A combined model for the description of austenitization,homogenization and grain growth in hypoeutectoid Fe–C steels during heating

A combined model which allows one to simulate all the steps of the reaustenitization process of ferrito-pearlitic plain carbon steel has been developed. The dissolution of pearlite, the transformation of ferrite into austenite and the homogenization of the carbon distribution is described with a finite volume method. The simulation is performed on a bidimensional domain where ferrite (α), pearlite (P) and austenite (γ) grains are represented. The dissolution of pearlite is described by the growth of spherical grains and simple nucleation and growth laws. The movement of α/γ interfaces is calculated by solving the diffusion equation for carbon in the α and γ phases and accounting for the solute flux balance at the interface using a pseudo-front tracking method. The diffusion model is coupled with a Monte Carlo simulation which describes the grain growth occurring in austenite at a later stage of austenitization. The evolution of the volume fractions of pearlite and ferrite, the maximum and minimum carbon concentrations in the domain and the mean austenite grain size are represented as a function of the temperature for a typical case of constant heating rate. The influence of the different steps of the austenitization process on the global kinetics is discussed.     

铸态GCr15钢在连续加热过程中的奥氏体化动力学特征与组织演变

利用DIL805A热膨胀仪记录了铸态GCr15钢在不同的加热速率下(0.5、3、5、30、100 ℃/s)的线膨胀量,获得了不同加热速率下的热膨胀曲线和奥氏体体积转变分数曲线,研究了加热速率对奥氏体化的影响。采用高温光学显微镜对该钢在连续加热过程中的奥氏体转变过程进行了观察分析。研究表明:GC15钢在连续加热过程中的奥氏体转变可分为3个阶段:在760~790 ℃为珠光体向奥氏体的转变、(Fe, Cr)₃C_II向奥氏体中的溶解和奥氏体的成分均匀化温度分别为790~890 ℃及890 ℃以上。并且随着加热速率提高,相变临界温度提高,相变速率提高。在连续加热过程中,铸态GCr15钢的奥氏体转变是一个形核和长大交替进行的过程。     

原奥氏体晶粒度对45V非调质钢连续冷却转变的影响

采用ＦｏｒｍａｓｔｏｒＦ热膨胀分析仪及金相显微镜研究了原奥氏体晶粒度对４５Ｖ非调质钢相变点及显微组织的影响。结果表明,在相同的冷速下,相变前奥氏体晶粒尺寸越大,先共析铁素体量越少,先共析铁素体和珠光体转变温度越低     

基于ABAUQS-Matlab对42CrMo钢表面感应淬火奥氏体化参数的研究

目的 确定42CrMo钢感应淬火过程的奥氏体相变动力学参数，并验证其可靠性。方法 根据不同加热速率下42CrMo钢奥氏体膨胀曲线，基于经典JMAK（Johnson-Mehl-Avrami-Kolmogorov）模型和Kissinger方法，确定了42CrMo钢奥氏体化相变动力学的参数。建立ABAQUS局部移动式感应淬火模型，选取淬火区域加热过程中点的温度变化曲线作为验证奥氏体化模型的对象。基于Scheil法则和JMAK相变动力学模型，采用文中求解得到的奥氏体化参数，采用Matlab对42CrMo连续转变过程离散为每个时间间隔的等温相变并求解，并对照相关学者采用的扩展解析动力学模型和JAMK模型，加以验证。结果 根据上述方法，得到的42CrMo奥氏体相变动力学参数为：激活能Q为2.04×106 J/mol，指前因子lnk0的值取230.78，Avrami指数n取0.427。将淬火加热过程离散为数量很大的均匀时间间隔，并以求解的动力学模型在每个间隔内进行对应温度条件下奥氏体体积分数的求解并顺次叠加，以模拟得到的奥氏体转变时间和转变温度等作为依据，该模型有良好的表现性。结论 对42CrMo非等温且加热速度不恒定的连续奥氏体转变过程，JAMK模型拟合表现良好，采用文中求解的参数组对表面感应淬火的奥氏体转变历程进行仿真预测是可行的。     

T7钢在奥珠转变中富碳的分布研究

综合运用全自动相变仪,扫描电镜及电子探针技术研究了成分已均匀化的Ｔ７钢在珠光体转变温度范围等温所形成的先共析铁素体周围奥氏体中的碳分布。发现先共析铁素体周围存在有富碳奥氏体薄层,且此富碳奥氏体薄层中的碳分布并非都是 ;此一富碳奥氏体薄层的特征与随后转变所变形成的珠光体及马氏体形态相关。     

