铁素体/珠光体型钢板内部质量及其影响因素研究
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摘要
钢铁工业中发展最迅速、最富有活力的钢种是低合金高强度钢,特别是屈服强度在500MPa以下的铁素体／珠光体型钢,该类型钢具备优良的强韧性能,是目前应用最广泛的钢种之一。目前生产铁素体/珠光体型钢的主要途径是在C-Mn钢或C-Mn-Si钢基础上添加微量合金元素铌、钒、钛等,通过TMCP (ThermoMechanical Control Process)工艺控制微合金碳氮化合物的析出和过冷奥氏体的相变行为,以达到优化组织、提高强韧性的目的。国内外研究者长期致力于提升铁素体/珠光体型钢板内部质量的研究,所谓钢板内部质量的好坏,实际上是指钢板内部组织的均匀性和完整性。就一定厚度的钢板而言,无论工艺如何改变,都将出现厚度方向从表层到心部的组织不一致,诸如：晶粒尺寸差异、铁素体形态差异及析出相分布和尺寸差异等。另外,如果钢板的成分设计不合理或工艺控制不当,就可能导致钢板内部出现非铁素体／珠光体组织及其它类型缺陷。
通过调研国内几家大型钢铁生产企业及工程机械和煤机制造企业,并查阅文献,发现部分批次的铁素体/珠光体型钢板存在内部质量缺陷,尤以分层缺陷最为突出。国内外学者、钢铁生产企业和用户均已发现钢板中的分层缺陷及其对力学性能的不良影响。但是,目前对分层缺陷的成因仍无统一认识,特别是有关连铸坯中心偏析是如何影响热轧钢板分层缺陷这一重要问题尚无深入阐述。对照研究有分层缺陷和无分层缺陷的钢板,发现有分层缺陷钢板的Mn元素含量普遍偏高,另外,部分企业生产的钢板仍然存在其它微合金元素使用过量的情况。
针对以上两类问题,本文优化了合金成分设计、TMCP工艺和连铸工艺；采用透射电子显微镜(TEM)、扫描俄歇微探针(SAM)、金属原位分析仪及力学性能检测等手段,分析了实验室试轧和工业化生产的钢板微观组织和力学性能。研究了连铸坯中心偏析与热轧钢板分层缺陷的继承性关系,并从热力学和动力学方面揭示了钢板中异常偏析带的形成机理。在此基础上得出各因素(包括：合金成分、连铸工艺、TMCP工艺及后期热处理)对钢板内部质量的影响规律。主要研究内容和结论如下：
1.通过研究C、Mn、Si、Nb、V、Ti等合金元素在钢中的作用,得出了合金成分减量后的铁素体/珠光体型钢板成分设计。本试验钢以C、Mn、Si作为基本元素,添加适量的Nb、V、Ti微合金元素,以及微量的B元素并尽量降低P、S等有害元素含量,与目前国内市场商用钢种的合金成分对比得出,本试验钢的合金元素加入量明显低于同级别商用钢种。用Gleeble热／力模拟方法测定了试验钢的再结晶曲线和CCT曲线等,优化了TMCP工艺参数,试验钢的奥氏体化温度为1200℃,粗轧阶段初期前4道次设定压下量8.5mm以下以增大再结晶晶粒的体积分数,末道次采取较大压下量以细化奥氏体晶粒,终轧温度控制在1020℃；精轧阶段开轧温度控制在900℃以下,避开900℃～1000℃部分再结晶温度区间,终轧温度控制在830～850℃；冷却速度根据钢板厚度控制在5～10℃/s,终冷温度控制在670～690℃,控冷后直接空冷至室温。设计钢板的工业化试验表明：新工艺流程顺畅,合金成本低于目前同级别的商用钢种,可以实现批量化生产。
2.通过热力学与动力学计算,结合TEM观察和EDS能谱分析研究了钢板中微合金碳氮化物在TMCP工艺过程中的固溶和析出规律,从细晶强化、固溶强化和析出强化等方面分析了钢板的强韧化机理。结果表明,微合金碳氮化物主要有TiN、VC和Nb(C,N),TiN的固溶和析出温度较高,形态经历了由球形向方形的长大过程,常与VC和Nb(C,N)复合析出,可以有效阻止奥氏体化过程及粗轧再结晶后的晶粒长大；VC呈圆片状,主要是在γ→α转变后的冷却过程中于铁素体晶粒内部共格随机析出的,引起钢板的析出强化；Nb(C,N)呈圆片状,尺寸约10nm,主要在晶界和位错附近形核,并在γ→α转变过程中析出,可以有效钉扎位错运动,强烈阻止形变奥氏体再结晶,具有一定的晶粒细化效果。按照位错绕过析出相的Orowan机制,计算得到析出强化产生的强度增量为143.9MPa,细晶强化产生的强度增量为261.9MPa,固溶强化产生的强度增量为92MPa,设计钢板的计算强度值为497.8MPa。由于细晶强化产生的强化效果超过总强度的40%,因此设计钢板具有良好的塑韧性能。
3.用金属原位分析仪等研究了连铸坯不同位置的化学成分分布,采取理论计算和统计分析的方法探讨了钢水过热度、二冷水强度、拉速、电磁搅拌及轻压下工艺与连铸坯内部质量和厚度方向组织之间的关系。结果表明,部分批次连铸坯中心处存在明显的C、Mn、S和P元素偏析,Gleeble热／力模拟试验表明,连铸坯热变形后在原中心偏析区出现了带状分布的贝氏体组织。TEM观察发现由连铸坯表层至中心处硫化物夹杂量逐渐增加,且在中心出现聚集分布,这些都与连铸坯中心处Mn偏析有关。控制合理的连铸工艺参数,将钢水过热度控制在30℃以内,适当增强二冷水强度、合理选择连铸坯拉速、控制电磁搅拌频率、选择适当位置进行适度轻压下等措施可以有效改善连铸坯内部质量。
