新型高强度和高塑性孪晶诱发塑性钢的研究
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摘要
孪晶诱发塑性（Twinning Induced Plasticity-简写TWIP）钢表现出高的抗拉强度（650～1100MPa），高的应变硬化率和极高的伸长率（19％～90％），可满足汽车轻量化的需求。本文研究了9种不同成分的TWIP钢的显微组织及在不同应变速率下的拉伸应变行为。动态拉伸试验在气动式间接杆杆型冲击拉伸试验机上进行，采用LOM、XRD、SEM和TEM等手段分析形变孪晶形态、大小和转变量随成分、应变速率以及应变量的演化规律。通过研究孪晶与周围基体中位错密度和亚结构的变化，分析了TWIP效应对材料强度和应变硬化行为的影响，同时分析了TWIP钢的断裂行为以及热轧、冷轧、退火、拉伸等状态下的织构演变情况。研究成果可为汽车工业的轻量化及防冲撞设计提供借鉴。
论文主要内容包括：
1、结合已有Fe-Mn相图的研究结果和热力学计算，确定了5种低碳TWIP钢和4种中碳TWIP钢。采用金相、X射线衍射法、透射电子显微分析对九种不同成分TWIP钢变形前后的组织进行观察。讨论了热处理工艺和合金元素对TWIP钢显微组织形貌和不同组织体积分数的影响。结果表明，1#钢的金相组织由奥氏体和第二相组成，变形过程中不产生形变孪晶；其余几种钢随着锰含量的增加，组织为全奥氏体，且变形过程中产生大量形变孪晶。
2、对九种TWIP钢在10-5～103s-1应变速率范围的室温拉伸性能进行了研究。结果表明，静态拉伸时，随着应变速率的升高，1#~5#材料的屈服强度增大，1#钢和2#钢抗拉强度下降，3#~5#钢抗拉强度变化不大；1#钢的均匀延伸率和断裂延伸率增大，2#~5#钢的均匀延伸率和断裂延伸率下降。z1#~z4#钢的屈服强度相差不大，抗拉强度略微下降，z1#~z4#钢的均匀延伸率、断裂延伸率和强塑积随应变速率的升高而下降；而与静态拉伸条件下相比，动态拉伸时，随着应变速率增加，2#~5#钢的屈服强度和抗拉强度增大，均匀延伸率变化不大，断裂延伸率有所上升。1#~5#钢均体现出显著的应变速率敏感性。动态拉伸条件下的屈服强度和抗拉强度要高，z1#~z4#钢的总延伸率较静态拉伸条件下都有所下降。
3、利用XRD分析了奥氏体的转变量随应变和应变速率的变化规律。结果发现，1#钢和2#钢变形过程中发生了马氏体相变，而3#钢变形过程中没有发生马氏体相变。奥氏体转变量随应变速率的增加而减小，随应变量的增加而增加。
4、分析研究了应变硬化指数n值随应变速率和应变的变化规律。结果表明：试验钢在拉伸过程中的应变硬化表现为阶段性多n值行为。1#钢的n值随应变呈抛物线关系，遵循关系式：n=aε2+bε+c；其它钢的n值与应变呈对数关系，遵循关系式： n=alnε+b。其应变硬化机制有两种：0.4%～3%左右应变区间为位错强化阶段，10％～50%左右应变区间为孪晶强化阶段。在此两个区间内n值皆为定值，而在4％～10％应变区间n值呈不断上升趋势。奥氏体的应变诱发相变和变形过程中产生的形变孪晶显著影响TWIP钢的应变硬化能力。
5、采用SEM检测了TWIP钢动态拉伸后的组织形态。结果发现，TWIP钢具有典型的延性断裂断口特征，其变形和断裂过程为微孔洞的形核、长大和聚合。含有第二相的TWIP钢（如1#钢）的断裂机制为：第二相和奥氏体相界面聚合力的减弱促使微孔形核，形变过程中产生的应力集中使微孔长大、聚合直至发生断裂。全奥氏体的TWIP钢（如5#钢）断裂机制为：形变过程中位错的运动受孪晶界的阻碍，形变孪晶与位错的交互作用使微孔形核于孪晶界处，应力集中使微孔长大、聚合直至材料发生断裂。
6、TWIP钢的变形机制主要为孪晶变形机制，其次为位错变形机制。在孪晶变形机制下，随着应变的增加、孪晶含量的增多，铜型织构转到其孪晶取向的位置CuT{552}<115>，在经过滑移机制作用下，CuT{552}<115>转变为G织构，原有的及新形成的G织构转变为B织构。织构转变后的强度随着应变率的不同而有所不同。
Deformation twins，martensite phase transformation and mechanical propertieshad been investigated. For steels with higher stacking fault energy，twinning is themain deformation mechanism. TWIP（Twinning Induced Plasticity）steels exhibit hightensile strength (650～1100MPa), extremely large elongation rate(19%~90%). Themicrostructures, mechanical properties and fracture behaviors of nine differentcomposition TWIP steels were investigated. Tensile tests were carried out at differentstrain rates, and the tensile strain behaviors under various strain rates of nine differentcomposition TWIP steels were investigated. The dynamic tensile tests were carriedout on the pneumatic indirect bar-bar tensile impact tester. The formation of twins andmartensite were analyzed by optical microscopy, XRD， SEM and TEM. Thecontribution of the dissertation lies in providing theoretical basis for lighting weightand anti-crashing of automobiles.
The primary coverage of the dissertation includes:
(1) The components of five kinds of low carbon TWIP steel and four kinds ofmedium carbon TWIP steel are determined based the research results of Fe-Mn phasediagram and the thermodynamic calculation. The microstructures of nine differentMn-content TWIP steels before and after deformation are investigated bymetallography, XRD and TEM. The effects of heat treatment and alloy elements onthe morphology and volume fraction of each phase are analyzed. The results showthat the microstructure of steel1#is composed of austenite and second-phase. Withthe increasing of manganese content, the microstructure of the TWIP steels changes toaustenite totally and deformation twins occurs during deformation.
(2) The tensile tests are carried out on nine TWIP steels in the strain rate range of10-5～103s-1. The results indicate that the yield strength increases and tensile strengthof steel1#and steel2#decreases, while those of steels3#~5#, z1#~z4#change little,and the uniform elongation rate and total elongation rate of steel1#increase, while these of other steels decrease with the strain rate. During dynamic tensile stage, thetensile strength, yield strength and total elongation increase, while the uniformelongation rate hardly changes with the strain rate, showing that the TWIP steels aresensitive to strain rate.
(3) The volume fraction of austenite after deformation as a function of strain andstrain rate is investigated by XRD. The results show that martensite transformationoccurred in steel1#and steel2#, but not in steel3#. The volume fraction oftransformed austenite decreases with the strain rate, while it increases with the strain.
(4) The strain-hardening exponent n as a function of strain and strain rate isdetermined. It shows that the n value varied during tensile deformation. The n valueof steel1#obeys a parabolic relation: n=aε2+bε+c. While the n value of fullaustenite TWIP steels obeys a logarithmic relation: n=alnε+b. In the strain rangeof0.4%～4%, the full austenite TWIP steels are strengthened by dislocation piling,but in the range of10%～50%, these steels are strengthened by twinning. In these twostages, the n value keeps constant. However, the n value increases continuously in thestrain range of4%～10%. Strain induced martensite transformation and formation oftwins during deformation significantly influence the strain-hardening behavior of theTWIP steels.
(5) The microstructure of the TWIP steels after dynamic tension test wascharacterized by SEM. The fractograph of the TWIP steels exhibits a typical ductilefracture pattern. Due to the presence of second phases, nucleation of micro-voids insteel1#occurred at the weak spot in the material, i.e. the austenite/second phaseinterface. However, due to the interaction of dislocations and twins, the nucleation ofmicro-voids in the full austenite steel5#occurred at boundaries of deformation twinsas well as the interface between deformation twins and dislocations. No matter whatthe mechanism is, the nucleation is followed by the growth and coalescence of themicro-voids in all samples.