Dynamic Phase Transformation and Spheroidization of Cementite of Hypereutectoid Steel Containing Aluminum during Deformation

利用Gleeble 1500热模拟试验机进行单轴热压缩实验, 研究了合金元素Al对过共析钢缓冷相变和 过冷奥氏体动态相变组织的影响. 结果表明: 在缓冷相变时, Al的加入抑制网状渗碳体形成, 细化珠光体 片层间距; 在过冷奥氏体形变过程中, 动态转变经历动态相变和相变所得珠光体中渗碳体球化及铁素体动 态再结晶等过程. 在动态相变过程中, 没有形成晶界网状渗碳体, 而直接产生珠光体. Al的加入使动态相变过程中奥氏体的稳定性提高、珠光体转变推迟, 进一步细化了珠光体片层间距. 在相变所得珠光体中渗碳体球化及铁素体动态再结晶的过程中, Al阻碍渗碳体粗化, 使渗碳体颗粒和铁素体晶粒尺寸细化.     

Pearlite to austenite transformation in an Fe–2.6Cr–1C alloy

The mechanism of austenite formation, the kinetics of cementite lamellae dissolution and the crystallography of the austenitization from pearlite have been studied in an Fe–2.6 wt% Cr–0.96 wt% C alloy. Austenite grains nucleate after rather long incubation time both at pearlite colony boundaries and at the ferrite/cementite interfaces within a pearlite. Characteristic morphologies of transformation products were observed at various stages of transformation. Particular attention was paid to the structural evolution close to the α/γ interfaces. No indications of the diffusion ahead of the α/γ interface were found. The kinetics of austenite growth is controlled initially by carbon diffusion but in later stages by chromium diffusion. The results are discussed by assuming local equilibrium at the moving interfaces with the software and database ThermoCalc. The method involves the driving force determination for the diffusion of carbon and substitutional element during austenitization. The orientation relationships between ferrite, martensite and cementite were also determined. The possible austenite orientations were evaluated assuming the α/θ, α/γ and γ/θ orientation relationships so far obtained.     

Mathematical model for austenitization kinetics of ductile iron

A mathematical model was developed in the current study to understand the progress of austenitization process in ductile irons. The austenitization time required to produce homogeneous austenite in a two-phase region of austenite and graphite has been estimated in terms of (a) time required for transformation of matrix to austenite and (b) time required for dissolution of graphite in austenite to attain uniform carbon content, which remains in equilibrium with graphite. The time required been related to the structural parameters of cast ductile iron-like radius of graphite nodule, radius of austenite cell, volume fraction of graphite, volume fraction of ferrite in cast matrix, and diffusion constant. The model was used to determine the minimum austenitization time required to achieve homogeneous austenite in three commercial ductile irons when austenitized at a temperature of 900 °C. The results were compared with those obtained. The uniformity of the carbon content in austenite of ductile iron was verified indirectly by measuring microhardness.     

Coupled thermodynamic/kinetic analysis of diffusional transformations during laser hardening and laser welding

Several important industrial material processes, such as welding and surface treatments with high energy beams, incorporate rapid thermal cycles characterized by high heating/cooling rates and short dwell times. Computational simulation of the evolution of microstructure under these extreme conditions has received rather limited attention. With the advent of modern computational tools regarding alloy thermodynamics and kinetics, it is possible to simulate the progress of diffusional phase transformations and thus to predict microstructural development. In the present work, moving boundary diffusion problems have been simulated for two cases. In the first case the rapid austenitization during laser transformation hardening of a hypoeutectoid steel was examined. The effects of heating rate, maximum temperature, dwell time and initial microstructure fineness were analyzed. In the second case the aging, dissolution and coarsening of strengthening precipitates in the heat affected zone of laser welds in Al–Mg–Si alloys was examined. The simulation provided the variation of the volume fraction and average size of the strengthening phase during the weld thermal cycle. In both cases the calculations were performed by applying the coupled thermodynamics and kinetics approach, incorporated in the DICTRA program. This kind of simulation provides useful information for the design of the above processes.     