4.用SEM和SAM等观察了工业化生产的钢板表层、1/4厚度和中心厚度处的微观组织,分别在对应厚度处截取薄试样测量局部区域的力学性能,并从热力学和动力学方面揭示异常偏析带的形成机理。结果表明,有分层缺陷钢板的中心处存在粒状贝氏体异常偏析带和一定程度的混晶,同时存在较多的硫化物夹杂,以上三个因素导致钢板出现分层缺陷。研究得出钢板异常偏析带区存在明显的C-Mn元素偏聚,钢板中的Mn偏聚继承自连铸坯的Mn偏析,异常偏析带区贝氏体的形成与连铸坯中心Mn偏析有直接关系。连铸坯中心处C-Mn偏聚形成的Fe-Mn-C原子团有效束缚了原子运动,增加了奥氏体相变时的晶格重构阻力,为贝氏体的形成创造了热力学条件；C-Mn偏聚使连铸坯中心处C曲线中珠光体转变曲线和贝氏体转变曲线发生相对位移,致使原来的C曲线形状变为河湾形状,为较低冷速下该区域的过冷奥氏体转变为贝氏体创造了动力学条件。有分层缺陷钢板的最佳正火处理工艺为900℃×3min/mm,该正火工艺无法消除Mn元素的偏析,但可以通过扩散降低异常偏析带区的C含量,并使异常偏析带区的贝氏体完全转变为珠光体,同时达到了消除钢板分层缺陷的目的。
The quickest developed and most invigorated steel grade in the steel industry is low alloy and high strength steel, especially the ferrite/pearlite steel with the yield strength below500MPa. This type steel has excellent strength and toughness properties, which is currently one of the most widely used steel grades. At present, the main production technology of ferrite/pearlite steel is adding trace Nb, V, Ti and other microalloying elements to C-Mn steel or C-Mn-Si steel. The precipitation behavior of microalloying carbonitrides, and the phase transition behavior of overcooling austenite were controlled by TMCP (ThermoMechanical Control Process) technology, in order to achieve the goal of optimizing microstructure and improving strength and toughness properties. The researchers at home and aboard are committed to the study of improving the internal quality of ferrite/pearlite steel plate for a long time. The so-called good or bad of internal quality of the steel plate, actually refers to the uniformity and integrity of microstructure of the steel plate. For the steel plate of a certain thickness, whatever the technology how to change, the microstructure will appear inconformity from the surface to the center along thickness direction of steel plate, such as the difference of grain size, the morphology difference of ferrite, also the distribution and size difference of precipitates, et al. In addition, if the composition design is unreasonable or the technology is improper, which may cause non ferrite/pearlite structure or other defects internal the steel plate.
