冷轧及中间退火过程中GH4700镍基合金管组织演变规律研究

利用光学金相显微镜研究了GH4700合金在冷轧以及中间退火过程中的组织演变规律,建立了中间退火过程中再结晶晶粒长大方程。实验结果表明:随着冷轧变形量增大,晶粒的变形均匀性逐渐变好,GH4700合金的屈服强度和抗拉强度增大,延伸率降低;当退火温度为1130℃、保温时间为15min时,组织发生完全再结晶且分布均匀,是较合适的一次冷轧中间退火工艺;所建立的晶粒长大模型预测结果与试验值吻合较好。     

脉冲电流处理对冷轧态GH3030合金再结晶组织性能的影响

目的 探究不同工艺参数下脉冲电流处理对冷轧态GH3030合金静态再结晶组织的影响.方法 利用电子背散射衍射(EBSD),探究脉冲电流处理(EPT)和常规退火处理(CHT)对GH3030合金静态再结晶的影响.探究了两种热处理方式下不同退火温度和时间对冷轧态GH3030合金静态再结晶体积分数、晶粒尺寸以及硬度的影响,计算两种热处理方式下不同工艺参数的静态再结晶动力学方程与激活能.结果 与常规退火处理相比,脉冲电流处理可以快速提高冷轧态GH3030合金的静态再结晶体积分数,并且得到了尺寸更加均匀的晶粒,而脉冲电流处理的合金其硬度值均小于相同条件下常规退火处理的合金.根据静态再结晶动力学方程的结果可知,脉冲电流处理的合金再结晶激活能低于常规退火处理的合金,脉冲电流处理下发生完全再结晶所需时间远远少于常规退火处理下所需时间.结论 脉冲电流处理促进了冷轧GH3030合金静态再结晶行为,并且加速了再结晶晶粒的成核和长大,但脉冲电流处理对改善GH3030合金的硬度效果不明显.     

镍基合金的热变形行为及智能热加工技术研究进展

镍基合金具有优异的高温强度,良好的抗疲劳、抗氧化和抗腐蚀性能,是目前航空航天领域内应用最为广泛的金属材料之一,已成为航空发动机热端部件不可替代的关键材料.镍基合金的高温变形抗力大、成形温度范围窄、微观组织演变复杂,给镍基合金零件的成形制造带来了巨大挑战.综述了近年来镍基合金的高温流变规律及建模、微观组织演变规律与建模、热加工工艺优化、热处理调优等方面的研究进展,讨论了镍基合金零件的智能加工技术发展现状,并展望了镍基合金及其零部件成形技术的发展趋势.获得如下重要结论:镍基合金的高温流变行为表征模型主要有唯象学本构模型、基于物理机制的本构模型和智能本构模型;镍基合金在塑性变形过程中的微观组织演变主要包括动态再结晶、亚动态再结晶、静态再结晶和晶粒长大行为;通过优化的锻后热处理工艺,可以减小组织的混晶程度;在镍基合金高温流变行为的本构描述与微观组织预测建模方面,还需深度挖掘成形工艺-微观组织-性能之间的映射规律,为镍基合金零件的高温成形工艺优化提供理论依据.     

径锻AZ61镁合金退火后晶粒长大及组织演变规律

目的 通过研究径锻AZ61镁合金棒材在后续退火处理时的晶粒长大和组织均匀性演变行为,构建等温条件下径锻AZ61镁合金晶粒长大模型,总结径锻镁合金退火后组织均匀性演变规律,为此棒材后续热处理工艺的制定提供理论借鉴和指导。方法 基于系统的等温正交退火试验,量化统计各退火条件下样品组织的平均晶粒尺寸和晶粒尺寸分布,分析径锻AZ61镁合金棒材的晶粒长大行为和组织均匀性演变规律。结果 退火后,径锻AZ61镁合金组织中晶粒趋于长大。在250~300 ℃温度区间内,晶粒长大速度较为缓慢。随着退火温度的升高,晶粒长大速率随之上升,尤其是退火温度升高到450 ℃以后,晶粒长大速率显著增大。当退火温度一定时,退火起始30 min内,晶粒快速长大。在之后的长时间退火过程中,晶粒长大速度逐渐放缓。同时,随着退火的进行,锻后样品中存在的超细晶条带状组织逐渐消失,样品组织均匀性显著提高。结论 通过研究晶粒长大现象构建的等温条件下径锻AZ61镁合金晶粒长大模型与试验结果拟合良好。结合组织均匀性演变规律,径锻AZ61镁合金退火后的组织状态能够被很好地预测。     

