Mg-6.3Zn-0.7Zr-0.9Y-0.3Nd镁合金的高温塑性变形行为的热压缩模拟

采用Gleeble-1500热压缩模拟试验机进行压缩实验,研究ZK60(0.9Y+0.3Nd)镁合金在变形温度623～773K、应变速率0.001～1s-1的范围内的变形行为,计算应力指数和变形激活能,并采用Zener-Hollomon参数法构建合金高温塑性变形的本构关系。结果表明:在实验变形条件下,合金的真应力—真应变曲线为动态再结晶型;在实验温度范围内,应力指数随着变形温度的升高而增大,变形激活能随着变形温度和应变速率的增加而增大。对比ZK60合金,ZK60(0.9Y+0.3Nd)合金的变形激活能提高38%。     

挤压态ZK60镁合金的热压缩变形行为

为了研究挤压态ZK60镁合金的热变形行为,利用Gleebe-3500热模拟机在变形温度为523~723 K、应变速率为0.01~10 s~(-1)的条件下对挤压态ZK60合金进行了热压缩变形试验。通过真应力-真应变曲线分析了挤压态ZK60合金流变应力与应变速率、变形温度之间的关系,通过引入Z参数建立了挤压态ZK60合金的流变应力本构方程,并观察了其在热压缩过程中的显微组织变化。结果表明:挤压态ZK60合金的真应力-真应变曲线属于动态再结晶型,并且合金的流变应力在高变形温度或低应变速率条件下较低。在变形温度降低或应变速率升高时,动态再结晶晶粒变小,但动态再结晶进行的不充分,再结晶晶粒分布不均匀。通过本构方程计算出挤压态ZK60镁合金的变形激活能Q=122.884 k J/mol,应力指数n=5.096。     

ZK60镁合金低挤压比棒材的热压缩变形行为

采用Gleebe-3500热模拟机研究了ZK60镁合金低挤压比棒材(挤压比为15),在变形温度为523~723K、应变速率为0.01~10s~(-1)条件下的热压缩变形行为。分析了应变速率、变形温度对合金流变应力的影响,引入Zenner-Hollomon参数建立了挤压态ZK60镁合金的流变应力本构方程,通过金相观察分析了热压缩过程中的组织演化。结果表明:挤压态ZK60镁合金热变形时的真应力-真应变曲线具有明显的动态再结晶特征;流变应力随着变形速率的提高和变形温度的降低而升高,同时,动态再结晶的晶粒尺寸和体积分数也随之变小;通过本构方程计算,得出在挤压比为15条件下,变形态ZK60镁合金的变形激活能Q为143.025 k J/mol,应力指数n为3.074。     

Mg-5.9Zn-1.6Zr-0.9Y-1.6Nd合金等温压缩变形行为

在温度523~723 K和应变速率0.001~1 s-1范围内,利用Geeble-1500热模拟试验机,对均匀化态的Mg-5.9Zn-1.6Zr-0.9Y-1.6Nd合金进行等温压缩试验,并获得了应力应变曲线。研究了变形工艺参数对该合金流变应力的影响规律,计算了热变形激活能,建立了本构模型。结果表明,Mg-5.9Zn-1.6Zr-0.9Y-1.6Nd合金在变形过程中真应力随变形温度的升高而降低,随应变速率升高而升高,该合金的流变应力曲线可以用双曲正弦函数来描述。并求得该合金的热变形激活能为181.902 6 k J/mol。     

ZK60镁合金热变形过程中的动态再结晶动力学

采用Gleeble-1500热模拟机对ZK60镁合金在温度为200～400℃、应变速率为0.001～10s-1、最大变形量为60%的条件下进行恒应变速率高温压缩实验,研究高温变形过程中合金的动态再结晶行为;采用EM模型描述合金的动态回复曲线,以此为基础,得出ZK60合金热压缩过程中的动态再结晶动力学Avrami方程.利用有限元模拟合金热压缩过程中的动态再结晶.结果表明ZK60合金热压缩过程中由于存在动态再结晶的软化作用,流变应力达到峰值后逐渐减小,并最终达到稳态;随着变形量的增加和变形温度的升高,动态再结晶体积分数增加,合金变形更加均匀;随着应变速率的增加,动态再结晶分数有所减小,且.变形也更不均匀.     

