Nb-Ti连铸坯热芯大压下轧制动态再结晶行为研究

采用热模拟单道次压缩实验,研究了Nb-Ti连铸坯热芯大压下轧制中动态再结晶行为及奥氏体晶粒转变规律。结果表明,变形温度越高,应变速率越低,发生动态再结晶的临界应变值越小,动态再结晶越充分。在变形温度1 350 ℃,继续增加应变至0.8和增加应变速率至10 s^-1,奥氏体晶粒尺寸并未得到进一步细化,反而较应变0.5和应变速率5 s^-1下的奥氏体晶粒更加粗大。这是因为高温粘塑性区的金属晶间粘性流动增加,位错增殖速度增大,在动态再结晶过程中会重新形成新的无畸变再结晶晶粒,这些新的无畸变晶粒的亚动态再结晶动力学极快,在较大驱动力下使奥氏体晶界快速迁移,从而使奥氏体发生一定程度的粗化。     

楔横轧不同变形阶段的微观组织演变分析

运用三维刚塑性有限元DEFORM-3D软件对GH4169合金零件的楔横轧成形进行变形、传热、微观组织演变的耦合数值模拟,揭示轧件在楔横轧成形过程中各个变形阶段(楔入段、展宽段和精整段)微观组织的演变规律,分析轧件平均晶粒尺寸在不同变形阶段变化的具体原因。结果表明,楔横轧成形GH4169合金轧件时,虽然温度低、应变率高,但楔横轧特有的大变形仍能使动态再结晶发生并完成,从而得到细小均匀的晶粒组织;轧件晶粒的细化程度随断面收缩率的增大而增大;轧件在高温下主要发生晶粒长大,因此减小精整段的长度以及缩短进入下道工序的时间,可以避免粗晶的产生,提高成形件的综合力学性能。     

两种连续局部塑性成形工艺对锻件微观组织的影响

通过模拟分析与实验分析结合的方法,验证连续局部塑性成形微观组织演变有限元模型的正确性,采用该模型对42CrMo钢坯料辊锻过程中的组织晶粒度进行预报,研究42CrMo钢辊锻过程的奥氏体晶粒尺寸演化规律;对楔横轧变形过程中组织晶粒度变化进行研究,并对两种连续局部塑性成形后锻件组织晶粒度进行对比。研究结果表明,辊锻变形坯料P1、P2、P3处奥氏体晶粒尺寸实验结果与有限元预报结果吻合良好,晶粒尺寸变化为动态再结晶细化;楔横轧变形过程中,动态再结晶和奥氏体晶粒长大作用同时发生;通过对两种连续局部塑性成形得到的锻件微观组织进行比较,楔横轧锻件整体平均晶粒尺寸更加细小、均匀。     

Nb-Ti连铸坯热芯大压下轧制动态再结晶行为研究

采用热模拟单道次压缩实验，研究了Nb-Ti连铸坯热芯大压下轧制中动态再结晶行为及奥氏体晶粒转变规律。结果表明，变形温度越高，应变速率越低，发生动态再结晶的临界应变值越小，动态再结晶越充分。在变形温度1 350 ℃，继续增加应变至0.8和增加应变速率至10 s^-1，奥氏体晶粒尺寸并未得到进一步细化，反而较应变0.5和应变速率5 s^-1下的奥氏体晶粒更加粗大。这是因为高温粘塑性区的金属晶间粘性流动增加，位错增殖速度增大，在动态再结晶过程中会重新形成新的无畸变再结晶晶粒，这些新的无畸变晶粒的亚动态再结晶动力学极快，在较大驱动力下使奥氏体晶界快速迁移，从而使奥氏体发生一定程度的粗化。     

GCr15钢动态组织演化的实验研究与数值模拟

通过在Gleeble-3800热力模拟实验机上进行单道次压缩试验,分析了GCr15钢的动态组织演化特点。实验结果表明,变形试样组织分布不均匀;在一定应变速率下,温度升高,动态再结晶晶粒增大,且应变速率越高,增长趋势越慢;在一定温度下,升高应变率会使动态再结晶晶粒变小,但这种趋势在较高的温度下才比较敏感。通过回归分析,得到了GCr15的动态组织演化模型,将其耦合到MSC.Marc软件子程序中计算,模拟了应变、动态再结晶份数及平均晶粒尺寸分布。模拟的晶粒尺寸和测量晶粒尺寸吻合较好。     