GH3028镍基合金的热变形动态再结晶及微观组织演变

目的 研究GH3028镍基合金动态再结晶过程中的晶粒尺寸变化情况,明晰微观组织形貌的演变规律。方法 利用DST3000PC型动态热模拟实验机,在温度为1 050~1 300 ℃、应变速率为1×10^?3~1×10^?1 s^?1、最大应变量为58%的条件下对GH3028镍基合金进行热压缩实验,通过构建动态再结晶和晶粒尺寸演变数值计算模型并结合实验进行验证。结果 峰值应力随温度的上升而有所下降,在1 050~1 300 ℃温度范围内,温度越高,合金试样越容易趋于稳态,动态再结晶特点越为明显。通过对实验数据进行优化和拟合,根据峰值应力值计算出热变形激活能Q为516 kJ/mol,进而求解出热变形方程。建立动态再结晶模型及晶粒尺寸模型,观察动态再结晶过程中的微观组织,发现当温度、应变速率不变时,动态再结晶的体积分数随应变量的增大而增大。温度的提升会显著增大动态再结晶体积分数和动态再结晶晶粒尺寸。晶粒尺寸受温度和应变速率的双重影响逐渐趋于稳态变化。结论 通过对模型预测值与实际实验数据进行对比,发现该模型可以实现对晶粒尺寸变化的预测,模型预测平均晶粒尺寸与实验平均晶粒尺寸的相对误差为2.36%,说明该模型对动态再结晶晶粒尺寸的控制具有指导意义。     

Inconel 718镍基高温合金热加工动态再结晶建模与计算

目的 建立Inconel 718镍基合金动态再结晶组织演变三维介观尺度计算模型.方法 采用Gleeble-1500型热力模拟试验机进行恒温恒应变速率压缩实验,获得Inconel 718高温合金热变形的真应力-应变曲线,并结合光学显微镜分析热变形后的材料的塑性流动规律与组织演化特征,获得材料参数.结果 基于流变和组织行为的分析,建立了考虑动态再结晶特征的组织演变三维元胞自动机模型.结论 该模型可以较准确地描述材料的热变形行为,追踪热变形过程再结晶晶粒的演变,为实际零件的锻造工艺制定提供宏微观计算依据.     

不同压下率低碳铝镇静钢板再结晶实验研究

将不同冷轧压下率的低碳铝镇静钢进行不同保温温度和时间的退火再结晶实验研究,利用维氏硬度计、金相显微镜和X射线衍射仪研究了退火后试样的硬度、金相显微组织及织构的变化情况。结果表明:在相同的退火工艺制度条件下,随着冷轧压下率的增加,再结晶开始和结束温度降低,晶粒尺寸减小。当冷轧压下率升高到68%后,冷轧压下率的增加对再结晶晶粒细化的作用减弱,甚至没有细化作用;680℃保温退火时,一开始就发生了再结晶,基本不需要孕育期。随着保温时间的延长,晶粒均匀长大,晶粒饼形程度增加;退火温度由660℃升高到720℃时,{111}面有利织构增加,{100}面不利织构减少,720℃退火温度较为适宜。冷轧压下率为58%的试样在760℃退火时发生了二次再结晶对实验钢板的力学性能产生不利影响。     

低温薄规格取向硅钢初次再结晶组织对二次再结晶行为的影响

取向硅钢成品带材具有锋锐的Goss织构,其前提是需要保证在高温退火过程中能发生完善的二次再结晶,而合适的初次再结晶组织是发生二次再结晶的关键要点之一,探索初次再结晶组织对二次再结晶行为的影响具有重要的研究意义。分析了低温薄规格取向硅钢在不同脱碳退火时间条件下的初次再结晶组织,并研究了初次再结晶组织对二次再结晶行为的影响规律。结果表明:在脱碳退火温度880℃条件下,最佳退火时间约为3 min,此时高温退火可发生完全二次再结晶。延长脱碳退火时间,初次再结晶组织平均晶粒尺寸增大,导致二次再结晶不完善,高温退火后出现"细晶"组织。二次再结晶不稳定很大程度是初次再结晶组织中心层的{100}〈025〉取向晶粒长大所致,最终未发生二次再结晶的"细晶"组织也多为{100}〈025〉取向。     

