微重力条件下Ni-Cu合金的快速枝晶生长研究

采用落管方法实现了Ni-50%Cu过冷熔体在微重力和无容器条件下的快速枝晶生长.对微重力条件下的晶体形核和快速生长进行了研究，发现随着过冷度的增大，晶体生长形态由粗大枝晶向规划均匀的等轴晶转变.实验中最大冷却速率达到8×103K/s，获得了218K(014TL)的最大过冷度.理论分析表明，过冷熔体中优先发生异质形核，形核率可达1012m-3s-1以上；Ni-50%Cu过冷熔体中的枝晶生长随过冷度的增大发生由溶质扩散控制向热扩散控制的生长动力学机理转变.在68K过冷度条件下，生长界面前沿的偏析程序最大. 关键词： 落管 微重力 深过冷 枝晶 熔体     

三维多相场数值模拟共晶CBr4-C2Cl6合金在不同抽拉速度下的形态选择

利用KKSO多相场模型对定向凝固共晶CBr₄-C₂Cl₆合金的三维恒速及变速生长过程进行了研究,再现了不同抽拉速度下共晶形态演化及选择过程,建立了形态选择图,研究了变速过程的界面平均生长速度及界面平均过冷度的变化.结果表明,变速前后的形态选择与恒速下的形态选择一致;变速过程的形态演变、界面平均生长速度和界面平均过冷度的变化均产生滞后效应;界面平均生长速度和界面平均过冷度之间的关系与理论结果符合较好. 关键词： 多相场模型 共晶生长 抽拉速度     

均聚物结晶与熔融化转变的稳态和亚稳态统计理论Ⅳ 分子分凝统计结晶动力学~结晶增长区域的区划和它们对温度和生长机制的依赖性

首先对高分子结晶增长动力学的实验规律进行全面总结,并指出了当前高分子结晶增长动力理论中存在的难题.然后按我们建议的评估微晶粒尺寸增长速率的新方法推导出了四种不同微观生长机制(折叠、伸直、折叠同伸直并联并存和折叠同伸直串联并存等方式)下微晶粒高分子链组的微晶粒尺寸增长速率定量表征式,又导出了四种不同生长机制下微晶粒尺寸增长速率同结晶温度和过冷温度间关系的表达式.根据四种不同微观生长机制同宏观增长方式差别和它们出现的结晶温度同过冷温度之积值高低,可把结晶动力学的结晶增长区域图中三组交叉线区划为三个不同增长区域,最后又根据三个增长区的理论关系式讨论了增长区中晶体形貌同结晶温度和过冷温度间的相关性,其理论预测能同近期实验观测基本符合.     

三维多相场数值模拟共晶CBr4-C2Cl6合金在不同抽拉速度下的形态选择

利用KKSO多相场模型对定向凝固共晶CBr4-C2Cl6合金的三维恒速及变速生长过程进行了研究,再现了不同抽拉速度下共晶形态演化及选择过程,建立了形态选择图,研究了变速过程的界面平均生长速度及界面平均过冷度的变化.结果表明,变速前后的形态选择与恒速下的形态选择一致;变速过程的形态演变、界面平均生长速度和界面平均过冷度的变化均产生滞后效应;界面平均生长速度和界面平均过冷度之间的关系与理论结果符合较好.     

弱熔体对流对定向凝固中棒状共晶生长的影响

利用渐近方法求出在弱对流熔体中定向凝固棒状共晶生长的浓度场的渐近解,研究了弱熔体对流对定向凝固中棒状共晶生长的影响.结果表明,弱熔体对流对定向凝固中棒状共晶生长有显著的作用;平均界面过冷度不仅与棒状共晶的棒间距、生长速度有关,还与流动强度有关;当生长速度一定时,随着流动强度增大,棒状共晶的平均界面过冷度减小.利用最小过冷原则,获得棒间距与生长速度和流动强度的关系.结果表明,当生长速度比较小时,随着流动强度增大,棒状共晶的棒间距增大;当生长速度比较大时,随着流动强度增大,棒状共晶的棒间距变化减弱;棒状共晶的生长速度越小,流动对棒状共晶生长的影响越大.利用本文的解析结果计算在对流条件下Al-Cu共晶的棒间距,结果显示随着转速增大或径向距离增大,共晶的间距增大,这与Junze等的实验结果相符合.     

