连续冷却快速凝固过程中相组成的计算模型

基于平面流铸快速凝固过程的牛顿冷却方式假定和过冷熔体中的枝晶生长理论，提出了凝固相重量分数计算的物理模型和数学计算方法。该模型可对快速凝固过程中不同相的过冷度，晶体的生长速度以及最终的相组成进行半定量的计算和预测。Ni31.5Al68.5合金条带的快速凝固过程的计算结果和试验测定数据有较好的吻合。     

过冷Fe-Co合金的包晶凝固

采用熔融玻璃净化法使Fe-Co包晶合金实现了深过冷快速凝固。当熔体过冷度较小时,Fe-Co包晶合金的凝固组织为典型的包晶组织。借助电子探针分析和DTA差热分析,证实了非平衡条件下Fe-Co包晶合金凝固过程中发生了包晶反应和包晶转变。研究表明,深过冷Fe-Co包晶合金的非平衡凝固过程从理论上可以划分为4个阶段:初生δ相的形核与生长、包晶反应、包晶转变和γ相的外延生长。     

基于热力学与动力学相结合的灰铸铁凝固数值模拟

以凝固理论、传热学原理和灰铸铁凝固特性等为基础,采用热力学方法与动力学方法相结合的模拟技术建立灰铸铁模拟框架。对初生奥氏体析出采用热力学计算模型,建立固相率与温度的关系;对共晶相采用动力学计算模型,即形核生长的计算模型,通过建立生长速度与过冷度的关系来确立固相率与过冷度的关系。通过对阶梯形铸件的实验和模拟的数据对比,验证了此方法可以正确地描述灰铸铁凝固过程的行为。     

快速凝固Fe-Co合金中的亚稳相

采用熔融玻璃净化和循环过热相结合的方法,研究了Fe-Co合金在深过冷快速凝固中的亚稳相。结果表明,当熔体的过冷度达到某一临界数值(△T_(crit))时,亚稳相(b.c.c)在竞争形核中优先形核生长,并在随后的冷却过程中保留在凝固组织中。在γ单相区内等温退火3 h后,亚稳相完全转变为稳定相;在过冷Fe-Co合金的凝固组织中亚稳相是竞争形核-重熔-γ相外延生长-不完全固态相变的产物。     

深过冷Ni80.3B19.7合金的再辉和非规则共晶的形成

采用熔融玻璃净化结合气体保护的方法,使Ni80 3B19 7过共晶合金获得了407 K的大过冷度,研究了其在不同过冷度下快速凝固过程中的再辉行为.结果表明,Ni80 3B19.7过共晶合金在0～112 K过冷度范围内无明显再辉,在112～323 K过冷度范围内,其再辉曲线表现为两个再辉峰,而在323～407 K过冷度范围内,其再辉曲线为一个再辉峰.初生固相含量的随着过冷度的增大而增大,导致一次再辉度随着过冷度的增大而增大.深过冷Ni80 3B19.7合金凝固组织中非规则共晶的形成,归因于共晶两相在快速凝固阶段以自由枝晶的形式进行的非耦合生长和再辉后的慢速凝固阶段两相枝晶所发生的形态上的转变.     

深过冷Ni-Cu-Si合金熔体中的快速枝晶生长

为了揭示多元合金中的枝晶生长规律,采用电磁悬浮技术实现了Ni-10%Cu-10%Si三元合金的深过冷与快速凝固,实验中合金熔体获得的最大过冷度为236K。对合金快速凝固过程中初生相-αNi的枝晶生长速度测定结果表明,其与过冷度之间存在幂函数关系:V=1.6×10-13ΔT5.7。当ΔT较小时,随着ΔT的增加V增加缓慢,当ΔT较大时,随着ΔT的增加V迅速增加。对比分析表明,溶质Si对-αNi枝晶的生长影响显著,而溶质Cu则几乎没有影响。随着过冷度的增加,未发现-αNi相的微观形态从枝晶向等轴晶转变,但-αNi晶粒尺寸均随着过冷度的增加而急剧细化。     

深过冷Cu-Pb偏晶合金的快速凝固行为和凝固组织

用熔融玻璃净化与循环过热相结合的方法,研究了亚偏晶Cu-25%Pb合金,Cu-37.4%Pb偏晶合金和过偏晶Cu-40%Pb(质量分数)合金过冷熔体凝固行为和凝固组织的演化规律,以及Cu-37.4%Pb偏晶合金的过冷度对磨损率的影响.研究表明:在过冷亚偏晶Cu 25%Pb合金熔体凝固过程中先形成α(Cu)初生相,随着过冷度的增大,凝固组织经历粗大枝晶重熔形成的细化枝晶向准球状晶粒演化的过程;在过冷Cu-37.4%Pb偏晶合金熔体凝固过程中初生相为L2相,当过冷度在20～150 K区间时,得到第二相S(Pb)弥散在α(Cu)枝晶间的凝固组织,并且在该过冷区间内随着过冷度的增加,材料的磨损率也逐渐降低;在过冷过偏晶Cu-40%Pb合金熔体凝固过程中初生相为L2相,在过冷度区间42～80 K时,得到以偏晶胞形式分布的凝固组织.     

