低镍奥氏体不锈钢热变形过程中的塑性及开裂机理
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摘要
奥氏体不锈钢在热变形加工过程中塑性较低,容易产生裂纹,本文针对两种低镍奥氏体不锈钢Cr17Mn6Ni4Cu2N和Cr15Mn9Cu2NiN,首先研究了其微观组织,然后分别利用高温拉伸试验、模拟热轧试验及熔炼凝固试验,研究了变形温度、应变速率、变形方式及化学成分对热塑性的影响,结合上述实验结果对热变形开裂的机理进行了讨论分析,提出了防止热变形开裂的措施,并将提出的措施应用到实际的生产过程中进行验证。
在Cr17Mn6Ni4Cu2N铸坯壳层,其组织为树枝状δ铁素体分布在柱状奥氏体晶粒内部(1#组织)；在芯部,δ铁素体以条状分布在奥氏体晶粒内部及晶界上(2#组织)；整个铸坯的凝固模式为FA模式。在Cr15Mn9Cu2NiN壳层,当距表面距离小于27.5mm时,微观组织由树枝状δ铁素体、通道状奥氏体和奥氏体基体组成(3#组织),凝固模式为FA和A模式共存。距离大于27.5mm时,壳层组织由树枝状δ铁素体和奥氏体基体组成；芯部为粗大的单相奥氏体柱状晶(4#组织)；凝固模式为FA模式。并测定了不同微观组织具有的热塑性。
对比铸态试样及具有等轴晶组织的热加工态试样发现,在1000～1250℃内,铸态试样的热塑性随变形温度的降低迅速下降,而在热加工态试样中则是缓慢下降。分析认为,正是由于铸态组织及其变形特性使得其在热变形过程中容易开裂,并且发现热变形中的开裂与焊接中的失塑裂纹具有相同的特点,属于同一机制。提出了热变形加工过程中失塑温度区间的概念,即容易开裂的温度区间。分析得出在应变速率为0.1s-1时,微观组织的失塑倾向由低到高分别为1#组织,3#组织,4#组织,2#组织,两种钢的失塑温度区间分别为850～1000℃和900～1250℃。
分析了应变速率对不同铸态组织的热塑性、裂纹形核位置及失塑温度区间的影响。低应变速率时,1#和3#组织的热塑性较高,提高应变速率会降低其热塑性,并导致裂纹形核位置由铁素体树枝晶处转移至奥氏体晶界处。在2#组织中,提高应变速率会明显提高其热塑性,并使裂纹的形核位置由晶界铁素体处变为奥氏体晶界和晶界铁素体处共存。高应变速率时,铁素体和奥氏体的强度均会升高,使得它们之间的强度差别减小,降低了铁素体处的应力集中,导致变形中的薄弱环节由铁素体处转至奥氏体晶界处,进而导致裂纹形核位置的改变。将变形过程的应变速率由0.1提高至10s-1,会增大1#和4#组织的失塑温度区间,使3#组织的失塑温度区间向低温端平移50℃,减小2#组织的失塑温度区间。在Cr17Mn6Ni4Cu2N中,应变速率为别1和10s-1时的失塑温度区间分别为950～1100℃和850～1250℃；而在Cr15Mn9Cu2NiN中,失塑温度区间分别为850～900℃和850～1050℃。
通过模拟热轧试验发现,在950～1250℃内,两种钢中均存在随着变形温度的降低临界开裂应变量迅速下降的情况,且铸态组织比经历再结晶的等轴晶组织更容易开裂。这与通过拉伸试验得到的结果是相同的。
根据以上的实验结果,提出了热变形开裂的机理。铸态奥氏体不锈钢在热变形过程中容易开裂,主要是由于铸态组织及其变形特性引起的。在铸态组织中以粗大的柱状晶为主,具有明显的结晶取向性,在热变形过程中随着变形温度的降低,屈服会迅速升高,导致各晶粒进行塑性变形及变形协调的能力变差,在较小的变形量下就会导致裂纹的形核；柱状晶晶界中,小角度晶界比例高,且单条晶界较长,变形时一旦裂纹形核就会沿柱状晶界迅速扩展；奥氏体不锈钢的堆垛层错能低,高温变形时的软化机制主要为动态再结晶,当铸态奥氏体不锈钢的变形量未达到再结晶所需的临界变形量,同时动态回复的软化作用受到抑制时,如在低的变形温度或高的应变速率,就会导致裂纹的形核。
在实际的热轧生产中,适当提高坯料预热时的在炉时间、预热温度及粗轧开轧温度或调整Cr15Mn9Cu2NiN中B的含量均会使板坯边裂及回炉的比例降低,而增加N的含量会导致边裂及回炉的比例升高。
Hot ductility in austenitic stainless steel (ASS) slab is low and prone to suffer from cracking during hot deformation. The factors which affect the hot ductility in ASS, such as microstructure, chemical composition, deformation temperature, strain rate and deformation mode have been studied—a case study of two kinds of low Ni ASSs Cr17Mn6Ni4Cu2N and Cr15Mn9Cu2NiN. Combined with the above results, the cracking mechanism was discussed and the measures that avoid cracking during hot deformation were proposed.
