应变速率对不同强度级别TRIP钢力学行为影响的研究
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摘要
作为车身用钢，车身部件在成形过程中的变形速率约在10-1～10s-1之间，在汽车行驶过程中发生撞击时其变形速率则处于102～103s-1范围。因此，研发TRIP(TRansformation Induced Plasticity)钢必须了解其在各种应变速率条件下的变形行为和微观组织的演化规律；认识钢中各组成相的力学响应特性，从本质上掌握TRIP钢在各种变形速率下的强化及失效机制。
本工作以600MPa、700MPa以及900MPa级TRIP钢作为主要研究对象，同时将DP钢（Dual Phase，拉伸过程中不发生相变）作为“参照系”展开实验分析。首先采用电子万能试验机、旋转盘式杆杆型冲击拉伸试验机和Zwick HTM5020并辅以红外测温仪对TRIP钢在不同应变率条件下的力学行为进行了分析，而后采用光学显微镜(OM)、扫描电镜(SEM)、透射电镜（TEM）等对拉伸前、后TRIP钢中的组织形貌进行了观察。此外，采用内耗仪以及原位测试试验装置对钢中相变行为进行了研究，并结合相图热力学理论对TRIP钢相变行为进行了初步的揭示。主要研究结果如下：
1、通过对实验钢在0.001～2000s-1应变率范围内的力学研究发现：随着应变速率的提高，三种TRIP钢的屈服强度、抗拉强度都增加，而断裂延伸率则先减小后增加，在应变速率600s-1附近时，三种TRIP钢断裂延伸率都达到最小；600MPa级TRIP钢应变率敏感性最大，不同应变速率下其强度和延伸率波动都最大。变形局部化导致动态下的TRIP钢和DP钢断裂延伸率都比静态下小，高应变速率下的绝热温升效应使得TRIP钢和DP钢的断裂延伸率增大。DP钢的绝热温升效应大于变形局部化效应，导致2000s-1应变速率下DP钢的断裂延伸率超过静态时的水平；TRIP钢中残余奥氏体“渐进式相变”被变形局部化所抑制，造成动态下TRIP钢的断裂延伸率无法达到静态时的水平。
2、TRIP钢的力学性能主要取决于残余奥氏体的含量和稳定性，通过对600MPa、700MPa以及900MPa级TRIP钢进行原位测试试验发现：600MPa级TRIP钢在屈服结束之后才产生马氏体相变，700MPa和900MPa级TRIP钢中的残余奥氏体分别在外加载荷502MPa(σ0.2=486MPa)和657.8MPa(σ0.2=538.8MPa)时产生向马氏体的转变；由此可以认为，TRIP钢中的残余奥氏体向马氏体的相变是应变导致相变。另外，通过TRIP钢在不同热处理条件下的残余奥氏体含量随应变转变的实验数据和文献中的相关数据，建立起残余奥氏体量与应变量的关系式，该公式预测的结果与实验结果符合的较好。
3、钢的马氏体转变开始温度（Ms点）对分析马氏体相变过程，指导合金设计，制定热处理工艺方面有重要意义。基于马氏体相变热力学和亚点阵模型，建立了Fe-C-Mn-Si系合金马氏体相变自由能表达式；利用Compaq VisualFortran6软件自行编写程序，应用Thermo-Calc软件及TQ接口模块，成功预测了不同成分Fe-C-Mn-Si系合金的Ms温度；
4、建立了TRIP钢静态下真应力-真应变表达式，该公式模拟的曲线与实验获得的数据非常吻合。结合前面残余奥氏体量与应变量的关系式和Ms温度计算方法，利用该表达式对残余奥氏体发生马氏体相变所需要的功做出量化描述。
5、在对TRIP钢变形与断裂机理研究时发现：TRIP钢的断裂形式为微孔洞的形核、长大和聚合引起的延性断裂。随着应变率增加孔洞长大速率增加，残余奥氏体的形变诱发相变延缓或者抑制孔洞的形核、减缓孔洞的长大速率，动态拉伸过程中孔洞主要集中在铁素体中。相同铁素体含量的DP钢的微孔洞形成临界应变量比TRIP钢的要小。在600MPa级TRIP钢准静态拉伸断裂后的颈缩区域中同时观察到孤岛状和薄膜状两种形态的残余奥氏体，而在动态拉伸后的断裂试样的颈缩区仅发现了薄膜状残余奥氏体。
When applied to manufacture car body parts, the steel is deformed at a rate inthe range of10-1～10s~(-1).Nevertheless, during a car crash, the steel is deformed at arate up to102～103s~(-1).Therefore, to clarify the mechanical behavior andmicrostructure evolution under various strain rates becomes a critical important topicduring the development of TRIP (TRansformation Induced Plasticity) steel. Withinthis topic, it is crucial to understand the mechanical response of each phase of thematerial and elucidate the strengthening and failure mechanism under various strainrates.