亚共晶Ni-Si合金的凝固组织特征研究

采用布里奇曼定向凝固技术制备了NiNi3Si亚共晶复合材料,系统地研究了Ni-Ni3Si亚共晶的定向凝固组织特征。在较低的凝固速率R=3μm/s时亚共晶成分的合金为规则的层片共晶组织。随着凝固速率的增大,当R=8μm/s时,平界面失稳,在第二相的旁边出现浅胞状组织。当R=25μm/s时在析出相的旁边出现了突起的胞状组织。当R=40μm/s时由于固液界面前沿的成分过冷逐渐增大,凝固组织生长成为典型的树枝晶组织。并根据"成分过冷"判据,评估了固液界面前沿的"成分过冷"的大小,理论计算与实验结果基本吻合。此外,根据BH模型计算和比较了α-Ni相的界面生长温度和共晶界面生长温度,证明较高速定向凝固下不太可能制备出全耦合生长的共晶组织。随凝固速率的增大,一次枝晶间距减小,组织细化。     

用相场方法模拟镍的枝晶生长

采用相场模型,计算了纯镍的过冷溶液在凝固过程中的枝晶生长。在相场方程中,采用均匀网格的一般显示有限差分方法求解,通过数值模拟显示了枝晶的形貌,包括一次臂、二次臂,以及在枝晶生长过程中出现的“缩颈”现象。     

深过冷熔体激发快速定向凝固

阐述了深过冷的方法，深过冷的遗传性，深过冷度的理论极限以及深过冷熔体激发发快速定向凝固的试验方法及其凝固过程，给出了深过冷熔体（Ｃｕ－５ｗｔ％）激发快速定向凝固与铸态试验激发快速定向凝固的初步试验结果。     

Modelling of solidification of Ti-45 at%Al alloy ingot by the stochastic model

A comprehensive stochastic model for simulating grain structure formation and evolution during solidification processes is developed, based on a finite differential method (FDM) for macroscopic heat flow calculation and a cellular automaton method (CA) for microscopic modelling of nucleation, growth, solute redistribution and solute diffusion. Formation of peritectic phases in the last solidified liquid regions is considered. The growth rates of peritectic phases are calculated by the peritectic growth kinetics model. The solidification contraction is also taken into account. The calculated results are compared with those obtained experimentally.     

定向凝固A1-Bi偏晶合金中第二相的粗化行为

为了获得第二相弥散分布的偏晶合金,在定向凝固条件下,对Al-Bi偏晶合金的凝固行为进行了研究,考察了第二相体积分数对凝固组织的影响,并对第二相粒子的粗化因素进行了分析.研究结果表明:用定向凝固方法可以制得具有弥散第二相分布的偏晶系Al-Bi合金;在一定的生长条件下,第二相粒子的半径随体积分数的增大而增大;第二相体积分数以及熔体中存在的Stokes流和Marangoni对流是引起第二相粒子粗化的主要因素.     

Two phases separate growth in directionally solidified Fe-4.2Ni alloy

A two phases separate growth microstructure is observed in directionally solidified Fe-4.2Ni alloy in diffusive regime. This structure consists of peritectic two solid phases, both of which grow with plane fronts in the pulling direction and occupy half width of the sample. A simple model was proposed to explain the formation of the separate growth structure in Fe-Ni alloy. It implies that the separate growth structure forms under predominantly diffusion-limited conditions and when the two phases grow steadily and independently in different solute fields.     

Effects of high magnetic fields on solidified structures of Mn-90.4 wt% Sb hypoeutectic alloy

Mn-90.4 wt% Sb alloy specimens were solidified under both uniform magnetic field and magnetic field gradient conditions. The solidification behavior was examined to elucidate the effects of high magnetic fields on the solidified structure evolution of this hypoeutectic alloy. The macrostructures on the longitudinal section of the alloys were investigated by optical microscopy and x-ray diffraction (XRD). The volume fraction of primary MnSb phases and the interrod spacing of the eutectic were measured by metallographic analysis. It was found that the segregation of the primary MnSb particles at the certain regions of the specimens occurred under the influence of high magnetic field gradients. The MnSb phases obtained under magnetic fields were oriented with their (h0 l) planes along the direction of the magnetic field. Both the volume fraction of primary MnSb phases and the interrod spacing of the eutectic were decreased upon the application of the high magnetic fields.     

