金属的后继屈服面研究—单试样与多试样测试

采用退火45号钢薄壁试样进行拉扭组合试验,测试材料经历预拉伸后的系列后继屈服面。试验采用偏移应变法定义屈服应力,讨论了不同的偏移应变、预变形程度对后继屈服面测试结果的影响;试验分别用单试样法和多试样法进行,分析讨论了两种方法的合理性与局限性。试验研究得到以下结果：（1）单试样法和多试样法确定的初始屈服面的形状与Mises圆很接近;（2）单试样法屈服点的测试顺序对所测得的屈服面的形状有很大影响,第一测试点与预加载方向相反时,所得屈服面会出现“内凹”现象,而若改变测试顺序,可不再出现“内凹”;（3）单试样法测得的后继屈服面与测试的屈服点数密切相关,当测试的屈服点数较多时,所得结果因累积塑性应变引起的应变强化作用而出现较大的偏离;（4）单试样法与多试样法测得的后继屈服面形状和大小有较明显的差异,测试过程中塑性变形的积累对单试样法的测试结果有明显影响,采用多试样法研究屈服面演化更为合理;（5）多试样法若采用较小目标偏移应变定义屈服,测得的后继屈服面也出现轻微内凹。     

一种基于物理机制的后继屈服面演化模型

考虑滑移为晶体塑性的主要变形机制,推广单晶滑移理论至多晶体,建立滑移构元模型,研究了后继屈服面的移动、变形等演化规律。基于滑移构元的包氏效应和潜在硬化的影响,后继屈服面的尾部缩进,变得较“平坦”,而前端突出,形成“高曲率区域”。为了验证模型的有效性,本文分别预测了单轴拉伸、纯扭转和拉—扭组合比例/非比例加载下的后继屈服面演化过程,与已有实验结果符合一致。关键词:滑移构元模型,后继屈服面,包氏效应,潜在硬化,非比例加载      

需要考虑材料泊松比的某些塑性力学问题

本文例举了用测应变值确定受拉扭的薄壁管外载,受内压的封闭薄壁圆管在比例加载下的应变分量比值,以及平面应变条件下的三种初始屈服准则,说明对于这些塑性力学问题考虑材料真实泊松比 v 的必要性.     

镍基单晶合金多轴非比例加载低周疲劳研究

基于正交设计, 分别在680℃和850℃下进行DD3镍基单晶合金薄壁圆管试样([001]取向)拉/扭非比例加载低周疲劳试验, 研究等效应变范围、应变路径角、拉/扭载荷相位角、循环特性和温度诸因素对镍基单晶合金多轴低周疲劳寿命的影响作用. 疲劳试验数据的极差分析表明, 应变路径角、拉/扭载荷相位角和等效应变范围是影响疲劳寿命的主要因素. 将菱形应变加载路径区分为比例加载段和非比例加载段, 提出了表征非比例加载效应的等效应变参量, 并通过引入单晶应变三轴性因子反映拉/扭应变路径角对多轴疲劳寿命的影响. 用考虑非比例加载效应的等效应变范围和单晶应变三轴性因子构造循环塑性应变能损伤参量, 进行多元线性回归分析, 疲劳寿命回归模型与试验寿命具有很好的相关性, 所有试验数据都落在2.0倍的偏差分布带之内.      

铜单晶拉伸试样表面滑移带痕迹的晶体塑性分析

采用建立在晶体塑性理论基础上的晶体塑性有限变形计算方法,针对铜单晶试样单轴拉伸过程中晶体滑移在试样表面留下的滑移带痕迹进行了数值研究.作者利用三维有限元模拟不同取向铜单晶试样的拉伸变形,通过晶体塑性滑移面与试样表面交线的几何分析,得到了试样在不同晶向拉伸下不同滑移系启动造成的试样表面滑移痕迹,并对数值计算的试样表面滑移...     

