高强塑积热变形淬火碳分配钢的研究
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摘要
开发低成本、加工性能和服役性能优良的高强度汽车钢,是节能减排、又保持汽车安全性的有效途径。因此,为开发具有超高强度、兼具良好塑性且成本低廉的高性能汽车钢,本文提出两种新型的钢材热变形可控淬火一体化处理方法:分别是热成形-淬火碳分配(Hot Stamping-Quenching & Partitioning, HS-QP)工艺和形变诱导铁素体相变-淬火碳分配(Deformation Induced Ferrite Transformation-Quenching & Partitioning,DIFT-QP)工艺。通过该工艺获得了高强度且具良好塑性的复相钢,其性能满足第三代汽车钢高性能的要求。并利用光学显微镜(OM)、扫描电镜(SEM)、透射电镜(TEM)、X射线衍射(XRD)、热膨胀仪和力学性能测试等多种方法研究了HS-QP和DIFT-QP先进超高强塑积钢的微观组织与力学性能。本文的主要研究内容及取得的结果如下:
首先,结合现有的研究结果,提出变形、相变和碳分配同时实现的高强度钢设计思想,即利用奥氏体区变形来细化组织,利用Q&P工艺实现对硬相马氏体和软相残余奥氏体的调控。同时,提出了一种新型的钢材热变形可控淬火一体化处理方法:热成形-淬火碳分配(HS-QP)工艺。HS-QP工艺包括:首先将钢迅速加热到奥氏体化温度等温一段时间进行热变形,使奥氏体晶粒细化。然后快速淬火到Ms和Mf之间某一淬火温度,以获得部分的过饱和马氏体和未发生马氏体相变的奥氏体。之后在特定淬火温度等温一段时间,使碳由马氏体向残余奥氏体分配,此时马氏体中的碳含量下降,奥氏体中的碳含量升高,从而使残余奥氏体富碳且能够稳定至室温。最后淬火到室温以获得细化的马氏体和残余奥氏体复相组织。通过合理的工艺参数设计,低碳硼钢(0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B)经过HS-QP处理后,其延伸率达到14%以上,抗拉强度达1500MPa以上,达到了预期目标。与仅用热成形工艺处理的性能相比,其强塑积可以从11000MPa%提高到22000MPa%。其微观组织主要是细化了的马氏体和残余奥氏体所组成的纳米级双相复合组织。残余奥氏体厚度在20~40nm之间,马氏体板条厚度在100~200nm之间。
其次,把形变诱导铁素体相变(DIFT)的细化晶粒技术引入Q&P处理工艺当中,提出了一种新型的热处理方法:形变诱导铁素体相变-淬火碳分配(DIFT-QP)工艺,利用形变诱导铁素体相变技术来细化晶粒并获得铁素体,利用Q&P工艺使钢发生相变且进行碳分配来实现对硬相马氏体和软相残余奥氏体的调控。DIFT-QP处理工艺包括:首先将钢迅速加热到奥氏体化温度等温一段时间;然后快速冷却到临界温度附近,在此温度附近进行形变诱导相变,使得晶粒细化且生成形变诱导铁素体;之后再淬火到一个特定淬火温度(Ms~Mf ),以获得马氏体和残余奥氏体组织;然后在此温度保温一段时间实现碳分配,使碳原子从过饱和马氏体到未转变奥氏体充分扩散以稳定奥氏体,高密度位错为碳原子提供有利的扩散通道。最后再淬火到室温,获得细板条位错型马氏体+细薄残余奥氏体+形变诱导铁素体的复相组织。低碳硼钢(0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B)经过合适的DIFT-QP处理,其抗拉强度达1700MPa,屈服强度超过900MPa,延伸率在15%以上,达到了预期目标,其微观组织为细板条位错型马氏体+细薄残余奥氏体+形变诱导铁素体的复相组织。并初步讨论了DIFT-QP处理过程中细化复相组织的演化规律,对DIFT-QP工艺处理过程中的马氏体形成机制进行了分析。
最后,提出了HS-QP工艺获得的细化复相组织演化模型,其演变过程为:应变初期,位错晶体学滑移而形成多种组态的小角位错界面,即亚晶界,包括变形带和位错墙等,大角度晶界的迁移性较高,原始晶界在应力作用下发生弯曲,奥氏体会形成不稳定的伸长的组织单元和亚晶。随着应变的增加,位错界面取向差增大并转变为随机取向界面,当累积应变达到一定程度后,这些亚晶会发生断裂,最终导致细晶粒的形成。形变奥氏体中的位错为随后Q&P处理时形成的马氏体所继承,马氏体转变的形核和长大会受到形变所产生的亚晶界的影响而细化,细化的马氏体组织对于细化晶粒起着重要的作用,它会在相变过程中进一步分割细小晶粒。并对变形+相变+碳分配获得细化复相组织的晶粒细化机制和塑性增强机制进行了分析。由于细化的复相组织能够使高强度钢具有较好强度和塑性,加之获得这种复合组织的工艺简单,且热变形可控淬火一体化处理工艺可以降低成本节约资源。因此,新型一体化处理工艺具有工业应用的广泛前景。
It is an effective way for energy saving, environmental protection and automobile safety to explore high strength steels, which have low cost, better processing property and service performance. Therefore, in order to develop advanced high strength steels which possess ultra-high strength with corresponding plasticity, low cost and good quality steel, we put forward two advanced heat treatment methods: Hot Stamping-Quenching & Partitioning (HS-QP) and Deformation Induced Ferrite Transformation-Quenching & Partitioning (DIFT-QP). The new types of high strength multiphase steels with corresponding plasticity were obtained through hot deformation plus Q&P process. The performances of steels meet the requirements of excellent properties of the third generation high strength automobile steel. The new designed steels were characterized and measured by means of optical microscopy (OM), scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffraction (XRD), thermal expansion device (TED) and Zwick T1-FR020TN A50 universal testing machine. The main contents and important results are showed as follows.
Firstly, according to the results of the present study, we recommend the integration of hot deformation, phase transformation and carbon partitioning can be conducted to obtain refined multiphase microstructure. Grain refinement can be realized through hot deformation at austenitizing temperature. Quenching and partitioning process is used to obtain hard phase martensite and soft phase retained austenite. Also,we put forward a technologically advanced heat treatment method of combination of hot stamping and controlled quenching: Hot Stamping-Quenching & Partitioning (HS-QP). HS-QP process includes: The first step is an austenitizing at a temperature and austenite is deformed at higher temperature so as to refine the grain size. The second step is a rapid quenching to a specific quenching temperature between martensite start temperature (Ms) and martensite finish temperature (Mf) to fabricate partially transformed supersaturated martensite and untransformed austenite. The third step is a carbon partitioning treatment from supersaturated martensite to untransformed austenite to increase the carbon content of untransformed austenite in absence of carbide formation. Finally, a refined multiphase microstructure of carbon-depleted martensite and carbon-enriched retained austenite films is fabricated at room temperature. Through proper optimize manufacturing process parameters, the new type of high strength steel (0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B) with tensile strength higher than 1500 MPa, elongation higher than 14% was obtained during the HS-QP process, and the anticipant results were achieved. Compared with the sample treated only by hot stamping, the product of strength and elongation of the sample treated by HS-QP process can increase from 11000MPa% to 22000MPa%。The results showed that a mixed microstructure of HS-QP steel was made up of refined martensite lathes (about 100~200nm) and slender interlath retained austenite (about 20~40nm).