Through surveying some domestic large scale iron and steel enterprises, engineering machinery and coal machine manufacturing enterprises, also a large number of literatures, we found that some batches of ferrite/pearlite steel plate appeared internal quality defects, especially the lamination defect. Scholars from home and aboard, steelmakers and users have found the lamination defect of steel plates and its adverse influence on mechanical properties. However, at present, there is no unified understanding on the cause of lamination defect, particularly, there is no elaboration about the influence of central segregation of billets on lamination of hot rolled steel plates. We found that the content of Mn element of the steel plate with lamination defect was generally higher through comparatively study on the steel plate with lamination defect and without lamination defect. In addition, we found the steel plates from some steelmakers still used excess other microalloying elements.
Pointing at these two problems above, the alloying composition design, TMCP technology and continuous casting technology were optimized; the microstructure and mechanical properties of steel plates from laboratory and industrial production were analyzed, with the means of Transmission Electron Microscopy (TEM), Scanning Auger Microprobe (SAM), Original Position Analyzer (OPA) and measurement of mechanical properties, et al.The inherited relation between central segregation of billets and lamination defect of hot rolled steel plates was researched, also the cause of abnormal segregation band was revealed from kinetics and thermodynamics. On this basis, we concluded the influences of the factors (such as, alloying composition, continuous casting technology, TMCP technology and heat treatment) on internal quality of steel plates. The research contents and conclusions are follows:
1. The reducing composition design of ferrite/pearlite steel plate was derived through studying the role of C, Mn, Si, Nb, V, Ti and other alloying elements in the steel plate. The essential elements such as C, Mn, Si, moderate microalloying elements such as Nb, V, Ti, and trace B element was adding to this experimental steel, also minimizing P, S and other harmful elements. Through contrasting the alloying composition of domestic commercial steels at present, it is derived that the addition of alloying elements of this experimental steel is significantly lower than that of commercial steels of the same level. The recrystallization curves and CCT curves of the experimental steel were determinated with the method of Gleeble thermal/mechanical simulation, and then the TMCP process was optimized. The austenitizing temperature of the experimental steel is1200℃. The first four passes of roughing rolling stage can be set below8.5mm in order to increase the volume fraction of recrystallized grains, and big reduction should be taken at last passes in order to refine austenite grains. The finishing rolling temperature can be controlled at1020℃. In the finishing rolling stage, the finishing rolling temperature can be controlled at830～850℃, and the cooling rate can be controlled at5～10℃/s according to the thickness of steel plates. The finishing cooling temperature can be controlled at670～690℃, then directly air cooling to room temperature after controlled cooling. The industrial experimental of designed steel plate indicates that the new technology is smooth, and the alloying cost is lower than that of commercial steels of the same level at present, also the mass production can be achieved.
2. Through thermodynamic and kinetic calculations, combined with TEM observation and EDS analysis, the soluting and precipitating behaviors of microalloying carbonitrides during TMCP process were researched. The strengthening and toughening mechanism of the steel plate was analyzed from grain refining, solid solution strengthening and precipitation strengthening. Results indicate that, microalloying carbonitrides of steel plates are mainly TiN、VC and Nb(C,N). The soluting and precipitating temperature of TiN is high. TiN experiences the growth process from sphericity to square, and forms diphase precipitate with VC and Nb(C,N), which can effectively suppress the coarsening of recrystallized grains during the austenitizing and roughing rolling stage. VC with shape of disk, mainly precipitating coherently and randomly at the ferrite interior during cooling after γ→α transformation, can cause the precipitation strengthening of steel plate. Nb(C,N) with shape of disk, its size is about10nm, mainly nucleates at grain boundaries and dislocations, and precipitates during γ→α transformation. They can effectively pin the dislocations motion, strongly discourage the recrystallization of deformed austenite, and have certain extent of grain refinement. According to the Orowan mechanism of dislocations rounding the precipitates, it is calculated that the strength increment from precipitation strengthening is143.9MPa, the strength increment from grain refining is261.9MPa, the strength increment from solid solution strengthening is92MPa, and the calculated strength of designed steel plate is497.8MPa. Due to the strength increment from grain refining is over40%of the total strength, the designed steel plate has well plasticity and toughness.
