初始取向及变形条件对AZ31镁合金压缩塑性行为影响的研究
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摘要
本文选用具有典型挤压织构的AZ31挤压棒材和具有很强基面织构的商用AZ31热轧板材，设计了七类不同初始取向的样品，取其压缩轴分别与挤压方向（ED）平行和垂直，与板材的法向（ND）成0°、30°、45°、60°和90°。在不同的变形条件下（温度、应变速率）进行准静态单轴、平面应变压缩及动态塑性压缩（DPD），利用电子背散射衍射（EBSD）技术，定量表征变形前后样品微观组织及织构演变的规律，结合晶体塑性模拟，详细分析了初始取向及变形条件对AZ31镁合金屈服行为、加工硬化行为和动态再结晶行为的影响，系统研究镁合金宏观力学性能与微观组织结构之间的关系。
主要得到以下结论：
①利用改进的Taylor模型（ACM）模拟计算AZ31镁合金不同温度下各滑移和孪生系统的CRSS值；利用改进的EBSD取向重构图研究由位错滑移引起的晶粒内部旋转分裂行为。
②初始取向对流变应力行为的影响与温度密切相关。低温下，初始取向影响孪生和滑移的竞争和协调，从而引起力学性能的各向异性，随着温度升高（250℃以上），孪生不易激活，初始取向影响减弱，流变应力各向异性逐渐消失。通过计算得到0°、30°、45°、60°和90°样品的热变形激活能分别为：146.71KJ/mol、141.88KJ/mol、127.56KJ/mol、137.62KJ/mol和151.37KJ/mol，45°样品的形变激活能最低，这是由于45°样品的初始取向最有利于基面滑移。
③初始取向影响变形后样品的宏观形貌。不同初始取向的圆柱样品在不同温度下变形，样品宏观形貌表现出明显的差异，即压缩面呈椭圆状，有明显的长径和短径方向，长径比的排序为：0°<30°<90°<45°<60°。
④初始取向对屈服行为及加工硬化行为具有显著影响。初始取向不同，室温下力学性能表现出强烈各向异性，加工硬化行为也呈现出不同特征。研究发现少量初始取向发生{10(?)2}拉伸孪生，即可造成明显的屈服行为发生。加工硬化率曲线第二阶段主要是由{10(?)2}孪生引起的织构强化贡献，这个阶段的应变量长度取决于发生的拉伸孪晶数量。
⑤Schmid定律可以解释大部分{10(?)2}拉伸孪生变体选择规律，即孪生Schmid因子最大的孪生变体优先发生，从孪生应变张量分析上看，能较好协调沿受力方向应变的变体优先发生。但Schmid定律无法解释所有晶粒中的孪生行为，需要结合晶粒内部的应力状态综合判断。
⑥对0°和90°样品，进行室温动态塑性变形（DPD），研究发现DPD促进孪生发生，对于0°样品，DPD变形时，观察到{10(?)1}，{10(?)2}以及{10(?)1}-{10(?)2}等孪晶发生，且{10(?)1}-{10(?)2}二次压缩孪生比{10ˉ12}拉伸孪生更严格符合Schmid因子规律；而在慢速下则无明显的孪生行为。对于90°样品，不管是慢速变形还是DPD变形，{10ˉ12}拉伸孪生都是主要的孪生类型，而且拉伸孪生变体选择机制对应变速率不敏感，大都符合Schmid因子规律。但应变速率对拉伸孪生形核和长大之间的竞争有明显影响。DPD下促进孪晶形核，慢速下则有利于孪晶片层生长。此外，在DPD条件下，个别晶粒内部可同时观察到多种孪晶类型共存，包括{10(?)1}，{10(?)2}以及{10(?)1}-{10(?)2}二次压缩孪晶。
⑦初始取向通过影响变形机制，从而影响动态再结晶进程。350℃下90°样品在变形初始阶段由于柱面滑移大量启动，减弱了应力集中程度，推迟了流变应力峰值的出现，从而延缓了动态再结晶发生的进程。
⑧应变速率通过影响滑移和孪生的启动来影响动态再结晶机制。0°样品250℃下变形，在应变速率0.001-0.01s~(-1)内，表现出连续动态再结晶、非连续动态再结晶和旋转动态再结晶的特征，在应变速率为1s~(-1)时，表现出旋转动态再结晶和孪生诱发动态再结晶机制的特征；当应变速率达到5s~(-1)时，则表现出孪生诱发动态再结晶机制的特征。
⑨在变形过程中，由于滑移所引起的晶粒内局部区域的旋转分裂，导致晶内变形带的形成，这些变形带具有严格的方向性，即与晶粒的{0001}面垂直，但与外力轴方向无关。在高温下，可分割细化晶粒，促进连续动态再结晶发生。
In this thesis commercial AZ31magnesium alloy in the forms of extruded bar witha strong fiber texture and hot rolled plate with a strong basal texture was chosen as thestarting material. In total, seven kinds of specimens for compression were prepared.Two types of specimens were cut from extruded bar with their compression axis alignedperpendicular or parallel to the extruded direction. The other five types of specimenswere cut form hot rolled plate with their compression axis aligned0o,30o,45o,60oor90oto the normal direction (ND) of the rolled sheet, respectively. Uniaxial compression,plane strain compression and dynamic plastic deformation (DPD) had been carried outat different temperatures and strain rates. The microstructure and texture evolutionduring deformation had been quantitatively characterized using electron backscatterdiffraction (EBSD). The EBSD data had also been applied to analyze in detail theinfluence of initial orientation and deformation conditions on yield behavior, workhardening behavior and dynamic recrystallization (DRX) of AZ31during compression,and thereby to understand the relationship between mechanical properties andmicrostructure better.