Secondly, grain refining technique of Deformation Induced Ferrite Transformation (DIFT) is introduced to Q&P process. We proposed another novel heat treatment processes: Deformation Induced Ferrite Transformation-Quenching & Partitioning (DIFT-QP). Grain refinement and generation of ferrite can be realized through DIFT. Quenching and partitioning process is used to obtain hard phase martensite and soft phase retained austenite. DIFT-QP process includes: The first step is an austenitizing at a temperature with a period of time; The second step is a rapid quenching to a specific quenching temperature near the intercritical temperature and microstructure is deformed at this temperature so as to refine the grain size and produce ferrite. The third step is a rapid quenching to a specific quenching temperature between martensite start temperature (Ms) and martensite finish temperature (Mf) to fabricate partially transformed supersaturated martensite and untransformed austenite. The fourth step is a carbon partitioning treatment from supersaturated martensite to untransformed austenite to increase the carbon content of untransformed austenite in absence of carbide formation. High dislocation density can provide diffusing channel for carbon, which is very important to improve the stability of retained austenite. Finally, a refined multiphase microstructure of carbon-depleted martensite, carbon-enriched retained austenite films and deformation induced ferrite is fabricated at room temperature. Through proper optimize manufacturing process parameters, the new type of high strength steel (0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B) with tensile strength higher than 1700 MPa, with the yield strength above 900 MPa and elongation more than 15% was obtained during the DIFT-QP process, and the anticipant results were achieved. The refined multiphase microstructure is made up of carbon-depleted martensite, carbon-enriched retained austenite films and deformation induced ferrite. The evolution of refined multiphase microstructure of DIFT-QP process was revealed and the mechanism of martensite formation during DIFT-QP process was analyzed.
Lastly, the evolution model of refined multiphase microstructure treated by HS-QP process has been proposed: in the initial deformation stage, dislocation crystallographic slips result in the formation of multiple configuration of small angle dislocation interface, namely the sub-grain boundary, deformation zone and dislocation wall, etc. Big-angle grain boundary is easy to move in the initial deformation stage and the original grain boundary becomes curved under the condition of stress. Austenite may become unstable and elongated microstructure unit and sub-grain. With the increase of rolling reduction dislocation interface orientation convert to random orientation interface. The cumulative strain to a certain extent, these sub-grains may fracture and lead to formation of refined grain. Dislocation in austenite treated by hot deformation was inherited for the martensite during Q&P process. Nucleation and growth of martensite transformation were affected by sub-grain boundary generated by deformation. The role of refined martensite is very important to refine grain size and grain can be