3. The composition distribution at different positions along thickness direction of the continuous casting billet was researched by Original Position Analyzer, also the relationship between the technology (molten steel superheat, second cooling intensity, casting speed, electromagnetic stirring, light reduction technology) and internal quality, microstructure along thicknees direction of the continuous casting billet were discussed by theoretical calculations and statistical analysis. Results indicate that, the center of some batches of billets appear obvious C, Mn, S and P element segregation. Gleeble thermal/mechanical simulation experiment shows that, after hot deformation of the billet with central segregation, banded bainitic structure appears at the original segregation region. TEM observation shows that the quantity of sulfide inclusions increases from the surface to the center, and the inclusions appear aggregated distribution at the center. Controlling reasonable continuous casting technology parameters, such as controlling the molten steel superheat below30℃, reasonable stronger second cooling intensity, properly choosing the casting speed, controlling the frequency of electromagnetic stirring and choosing rational position with modest reduction, these measures can obviously improve the internal quality of continuous casting billets.
4. The microstructure of the surface,1/4thickness and center of the steel plate from industrial production was observed by SEM and SAM. The mechanical properties of local region were measured with the method of cutting thin specimens from corresponding thickness. Then the formation mechanism of abnormal segregation band was disclosed from thermodynamic and kinetics analysis. Results indicate that, the granular bainitic abnormal segregation band and a certain degree of mixed grain appear at the center of the steel plate with lamination defect, simultaneously, some sulphide inclusions appear at this region. These three factors lead to lamination defect of the steel plate. Obvious C-Mn segregation appears at the abnormal segregation region of the steel plate, and the Mn segregation of the steel plate inherites from the Mn segregation of the billet. The formation of the bainite at abnormal segregation region has immediate relationship with the central segregation of the billet. The Fe-Mn-C clusters segregation region caused by the C-Mn segregation at the center of the billet can effectively bind the atomic motion, and increase the lattice reconstruction resistance of austenite transformation, which provide thermodynamic conditions for the bainite. The C-Mn segregation causes the relative displacement of pearlite transformation curve and bainite transformation curve of the corresponding C curve at the center of the billet, so the original C curve of the center of the billet becomes bay-like shape, which creates the kinetics conditions for the transformation from undercooled austenite to bainite with lower cooling rate at this region. The best normalizing technology of the steel plate with lamination defect is900℃×3min/mm, this technology can not eliminate Mn segregation, but can decrease C content of the abnormal segregation band region by diffusing. This technology can also make the bainite of the abnormal segregation band region to transform into pearlite completely, simultaneously, achieve the purpose of eliminating the lamination defect of the steel plate.
通过调研国内几家大型钢铁生产企业及工程机械和煤机制造企业,并查阅文献,发现部分批次的铁素体/珠光体型钢板存在内部质量缺陷,尤以分层缺陷最为突出。国内外学者、钢铁生产企业和用户均已发现钢板中的分层缺陷及其对力学性能的不良影响。但是,目前对分层缺陷的成因仍无统一认识,特别是有关连铸坯中心偏析是如何影响热轧钢板分层缺陷这一重要问题尚无深入阐述。对照研究有分层缺陷和无分层缺陷的钢板,发现有分层缺陷钢板的Mn元素含量普遍偏高,另外,部分企业生产的钢板仍然存在其它微合金元素使用过量的情况。