Main conclusions found are as following:
①The CRSSs for slip and twinning systems in AZ31magnesium alloy areestimated via an advanced Taylor model. A reconstruction mapping methods forenhancing the EBSD map contrast has been developed in order to reveal strong grainsubdivision behavior.
②The effect of initial texture on stress-strain behavior is strongly dependent ontemperature. At low temperature, the mechanical behavior is highly anisotropicoriginated from the initial texture, which affects the activation of twinning and slip.With increasing temperature (above250℃), the twinning activity decreasessignificantly, thus the mechanical behaviors become more isotropic due to the operationof a larger number of slip modes. The activation energy for0o,30o,45o,60oand90ospecimen is146.71KJ/mol,141.88KJ/mol,127.56KJ/mol,137.62KJ/mol and151.37KJ/mol, respectively. The activation energy of45ospecimen is the lowest due to itsinitial texture is favorable for basal slip.
③Initial texture has a significant influence on the macroscopic morphology ofdeformed specimens. The macroscopic morphology of specimens compressed at different temperatures and strain rates are highly anisotropic. The shape of thecompression face of deformed specimens varies with initial texture in the form ofellipse. The order of the ratio of long axis to short axis is0°<30°<90°<45°<60°.
④Initial texture has an important effect on yield stress and strain hardeningbehavior. Compressive stress-strain behavior is highly anisotropic with respect to theinitial texture at room temperature. The significant yield behavior can be observed ifonly a small volume of twins are activated. The increasing strain hardening rate(corresponding to the stage II) is mainly caused by texture strengthening, which rotatesgrain orientations into hard orientations due to {10(?)2} twinning. The length of the stageII is determined by the volume fraction of grains which are favorable for {10(?)2}twinning.
⑤{10(?)2} twinning variant selection mechanism can be explained by the Schmidfactor (SF) statistically. In general twinning variants with the highest SF are mostfrequently observed, however the SF alone cannot explain all the twinning activated.
⑥Twinning activities of0oand90ospecimens are largely enhanced by DPD.Several twinning modes including {10(?)1},{10(?)2} and {10(?)1}-{10(?)2} are observed in0ospecimen. The {10(?)1}-{10(?)2} double twinning behavior exhibits strong orientationdependence because of its high CRSS, while {10(?)2} twinning occurs over a wide rangeof Schmid factor from0.05to0.5. For the90ospecimen,{10(?)2} twinning is dominantunder both DPD and quasi-static conditions, and the {10(?)2} twinning variant selectionmechanism is governed by the Schmid factor criterion, which is insensitive to strain rate.However, strain rate could significantly affect the competition between twin nucleationand twin growth. Twin nucleation will be largely enhanced by DPD while twin growthwill be favored under quasi-static loading.
⑦The DRX process is closely related to initial texture. The DRX process in90ospecimen is significantly retarded compared with that in0ospecimen compressed at350℃. The difference of DRX process between0oand90ospecimens is attributed todifferent deformation mechanisms at the starting deformation stage. With respect to0ospecimen, pyramidal slip is considered as the main deformation mechanism. For90ospecimen, prismatic slip is the dominant deformation mechanism.
⑧The effect of strain rate on DRX behavior is caused by its influence on the slipand twinning deformation mechanisms. For the0ospecimen compressed at250℃,continuous DRX, discontinuous DRX and rotation DRX are mainly observed at thestrain rate ranging from0.001to0.01s~(-1), while rotation DRX and twinning induced DRX are mainly observed at the strain rate of1s-1, and {10(?)1}-{10(?)2} double twinninginduced DRX is mainly observed at the strain rate of5s~(-1).