further segmented to small grain. Moreover, the mechanisms of microstructure refinement and elongation enhancement of the refined multiphase microstructure obtained by hot deformation, phase transformation and carbon partitioning have been analyzed. The refined multiphase microstructure can make high strength steel perform good strength and toughness and the combined heat treatment process is simple. Also, the combination of hot deformation and Q&P process can reduce cost and save resources. Therefore, the new combined heat treatment process will have wide prospect of industrial applications.
首先,结合现有的研究结果,提出变形、相变和碳分配同时实现的高强度钢设计思想,即利用奥氏体区变形来细化组织,利用Q&P工艺实现对硬相马氏体和软相残余奥氏体的调控。同时,提出了一种新型的钢材热变形可控淬火一体化处理方法:热成形-淬火碳分配(HS-QP)工艺。HS-QP工艺包括:首先将钢迅速加热到奥氏体化温度等温一段时间进行热变形,使奥氏体晶粒细化。然后快速淬火到Ms和Mf之间某一淬火温度,以获得部分的过饱和马氏体和未发生马氏体相变的奥氏体。之后在特定淬火温度等温一段时间,使碳由马氏体向残余奥氏体分配,此时马氏体中的碳含量下降,奥氏体中的碳含量升高,从而使残余奥氏体富碳且能够稳定至室温。最后淬火到室温以获得细化的马氏体和残余奥氏体复相组织。通过合理的工艺参数设计,低碳硼钢(0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B)经过HS-QP处理后,其延伸率达到14%以上,抗拉强度达1500MPa以上,达到了预期目标。与仅用热成形工艺处理的性能相比,其强塑积可以从11000MPa%提高到22000MPa%。其微观组织主要是细化了的马氏体和残余奥氏体所组成的纳米级双相复合组织。残余奥氏体厚度在20~40nm之间,马氏体板条厚度在100~200nm之间。
其次,把形变诱导铁素体相变(DIFT)的细化晶粒技术引入Q&P处理工艺当中,提出了一种新型的热处理方法:形变诱导铁素体相变-淬火碳分配(DIFT-QP)工艺,利用形变诱导铁素体相变技术来细化晶粒并获得铁素体,利用Q&P工艺使钢发生相变且进行碳分配来实现对硬相马氏体和软相残余奥氏体的调控。DIFT-QP处理工艺包括:首先将钢迅速加热到奥氏体化温度等温一段时间;然后快速冷却到临界温度附近,在此温度附近进行形变诱导相变,使得晶粒细化且生成形变诱导铁素体;之后再淬火到一个特定淬火温度(Ms~Mf ),以获得马氏体和残余奥氏体组织;然后在此温度保温一段时间实现碳分配,使碳原子从过饱和马氏体到未转变奥氏体充分扩散以稳定奥氏体,高密度位错为碳原子提供有利的扩散通道。最后再淬火到室温,获得细板条位错型马氏体+细薄残余奥氏体+形变诱导铁素体的复相组织。低碳硼钢(0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B)经过合适的DIFT-QP处理,其抗拉强度达1700MPa,屈服强度超过900MPa,延伸率在15%以上,达到了预期目标,其微观组织为细板条位错型马氏体+细薄残余奥氏体+形变诱导铁素体的复相组织。并初步讨论了DIFT-QP处理过程中细化复相组织的演化规律,对DIFT-QP工艺处理过程中的马氏体形成机制进行了分析。
最后,提出了HS-QP工艺获得的细化复相组织演化模型,其演变过程为:应变初期,位错晶体学滑移而形成多种组态的小角位错界面,即亚晶界,包括变形带和位错墙等,大角度晶界的迁移性较高,原始晶界在应力作用下发生弯曲,奥氏体会形成不稳定的伸长的组织单元和亚晶。随着应变的增加,位错界面取向差增大并转变为随机取向界面,当累积应变达到一定程度后,这些亚晶会发生断裂,最终导致细晶粒的形成。形变奥氏体中的位错为随后Q&P处理时形成的马氏体所继承,马氏体转变的形核和长大会受到形变所产生的亚晶界的影响而细化,细化的马氏体组织对于细化晶粒起着重要的作用,它会在相变过程中进一步分割细小晶粒。并对变形+相变+碳分配获得细化复相组织的晶粒细化机制和塑性增强机制进行了分析。由于细化的复相组织能够使高强度钢具有较好强度和塑性,加之获得这种复合组织的工艺简单,且热变形可控淬火一体化处理工艺可以降低成本节约资源。因此,新型一体化处理工艺具有工业应用的广泛前景。
It is an effective way for energy saving, environmental protection and automobile safety to explore high strength steels, which have low cost, better processing property and service performance. Therefore, in order to develop advanced high strength steels which possess ultra-high strength with corresponding plasticity, low cost and good quality steel, we put forward two advanced heat treatment methods: Hot Stamping-Quenching & Partitioning (HS-QP) and Deformation Induced Ferrite Transformation-Quenching & Partitioning (DIFT-QP). The new types of high strength multiphase steels with corresponding plasticity were obtained through hot deformation plus Q&P process. The performances of steels meet the requirements of excellent properties of the third generation high strength automobile steel. The new designed steels were characterized and measured by means of optical microscopy (OM), scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffraction (XRD), thermal expansion device (TED) and Zwick T1-FR020TN A50 universal testing machine. The main contents and important results are showed as follows.