Effects of high magnetic fields on solidified structures of Mn-90.4 wt% Sb hypoeutectic alloy

Abstract

Mn-90.4 wt% Sb alloy specimens were solidified under both uniform magnetic field and magnetic field gradient conditions. The solidification behavior was examined to elucidate the effects of high magnetic fields on the solidified structure evolution of this hypoeutectic alloy. The macrostructures on the longitudinal section of the alloys were investigated by optical microscopy and x-ray diffraction (XRD). The volume fraction of primary MnSb phases and the interrod spacing of the eutectic were measured by metallographic analysis. It was found that the segregation of the primary MnSb particles at the certain regions of the specimens occurred under the influence of high magnetic field gradients. The MnSb phases obtained under magnetic fields were oriented with their (h0 l) planes along the direction of the magnetic field. Both the volume fraction of primary MnSb phases and the interrod spacing of the eutectic were decreased upon the application of the high magnetic fields.     

Tungsten wires and porous NiAl prepared through directional solidification and selective dissolution

The combination of directional solidification and selective dissolution was applied to fabricate tungsten (W) wires and porous NiAl matrix. A NiAl–W pseudobinary eutectic alloy with 1.5?at.% tungsten was directionally solidified in a Bridgman-type oven at 1700°C. Results confirmed that the relationships of the growth rate with the interfibrous spacing and diameter of W fibrous phases in the directionally solidified samples are in accordance with the Jackson and Hunt (J?H) model. Afterward, the NiAl matrix was selectively dissolved in an HCl:H₂O₂ solution to reveal W wires, which present various three-dimensional (3D) morphologies at different growth rates. The W fibrous phases in the NiAl–W alloy samples were then selectively removed with a mixed etchant of ammonium acetate to form a porous NiAl matrix at a constant potential. Dynamic corrosion curves revealed that etching W from the NiAl matrix was inhibited after 2–3?h. The porous structures of NiAl after removing W phases are linked to the 3D morphologies of W fibrous phases embedded in the NiAl matrix. The aspect ratio of W wires and the structures of porous NiAl can be adjusted by selecting the process parameters of this combined technology.     

Mechanical properties characterization of the broken-lamellar eutectic composite Cd-Ge

The tensile and compressive properties of the unidirectionally solidified Cd-Ge eutectic have been examined. With increasing growth rate the broken-lamellar Ge-rich phase becomes increasingly fibrous. This morphological change was accompanied by a marked increase in tensile properties, similar to the changes observed for both Zn-Ge and Al-Si. However, a less dramatic increase in compressive properties took place. The presence of Cd dendrites did not reduce the UCS (ultimate compressive strength) as has been reported for Cd-Zn and Sb-Ge. Large matrix constraints arise in this eutectic even though the weight fraction of the Ge phase is only 2%.     

Simulation of microsegregation and microstructural evolution in directionally solidified superalloys

Abstract

A two-dimensional model for solidification and secondary phase precipitation in directionally solidified superalloys is presented, which makes use of a shape function approximation for the isothermal cross-section of the primary dendrites. The phase boundary is represented by a diffuse interface on a finite difference grid, as in phasefield methods. Thus, two-dimensional multicomponent diffusion can be calculated for all phases. Via a Fortran interface, the model is coupled to thermodynamic databases assessed using the ‘calculation of phase diagrams’ (Calphad) approach. In this way, for each time step actual data are available for partitioning, dendritic growth, and nucleation of secondary phases. The model is applied to Ni–Al–Cr as a ternary model system and to the commercial superalloy IN706.     

Carbide Formation Process in Directionally Solidified MAR-M247 LC Superalloy

1.IntroductionSeveralphasesforminthesolidificationandcool-.ingprocessofcastsuperalloys['].MCcarbidesand7'precipitatesarethemainphasestoprovidehightemperaturestrengthinthesuperalloys.TheMCcarbidesstrengthengrainboundariesandsub-grainboundariesatelevatedtemperature.Theirvolumefraction,sizeandmorphologyhaveaveryimpor-tanteffectonthemechanicalpropertiesofNi-basesuperalloys['l.Considerable..,..,.h.s[3~14]havebeencarriedoutfromslowtorapidsolidificationconditionstocharacterizethesequenceofformation…     

Effect of strontium and phosphorus on solid/liquid interface of Al–Si eutectic

Abstract

A high resolution quenched interface technique has been used to study the solid/liquid interface of the Al–Si eutectic solidified at extremely low growth rates. The interface morphology of the pure eutectic and also that of samples doped with Sr or P were studied. The observations were consistent with the twin plane re-entrant edge (TP RE) growth model for the pure eutectic and with a change to non-TPRE growth in the presence of Sr. On the other hand, P was found to have an effect on the relative tendencies towards faceting of the two phases.

MST/923