金属拉扭强度关于材料声速及加载速率最小二乘法的回归模型

为了研究不同加载速率下金属的拉扭强度及其预测方法,利用声发射检测仪及电子拉扭试验机分别对铸铁和中碳钢标准试件进行了声速测定及不同加载速率、加载路径下的拉伸-扭转组合变形试验,得到了各试件材料的声速值及相应加载方案下的载荷-变形曲线;根据平面应力状态及强度理论,推导出了材料拉扭破坏的最大正应力、最大剪应力;利用试验中采集的最大轴力、最大扭矩计算得到了材料的拉扭破坏应力、破坏面方向;基于最小二乘法拟合得到了材料拉扭强度关于材料声速值、拉伸与扭转加载速率的多元回归模型。研究表明:随着拉伸与扭转加载速率的增加,铸铁、碳钢的破坏应力分别呈现总体上升、总体下降的趋势;相同加载速率、不同加载路径下材料的破坏强度各不相同;建立的回归模型能较好地预测给定材料在不同加载速率下的破坏应力,并以此建立塑性及脆性材料的拉扭强度条件。     

准脆性材料的弹塑性各向异性损伤耦合本构模型研究

针对准脆性材料的非线性特征：强度软化和刚度退化、单边效应、侧限强化和拉压软化、不可恢复变形、剪胀及非弹性体胀,在热动力学框架内,建立了准脆性材料的弹塑性与各向异性损伤耦合的本构关系。对准脆性材料的变形机理和损伤诱发的各向异性进行了诠释,并给出了损伤构形和有效构形中各物理量之间的关系。在有效应力空间内,建立了塑性屈服准则、拉压不同的塑性随动强化法则和各向同性强化法则。在损伤构形中,采用应变能释放率,建立了拉压损伤准则、拉压不同的损伤随动强化法则和各向同性强化法则。基于塑性屈服准则和损伤准则,构建了塑性势泛函和损伤势泛函,并由正交性法则,给出了塑性和损伤强化效应内变量的演化规律,同时,联立塑性屈服面和损伤加载面,给出了塑性流动和损伤演化内变量的演化法则。将损伤力学和塑性力学结合起来,建立了应变驱动的应力-应变增量本构关系,给出了本构数值积分的要点。以单轴加载-卸载往复试验识别和校准了本构材料常数,并对单轴单调试验、单轴加载-卸载往复试验、二轴受压、二轴拉压试验和三轴受压试验进行了预测,并与试验结果作了比较,结果表明,所建本构模型对准脆性材料的非线性材料性能有良好的预测能力。     

拉─扭复合加载下不锈钢的弹塑性本构关系─I．实验

讨论了１Ｃｒ１８Ｎｉ９Ｔｉ不锈钢薄壁圆管试件沿三段折线、不同曲率的圆形和椭圆应变路径承受拉－扭复合载荷的实验．在塑性应变空间中，观察加载路径的内蕴几何参数对应力矢量大小、方向影响的规律．结果表明：响应的延迟角、瞬时软化和重新强化性质与路径的内蕴几何学密切相关；Ｌｅｎｓｋｙ的“局部确定性”假设不完全符合事实；变形历史和应变分量相互间的耦合效应对响应存在显著的影响．初步的电镜实验表明，材料中的位错组态和塑性应变历史密切相关     

考虑运动硬化的DD3镍基合金力学行为研究

详细介绍了镍基合金的晶体塑性本构模型,在Asaro大变形晶体塑性框架下,详细介绍了镍基合金的晶体塑性本构模型,在Asaro大变形晶体塑性框架下,引入了运动硬化规律,考虑了温度和应变率对晶体塑性变形的影响,通过针对每个滑移系考虑屈服准则和流动规律建立了晶体塑性模型. 对积分过程进行了推导,通过编写ABAQUS材料用户子程序(UMAT), 实现本构模型的有限元积分算法. 在此基础上模拟了DD3镍基单晶合金在单轴拉伸和循环载荷下的响应,并与实验数据进行了对比. 利用该模型可以很好地模拟镍基单晶所具有的各向异性特性,体现了镍基单晶在循环载荷作用下的拉-压不对称性.      