热变形镁合金退火显微组织的定量研究

对热变形AZ31镁合金的显微组织、晶粒尺寸分布、平均晶粒尺寸、再结晶晶粒数目以及变形织构随退火时间的变化进行了定量分析,研究了不同热变形量AZ31镁合金在503 K的等温退火行为。结果表明:热变形AZ31镁合金的细晶组分随着退火时间的延长不断降低,退火过程按退火温度可分为孕育、再结晶急速长大和晶粒正常长大三个阶段,且各阶段的其长短几乎不受变形程度的影响。变形形成的微观织构在整个退火过程中几乎没有变化,说明热变形镁合金在退火过程中没有新核形成,即为连续静态再结晶。     

轧制ZK61镁合金板材晶粒长大行为

通过对热轧的ZK61镁合金板材试样分别进行不同温度和不同保温时间的退火实验,利用金相显微镜(OM)观察显微组织,对晶粒尺寸进行分析和处理,并建立数学模型,系统研究了轧制ZK61镁合金的晶粒长大行为。研究结果表明,晶粒尺寸随着退火温度的升高与退火时间的延长而粗化,退火温度对晶粒长大的影响比退火时间的影响明显。对于ZK61镁合金在250~450℃温度区间的晶粒长大过程,其晶粒尺寸与加热时间的关系可用Beck方程D~n-D_0~n=kt描述,其中k=k_0exp[-Q_g/(RT)]。计算可得晶粒长大指数n为3.5,长大激活能Qg为45kJ/mol。     

Methods and mechanisms for uniformly refining deformed mixed and coarse grains inside a solution-treated Ni-based superalloy by two-stage heat treatment

The uniform refinement mechanisms and methods of deformed mixed and coarse grains inside a solution-treatment Ni-based superalloy during two-stage annealing treatment have been investigated.The two-stage heat treatment experiments include an aging annealing treatment(AT)and a subsequent recrystallization annealing treatment(RT).The object of AT is to precipitate some δ phases and consume part of storage energy to inhibit the grain growth during RT,while the RT is to refine mixed and coarse grains by recrystallization.It can be found that the recrystallization grains will quickly grow up to a large size when the AT time is too low or the RT temperature is too high,while the deformed coarse grains cannot be eliminated when the AT time is too long or the RT temperature is too low.In addition,the mixed microstructure composed of some abnormal coarse recrystallization grains(ACRGs)and a large number of fine grains can be observed in the annealed specimen when the AT time is 3 h and RT tem-perature is 980℃.The phenomenon attributes to the uneven distribution of δ phase resulted from the heterogeneous deformation energy when the AT time is too short.In the regions with a large number of δ phases,the recrystallization nucleation rate is promoted and the growth of grains is limited,which results in fine grains.However,in the regions with few δ phases,the recrystallization grains around grain boundaries can easily grow up,and the new recrystallization nucleus is difficult to form inside grain,which leads to ACRGs.Thus,in order to obtain uniform and fine annealed microstructure,it is a prereq-uisite to precipitate even-distributed δ phase by choosing a suitable AT time,such as 12 h.Moreover,a relative high RT temperature is also needed to promote the recrystallization nucleation around δ phase.The optimal annealing parameters range for uniformly refining mixed crystal can be summarized as:900℃×12 h+990℃×(40-60 min)and 900℃×12 h+1000℃×(10-15 min).     

Recrystallization of the ODS superalloy PM-1000

The primary recrystallization of a 1 0 0-fiber textured coarse-grained oxide dispersion strengthened nickel-based superalloy (PM-1000) has been investigated by high-resolution electron backscatter diffraction. The annealing behavior of this alloy is quite complex. Even at high annealing temperatures (e.g. 1200 °C), recrystallization is only partial. The microstructure of this superalloy in the annealed state consists of a blurred subgrain structure, coarse grains with sizes of about 10–20 μm at the pre-existing grain boundaries and a significant fraction of small crystals in the interior of the recovered grains. These small grains are elongated and display anisotropic growth. In the present paper we present a detailed explanation for this peculiar microstructure. Particular focus is placed on the origin of the new grains in the recovered structure in a [1 0 0]-oriented grain.     

