dendritic growth into undercooled melt

The influence of the interface width value on the simulation results and its dependence upon thermo-physical parameters in the phase-field simulation of dendritic growth into undercooled melt are investigated. After choosing the reasonable interface width value, the tip velocities of dendritic growth in Ni melt under different undercoolings are calculated and compared with the experimental data in order to benchmark our results. It is shown that the reasonable interface width value， which is determined by the undercooling, anisotropy, interface kinetic, and thermal diffusivity， has to be taken low enough, and the agreement of our results with experimental data verifies that the credible results can be achieved as long as the interface width value is adequately low. This paper provides the basis of determining interface width value in simulating dendritic growth into undercooled melt by phase-field approach.     

Rapid growth of FeAl intermetallic compound under high undercooling conditions

Fe-58at%Al alloy is undercooled up to 222K (0.15TL) with the drop tube technique.It is found that there exists a critical undercooling about 185 K,beyond which a “dendrite-equiaxed” growth morphology transition occurs in FeAl intermetallic compound. This transition is characterized by sharp decrease of its grain size.Once the undercooling exceeds 215 K, the peritectic transformation is suppressed completely and a fibrous structure is formed,which results from the cooperative growth of FeAl and FeAl2 compounds.     

基于GPU的流动影响枝晶生长相场方法

将自适应压力迭代法修正的Sola算法与相场模型相结合,建立过冷熔体在强迫流动状态下枝晶生长的Sola-相场模型.针对传统方法求解多场耦合相场模型时存在的计算量大,计算时间长,计算效率低等问题,提出基于CUDA+GPU软硬件体系结构的高性能计算方法.以高纯丁二腈(SCN)过冷熔体为例,在CPU+GPU异构平台上实现了存在流动时凝固微观组织演化过程的并行求解,并对基于CPU+GPU平台与CPU平台的计算结果及计算效率进行比较.结果表明,当计算规模达到百万量级时,与CPU平台上的串行算法相比,在CPU+GPU异构平台上达到了24.39倍的加速比,大大提高计算效率,并得到与串行计算相一致的结果.     

Rapid solidification mechanism of Ag60Sb34Cu6 ternary alloy in drop tube

Ternary eutectic growth involves competitive nu-cleation and growth of three solids from one liquid. Thesolidification behavior of ternary eutectic alloy is morecomplex than that of binary eutectic alloy due to the addi-tion of the third component[1—4]. Up to now, most scientificinvestigations on ternary eutectic alloy focus on the influ-ence of changing the component or adding a fourth even afifth element on the performance of the alloy[5—8]. How-ever, the information on crystal growth char…     

基于PF-LBM模型的自然对流影响枝晶生长模拟

基于二元合金枝晶生长的相场模型,建立耦合流场、温度场和溶质场等物理外场的多元合金相场模型,模拟了单晶粒和多晶粒在自然对流作用下的生长,观察了枝晶凝固过程中的枝晶形貌、流场以及溶质场的变化.研究发现：温度梯度和浓度梯度改变引起自然对流,使枝晶整体的对称性遭到破坏,上游枝晶尖端生长受到促进,生长速度大于下游,水平方向枝晶尖端生长速度介于上下游之间,二次枝晶臂生长速度、浓度与一次枝晶臂基本相同,能量起伏和结构起伏使枝晶受到的影响更加明显.此外,随着各向异性强度增加,枝晶尺寸变大,生长速度加快,主枝晶臂变细,内部凹陷变明显,尖端变尖锐,二次枝晶臂间距增大.当单晶粒各向异性强度为0.05时,出现明显的“颈缩”现象,多晶粒在各向异性强度为0.03时,出现明显“颈缩”现象.     

纯物质过冷熔体中自由枝晶生长相场模型的自适应有限元法模拟

基于自适应有限元方法,通过求解表征纯物质相场模型的非线性抛物型方程,研究镍过冷熔体中不同起伏情况下单个完整等轴枝晶的演化过程.模拟结果表明:采用自适应有限元方法求解相场模型时结果更接近真实物理模型,在计算终止时整个计算域节点数仅为2.79×105个,远小于采用相同网格间距普通方法的1.6×106个,较大不同计算域对枝晶尖端速度的平衡值影响不大;随着起伏强度的增大,枝晶尖端获得更高的温度梯度,等温线波动更大,一次枝晶臂表面失稳,二次枝晶臂向过冷溶液中凸起的趋势越强,二次枝晶臂越发达.     

Forming mechanism of refined granular crystalline of Cu70Ni30 alloy by undercooled solidification

Moth glass fluxing and cyclic superheating techniques were adopted to effectively uudercool the Cu₇₀Ni₃₀ alloy in vacuum. Within the undercooling range of 21 K to 270 K, the microstructure evolution ol the alloy was investigated. When the inell was undercooled to △T > △T', (210 K) , the grain refinement took place abruptly, liascd on the observation of the solidified microstructure, the rnierocheinieal-analysis and the calculated results with UCT model, it is found that the secondary grain refinement mechanism consists of two stages. The dendrite is, firstly, broken into hag-ments owing to the stress caused by uneven shrinking during rapid solidilication, then the fragments, under the driving force of surface and strain energies, merge through the migration of l>ouinlaries, i. c. recryslallization, thus leading to the formation of secondary granular-crystalline .     

过冷纯熔体中晶体生长扰动解的可解性条件

在晶体液固界面上考虑动力过冷,对凝固系统控制方程的扰动解进行渐近展开,分别求其零级、一级近似解.推出判别液固平界面稳定性的色散关系,该关系式适合于任意的扰动波长.结果表明,过冷纯熔体中非快速凝固晶体生长的液固界面是不稳定的.     

Recalescence behavior and solidification structure of the undercooled Fe82B17Si1 eutectic alloy

By cyclic superheating incorporated with glass fluxing denucleation method the Fes2Bl7Si1 eutectic al-loy was undercooled up to △ T = 342 K. The relations between recalescence behavior and solidification structures weresystematically studied in the undercooling range of 6-342 K. Two critical undercoolings were observed: mixed eutecticwas the unique growth morphology when the undercooling was less than △T1 = 63 K; but the microstructure transformedto complete undercooled anomalous eutectic when the undercooling was greater than △T2 = 164 K. The two eutecticphases α(Fe,Si) and Fe2B conformed to the non-reciprocal nucleation effect. The boundary of the coupled zone of α(Fe, Si)-Fe2 B system shifted toward the Fe2 B side, and intersected the eutectic composition line at △ T = 154 K and△x T= 264 K, whose valley was at about △ T = 207 K.