Three grades of TRIP-aided steels,600MPa、700MPa and900MPa, wereselected in the current work. A Dual Phase steel (DP) is employed as a reference dueto its characteristic of no phase transformation during dynamic impact. Themechanical behaviors of samples were investigated by universal material testmachine, rotation disk bar-bar tensile impact apparatus as well as high-speedmaterial testing machine Zwick HTM5020equipped with an infrared radiationthermometer. The microstructure of the samples before and after tensile test wascharacterized by OM (optical microscopy), SEM (scanning electron microscope) andTEM (transmission electron microscope). Moreover, the phase transformationbehaviors of steels were investigated by thermodynamics and experiments via aninternal friction instrument plus an in-situ tensile test apparatus. The mainconclusions can be drawn as follows:
1, The results of mechanical behaviors show that the yield strength and tensilestrength of TRIP-aided steels increase with the strain rate in the range of0.001～2000s~(-1). The elongation to fracture of TRIP-aided steels firstly decrease with strainrate, then increase as the rate reached around600s~(-1).600MPa grade TRIP-aided steelhas the biggest strain rate sensitivity because its strength and elongation are most fluctuant. Compared with the situation under static tensile load, the localization ofdeformation leads to even lower fracture elongation, while the adiabatic heating athigh strain rate leads to the increase of fracture elongation. Since the influence ofadiabatic heating is greater than that of deformation localization under the rate of2000s~(-1), DP steel shows higher elongation to fracture compared with that under statictensile load. Because the “gradual transformation” of retained austenite is inhibitedby deformation localization, TRIP-aided steels show lower elongation than thatunder static tensile load.
2, The mechanical properties of TRIP-aided steel mainly depends on the contentand stability of retained austenite. The in-situ tensile test results of three grades ofTRIP-aided steels show that the martensite transformation in600MPa gradeTRIP-aided steel only occurred after the yielding stage, and the retained austenite in700MPa and900MPa grade TRIP-aided steel transform to martensite at the appliedload502MPa(σ0.2=486MPa) and657.8MPa(σ0.2=538.8MPa). It can be concludedthat this martensite transformation is caused by the strain. Furthermore, this workdetermined a relationship between the content of retained austenite and strain. Therelationship is based on experiment results on strain induced transformation behaviorof retained austenite and some other data from literatures. It shows that theprediction of this expression accords very well with the experiment results.
3, The martensite transformation start temperature is of great importance forunderstanding the martensite transformation, designing new alloys and establishingthe heat treatment procedures. Based on the thermodynamics of martensitetransformation and sub-lattice model, this work worked out the expression of Gibbsenergy for martensite transformation of Fe-C-Mn-Si alloy. Combined withThermo-Calc and TQ interface, modeling with Compaq Visual FORTRAN6wascarried out to calculate the Ms temperature of Fe-C-Mn-Si alloy.
4, Established the relationship between the real stress and real strain. And themodeling results agree well with the experiment. Combined with the relationship between retained austenite and strain as well as the Ms temperature model, it made aquantitative description about the energy of martensitic transformation of retainedaustenite.
5, The investigation on the mechanism of fracture shows that TRIP-aided steelsshow a typical ductile fracture pattern including the nucleation, growth andcoalescence of micro-voids. The growth rate of micro-voids increases with the strainrate. And the nucleation and growth of micro-voids are retarded by the strain inducedtransformation of retained austenite. Moreover, the micro-voids are mainlydistributed in ferrite under dynamic tensile load. The critical strain for formation ofmicro-voids in TRIP-aided steels is higher than that in DP steel which possesses thesame content of ferrite with the former. For600MPa grade TRIP-aided steel, islandand film shaped retained austenite was detected in necking zone after static tensiletest, while only film shaped retained austenite was detected in necking zone afterdynamic tensile test.