In the slab shell of Cr17Mn6Ni4Cu2N, the microstructure is dendrite8ferrite which distributing in columnar austenite grains (1#microstructure); in the core,δ ferrite distributes in the interior of austenite and on the austenite boundaries in the form of bar (2#microstructure); the solidification mode of this steel is FA.
In the shell of Cr15Mn9Cu2NiN, as the distance from slab surface shorter than27.5mm, the microstructure is consist of dendrite8ferrite, austenite matrix and channel-like austenite (3#microstructure), the solidification mode is the co-existence of FA and A; as the distance longer than27.5mm, the microstructure is consist of ferrite and austenite; in core, the microstructure is coarse austenite columnar grains (4#microstructure), and the solidification mode is FA.
Though the comparison of hot ductility in specimens which made from slab and hot-rolled plate, it is found as deforming temperature in the range of1000-1250℃, RA in slab decreased rapidly with temperature. Analysis suggested that, the as-cast microstructure and its deformation characters induce the cracking problem during hot deformation. Through the comparison of cracking in hot working and ductility-dip cracking in welding, it is found that they have the same characters and induced by the same mechanism. The concept of ductility-dip temperature range (DDTR) during hot deformation was proposed in this article. As the strain rate is0.1s-1, the cracking tendency of each microstructure from high to low is1#,3#,4#,2#, respectively.
The influence of strain rate on hot ductility, cracks nucleating positions and DDTR were analyzed. As the strain rate is lower, RA in1#and3#microstructure is high, while increasing the strain rate would decrease the hot ductility and the positions of crack nucleuses were changed from δ ferrite dendrites to austenite GB. In2#microstructure, RA increases with strain rate, and the positions of cracks nucleuses are changed from GB ferrite to the co-existence of GB ferrite and austenite GB. As the materials deformation at higher strain rate, the strength can be improved both in austenite and ferrite, which will decrease the stress concentration on ferrite and transfer the weak location from ferrite to austenite GB, then induce the change of nucleating positions of cracks. As increasing the strain rate from0.1to10s-1will enlarge the DDTR in1#and4#microstructure, move the DDTR50℃to the low temperature side in3#microstructure, decrease the DDTR in2#microstructure.
According to the hot rolling experiment results, in the range of1000-1250℃, in the two steels, the critical cracking strain deceases rapidly with deformation temperature, In multi-pass hot rolling, the microstructure in Cr15Mn9Cu2NiN slab easier suffer from cracking than the equiaxed grains which from recrystallization, all of this is consistent with the results from tensile tests.
According to the above results, the cracking mechanism of as-cast austenitic stainless steel during hot working is proposed. The reason that as-cast ASSs are easier suffer from cracking problems during hot working, mainly due to the as-cast microstructure and its deformation characters. The as-cast microstructure is consisting of coarse columnar grains, which has obviously crystal orientation. During deformation, as decreasing deformation temperature, the columnar grains are easy to strengthen, leading to higher yield strength, the deformation coordination ability is poor, and under a small deformation amount, the cracks will nucleate at the boundaries of columnar grains. The majority of columnar grains boundaries are high angle GB. During deformation, once the cracks nucleate on columnar GBs, they will grow and propagate along them. The stacking faults energy in ASSs is low, and the soften mechanism in which is dynamic recrystallization during elevated-temperature deformation. As the strain lower than the critical strain that needed for dynamic recrystallization, and the dynamic recovery is suppressed, such as at lower deformation temperature or higher strain rate, the cracks will nucleate quickly.
In the practical hot rolling produce of Cr15Mn9Cu2NiN, increasing the time in the furnace, preheating temperature and roughing rolling start temperature or adjusting the content of B will reduce the proportion of edge-cracking in strip. But increasing the content of N will deteriorate the hot ductility in slab, and increase the proportion of edge-cracking in strip.