(6) In present work, the dominating deformation mechanism of the TWIP steels is twinning, also accompanied by dislocation mechanism. For the twinningmechanism, the content of twins increases with strain, and Cu{112}<111> orientationrotates its orientation to the twinned position CuT {552}<115>. Meanwhile, underthe continuous action of the dislocation mechanism, the CuT {552}<115> rotates toG{011}<100> orientation, and the G{011}<100> rotates to B{011}<211>. After therotation, the intensities of textures vary with the strain.
论文主要内容包括：
1、结合已有Fe-Mn相图的研究结果和热力学计算，确定了5种低碳TWIP钢和4种中碳TWIP钢。采用金相、X射线衍射法、透射电子显微分析对九种不同成分TWIP钢变形前后的组织进行观察。讨论了热处理工艺和合金元素对TWIP钢显微组织形貌和不同组织体积分数的影响。结果表明，1#钢的金相组织由奥氏体和第二相组成，变形过程中不产生形变孪晶；其余几种钢随着锰含量的增加，组织为全奥氏体，且变形过程中产生大量形变孪晶。
2、对九种TWIP钢在10-5～103s-1应变速率范围的室温拉伸性能进行了研究。结果表明，静态拉伸时，随着应变速率的升高，1#~5#材料的屈服强度增大，1#钢和2#钢抗拉强度下降，3#~5#钢抗拉强度变化不大；1#钢的均匀延伸率和断裂延伸率增大，2#~5#钢的均匀延伸率和断裂延伸率下降。z1#~z4#钢的屈服强度相差不大，抗拉强度略微下降，z1#~z4#钢的均匀延伸率、断裂延伸率和强塑积随应变速率的升高而下降；而与静态拉伸条件下相比，动态拉伸时，随着应变速率增加，2#~5#钢的屈服强度和抗拉强度增大，均匀延伸率变化不大，断裂延伸率有所上升。1#~5#钢均体现出显著的应变速率敏感性。动态拉伸条件下的屈服强度和抗拉强度要高，z1#~z4#钢的总延伸率较静态拉伸条件下都有所下降。
3、利用XRD分析了奥氏体的转变量随应变和应变速率的变化规律。结果发现，1#钢和2#钢变形过程中发生了马氏体相变，而3#钢变形过程中没有发生马氏体相变。奥氏体转变量随应变速率的增加而减小，随应变量的增加而增加。
4、分析研究了应变硬化指数n值随应变速率和应变的变化规律。结果表明：试验钢在拉伸过程中的应变硬化表现为阶段性多n值行为。1#钢的n值随应变呈抛物线关系，遵循关系式：n=aε2+bε+c；其它钢的n值与应变呈对数关系，遵循关系式： n=alnε+b。其应变硬化机制有两种：0.4%～3%左右应变区间为位错强化阶段，10％～50%左右应变区间为孪晶强化阶段。在此两个区间内n值皆为定值，而在4％～10％应变区间n值呈不断上升趋势。奥氏体的应变诱发相变和变形过程中产生的形变孪晶显著影响TWIP钢的应变硬化能力。
5、采用SEM检测了TWIP钢动态拉伸后的组织形态。结果发现，TWIP钢具有典型的延性断裂断口特征，其变形和断裂过程为微孔洞的形核、长大和聚合。含有第二相的TWIP钢（如1#钢）的断裂机制为：第二相和奥氏体相界面聚合力的减弱促使微孔形核，形变过程中产生的应力集中使微孔长大、聚合直至发生断裂。全奥氏体的TWIP钢（如5#钢）断裂机制为：形变过程中位错的运动受孪晶界的阻碍，形变孪晶与位错的交互作用使微孔形核于孪晶界处，应力集中使微孔长大、聚合直至材料发生断裂。
6、TWIP钢的变形机制主要为孪晶变形机制，其次为位错变形机制。在孪晶变形机制下，随着应变的增加、孪晶含量的增多，铜型织构转到其孪晶取向的位置CuT{552}<115>，在经过滑移机制作用下，CuT{552}<115>转变为G织构，原有的及新形成的G织构转变为B织构。织构转变后的强度随着应变率的不同而有所不同。
Deformation twins，martensite phase transformation and mechanical propertieshad been investigated. For steels with higher stacking fault energy，twinning is themain deformation mechanism. TWIP（Twinning Induced Plasticity）steels exhibit hightensile strength (650～1100MPa), extremely large elongation rate(19%~90%). Themicrostructures, mechanical properties and fracture behaviors of nine differentcomposition TWIP steels were investigated. Tensile tests were carried out at differentstrain rates, and the tensile strain behaviors under various strain rates of nine differentcomposition TWIP steels were investigated. The dynamic tensile tests were carriedout on the pneumatic indirect bar-bar tensile impact tester. The formation of twins andmartensite were analyzed by optical microscopy, XRD， SEM and TEM. Thecontribution of the dissertation lies in providing theoretical basis for lighting weightand anti-crashing of automobiles.