本工作以600MPa、700MPa以及900MPa级TRIP钢作为主要研究对象，同时将DP钢（Dual Phase，拉伸过程中不发生相变）作为“参照系”展开实验分析。首先采用电子万能试验机、旋转盘式杆杆型冲击拉伸试验机和Zwick HTM5020并辅以红外测温仪对TRIP钢在不同应变率条件下的力学行为进行了分析，而后采用光学显微镜(OM)、扫描电镜(SEM)、透射电镜（TEM）等对拉伸前、后TRIP钢中的组织形貌进行了观察。此外，采用内耗仪以及原位测试试验装置对钢中相变行为进行了研究，并结合相图热力学理论对TRIP钢相变行为进行了初步的揭示。主要研究结果如下：
1、通过对实验钢在0.001～2000s-1应变率范围内的力学研究发现：随着应变速率的提高，三种TRIP钢的屈服强度、抗拉强度都增加，而断裂延伸率则先减小后增加，在应变速率600s-1附近时，三种TRIP钢断裂延伸率都达到最小；600MPa级TRIP钢应变率敏感性最大，不同应变速率下其强度和延伸率波动都最大。变形局部化导致动态下的TRIP钢和DP钢断裂延伸率都比静态下小，高应变速率下的绝热温升效应使得TRIP钢和DP钢的断裂延伸率增大。DP钢的绝热温升效应大于变形局部化效应，导致2000s-1应变速率下DP钢的断裂延伸率超过静态时的水平；TRIP钢中残余奥氏体“渐进式相变”被变形局部化所抑制，造成动态下TRIP钢的断裂延伸率无法达到静态时的水平。
2、TRIP钢的力学性能主要取决于残余奥氏体的含量和稳定性，通过对600MPa、700MPa以及900MPa级TRIP钢进行原位测试试验发现：600MPa级TRIP钢在屈服结束之后才产生马氏体相变，700MPa和900MPa级TRIP钢中的残余奥氏体分别在外加载荷502MPa(σ0.2=486MPa)和657.8MPa(σ0.2=538.8MPa)时产生向马氏体的转变；由此可以认为，TRIP钢中的残余奥氏体向马氏体的相变是应变导致相变。另外，通过TRIP钢在不同热处理条件下的残余奥氏体含量随应变转变的实验数据和文献中的相关数据，建立起残余奥氏体量与应变量的关系式，该公式预测的结果与实验结果符合的较好。
3、钢的马氏体转变开始温度（Ms点）对分析马氏体相变过程，指导合金设计，制定热处理工艺方面有重要意义。基于马氏体相变热力学和亚点阵模型，建立了Fe-C-Mn-Si系合金马氏体相变自由能表达式；利用Compaq VisualFortran6软件自行编写程序，应用Thermo-Calc软件及TQ接口模块，成功预测了不同成分Fe-C-Mn-Si系合金的Ms温度；
4、建立了TRIP钢静态下真应力-真应变表达式，该公式模拟的曲线与实验获得的数据非常吻合。结合前面残余奥氏体量与应变量的关系式和Ms温度计算方法，利用该表达式对残余奥氏体发生马氏体相变所需要的功做出量化描述。
5、在对TRIP钢变形与断裂机理研究时发现：TRIP钢的断裂形式为微孔洞的形核、长大和聚合引起的延性断裂。随着应变率增加孔洞长大速率增加，残余奥氏体的形变诱发相变延缓或者抑制孔洞的形核、减缓孔洞的长大速率，动态拉伸过程中孔洞主要集中在铁素体中。相同铁素体含量的DP钢的微孔洞形成临界应变量比TRIP钢的要小。在600MPa级TRIP钢准静态拉伸断裂后的颈缩区域中同时观察到孤岛状和薄膜状两种形态的残余奥氏体，而在动态拉伸后的断裂试样的颈缩区仅发现了薄膜状残余奥氏体。
When applied to manufacture car body parts, the steel is deformed at a rate inthe range of10-1～10s~(-1).Nevertheless, during a car crash, the steel is deformed at arate up to102～103s~(-1).Therefore, to clarify the mechanical behavior andmicrostructure evolution under various strain rates becomes a critical important topicduring the development of TRIP (TRansformation Induced Plasticity) steel. Withinthis topic, it is crucial to understand the mechanical response of each phase of thematerial and elucidate the strengthening and failure mechanism under various strainrates.