针对以上两类问题,本文优化了合金成分设计、TMCP工艺和连铸工艺；采用透射电子显微镜(TEM)、扫描俄歇微探针(SAM)、金属原位分析仪及力学性能检测等手段,分析了实验室试轧和工业化生产的钢板微观组织和力学性能。研究了连铸坯中心偏析与热轧钢板分层缺陷的继承性关系,并从热力学和动力学方面揭示了钢板中异常偏析带的形成机理。在此基础上得出各因素(包括：合金成分、连铸工艺、TMCP工艺及后期热处理)对钢板内部质量的影响规律。主要研究内容和结论如下：
1.通过研究C、Mn、Si、Nb、V、Ti等合金元素在钢中的作用,得出了合金成分减量后的铁素体/珠光体型钢板成分设计。本试验钢以C、Mn、Si作为基本元素,添加适量的Nb、V、Ti微合金元素,以及微量的B元素并尽量降低P、S等有害元素含量,与目前国内市场商用钢种的合金成分对比得出,本试验钢的合金元素加入量明显低于同级别商用钢种。用Gleeble热／力模拟方法测定了试验钢的再结晶曲线和CCT曲线等,优化了TMCP工艺参数,试验钢的奥氏体化温度为1200℃,粗轧阶段初期前4道次设定压下量8.5mm以下以增大再结晶晶粒的体积分数,末道次采取较大压下量以细化奥氏体晶粒,终轧温度控制在1020℃；精轧阶段开轧温度控制在900℃以下,避开900℃～1000℃部分再结晶温度区间,终轧温度控制在830～850℃；冷却速度根据钢板厚度控制在5～10℃/s,终冷温度控制在670～690℃,控冷后直接空冷至室温。设计钢板的工业化试验表明：新工艺流程顺畅,合金成本低于目前同级别的商用钢种,可以实现批量化生产。
2.通过热力学与动力学计算,结合TEM观察和EDS能谱分析研究了钢板中微合金碳氮化物在TMCP工艺过程中的固溶和析出规律,从细晶强化、固溶强化和析出强化等方面分析了钢板的强韧化机理。结果表明,微合金碳氮化物主要有TiN、VC和Nb(C,N),TiN的固溶和析出温度较高,形态经历了由球形向方形的长大过程,常与VC和Nb(C,N)复合析出,可以有效阻止奥氏体化过程及粗轧再结晶后的晶粒长大；VC呈圆片状,主要是在γ→α转变后的冷却过程中于铁素体晶粒内部共格随机析出的,引起钢板的析出强化；Nb(C,N)呈圆片状,尺寸约10nm,主要在晶界和位错附近形核,并在γ→α转变过程中析出,可以有效钉扎位错运动,强烈阻止形变奥氏体再结晶,具有一定的晶粒细化效果。按照位错绕过析出相的Orowan机制,计算得到析出强化产生的强度增量为143.9MPa,细晶强化产生的强度增量为261.9MPa,固溶强化产生的强度增量为92MPa,设计钢板的计算强度值为497.8MPa。由于细晶强化产生的强化效果超过总强度的40%,因此设计钢板具有良好的塑韧性能。
3.用金属原位分析仪等研究了连铸坯不同位置的化学成分分布,采取理论计算和统计分析的方法探讨了钢水过热度、二冷水强度、拉速、电磁搅拌及轻压下工艺与连铸坯内部质量和厚度方向组织之间的关系。结果表明,部分批次连铸坯中心处存在明显的C、Mn、S和P元素偏析,Gleeble热／力模拟试验表明,连铸坯热变形后在原中心偏析区出现了带状分布的贝氏体组织。TEM观察发现由连铸坯表层至中心处硫化物夹杂量逐渐增加,且在中心出现聚集分布,这些都与连铸坯中心处Mn偏析有关。控制合理的连铸工艺参数,将钢水过热度控制在30℃以内,适当增强二冷水强度、合理选择连铸坯拉速、控制电磁搅拌频率、选择适当位置进行适度轻压下等措施可以有效改善连铸坯内部质量。
4.用SEM和SAM等观察了工业化生产的钢板表层、1/4厚度和中心厚度处的微观组织,分别在对应厚度处截取薄试样测量局部区域的力学性能,并从热力学和动力学方面揭示异常偏析带的形成机理。结果表明,有分层缺陷钢板的中心处存在粒状贝氏体异常偏析带和一定程度的混晶,同时存在较多的硫化物夹杂,以上三个因素导致钢板出现分层缺陷。研究得出钢板异常偏析带区存在明显的C-Mn元素偏聚,钢板中的Mn偏聚继承自连铸坯的Mn偏析,异常偏析带区贝氏体的形成与连铸坯中心Mn偏析有直接关系。连铸坯中心处C-Mn偏聚形成的Fe-Mn-C原子团有效束缚了原子运动,增加了奥氏体相变时的晶格重构阻力,为贝氏体的形成创造了热力学条件；C-Mn偏聚使连铸坯中心处C曲线中珠光体转变曲线和贝氏体转变曲线发生相对位移,致使原来的C曲线形状变为河湾形状,为较低冷速下该区域的过冷奥氏体转变为贝氏体创造了动力学条件。有分层缺陷钢板的最佳正火处理工艺为900℃×3min/mm,该正火工艺无法消除Mn元素的偏析,但可以通过扩散降低异常偏析带区的C含量,并使异常偏析带区的贝氏体完全转变为珠光体,同时达到了消除钢板分层缺陷的目的。
The quickest developed and most invigorated steel grade in the steel industry is low alloy and high strength steel, especially the ferrite/pearlite steel with the yield strength below500MPa. This type steel has excellent strength and toughness properties, which is currently one of the most widely used steel grades. At present, the main production technology of ferrite/pearlite steel is adding trace Nb, V, Ti and other microalloying elements to C-Mn steel or C-Mn-Si steel. The precipitation behavior of microalloying carbonitrides, and the phase transition behavior of overcooling austenite were controlled by TMCP (ThermoMechanical Control Process) technology, in order to achieve the goal of optimizing microstructure and improving strength and toughness properties. The researchers at home and aboard are committed to the study of improving the internal quality of ferrite/pearlite steel plate for a long time. The so-called good or bad of internal quality of the steel plate, actually refers to the uniformity and integrity of microstructure of the steel plate. For the steel plate of a certain thickness, whatever the technology how to change, the microstructure will appear inconformity from the surface to the center along thickness direction of steel plate, such as the difference of grain size, the morphology difference of ferrite, also the distribution and size difference of precipitates, et al. In addition, if the composition design is unreasonable or the technology is improper, which may cause non ferrite/pearlite structure or other defects internal the steel plate.