The primary coverage of the dissertation includes:
(1) The components of five kinds of low carbon TWIP steel and four kinds ofmedium carbon TWIP steel are determined based the research results of Fe-Mn phasediagram and the thermodynamic calculation. The microstructures of nine differentMn-content TWIP steels before and after deformation are investigated bymetallography, XRD and TEM. The effects of heat treatment and alloy elements onthe morphology and volume fraction of each phase are analyzed. The results showthat the microstructure of steel1#is composed of austenite and second-phase. Withthe increasing of manganese content, the microstructure of the TWIP steels changes toaustenite totally and deformation twins occurs during deformation.
(2) The tensile tests are carried out on nine TWIP steels in the strain rate range of10-5～103s-1. The results indicate that the yield strength increases and tensile strengthof steel1#and steel2#decreases, while those of steels3#~5#, z1#~z4#change little,and the uniform elongation rate and total elongation rate of steel1#increase, while these of other steels decrease with the strain rate. During dynamic tensile stage, thetensile strength, yield strength and total elongation increase, while the uniformelongation rate hardly changes with the strain rate, showing that the TWIP steels aresensitive to strain rate.
(3) The volume fraction of austenite after deformation as a function of strain andstrain rate is investigated by XRD. The results show that martensite transformationoccurred in steel1#and steel2#, but not in steel3#. The volume fraction oftransformed austenite decreases with the strain rate, while it increases with the strain.
(4) The strain-hardening exponent n as a function of strain and strain rate isdetermined. It shows that the n value varied during tensile deformation. The n valueof steel1#obeys a parabolic relation: n=aε2+bε+c. While the n value of fullaustenite TWIP steels obeys a logarithmic relation: n=alnε+b. In the strain rangeof0.4%～4%, the full austenite TWIP steels are strengthened by dislocation piling,but in the range of10%～50%, these steels are strengthened by twinning. In these twostages, the n value keeps constant. However, the n value increases continuously in thestrain range of4%～10%. Strain induced martensite transformation and formation oftwins during deformation significantly influence the strain-hardening behavior of theTWIP steels.
(5) The microstructure of the TWIP steels after dynamic tension test wascharacterized by SEM. The fractograph of the TWIP steels exhibits a typical ductilefracture pattern. Due to the presence of second phases, nucleation of micro-voids insteel1#occurred at the weak spot in the material, i.e. the austenite/second phaseinterface. However, due to the interaction of dislocations and twins, the nucleation ofmicro-voids in the full austenite steel5#occurred at boundaries of deformation twinsas well as the interface between deformation twins and dislocations. No matter whatthe mechanism is, the nucleation is followed by the growth and coalescence of themicro-voids in all samples.
(6) In present work, the dominating deformation mechanism of the TWIP steels is twinning, also accompanied by dislocation mechanism. For the twinningmechanism, the content of twins increases with strain, and Cu{112}<111> orientationrotates its orientation to the twinned position CuT {552}<115>. Meanwhile, underthe continuous action of the dislocation mechanism, the CuT {552}<115> rotates toG{011}<100> orientation, and the G{011}<100> rotates to B{011}<211>. After therotation, the intensities of textures vary with the strain.
引文
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