Recrystallization and the possibility of the realization of the α-γ diffusionless transformation during the ultrarapid laser heating of steels

Analysis is given of phase and structural transformations occurring upon ultrarapid laser heating in steels with different initial structures, namely, after annealing, after preliminary quenching, quenching and tempering, and after quenching with subsequent deformation and tempering. It is shown that a significant suppression of diffusion processes occurs during laser heating; this circumstance substantially affects the nature of the phase and structural transformations proceeding during laser processing. Special attention is given to studying the process of recrystallization and to the phenomenon of structural heredity during laser heating. The process of recrystallization during laser heating is considered as consisting of two stages, namely, an ordered lattice rearrangement (α-γ transformation) and the recrystallization of austenite that suffered phase-transformation-induced hardening (“phase naklep”). The effect of tempering and plastic deformation on the recrystallization of a preliminarily quenched steel consists in the intensification of the second stage, i.e., of the recrystallization of the transformation-hardened austenite. It is shown that the α-γ transformation during the laser heating of steels with the initial structure of lath martensite occurs by the “mechanism of recovery,” i.e., via the formation and growth of austenite nuclei. In steels with the initial structure of pearlite, the nucleation of austenite during laser heating can occur by a shear martensite-like diffusionless mechanism with the observance of characteristic orientation relationships between the initial ferrite and the newly formed austenite.     

钢中珠光体相变机制的研究进展

简要总结了钢中珠光体相变的机制，特别是珠光体形核的晶体学和长大的动力学。基于形核时的最小形核能和渗碳体与铁素体“合作”生长的要求，珠光体通常在奥氏体晶界形核并只向某一晶粒内生长，因而晶界珠光体与相邻晶粒存在特定取向关系而与生长进入的晶粒无特定取向关系。晶体学研究表明，珠光体形核的领先相与碳浓度及渗碳体与铁素体间的取向关系(分别为Pitsch-Petch、Bagaryatsky或lsaichev)无关。最近的研究发现，具Bl结构的非共格杂质粒子界面是过共析钢中晶内珠光体形核的有效位置，初步的结果表明，晶内珠光体形核的原因在于杂质粒子生长造成的局部区域碳贫化及低能的珠光体，杂质界面取代高能的奥氏体，杂质界面。特定过冷度下的层片间距与正向界面推移速率的关系是珠光体生长动力学的主要问题。基于珠光体与奥氏体间的无序界面假设和稳态扩散方程分别发展了以体扩散控制和以界面扩散控制为主的动力学理论。两种理论均与实验结果符合较好，但后者似更合理。最近的实验在珠光体中发现了生长台阶与结构台阶，表明生长动力学方程需要修正。     

采用定量金相法分析亚共析钢拉拔变形中先共析铁素体应变量

采用定量金相法分析计算了亚共析钢拉拔变形中先共析铁素体应变量。结果表明，拉拔变形初期先共析铁素体应变量增大趋势远高于珠光体应变量；当应变量达到一定程度ε≈1．0时，两者同步增长，但最终先共析铁素体应变量仍远大于珠光体应变量。     

THEORETICAL PREDICTION OF PROEUTECTOID FERRITIC TRANSFORMATION IN HYPO-PROEUTECTOID STRUCTRAL STEELS

1.IntroductionInordertodevelopnewtypeofsteels,itisveryimportanttoderiveamuchgeneralruleoftheaustenitedecompositionfromexperimentaldataofknownsteels.Recently)someworkhasmadeencouragingprogressinthisfieldtl--6].Butdifficultiesandsuspicionsarestillobyiousbecausethethermodynamicaldataofmulticomponelltsteelarescatteredanddisordered.PuremathematicalsimulationmaybeusedtocalculateTTTandCCTc...es[4],butithasapremisethatsomespecialpointsofTTTcurvessuchasthenosepointmustbeknowninadvance,whichprevents…     

TiNbV微合金钢焊接接头HAZ晶粒长大及相变原位观察

采用激光共聚焦显微镜原位观察方法，研究了大热输入用TiNbV微合金钢在模拟焊接热循环作用下焊接热影响区(HAZ)晶粒长大过程及相变的规律. 热循环过程中加热温度升高至860 ~ 980 ℃时，发生由铁素体和珠光体向奥氏体的转变，1 100 ℃时，奥氏体晶粒开始有明显长大的趋势，1 300 ~ 1 400 ℃时，晶粒以合并长大方式迅速长大；冷却过程中温度降低至1 400 ~ 1 350 ℃时，晶粒以晶界迁移方式缓慢长大，660 ~ 580 ℃时，发生奥氏体迅速向贝氏体转变，焊接HAZ主要由贝氏体与铁素体组成，贝氏体的尺寸是由奥氏体晶粒大小决定的. 热循环高温停留时间延长，奥氏体与贝氏体的形成、终了、转变温度区间均有下降. 结果表明，组织中先共析铁素体含量先降低后增加，贝氏体含量降低，多边形铁素体消失，先共析铁素体含量增加，冷却组织趋于均匀粗大. 焊接过程中，选择合适的高温停留时间可提高组织中IAF的含量，提高力学性能.     