抽拉速度对SCN-DC共晶生长形貌的影响

本文采用类金属透明模型合金丁二腈-23.6 wt%樟脑 (SCN-23.6 wt%DC) 合金, 研究了棒状共晶定向凝固组织的演化行为, 考察了抽拉速度对棒状共晶合金组织形貌演化的影响规律. 结果表明, 在共晶生长初期, 共晶组织首先起源于晶粒晶界或者试样盒型壁处, 随后沿液/固界面和平行于热流方向生长; 在较小的抽拉速度 (0.064–0.44 μm/s)下, 棒状共晶界面前沿呈现平界面形态, 内部两相棒状组织平行生长, 并且随着抽拉速度的增大,棒状共晶逐渐细化, 棒状间距减小; 而在较大的抽拉速度 (0.67–1.56 μm/s)下, 共晶界面前沿呈现胞状生长形貌, 胞内的棒状共晶呈放射状生长, 同样, 随着抽拉速度的增大, 胞内棒状共晶逐渐细化, 棒状间距减小. 关键词： 定向凝固 共晶形貌 抽拉速度 共晶间距     

界面动力学对过冷熔体中球晶生长界面形态的影响

考虑了在非平衡凝固条件下球晶生长过程中界面动力学系数随界面温度的变化,利用渐近分析方法求出了在过冷熔体中球晶生长温度场和界面的近似解析解,研究了非线性界面动力学过冷对于过冷熔体中球晶界面形态和生长速度的影响.研究表明,界面动力学系数越大,球晶的生长速度越快; 反之,表明界面动力学系数越小,球晶的生长速度越慢.与忽略界面动力学的情形比较,在球晶生长过程中依赖于界面温度变化的界面动力学显著地减缓了晶体生长的速度. 关键词： 球晶 界面形态 渐近分析     

基于改进元胞自动机模型的三元合金枝晶生长的数值模拟

在二元合金元胞自动机模型的基础上,通过耦合多元合金热力学相平衡求解器PanEngine, 建立了三元合金改进的元胞自动机模型,可模拟初生相枝晶的生长过程. 模型考虑了曲率过冷和成分过冷对界面平衡溶质成分的影响,通过不同组元的无量纲溶质过饱和度方程和界面溶质守恒方程之间的耦合来求解界面生长速率,并通过PanEngine计算界面处的液相线温度. 采用本模型模拟了Al-7%Si-xMg三元合金自由枝晶的生长形态, 结果表明Mg含量的增加会抑制枝晶一次臂的生长和二次臂的产生.同时模拟了不同抽拉速度下 Al-7%Si-0.5%Mg合金柱状枝晶的竞争生长过程,随着抽拉速度的增大,柱状枝晶一次枝晶臂间距逐渐减小, 与Hunt理论模型符合较好.     

液态Ti-Al合金的深过冷与快速枝晶生长

采用电磁悬浮和自由落体两种试验技术研究了液态Ti-25 wt.%Al合金的亚稳过冷能力、晶体形核机制和枝晶生长过程. 试验发现, 即使电磁悬浮无容器状态下仍难以消除润湿角θ ≥60°的异质晶核, 合金熔体过冷度可达210 K (0.11T_L). β-Ti相形核的热力学驱动力随过冷度近似以线性方式增大, 其枝晶生长速度高达11.2 m/s, 从而在慢速冷却条件下实现了快速凝固. 理论计算表明, 随着过冷度的逐步增大, β相枝晶生长从溶质扩散控制转变为热扩散控制. 当过冷度超过100 K时, 非平衡溶质截留效应可使合金熔体发生无偏析凝固. 然而, 单靠深过冷状态不足以抑制β相的后续固态相变. 对于落管中快速凝固的直径77-1048 μm合金液滴, 其冷却速率最高达1.05×10⁵ K/s, 深过冷与快速冷却的耦合作用能更有效地调控凝固组织形成过程.     

金属基复合材料原位反应相场模型

原位反应法制备金属基复合材料具有增强体与基体间无杂质、无污染、颗粒分布均匀等优点,已成为制备金属基复合材料的一种重要方法,揭示其动力学机制及规律具有重要的理论及工业价值.然而,原位反应过程具有反应时间短、随机发生、温度高等特点,目前采用原位实验观测其反应过程仍存在较大困难.本文采用相场法模拟金属熔体内的原位反应过程,首先建立了能够描述双束金属熔体界面反应形核的相场模型,并采用该模型模拟了不同参数下相界反应形核过程.结果表明,形核率随着曲率半径及噪声强度的增大而增大,小曲率半径及强噪声条件下新相颗粒尺寸分布更加均匀,形核率随着过冷度的增大而先增大后减小.     