Mg-Gd-Y-Mn耐热镁合金的压缩变形行为研究

采用Gleeble-1500热模拟机对Mg-Gd-Y-Mn稀土镁合金在温度为300～500℃、应变速率为0.001～1.0s-1、最大变形程度为60%的条件下,进行恒应变速率高温压缩模拟实验研究.分析了实验合金高温变形时流变应力与应变速率及变形温度之间的关系以及组织变化,计算了表观激活能及相应的应力指数,为选择这种合金的热变形加工条件提供了实验依据.结果表明:合金的稳态流变应力随应变速率的增大而增大,在恒应变速率条件下,合金的真应力水平随温度的升高而降低;在给定的变形条件下,计算得出的表观激活能和应力指数分别为200kJ·mol-1和5.1.根据实验分析,合金的热加工宜在400～500℃温度范围内进行.     

Mg-10Gd-4.8Y-0.6Zr镁合金热变形行为与加工图

在Gleeble-1500热/力模拟机上,对Mg-10Gd-4.8Y-0.6Zr镁合金进行高温压缩试验,压缩时设定应变速率范围为0.001～1 s-1,温度范围为623～773 K,最大真应变为1.3;研究该合金高温变形时流变应力与应变速率、变形温度之间的关系及变形过程中的微观组织演化;计算塑性变形表观激活能及相应的应力指数;建立该合金的加工图。结果表明:在该合金的加工图中,功率耗散系数η随应变速率的降低及温度的升高而不断增加,失稳区域随应变量的增加而扩大;综合得出该合金的最佳实际变形工艺为温度723～773 K、应变速率0.1～1 s-1。     

ZK31-1.5Y镁合金热变形行为及加工图

研究了ZK31-1.5Y镁合金在变形温度为250~450℃、应变速率为0.001~1 s-1条件下的热压缩变形特性,基于动态材料模型建立了热加工图,并结合真应力-真应变曲线确定了该合金在实验条件下的热变形机制及最佳工艺参数。结果表明:ZK31-1.5Y合金的真应力-真应变曲线主要以动态再结晶和动态回复软化机制为特征,峰值应力和稳态应力随变形温度的降低或应变速率的升高显著增加。合金功率耗散图和失稳图中分别包含了3个效率峰值区和1个马鞍形流变失稳区,峰区效率范围为38%~65%,叠加后形成的加工图给出了实验参数范围内热变形时的最优工艺参数,其热变形温度为350~450℃、应变速率为0.1~1 s-1。当应变量由0.1~0.6逐渐增大时对加工图分布规律影响不大。     

Ti600合金的高温本构方程

采用热模拟压缩试验研究了Ti600合金在变形温度为800～1100℃、应变速率为0.001～10s-1范围内应力-应变曲线的变化规律。研究结果表明:Ti600高温钛合金热变形的流变应力随温度的升高和应变速率的降低而减小;随着应变的增大,合金的真应力-真应变曲线在经历了明显的加工硬化阶段后达到最大值,然后渐渐出现流变“软化”现象。以经典的双曲正弦形式的模型为基础建立了Ti600合金热变形的本构方程,同时也通过对数据回归处理确定了合金不同温度下的应力指数n、应变激活能Q等数值。     

基于人工神经网络的ZK60镁合金热压缩变形行为

在变形温度为200～400℃、应变速率为0.001～1s-1条件下,对ZK60镁合金进行热压缩实验,建立一个单隐层前馈误差反向传播人工神经网络模型,研究该镁合金的流变行为。模型的输入参数分别为变形温度、应变速率和应变,输出为流变应力,中间隐含层包含23个神经元,并采用Levenberg-Marquardt算法对此网络模型进行训练。结果表明:ZK60镁合金的流变应力随变形温度升高和应变速率降低而减小;其高温压缩流变应力曲线可描述为加工硬化、过渡、软化和稳态流变4个阶段,但在较高温度和较低应变速率时,过渡阶段不很明显;所建神经网络模型可以很好地描述ZK60镁合金的流变应力,其预测值与实验值吻合很好;利用该模型预测的变形温度和应变速率对流变应力的影响结果与一般热加工理论所得结果一致。     