⑨Grain subdivision behavior which corresponds of course to different slipsystem activity/combinations in different parts of each grain is observed. The deformedbands are nearly perpendicular to the (0001) basal plane. However, there is no directrelationship between the bands and the loading direction. The DRX would be enhanceddue to the grain splitting by the deformation bands.
主要得到以下结论：
①利用改进的Taylor模型（ACM）模拟计算AZ31镁合金不同温度下各滑移和孪生系统的CRSS值；利用改进的EBSD取向重构图研究由位错滑移引起的晶粒内部旋转分裂行为。
②初始取向对流变应力行为的影响与温度密切相关。低温下，初始取向影响孪生和滑移的竞争和协调，从而引起力学性能的各向异性，随着温度升高（250℃以上），孪生不易激活，初始取向影响减弱，流变应力各向异性逐渐消失。通过计算得到0°、30°、45°、60°和90°样品的热变形激活能分别为：146.71KJ/mol、141.88KJ/mol、127.56KJ/mol、137.62KJ/mol和151.37KJ/mol，45°样品的形变激活能最低，这是由于45°样品的初始取向最有利于基面滑移。
③初始取向影响变形后样品的宏观形貌。不同初始取向的圆柱样品在不同温度下变形，样品宏观形貌表现出明显的差异，即压缩面呈椭圆状，有明显的长径和短径方向，长径比的排序为：0°<30°<90°<45°<60°。
④初始取向对屈服行为及加工硬化行为具有显著影响。初始取向不同，室温下力学性能表现出强烈各向异性，加工硬化行为也呈现出不同特征。研究发现少量初始取向发生{10(?)2}拉伸孪生，即可造成明显的屈服行为发生。加工硬化率曲线第二阶段主要是由{10(?)2}孪生引起的织构强化贡献，这个阶段的应变量长度取决于发生的拉伸孪晶数量。
⑤Schmid定律可以解释大部分{10(?)2}拉伸孪生变体选择规律，即孪生Schmid因子最大的孪生变体优先发生，从孪生应变张量分析上看，能较好协调沿受力方向应变的变体优先发生。但Schmid定律无法解释所有晶粒中的孪生行为，需要结合晶粒内部的应力状态综合判断。
⑥对0°和90°样品，进行室温动态塑性变形（DPD），研究发现DPD促进孪生发生，对于0°样品，DPD变形时，观察到{10(?)1}，{10(?)2}以及{10(?)1}-{10(?)2}等孪晶发生，且{10(?)1}-{10(?)2}二次压缩孪生比{10ˉ12}拉伸孪生更严格符合Schmid因子规律；而在慢速下则无明显的孪生行为。对于90°样品，不管是慢速变形还是DPD变形，{10ˉ12}拉伸孪生都是主要的孪生类型，而且拉伸孪生变体选择机制对应变速率不敏感，大都符合Schmid因子规律。但应变速率对拉伸孪生形核和长大之间的竞争有明显影响。DPD下促进孪晶形核，慢速下则有利于孪晶片层生长。此外，在DPD条件下，个别晶粒内部可同时观察到多种孪晶类型共存，包括{10(?)1}，{10(?)2}以及{10(?)1}-{10(?)2}二次压缩孪晶。
⑦初始取向通过影响变形机制，从而影响动态再结晶进程。350℃下90°样品在变形初始阶段由于柱面滑移大量启动，减弱了应力集中程度，推迟了流变应力峰值的出现，从而延缓了动态再结晶发生的进程。
⑧应变速率通过影响滑移和孪生的启动来影响动态再结晶机制。0°样品250℃下变形，在应变速率0.001-0.01s~(-1)内，表现出连续动态再结晶、非连续动态再结晶和旋转动态再结晶的特征，在应变速率为1s~(-1)时，表现出旋转动态再结晶和孪生诱发动态再结晶机制的特征；当应变速率达到5s~(-1)时，则表现出孪生诱发动态再结晶机制的特征。
⑨在变形过程中，由于滑移所引起的晶粒内局部区域的旋转分裂，导致晶内变形带的形成，这些变形带具有严格的方向性，即与晶粒的{0001}面垂直，但与外力轴方向无关。在高温下，可分割细化晶粒，促进连续动态再结晶发生。
In this thesis commercial AZ31magnesium alloy in the forms of extruded bar witha strong fiber texture and hot rolled plate with a strong basal texture was chosen as thestarting material. In total, seven kinds of specimens for compression were prepared.Two types of specimens were cut from extruded bar with their compression axis alignedperpendicular or parallel to the extruded direction. The other five types of specimenswere cut form hot rolled plate with their compression axis aligned0o,30o,45o,60oor90oto the normal direction (ND) of the rolled sheet, respectively. Uniaxial compression,plane strain compression and dynamic plastic deformation (DPD) had been carried outat different temperatures and strain rates. The microstructure and texture evolutionduring deformation had been quantitatively characterized using electron backscatterdiffraction (EBSD). The EBSD data had also been applied to analyze in detail theinfluence of initial orientation and deformation conditions on yield behavior, workhardening behavior and dynamic recrystallization (DRX) of AZ31during compression,and thereby to understand the relationship between mechanical properties andmicrostructure better.