Three grades of TRIP-aided steels,600MPa、700MPa and900MPa, wereselected in the current work. A Dual Phase steel (DP) is employed as a reference dueto its characteristic of no phase transformation during dynamic impact. Themechanical behaviors of samples were investigated by universal material testmachine, rotation disk bar-bar tensile impact apparatus as well as high-speedmaterial testing machine Zwick HTM5020equipped with an infrared radiationthermometer. The microstructure of the samples before and after tensile test wascharacterized by OM (optical microscopy), SEM (scanning electron microscope) andTEM (transmission electron microscope). Moreover, the phase transformationbehaviors of steels were investigated by thermodynamics and experiments via aninternal friction instrument plus an in-situ tensile test apparatus. The mainconclusions can be drawn as follows:
1, The results of mechanical behaviors show that the yield strength and tensilestrength of TRIP-aided steels increase with the strain rate in the range of0.001～2000s~(-1). The elongation to fracture of TRIP-aided steels firstly decrease with strainrate, then increase as the rate reached around600s~(-1).600MPa grade TRIP-aided steelhas the biggest strain rate sensitivity because its strength and elongation are most fluctuant. Compared with the situation under static tensile load, the localization ofdeformation leads to even lower fracture elongation, while the adiabatic heating athigh strain rate leads to the increase of fracture elongation. Since the influence ofadiabatic heating is greater than that of deformation localization under the rate of2000s~(-1), DP steel shows higher elongation to fracture compared with that under statictensile load. Because the “gradual transformation” of retained austenite is inhibitedby deformation localization, TRIP-aided steels show lower elongation than thatunder static tensile load.
2, The mechanical properties of TRIP-aided steel mainly depends on the contentand stability of retained austenite. The in-situ tensile test results of three grades ofTRIP-aided steels show that the martensite transformation in600MPa gradeTRIP-aided steel only occurred after the yielding stage, and the retained austenite in700MPa and900MPa grade TRIP-aided steel transform to martensite at the appliedload502MPa(σ0.2=486MPa) and657.8MPa(σ0.2=538.8MPa). It can be concludedthat this martensite transformation is caused by the strain. Furthermore, this workdetermined a relationship between the content of retained austenite and strain. Therelationship is based on experiment results on strain induced transformation behaviorof retained austenite and some other data from literatures. It shows that theprediction of this expression accords very well with the experiment results.
3, The martensite transformation start temperature is of great importance forunderstanding the martensite transformation, designing new alloys and establishingthe heat treatment procedures. Based on the thermodynamics of martensitetransformation and sub-lattice model, this work worked out the expression of Gibbsenergy for martensite transformation of Fe-C-Mn-Si alloy. Combined withThermo-Calc and TQ interface, modeling with Compaq Visual FORTRAN6wascarried out to calculate the Ms temperature of Fe-C-Mn-Si alloy.
4, Established the relationship between the real stress and real strain. And themodeling results agree well with the experiment. Combined with the relationship between retained austenite and strain as well as the Ms temperature model, it made aquantitative description about the energy of martensitic transformation of retainedaustenite.
5, The investigation on the mechanism of fracture shows that TRIP-aided steelsshow a typical ductile fracture pattern including the nucleation, growth andcoalescence of micro-voids. The growth rate of micro-voids increases with the strainrate. And the nucleation and growth of micro-voids are retarded by the strain inducedtransformation of retained austenite. Moreover, the micro-voids are mainlydistributed in ferrite under dynamic tensile load. The critical strain for formation ofmicro-voids in TRIP-aided steels is higher than that in DP steel which possesses thesame content of ferrite with the former. For600MPa grade TRIP-aided steel, islandand film shaped retained austenite was detected in necking zone after static tensiletest, while only film shaped retained austenite was detected in necking zone afterdynamic tensile test.
引文
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