淬硬GCr15钢在高温和高应变率下的动态再结晶动力学模型

为得到淬硬GCr15钢在高温和高应变率下的动态再结晶动力学模型,采用分离式霍普金森压杆,在20~800 ℃的温度范围和2000~8000 s-1的应变率范围内,对淬硬GCr15钢（55 HRC）进行动态压缩力学性能试验,得到应力应变曲线。对试验数据进行拟合,得到了淬硬GCr15钢的临界应力和峰值应变模型、动态再结晶激活能以及建立了动态再结晶晶粒尺寸模型。并对晶粒尺寸模型进行了试验验证,结果表明建立的晶粒尺寸模型较为精确。     

磨粒强化加工表面材料动态再结晶行为的研究

目的 基于磨粒强化加工非线性热力耦合效应,研究加工表面材料动态再结晶行为.方法 以45#钢为研究对象,首先建立基于砂轮轮廓及磨粒分布特征的热力耦合全尺度有限元模型,然后利用三维元胞自动机法,构建奥氏体晶粒的位错密度增长控制方程,研究动态热力耦合作用对奥氏体晶粒动态再结晶过程的影响机理.最后,结合磨粒强化加工实验,验证不同进给速度与磨削深度下再结晶晶粒尺寸与体积分数的沿层变化规律,提出加工表面材料晶粒细化过程的参数化控制方法.结果 加工过程中,部分奥氏体组织会发生动态再结晶现象,并在工件表面形成细化层,细化层的厚度远小于强化层.随着与表面距离的增加,再结晶晶粒平均尺寸逐渐增大,体积分数先增大、后减小.改变磨削深度和进给速度,可使再结晶晶粒的体积分数和平均尺寸分别提高5倍和15％以上.结论 通过对比实验与模拟结果,发现加工过程中热力耦合效应沿层分布差异性明显.加工应变场的作用效果远小于动态温度场的影响,这限制了表面细化层的厚度;应变场沿层递减分布,越靠近加工表面,晶粒细化现象越明显;受层间应变与应变率差异性的影响,表层再结晶晶粒形核较快,但生长速度缓慢,再结晶晶粒体积分数偏小.增大切深与进给速度会使接触区金属的去除量增加、表面温度升高且晶粒畸变现象明显,有利于细化层的形成.     

压下变形参数对超高强钢再结晶规律的影响

以一种超高强钢为研究对象,对其进行了热力学计算分析和热模拟压下实验,采用金相组织和扫描形貌分析等手段,研究了压下变形参数对超高强钢再结晶的影响规律。研究结果表明：变形速率越大,变形温度越低,实验钢动态再结晶越不容易发生;变形温度为950 ℃,变形速率为0.1 s-1时,真应变为0.1,奥氏体晶粒尺寸为6524 μm;真应变为05时,稳态连续再结晶形成的奥氏体沿着原来奥氏体向晶内长大,尺寸较为均匀,晶粒细化到4821 μm;真应变为08时,发生非连续再结晶,晶粒细化到3045 μm,呈现多边形等轴状。     

65Mn钢的动态再结晶行为

采用Gleeble-3500热模拟试验机对65Mn钢进行热压缩试验,变形温度850~1150℃、应变速率0.02~20 s~(-1),最大真应变1.0,研究材料在上述试验条件下的动态再结晶行为,以及变形条件对再结晶晶粒尺寸的影响。结果表明:试验钢的真应力-真应变曲线在高温、低应变速率条件下出现明显峰值,随着温度的升高和应变速率的降低,临界应变变小,有利于动态再结晶发生;奥氏体再结晶晶粒尺寸与变形参数相关,应变速率降低,再结晶晶粒尺寸增大;变形温度降低,有利于再结晶晶粒尺寸细化。     

Fe-18Mn-0.6C TWIP钢的热变形行为

在Gleeble-3500热模拟实验机上通过单道次压缩实验,研究了变形温度、应变速率和变形量对TWIP钢流变应力和临界动态再结晶行为的影响规律。结果表明,试验TWIP钢热变形的峰值应力随温度的升高而降低,随着应变速率的增大而升高;各种变形条件下,TWIP钢的奥氏体晶粒尺寸有很大差异,随着变形温度的升高,再结晶晶粒粗化,而应变速率和应变量的增加有利于晶粒细化;最后采用线性回归方法计算出TWIP钢的热变形激活能为443.3 kJ/mol,并求出了该钢种动态再结晶临界条件与Z参数之间的关系,以及动态再结晶动力学规律。     

热连轧棒材变形过程模拟研究

应用刚塑性有限元法开发了轧制过程单道次变形分析的通用程序，与解析法结合对实际热连轧生产GCr15棒材的粗轧和中轧过程中的应变-应变速率进行了计算值与实际应变的对比。结果二者基本一致，但数值有一定偏差，为此分析了产生偏差的原因，预计该程序进一步完善后将可应用于实际工业生产中。     