冷速对过冷奥氏体稳定性的影响

分别测定了冷速对奥氏体稳定性不同的五种钢种先共析铁素体、珠光体、贝氏体等温转变孕育期以及TTT曲线的影响,并对所得结果给出理论解释。     

强磁场对硅锰铸钢等温珠光体粒化的影响

对硅锰铸钢在相变温度(A1)附近进行等温处理的研究表明,经磁场处理后的试样组织中存在更多的粒状珠光体组织。此粒状珠光体由两部分构成:一部分来自块状铁素体中直接析出粒状的不连续渗碳体;一部分来自等温过程中片状渗碳体的熔断。磁场通过促进铁素体的形核与长大,使较多的碳原子"陷落"在铁素体内以沉淀析出方式形成粒状渗碳体,处理温度越低,此作用越明显。此外,磁场下珠光体组成相磁致伸缩率存在差异,引起珠光体两组成相之间的应变能变化,有利于渗碳体以球状析出于奥氏体或铁素体中,也对粒状珠光体分数的增加作出贡献。     

SWRCH35K钢连续冷却转变曲线的测定与分析

使用DIL805A热膨胀仪测定了SWRCH35K钢的热膨胀曲线。采用切线法结合微观组织及硬度,绘制了试验钢的连续冷却转变(CCT)曲线,分析了冷却速率对试验钢连续冷却过程组织演变的影响。结果表明,冷速在0.1～1℃/s范围时,试验钢的组织为多边形先共析铁素体和珠光体,随着冷速增加,组织细化,珠光体含量增加,硬度为148～165 HV;冷速为3℃/s时,开始出现少量魏氏组织及贝氏体,硬度增加至189 HV;冷速为5～50℃/s时,铁素体沿晶界呈网状,针状魏氏组织增加,组织为晶界铁素体、珠光体、魏氏组织和贝氏体,其中冷速为30～50℃/s时,铁素体含量大幅减少且尺寸明显减小,硬度为225～237 HV。珠光体在不同冷速下的形态不同,冷速较小时以片层及短棒状为主,还有少量球状,随着冷速增加,短棒状珠光体占比增加,片层及球状珠光体占比减小。     

中碳钢过冷奥氏体形变过程中碳的分布与扩散

利用热模拟压缩变形实验以及SEM、XRD和热磁法,研究了中碳钢过冷奥氏体变形时组织演变过程中碳原子的分布与扩散.结果表明,动态相变过程中碳的有效扩散系数与等温过程相比明显增大,相变完成时间显著缩短.在随后的片层状珠光体的球化过程中,相界以及形变过程中产生的高密度位错和空位等缺陷促进了间隙碳原子的扩散,使得球化动力学过程与等温退火相比显著缩短.渗碳体的溶解和铁素体中碳的过饱和现象得到证实,其中过饱和碳原子高度聚集在铁素体晶界和位错核心处,而不是均匀地分布在铁素体点阵的间隙位置.     

脉冲电流辅助热处理对EA4T车轴钢带状组织的影响

对EA4T车轴钢试样分别在奥氏体化保温以及冷却相变过程通入脉冲电流,对不同冷却速度下的组织变化进行研究。试验表明：在脉冲电流的作用下,EA4T钢带状组织能够在一定程度上得到抑制。脉冲电流能促进奥氏体状态下的碳原子及合金元素的扩散,同时也能在相变过程中抑制先共析铁素体的形核,消除带状组织。     

Micro-scale Cellular Automaton Modeling of Interface Evolution During Reaustenitization from Pearlite Structure in Steels

A modified cellular automaton model is developed to depict the interface evolution inside the cementite plus ferrite lamellar microstructures during the reaustenitization of a pearlite steel. In this model, migrations of both the austenite–ferrite and austenite–cementite interfaces coupled with the carbon diffusion and redistribution are integrated. The capillarity effect derived from local interface curvatures is also carefully considered by involving the concentration given by the phase diagram modified by the Gibbs–Thomson effect. This allows the interface evolution from a transient state to a steady state under different annealing conditions and various interlamellar spacings to be simulated. The proposed cellular automaton approach could be readily used to describe the kinetics of austenite formation from the lamellar pearlites and virtually reveal the kinematics of the moving interfaces from the microstructural aspect.