拉—扭复合加载下不锈钢的弹塑性本构关系——Ⅰ.实验

讨论了１Ｃｒ１８Ｎｉ９Ｔｉ不锈钢薄壁圆管试件沿三段折线、不同曲率的圆形和椭圆应变路径承受拉－扭复合载荷的实验，在塑性应变空间中，观察加载路径的内蕴几何参数对应力矢量大小、方向影响的规律。结果表明：响应的延迟角、瞬时软化和重新强化性质与的内蕴几何学密切相关，Ｌｅｎｓｋｙ的“局部确定性”假设不完全符合事实；变形历史和应变分量相互间的耦合效应对响应存在显著的影响，初步的电镜实验表明，材料中位错组态和塑料     

Effect of loading-path on the evolution of yield surface for anisotropic metals subjected to large pre-strain

A theory of plasticity previously formulated by the author to discuss the free-end torsion problem has been extended to the more general case of combined axial-torsion of a thin-walled tube. This paper is devoted to the discussion of evolution of the yield surface due to different (proportional and non-proportional) loading paths with pre-strains in the large strain range. Experimental yield surfaces with axial and torsion pre-strains of magnitudes up to 40 and 45%, respectively, are presented, and theoretical results are compared with the experimental data.     

大变形扭转塑性硬化的实验和仿真研究

通过拉伸和扭转实验以及理论分析发现:在扭转实验中,当等效名义伸长率达到 286％时发生扭断,在此之前无明显局部化现象出现;相比较而言,单轴拉伸实验中的试件在颈缩失稳断裂时标距的最大伸长率仅为 29％.因此,用实心圆柱的扭转实验作为研究低碳钢这类弹塑性材料在大变形特征下的更为有效的基本实验,而以单轴拉伸实验作为补充是十分必要的.并通过数值模拟对在扭转过程中弹性核演变的历史进行了分析.     

Deformation and failure mechanisms of single crystal superalloy under temperature gradient

The crystallographic constitutive model under temperature gradient is developed and introduced to study the deformation and failure mechanisms of single crystal superalloy. Tensile tests of thin-walled pipe specimen at different temperatures without cooled air flow were carried out. Based on the experimental results, the temperature dependence of constitutive model was studied and the basic parameters of constitutive model were obtained. To investigate the deformation and failure mechanisms, the thin-walled pipe specimen with cooled air flow under temperature gradient were tested. Considered the fluid-solid interface (FSI), a finite element method (FEM) was proposed to simulate the process of tension. In FEM, the activation rate of slip system was defined as the failure law of specimen under temperature gradient. The simulation result was in good agreement with the experiment result. Furthermore, the fracture surface of the specimen was observed by the scanning electron microscopy (SEM). The microstructure revealed that the slip deformation belonged to {1 1 1} crystalplane is a principal failure mechanism of single crystal superalloy under temperature gradient. The results of the SEM also implied that the proposed FEM method can be used to systemically study the deformation and failure behavior of single crystal superalloy cooled blade.     

An experimental study on subsequent yield surface after finite shear prestraining

An equimodulus surface is introduced and the subsequent yield surface after large finite shear prestraining is experimentally investogated. Fully annealed, thin-walled copper tubular specimens were subjected to large torsional loading and partial unloading; strain gages were carefully mounted on the specimen after the application of pure shear loading. Specimens were then subjected to various combined tension-torsion loadings. Influences of he von Mises and Tresca equivalent offset strains on the subsequent yield surfaces are studied. On examining the experimental results reported in this article, it was found that the smaller the offset strains, the more distorted are the subsequent yield surfaces. At the torsional preloading point, a rounded corner was developed, whereas in the region opposite to the preloading point, the subsequent yield surface was flattened. When large von Mises offset strains were used, the corresponding subsequent yield surfaces passed through the von Mises loading surface. But this was not the case when Tresca offset strains were used. The subsequent yield surface determined by the back extrapolation method was almost completely outside the von Mises loading surface. On the other hand, the subsequent yield surface determined by the back extrapolation method was close to the Tresca loading surface. It is also found that the equimodulus surface is distorted and cannot simply be described by the combined kinematic and isotropic hardening rule.     