石钢GCr15轴承钢再结晶规律研究

为实现奥氏体再结晶控制轧制，分析了变形量及变形温度对石家庄钢铁有限责任公司转炉生产的GCr15轴承钢再结晶规律的影响，确定了该钢的再结晶全图。并得出为避免出现混晶组织，GCr15钢的控制轧制应在完全再结晶区进行。     

Static recrystallization behavior of a martensitic heat-resistant stainless steel 403Nb

A static recrystallization behavior between the rolling passes of a martensitic heat-resistant stainless steel 403Nb has been studied by OM,TEM and double-hit thermo-mechanical simulator to explore the effects of deformation temperature,strain rate,strain and the prior austenite grain size. The results show that increases of deforma-tion temperature and strain rate and strain can promote the static recrystallization of 403Nb steel. Static recrystallization also proceeds faster when the prior austenite grain...     

控锻控冷工艺对GCr15轴承钢组织演变规律的影响

采用微观组织表征的方法对比研究了GCr15轴承钢在传统工艺和控锻控冷工艺下的组织和网状碳化物分布的演变规律,并统计和分析了不同工艺下的晶粒度和残留奥氏体含量的变化规律。结果表明,GCr15轴承钢经控锻控冷工艺处理后,GCr15钢中粒状珠光体组织相对更细小,淬回火组织基体中的C元素分布更为均匀,同时洛氏硬度提高0.7 HRC;残留奥氏体含量降低;碳化物颗粒尺寸细化,平均颗粒尺寸减小40%以上,同时抑制粗大碳化物网状的形成;可使奥氏体晶粒度细化2级以上。     

A new approach to predicting partial recrystallization in the multi-pass hot rolling process

An exploratory approach to handling partial recrystallization in multi-pass hot rolling where the heterogeneity of steel microstructures is inherent is presented. The proposed model is based on a modification of the conventional model in which the microstructure of deformed austenite at each pass is simply taken as homogeneous during the multi-pass rolling. The usefulness of the modified model is demonstrated by applying it to a four-pass oval-round (or round-oval) rod rolling sequence. The pass-by-pass recrystallized fraction and austenite grain size (AGS) computed from the modified model are compared with those from the conventional model. The result showed that in multi-pass rolling at higher rolling speed, the recrystallization behavior and evolution of the austenite grain size at a given pass was strongly influenced by the modeling method of the partial recrystallization attributed to microstructural heterogeneity.     

A study of the effect of the deformation parameters on recrystallization behavior in the rod rolling process

Rod rolling is a process in which the deformation of the workpiece between the work rolls is quite different from the rod drawing process, but the area strains (natural logarithm of area reduction ratio) multiplied by a constant have been used in the calculation of the pass-by-pass evolution of austenite grain size in rod (or bar) rolling without any verification. Considering that the deformation parameters (strain and strain rate) at a given pass play a crucial role in determining recrystallization behavior, the calculation method for the deformation parameters associated with rod rolling should be examined. In this study, a series of numerical simulations has been carried out using an area strain model [5] and an analytic model [6] which calculate the pass-by-pass strain in the rod rolling process, focusing on the effect of the calculation method for the pass-by-pass strain on the recrystallization behavior and evolution of AGS (austenite grain size) during a given pass. These have been investigated for a six-pass rolling sequence (oval-round or round-oval) designed for this study by incorporating the recrystallization and AGS evolution model being widely used in hot rolling. It was found that the recrystallization behavior and evolution of AGS during a given pass were significantly influenced by the calculation methods for deformation parameters. The area strain model lacks mathematical grounds to be used as input to the equations for recrystallization and AGS evolution.     

Structure and properties of low-alloy steels after controlled rolling

Conclusions To obtain the best combination of strength and toughness due to grain refining and controlled precipitation hardening with particles of carbonitride phase, controlled rolling is carried out in the lower range of the austenite region, followed by cooling at a certain rate. This treatment can be called high-temperature thermomechanical treatment for low-alloy steels. The effect of thermomechanical treatment (controlled rolling) increases as the initial and final rolling temperatures are lowered and the degree of deformation in the last passes is increased, and also with the addition of elements that inhibit the recrystallization of austenite (Nb, V, Ti).The effect of controlled rolling can be utilized most completely only for steels with carbonitride-forming elements that promote grain refining, inhibit recrystallization of austenite, and thus strengthen the steel due to precipitation hardening and increase its resistance to brittle fracture.I. P. Bardin Central Scientific-Research Institute of Ferrous Metallurgy. Translated from Metallovedenie i Termicheskaya Obrabotka Metallov, No. 12, pp. 2–11, December, 1975.