Asymmetrical contribution of eutectic growth kinetics on the coupled growth behaviour in rapid eutectic solidification

The interface undercooling in classical eutectic growth theories consists of solute and curvature undercooling with different expression formats. However, a significant difference in interface kinetic coefficients arises for a disordered non-facetted solid solution and an ordered facetted intermetallic compound in that different growth kinetics govern the attachment kinetics at the solid–liquid interface, which correspond to a typical eutectic reaction with a solid solution and an intermetallic compound as its terminal eutectic phases. Following the pioneering work of Jackson and Hunt (Trans. Metall. Soc. AIME 236 1129 (1966) ), the kinetic undercooling is supplemented to interface undercooling and two eutectic phases are considered separately so as to diagnose the effect of the asymmetrical contribution of kinetic undercooling on the coupled eutectic growth behaviour. Further analysis indicates that it is the asymmetrical contribution of kinetic undercoolings of the facetted and non-facetted phases that enables the coupled eutectic composition shift to the facetted phase side so as to weaken the solute undercooling of the facetted phase and balance the kinetic contribution in the rapid solidification of coupled eutectics.     

Influence of isothermal approximation on the phase-field simulation of directional growth in undercooled melt

By using the phase-field approach,we have simulated the directional growth of alloys in undercooled moten states under the isothermal and nonisothermal conditions.The influences of the isothermal approximation on simulation results are discussed.We found that for undercooling greater than 25K,the isothermal approximation overestimates the interface growth velocity and reduces a critical velocity for an absolute stable planar interface,thus in this simulation,the uinterface morphology shows the plane-cell-plane transition with increasing initial undercooling of the mele,and the planar interface obtained under a large undercooling is absolutely stable.Whereas in the nonisothermal simulation,only plane-cell transition occures in the same range of the initial undercoolings of the melt,and the planar interface tends to be destabilized and evolve into cells.     

Influence of initial solid–liquid interface morphology on further microstructure evolution during directional solidification

Preparation of the initial solid–liquid interface on which growth is started is a very critical step in directional solidification experiments. Dedicated experiments concerning preparation of the initial solid–liquid interface morphology and its influence on further directionally solidified microstructure were performed on Cu-20 wt% Sn peritectic alloy in a Bridgman-type furnace. To verify the morphology of the initial solid–liquid interface, steady-state directional dendritic growth was interrupted by thermal stabilization ranging from 0 to 1 h prior to quenching. With thermal stabilization duration increase, the solid–liquid interface morphology degenerated from dendritic to cellular and finally to planar. To verify the influence of the initial state on further solidification microstructure, directional solidification experiments were performed at a low pulling rate of 1 μm/s with different initial solid–liquid interface morphologies. The initial state affects solute redistribution and formation of peritectic coupled growth structure in the subsequent directional solidification process.     

Numerical simulation of dendrite growth and microsegregation formation of binary alloys during solidification process

The dendrite growth and solute microsegregation of Fe-C binary alloy are simulated during solidification process by using cellular automaton method. In the model the solid fraction is deduced from the relationship among the temperature, solute concentration and curvature of the solid/liquid interface unit, which can be expressed as a quadric equation, instead of assuming the interface position and calculating the solid fraction from the interface velocity. Then by using this model a dendrite with 0 and 45 degree of preferential growth direction are simulated respectively. Furthermore, a solidification microstructure and solute microsegregation are simulated by this method. Finally, different Gibbs-Thomson coefficient and liquid solute diffusing coefficient are adopted to investigate their influences on the morphology of dendrite.     

Nanosecond-time-resolution thermal emission measurement during pulsed excimer-laser interaction with materials

A nanosecond-time-resolution pyrometer has been developed for measuring the transient surface temperature of a solid material heated by pulsed excimer-laser irradiation. Fast germanium diodes are employed to capture the transient thermal emission signals in the wavelength range between 1.2 and 1.6 pm. The surface temperature is derived from the measured spectral thermal emission. The directional spectral emissivity is determined in situ by measuring the transient directional spectral reflectivity and applying Kirchhoffs law. The experimental results are in good agreement with numerical thermal modeling predictions. The pyrometric thermal emission measurement also yields the solid/liquid interface temperature during the pulsed excimer-laser-induced melting. The relation between the measured interface superheating temperature and the interface velocity reveals the melting kinetic relation during the high-power, short-pulse laser-induced phase-change processes.