Through surveying some domestic large scale iron and steel enterprises, engineering machinery and coal machine manufacturing enterprises, also a large number of literatures, we found that some batches of ferrite/pearlite steel plate appeared internal quality defects, especially the lamination defect. Scholars from home and aboard, steelmakers and users have found the lamination defect of steel plates and its adverse influence on mechanical properties. However, at present, there is no unified understanding on the cause of lamination defect, particularly, there is no elaboration about the influence of central segregation of billets on lamination of hot rolled steel plates. We found that the content of Mn element of the steel plate with lamination defect was generally higher through comparatively study on the steel plate with lamination defect and without lamination defect. In addition, we found the steel plates from some steelmakers still used excess other microalloying elements.
Pointing at these two problems above, the alloying composition design, TMCP technology and continuous casting technology were optimized; the microstructure and mechanical properties of steel plates from laboratory and industrial production were analyzed, with the means of Transmission Electron Microscopy (TEM), Scanning Auger Microprobe (SAM), Original Position Analyzer (OPA) and measurement of mechanical properties, et al.The inherited relation between central segregation of billets and lamination defect of hot rolled steel plates was researched, also the cause of abnormal segregation band was revealed from kinetics and thermodynamics. On this basis, we concluded the influences of the factors (such as, alloying composition, continuous casting technology, TMCP technology and heat treatment) on internal quality of steel plates. The research contents and conclusions are follows:
1. The reducing composition design of ferrite/pearlite steel plate was derived through studying the role of C, Mn, Si, Nb, V, Ti and other alloying elements in the steel plate. The essential elements such as C, Mn, Si, moderate microalloying elements such as Nb, V, Ti, and trace B element was adding to this experimental steel, also minimizing P, S and other harmful elements. Through contrasting the alloying composition of domestic commercial steels at present, it is derived that the addition of alloying elements of this experimental steel is significantly lower than that of commercial steels of the same level. The recrystallization curves and CCT curves of the experimental steel were determinated with the method of Gleeble thermal/mechanical simulation, and then the TMCP process was optimized. The austenitizing temperature of the experimental steel is1200℃. The first four passes of roughing rolling stage can be set below8.5mm in order to increase the volume fraction of recrystallized grains, and big reduction should be taken at last passes in order to refine austenite grains. The finishing rolling temperature can be controlled at1020℃. In the finishing rolling stage, the finishing rolling temperature can be controlled at830～850℃, and the cooling rate can be controlled at5～10℃/s according to the thickness of steel plates. The finishing cooling temperature can be controlled at670～690℃, then directly air cooling to room temperature after controlled cooling. The industrial experimental of designed steel plate indicates that the new technology is smooth, and the alloying cost is lower than that of commercial steels of the same level at present, also the mass production can be achieved.