基于VPSC仿真的ZK60镁合金拉伸变形行为

通过实验和粘塑性自洽（VPSC）模型,研究了在室温下挤压态ZK60镁合金沿不同方向拉伸时的变形机制开动情况,及其与流动曲线、织构演变和显微组织的对应关系。通过调节VPSC模型的参数,建立了滑移和孪生耦合的晶体塑性力学模型。比较了不同方向拉伸过程中织构演变的差异,分析了变形机制对屈服不对称性的影响。实验和模拟结果表明：当沿垂直于挤压方向（PED）拉伸时,由于｛102｝孪晶开动,大部分晶粒发生大角度旋转（约90°）。柱面<a>滑移是导致ZK60合金沿不同方向拉伸时出现明显屈服不对称的主要变形机理。当ZK60合金沿挤压方向（ED）拉伸时,由于晶粒的择优取向分布,｛101｝孪晶难以开动,导致ZK60挤压态镁合金拉伸屈服强度较高。ZK60镁合金沿着与ED成45°的方向拉伸时,屈服应力高于沿PED拉伸,但随着拉应力逐渐增大,由于沿PED拉伸时柱面<a>滑移逐渐开动,沿PED应变后期的应力曲线逐渐高于沿与ED成45°方向应变的应力曲线。     

ZK60镁合金热变形过程中的应变强化与动态再结晶行为(英文)

研究ZK60合金的高温流变应力行为。分别采用Kocks-Mecking模型和Avrami方程对合金的应变强化和动态再结晶过程进行模拟,在此基础上,构建一个考虑合金动态再结晶软化的流变应力方程并对流变应力进行预测。结果表明:预测曲线与实验结果具有很高的相关系数,所构建的流变应力方程能准确地描述热变形过程中合金的流变应力行为。微观组织观察表明在变形初期合金组织主要为动态回复组织,随着应变增加,逐渐转变为再结晶组织。     

ZK60镁合金热压缩变形流变应力行为与预测

在变形温度为523---673 K, 应变速率为0.001---1 s^-1的条件下, 采用Gleeble--1500热模拟试验机对ZK60镁合金的热变形行为进行了研究. 结果表明, ZK60镁合金流变应力随变形温度升高和应变速率的降低而减小. 其高温压缩流变应力曲线可描述为加工硬化、过渡、软化和稳态流变4个阶段, 但在温度较高和应变速率较小时, 过渡阶段不很明显. 建立了一个包含应变的流变应力预测模型, 模型中的9个独立参数可以通过非线性最小二乘法拟合求得, 预测的流变应力曲线与实验结果吻合较好.     

Influence of impurities on microstructure and mechanical properties of ZK60 magnesium alloy

The influence of impurity content on the microstructure and mechanical properties of ZK60 magnesium alloys was investigated by optical microscopy, scanning electron microscopy and tensile test. ZK60 alloys were prepared by changing holding time of alloy melt during semi-continuous casting in order to control the content of impurity elements. The alloy with lower purity content is found to have less second precipitates and larger grain size in the as-cast state. However, in the as-extruded state, reducing impurities brings about a decrease in grain size and an increase in yield strength from 244 MPa to 268 MPa, while the elongations in the as-extruded alloys with different contents of impurities are almost the same. After T5 treatment, impurity content is found to have more obvious effect on the yield strength of ZK60 alloy. The yield strength of ZK60-45 alloys with low impurity content is increased up to 295 MPa after T5 treatment.     

Strain-dependent constitutive analysis of hot deformation and hot workability of T4-treated ZK60 magnesium alloy

The hot deformation behavior of T4-treated ZK60 magnesium alloy was investigated in a compression test conducted with a thermo-mechanical simulator at a temperature range of 523 K to 673 K and a strain rate of 0.001 s^?1 to 1 s^?1. The results show that the flow stress increases as the deformation temperature decreases and the strain rate increases. Strain-dependent constitutive relationships were developed using regression method and artificial neural network, and good agreements between the experimentally measured values and the predicted ones were achieved. The work hardening analysis and onset of dynamic recrystallization (DRX) were investigated. The processing map reveals a domain of DRX at the temperature range of 620–673 K and strain rate range of 0.001–0.01 s^?1, with its peak efficiency of 32% at 623 K and 0.001 s^?1, which are the optimum values of the parameters for hot working of the T4-treated ZK60 alloy. The strain level has a great effect on the processing maps and lower temperatures and higher strain rates should be avoided during hot working processes. DRX model indicates that DRX of ZK60 alloy is controlled by the rate of nucleation, which is slower than the rate of migration.     