Firstly, according to the results of the present study, we recommend the integration of hot deformation, phase transformation and carbon partitioning can be conducted to obtain refined multiphase microstructure. Grain refinement can be realized through hot deformation at austenitizing temperature. Quenching and partitioning process is used to obtain hard phase martensite and soft phase retained austenite. Also,we put forward a technologically advanced heat treatment method of combination of hot stamping and controlled quenching: Hot Stamping-Quenching & Partitioning (HS-QP). HS-QP process includes: The first step is an austenitizing at a temperature and austenite is deformed at higher temperature so as to refine the grain size. The second step is a rapid quenching to a specific quenching temperature between martensite start temperature (Ms) and martensite finish temperature (Mf) to fabricate partially transformed supersaturated martensite and untransformed austenite. The third step is a carbon partitioning treatment from supersaturated martensite to untransformed austenite to increase the carbon content of untransformed austenite in absence of carbide formation. Finally, a refined multiphase microstructure of carbon-depleted martensite and carbon-enriched retained austenite films is fabricated at room temperature. Through proper optimize manufacturing process parameters, the new type of high strength steel (0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B) with tensile strength higher than 1500 MPa, elongation higher than 14% was obtained during the HS-QP process, and the anticipant results were achieved. Compared with the sample treated only by hot stamping, the product of strength and elongation of the sample treated by HS-QP process can increase from 11000MPa% to 22000MPa%。The results showed that a mixed microstructure of HS-QP steel was made up of refined martensite lathes (about 100~200nm) and slender interlath retained austenite (about 20~40nm).
Secondly, grain refining technique of Deformation Induced Ferrite Transformation (DIFT) is introduced to Q&P process. We proposed another novel heat treatment processes: Deformation Induced Ferrite Transformation-Quenching & Partitioning (DIFT-QP). Grain refinement and generation of ferrite can be realized through DIFT. Quenching and partitioning process is used to obtain hard phase martensite and soft phase retained austenite. DIFT-QP process includes: The first step is an austenitizing at a temperature with a period of time; The second step is a rapid quenching to a specific quenching temperature near the intercritical temperature and microstructure is deformed at this temperature so as to refine the grain size and produce ferrite. The third step is a rapid quenching to a specific quenching temperature between martensite start temperature (Ms) and martensite finish temperature (Mf) to fabricate partially transformed supersaturated martensite and untransformed austenite. The fourth step is a carbon partitioning treatment from supersaturated martensite to untransformed austenite to increase the carbon content of untransformed austenite in absence of carbide formation. High dislocation density can provide diffusing channel for carbon, which is very important to improve the stability of retained austenite. Finally, a refined multiphase microstructure of carbon-depleted martensite, carbon-enriched retained austenite films and deformation induced ferrite is fabricated at room temperature. Through proper optimize manufacturing process parameters, the new type of high strength steel (0.22C-1.58Mn-0.81Si-0.022Ti-0.0024B) with tensile strength higher than 1700 MPa, with the yield strength above 900 MPa and elongation more than 15% was obtained during the DIFT-QP process, and the anticipant results were achieved. The refined multiphase microstructure is made up of carbon-depleted martensite, carbon-enriched retained austenite films and deformation induced ferrite. The evolution of refined multiphase microstructure of DIFT-QP process was revealed and the mechanism of martensite formation during DIFT-QP process was analyzed.
Lastly, the evolution model of refined multiphase microstructure treated by HS-QP process has been proposed: in the initial deformation stage, dislocation crystallographic slips result in the formation of multiple configuration of small angle dislocation interface, namely the sub-grain boundary, deformation zone and dislocation wall, etc. Big-angle grain boundary is easy to move in the initial deformation stage and the original grain boundary becomes curved under the condition of stress. Austenite may become unstable and elongated microstructure unit and sub-grain. With the increase of rolling reduction dislocation interface orientation convert to random orientation interface. The cumulative strain to a certain extent, these sub-grains may fracture and lead to formation of refined grain. Dislocation in austenite treated by hot deformation was inherited for the martensite during Q&P process. Nucleation and growth of martensite transformation were affected by sub-grain boundary generated by deformation. The role of refined martensite is very important to refine grain size and grain can be further segmented to small grain. Moreover, the mechanisms of microstructure refinement and elongation enhancement of the refined multiphase microstructure obtained by hot deformation, phase transformation and carbon partitioning have been analyzed. The refined multiphase microstructure can make high strength steel perform good strength and toughness and the combined heat treatment process is simple. Also, the combination of hot deformation and Q&P process can reduce cost and save resources. Therefore, the new combined heat treatment process will have wide prospect of industrial applications.
引文
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