2. Through thermodynamic and kinetic calculations, combined with TEM observation and EDS analysis, the soluting and precipitating behaviors of microalloying carbonitrides during TMCP process were researched. The strengthening and toughening mechanism of the steel plate was analyzed from grain refining, solid solution strengthening and precipitation strengthening. Results indicate that, microalloying carbonitrides of steel plates are mainly TiN、VC and Nb(C,N). The soluting and precipitating temperature of TiN is high. TiN experiences the growth process from sphericity to square, and forms diphase precipitate with VC and Nb(C,N), which can effectively suppress the coarsening of recrystallized grains during the austenitizing and roughing rolling stage. VC with shape of disk, mainly precipitating coherently and randomly at the ferrite interior during cooling after γ→α transformation, can cause the precipitation strengthening of steel plate. Nb(C,N) with shape of disk, its size is about10nm, mainly nucleates at grain boundaries and dislocations, and precipitates during γ→α transformation. They can effectively pin the dislocations motion, strongly discourage the recrystallization of deformed austenite, and have certain extent of grain refinement. According to the Orowan mechanism of dislocations rounding the precipitates, it is calculated that the strength increment from precipitation strengthening is143.9MPa, the strength increment from grain refining is261.9MPa, the strength increment from solid solution strengthening is92MPa, and the calculated strength of designed steel plate is497.8MPa. Due to the strength increment from grain refining is over40%of the total strength, the designed steel plate has well plasticity and toughness.
3. The composition distribution at different positions along thickness direction of the continuous casting billet was researched by Original Position Analyzer, also the relationship between the technology (molten steel superheat, second cooling intensity, casting speed, electromagnetic stirring, light reduction technology) and internal quality, microstructure along thicknees direction of the continuous casting billet were discussed by theoretical calculations and statistical analysis. Results indicate that, the center of some batches of billets appear obvious C, Mn, S and P element segregation. Gleeble thermal/mechanical simulation experiment shows that, after hot deformation of the billet with central segregation, banded bainitic structure appears at the original segregation region. TEM observation shows that the quantity of sulfide inclusions increases from the surface to the center, and the inclusions appear aggregated distribution at the center. Controlling reasonable continuous casting technology parameters, such as controlling the molten steel superheat below30℃, reasonable stronger second cooling intensity, properly choosing the casting speed, controlling the frequency of electromagnetic stirring and choosing rational position with modest reduction, these measures can obviously improve the internal quality of continuous casting billets.
4. The microstructure of the surface,1/4thickness and center of the steel plate from industrial production was observed by SEM and SAM. The mechanical properties of local region were measured with the method of cutting thin specimens from corresponding thickness. Then the formation mechanism of abnormal segregation band was disclosed from thermodynamic and kinetics analysis. Results indicate that, the granular bainitic abnormal segregation band and a certain degree of mixed grain appear at the center of the steel plate with lamination defect, simultaneously, some sulphide inclusions appear at this region. These three factors lead to lamination defect of the steel plate. Obvious C-Mn segregation appears at the abnormal segregation region of the steel plate, and the Mn segregation of the steel plate inherites from the Mn segregation of the billet. The formation of the bainite at abnormal segregation region has immediate relationship with the central segregation of the billet. The Fe-Mn-C clusters segregation region caused by the C-Mn segregation at the center of the billet can effectively bind the atomic motion, and increase the lattice reconstruction resistance of austenite transformation, which provide thermodynamic conditions for the bainite. The C-Mn segregation causes the relative displacement of pearlite transformation curve and bainite transformation curve of the corresponding C curve at the center of the billet, so the original C curve of the center of the billet becomes bay-like shape, which creates the kinetics conditions for the transformation from undercooled austenite to bainite with lower cooling rate at this region. The best normalizing technology of the steel plate with lamination defect is900℃×3min/mm, this technology can not eliminate Mn segregation, but can decrease C content of the abnormal segregation band region by diffusing. This technology can also make the bainite of the abnormal segregation band region to transform into pearlite completely, simultaneously, achieve the purpose of eliminating the lamination defect of the steel plate.
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