Dynamic recrystallization behavior of a typical nickel-based superalloy during hot deformation

The dynamic recrystallization (DRX) behavior of a typical nickel-based superalloy is investigated by the hot compression tests. Based on the conventional DRX kinetics model, the volume fractions of DRX are firstly estimated. Results show that there is an obvious deviation between the experimental and predicted volume fractions of DRX when the forming temperature is below 980 °C, which is induced by the slow dynamic recrystallization rate under low forming temperatures. Therefore, the segmented models are proposed to describe the kinetics of DRX for the studied superalloy. Comparisons between the experimental and predicted results indicate that the proposed segmented models can give an accurate and precise estimation of the volume fractions of DRX for the studied superalloy. In addition, the optical observation of the deformed microstructure confirms that the dynamically recrystallized grain size can be well characterized by a power function of Zener–Hollumon parameter.     

退火工艺参数及母材性能对取向硅钢超薄带磁性能的影响EI北大核心CSCD

采用EBSD技术对不同退火工艺处理后的冷轧取向硅钢超薄带样品进行研究,分析退火样品的显微组织、织构与磁性能的关系,讨论母材性能对超薄带性能的影响。结果表明:冷轧超薄带的退火组织均匀、Goss取向度高以及母材磁性能优良均可有效提升磁性能;退火升温速率主要影响晶粒尺寸、Goss取向度及磁性能;再结晶的平均晶粒尺寸改变,会影响最终超薄带的磁感应强度及铁损;在900℃退火5 min以上会明显发生再结晶,10~30 min内退火的超薄带磁性能变化较小,退火15 min获得最佳磁性能。此外,在1000℃及1100℃下退火的时间均不宜超过10 min,否则会恶化磁性能。     

Recrystallization behaviour during annealing of cold-rolled Cu–5Fe–2Sn alloy

The recrystallization behaviour during annealing of cold-rolled Cu–5Fe–2Sn alloy was clarified in this paper. The effects of annealing temperature and time on the microstructure and properties of the Cu–5Fe–2Sn alloy were investigated. The equations of electrical conductivity and recrystallization kinetics during annealing were obtained with Martition's rule and Avrami empirical formula. The variations of recrystallization volume fraction and the growth of recrystallization grain for Cu–5Fe–2Sn alloy after 40% cold rolling were discussed. The calculated conductivity and volume fraction of recrystallization have a good match with experimental results. The variations of the properties of annealed Cu–5Fe–2Sn alloy are attributed to the growth rate of recrystallization phase and the size of recrystallization grains.     

In-situ scanning electron microscopy studies of small fatigue crack growth in recrystallized layer of a directionally solidified superalloy

The small fatigue crack behavior in the surface recrystallized layer of a nickel-based directionally solidified superalloy DZ4 was studied by in-situ scanning electron microscopy. Transgranular cracking manner was identified at 350 °C, distinct from the intergranular fracture of recrystallized grains reported formerly. The transition of fracture mode is attributed to the effect of temperature, which should be particularly concerned in the safety of turbine components with recrystallization. The discontinuous crack growth in recrystallized layer is associated with the local microstructure. Carbide can act as crack source, and barrier to the crack growth as well. Effect of twin boundary on impeding the fatigue crack is evident.     

Competition between recovery and recrystallization in two tungsten supplies according to ITER specifications

In thermonuclear fusion devices, tungsten, implemented as armour material of plasma facing components, is in direct contact with the plasma. Due to high heat flux (20 MW/m\(^{2}\) ), a premature cracking can be observed in relation with the loss of tungsten mechanical properties. It is usually attributed to two competing restoration processes: recovery and recrystallization. A recent investigation on two tungsten supplies according to ITER specifications has highlighted that hardness abatement at high temperature leads to overestimate the recrystallization fraction, which may be a consequence of the significant contribution of recovery during annealing. The present article aims at investigating this phenomenon through the use of a dedicated mean field recrystallization model that, unlike JMAK models, accounts for physical parameters at the microstructure scale such as recovery parameter or grain boundary mobility. The methodology is applied on the two tungsten supplies for ITER. It allows discriminating, for the first time, the respective contributions of recovery and recrystallization to the macroscopic softening in the high temperature range (from 1450 to \(1800\,^{\circ }{\text {C}}\)) and annealing times (0–3500 s). The approach has led to the conclusions that the two supplies merely differ from their initial (delivery) state through the stored energy, the initial recrystallized fraction and the grain size but not from intrinsic physical parameters such as recovery parameter or grain boundary mobility.