Evolution of subsequent yield surfaces and elastic constants with finite plastic deformation. Part II: A very high work hardening aluminum alloy (annealed 1100 Al)

Results are presented on the evolution of subsequent yield surfaces with finite deformation in a very high work hardening annealed 1100 aluminum alloy. In Part I [Khan, A.S., Kazmi, R., Stoughton, T., Pandey, A., 2009a. Evolution of subsequent yield surfaces and elastic constants with finite plastic deformation. Part 1: a very low work hardening aluminum alloy (Al-6061–T6511) 25, 1611–1625.] of this paper, similar results are presented for a very low work hardening aluminum alloy. Those results were very different from the present ones, and all the results were for proportional loading paths. The subsequent yield surfaces are determined in tension, free end torsion and combined tension–torsion proportional and non-proportional loading paths, using 10 με deviation from linearity definition of yield. Yield surfaces are also determined after linear, bi-linear, and non-linear unloading paths after finite deformation under tension, free end torsion, and combined tension–torsion loading. The initial yield surface is closer to the von-Mises surface and the subsequent yield surfaces show distortion, expansion, positive cross-effect, and “nose” in the loading direction. Additionally, the subsequent yield surfaces after non-proportional loading paths show shrinkage and compounded distortion. The yield surfaces after unloading depict strong anisotropy, positive cross-effect and exhibits different proportion of distortion in each loading conditions. The Young’s and shear modulus decrease with plastic deformation and this decrease is much less than those reported in the published literature.     

Correlation between swift effects and tension–compression asymmetry in various polycrystalline materials

The Swift phenomenon, which refers to the occurrence of permanent axial deformation during monotonic free-end torsion, has been known for a very long time. While plastic anisotropy is considered to be its main cause, there is no explanation as to why in certain materials irreversible elongation occurs while in others permanent shortening is observed.In this paper, a correlation between Swift effects and the stress–strain behavior in uniaxial tension and compression is established. It is based on an elastic–plastic model that accounts for the combined influence of anisotropy and tension–compression asymmetry. It is shown that, if for a given orientation the uniaxial yield stress in tension is larger than that in compression, the specimen will shorten when twisted about that direction; however, if the yield stress in uniaxial compression is larger than that in uniaxial tension, axial elongation will occur. Furthermore, it is shown that on the basis of a few simple mechanical tests it is possible to predict the particularities of the plastic response in torsion for both isotropic and initially anisotropic materials. Unlike other previous interpretations of the Swift effects, which were mainly based on crystal plasticity and/or texture evolution, it is explained the occurrence of Swift effects at small to moderate plastic strains. In particular, the very good quantitative agreement between model and data for a strongly anisotropic AZ31–Mg alloy confirm the correlation established in this work between tension–compression asymmetry and Swift effects. Furthermore, it is explained why the sign of the axial plastic strains that develop depends on the twisting direction.     

Evolution of subsequent yield surfaces and elastic constants with finite plastic deformation. Part-I: A very low work hardening aluminum alloy (Al6061-T6511)

In the present study, the initial and subsequent yield surfaces in Al 6061-T6511, based on 10 με deviation from linearity definition of yield, are presented. The subsequent yield surfaces are determined during tension, free end torsion, and combined tension–torsion proportional loading paths after reaching different levels of strains. The yield surfaces are also obtained after linear, bi-linear and non-linear unloading paths after finite plastic deformation. The initial yield surface is very close to the von-Mises yield surface and the subsequent yield surfaces undergo translation and distortion. In the case of this low work hardening material, the size of the yield surfaces is smaller and negative cross-effect is observed with finite plastic deformation. The subsequent yield have a usual “nose” in the loading direction and flattened shape in the reverse loading direction; the observed nose is more dominant in the case of tension and combined tension–torsion loading than in torsional loading. The size of the yield surfaces after unloading is smaller than the initial yield surface but larger than subsequent yield surfaces obtained during prior loading, show much smaller cross-effect, and the shape of these yield surfaces depends strongly on the loading and unloading paths. Elastic constants (Young’s and shear moduli) are also measured within each subsequent yield surfaces. Evolution of these constants with finite deformation is also presented. The decrease of the two moduli is found to be much smaller than reported earlier in tension by Cleveland and Ghosh [Cleveland, R.M., Ghosh, A.K., 2002. Inelastic effects on springback in metals. Int. J. Plast. 18, 769–785]. Part-II and III [(Khan et al., 2009a) and (Khan et al., 2009b)] of the papers will include experimental results on annealed 1100 Al (a very high work hardening material) and on both Al alloys (Al6061-T6511 and annealed 1100 Al) in tension- tension stress space, respectively. The results for both cases are quite different than the ones that are presented in this paper.