Main conclusions found are as following:
①The CRSSs for slip and twinning systems in AZ31magnesium alloy areestimated via an advanced Taylor model. A reconstruction mapping methods forenhancing the EBSD map contrast has been developed in order to reveal strong grainsubdivision behavior.
②The effect of initial texture on stress-strain behavior is strongly dependent ontemperature. At low temperature, the mechanical behavior is highly anisotropicoriginated from the initial texture, which affects the activation of twinning and slip.With increasing temperature (above250℃), the twinning activity decreasessignificantly, thus the mechanical behaviors become more isotropic due to the operationof a larger number of slip modes. The activation energy for0o,30o,45o,60oand90ospecimen is146.71KJ/mol,141.88KJ/mol,127.56KJ/mol,137.62KJ/mol and151.37KJ/mol, respectively. The activation energy of45ospecimen is the lowest due to itsinitial texture is favorable for basal slip.
③Initial texture has a significant influence on the macroscopic morphology ofdeformed specimens. The macroscopic morphology of specimens compressed at different temperatures and strain rates are highly anisotropic. The shape of thecompression face of deformed specimens varies with initial texture in the form ofellipse. The order of the ratio of long axis to short axis is0°<30°<90°<45°<60°.
④Initial texture has an important effect on yield stress and strain hardeningbehavior. Compressive stress-strain behavior is highly anisotropic with respect to theinitial texture at room temperature. The significant yield behavior can be observed ifonly a small volume of twins are activated. The increasing strain hardening rate(corresponding to the stage II) is mainly caused by texture strengthening, which rotatesgrain orientations into hard orientations due to {10(?)2} twinning. The length of the stageII is determined by the volume fraction of grains which are favorable for {10(?)2}twinning.
⑤{10(?)2} twinning variant selection mechanism can be explained by the Schmidfactor (SF) statistically. In general twinning variants with the highest SF are mostfrequently observed, however the SF alone cannot explain all the twinning activated.
⑥Twinning activities of0oand90ospecimens are largely enhanced by DPD.Several twinning modes including {10(?)1},{10(?)2} and {10(?)1}-{10(?)2} are observed in0ospecimen. The {10(?)1}-{10(?)2} double twinning behavior exhibits strong orientationdependence because of its high CRSS, while {10(?)2} twinning occurs over a wide rangeof Schmid factor from0.05to0.5. For the90ospecimen,{10(?)2} twinning is dominantunder both DPD and quasi-static conditions, and the {10(?)2} twinning variant selectionmechanism is governed by the Schmid factor criterion, which is insensitive to strain rate.However, strain rate could significantly affect the competition between twin nucleationand twin growth. Twin nucleation will be largely enhanced by DPD while twin growthwill be favored under quasi-static loading.
⑦The DRX process is closely related to initial texture. The DRX process in90ospecimen is significantly retarded compared with that in0ospecimen compressed at350℃. The difference of DRX process between0oand90ospecimens is attributed todifferent deformation mechanisms at the starting deformation stage. With respect to0ospecimen, pyramidal
⑧The effect of strain rate on DRX behavior is caused by its influence on the slipand twinning deformation mechanisms. For the0ospecimen compressed at250℃,continuous DRX, discontinuous DRX and rotation DRX are mainly observed at thestrain rate ranging from0.001to0.01s~(-1), while rotation DRX and twinning induced DRX are mainly observed at the strain rate of1s-1, and {10(?)1}-{10(?)2} double twinninginduced DRX is mainly observed at the strain rate of5s~(-1).
⑨Grain subdivision behavior which corresponds of course to different slipsystem activity/combinations in different parts of each grain is observed. The deformedbands are nearly perpendicular to the (0001) basal plane. However, there is no directrelationship between the bands and the loading direction. The DRX would be enhanceddue to the grain splitting by the deformation bands.
引文
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