ZK60镁合金高应变速率压缩变形的流变行为及显徽组织

在250-400℃的温度范围和0.1-50 s^-1的应变速率范围内对ZK60合金进行压缩变形,对其流变行为和显微组织进行研究。结果表明,在低应变速率（0.1-1 s^-1）下压缩变形时,再结晶主要发生在初始晶界上;在高应变速率（10-50 s^-1）下压缩变形时,再结晶同时在初始晶界和孪晶上发生。合金在应变速率10-50 s^-1和温度250-350℃的变形条件下获得均匀、细小的再结晶组织。因此,合金的最佳热加工工艺范围为应变速率10-50 s^-1、变形温度250-350℃。高应变速率压缩变形条件下的孪生诱发动态再结晶过程分三步,首先,高位错密度孪晶分割初始晶粒;然后,孪晶内的位错发生重排形成亚晶;最后,随着应变的增加而形成再结晶晶粒。     

轧制路径对ZK60镁合金板材组织和性能的影响

在250 ℃对轧制-热处理态ZK60镁合金板材进行9道次不同路径的轧制试验。采用光学显微镜、电子万能试验机、SEM、XRD等研究了轧制试验后ZK60镁合金的显微组织、室温拉伸性能、断口形貌及晶粒择优取向。结果表明:轧制路径对ZK60镁合金板材的晶粒尺寸变化无明显影响,但压下量对镁合金组织内的孪晶变化有很大影响;轧制路径的变化对ZK60镁合金板材的各向异性和力学性能有较大影响,在交叉+45°的路径下轧制后ZK60镁合金板材,各向异性较弱,具有良好的综合力学性能和轧制成形能力,其屈服强度、抗拉强度和伸长率分别达到244.31 MPa、371.14 MPa和25.46%;交叉+45°路径轧制对ZK60镁合金的晶粒择优取向有明显影响,能够改善镁合金板材的晶粒择优取向和各向异性,提高ZK60镁合金的力学性能。     

SUPERPLASTICITY IN SiCw／ZK60 COMPOSITE

The superplastic deformation behavior of SiCw/ZK60 composite was investigated at temperatures ranging from 573K to 723K and at initial strain rates ranging from 8.3x10-4s-1 to 8.3x10-2s-1. A maximum elongation of 200% with a m-value of 0.35 was obtained at 613K and a initial strain rate of 1.67x 10-2s-1. The apparent activation energy (98kJ/mol) approximates that for grain boundary diffusion (92kJ/mol) in magnesium. It is proposed that the dominant mechanism of superplastic deformation in the present composite is grain boundary sliding accommodated by diffusional transport, besides, interfacial sliding plays an important role in the superplastic deformation.     

Comparison of corrosion behaviors of AZ31, AZ91, AM60 and ZK60 magnesium alloys

The corrosion behaviours of four kinds of rolled magnesium alloys of AZ31, AZ91, AM60 and ZK60 were studied in 1 mol/L sodium chloride solution. The results of EIS and potentiodynamic polarization show that the corrosion resistance of the four materials is ranked as ZK60＞AM60＞AZ31＞AZ91. The corrosion processes of the four magnesium alloys were also analyzed by SEM and energy dispersive spectroscopy(EDS). The results show that the corrosion patterns of the four alloys are localized corrosion and the galvanic couples formed by the second phase particles and the matrix are the main source of the localized corrosion of magnesium alloys. The corrosion resistance of the different magnesium alloys has direct relationship with the concentration of alloying elements and microstructure of magnesium alloys. The ratio of the β phase in AZ91 is higher than that in AZ31 and the β phase can form micro-galvanic cell with the alloy matrix, as a result, the corrosion resistance of AZ31 will be higher than AZ91. The manganese element in AM60 magnesium alloy can form the second phase particle of AlMnFe, which can reduce the Fe content in magnesium alloy matrix, purifying the microstructure of alloy, as a result, the corrosion resistance of AM60 is improved. However, due to the more noble galvanic couples of AlMnFe and matrix, the microscopic corrosion morphology of AM60 is more localized. The zirconium element in ZK60 magnesium alloy can refine grain, form stable compounds with Fe and Si, and purify the composition of alloy, which results in the good corrosion resistance of ZK60 magnesium alloy.