在Cr17Mn6Ni4Cu2N铸坯壳层,其组织为树枝状δ铁素体分布在柱状奥氏体晶粒内部(1#组织)；在芯部,δ铁素体以条状分布在奥氏体晶粒内部及晶界上(2#组织)；整个铸坯的凝固模式为FA模式。在Cr15Mn9Cu2NiN壳层,当距表面距离小于27.5mm时,微观组织由树枝状δ铁素体、通道状奥氏体和奥氏体基体组成(3#组织),凝固模式为FA和A模式共存。距离大于27.5mm时,壳层组织由树枝状δ铁素体和奥氏体基体组成；芯部为粗大的单相奥氏体柱状晶(4#组织)；凝固模式为FA模式。并测定了不同微观组织具有的热塑性。
对比铸态试样及具有等轴晶组织的热加工态试样发现,在1000～1250℃内,铸态试样的热塑性随变形温度的降低迅速下降,而在热加工态试样中则是缓慢下降。分析认为,正是由于铸态组织及其变形特性使得其在热变形过程中容易开裂,并且发现热变形中的开裂与焊接中的失塑裂纹具有相同的特点,属于同一机制。提出了热变形加工过程中失塑温度区间的概念,即容易开裂的温度区间。分析得出在应变速率为0.1s-1时,微观组织的失塑倾向由低到高分别为1#组织,3#组织,4#组织,2#组织,两种钢的失塑温度区间分别为850～1000℃和900～1250℃。
分析了应变速率对不同铸态组织的热塑性、裂纹形核位置及失塑温度区间的影响。低应变速率时,1#和3#组织的热塑性较高,提高应变速率会降低其热塑性,并导致裂纹形核位置由铁素体树枝晶处转移至奥氏体晶界处。在2#组织中,提高应变速率会明显提高其热塑性,并使裂纹的形核位置由晶界铁素体处变为奥氏体晶界和晶界铁素体处共存。高应变速率时,铁素体和奥氏体的强度均会升高,使得它们之间的强度差别减小,降低了铁素体处的应力集中,导致变形中的薄弱环节由铁素体处转至奥氏体晶界处,进而导致裂纹形核位置的改变。将变形过程的应变速率由0.1提高至10s-1,会增大1#和4#组织的失塑温度区间,使3#组织的失塑温度区间向低温端平移50℃,减小2#组织的失塑温度区间。在Cr17Mn6Ni4Cu2N中,应变速率为别1和10s-1时的失塑温度区间分别为950～1100℃和850～1250℃；而在Cr15Mn9Cu2NiN中,失塑温度区间分别为850～900℃和850～1050℃。
通过模拟热轧试验发现,在950～1250℃内,两种钢中均存在随着变形温度的降低临界开裂应变量迅速下降的情况,且铸态组织比经历再结晶的等轴晶组织更容易开裂。这与通过拉伸试验得到的结果是相同的。
根据以上的实验结果,提出了热变形开裂的机理。铸态奥氏体不锈钢在热变形过程中容易开裂,主要是由于铸态组织及其变形特性引起的。在铸态组织中以粗大的柱状晶为主,具有明显的结晶取向性,在热变形过程中随着变形温度的降低,屈服会迅速升高,导致各晶粒进行塑性变形及变形协调的能力变差,在较小的变形量下就会导致裂纹的形核；柱状晶晶界中,小角度晶界比例高,且单条晶界较长,变形时一旦裂纹形核就会沿柱状晶界迅速扩展；奥氏体不锈钢的堆垛层错能低,高温变形时的软化机制主要为动态再结晶,当铸态奥氏体不锈钢的变形量未达到再结晶所需的临界变形量,同时动态回复的软化作用受到抑制时,如在低的变形温度或高的应变速率,就会导致裂纹的形核。
在实际的热轧生产中,适当提高坯料预热时的在炉时间、预热温度及粗轧开轧温度或调整Cr15Mn9Cu2NiN中B的含量均会使板坯边裂及回炉的比例降低,而增加N的含量会导致边裂及回炉的比例升高。
Hot ductility in austenitic stainless steel (ASS) slab is low and prone to suffer from cracking during hot deformation. The factors which affect the hot ductility in ASS, such as microstructure, chemical composition, deformation temperature, strain rate and deformation mode have been studied—a case study of two kinds of low Ni ASSs Cr17Mn6Ni4Cu2N and Cr15Mn9Cu2NiN. Combined with the above results, the cracking mechanism was discussed and the measures that avoid cracking during hot deformation were proposed.
In the slab shell of Cr17Mn6Ni4Cu2N, the microstructure is dendrite8ferrite which distributing in columnar austenite grains (1#microstructure); in the core,δ ferrite distributes in the interior of austenite and on the austenite boundaries in the form of bar (2#microstructure); the solidification mode of this steel is FA.
In the shell of Cr15Mn9Cu2NiN, as the distance from slab surface shorter than27.5mm, the microstructure is consist of dendrite8ferrite, austenite matrix and channel-like austenite (3#microstructure), the solidification mode is the co-existence of FA and A; as the distance longer than27.5mm, the microstructure is consist of ferrite and austenite; in core, the microstructure is coarse austenite columnar grains (4#microstructure), and the solidification mode is FA.
Though the comparison of hot ductility in specimens which made from slab and hot-rolled plate, it is found as deforming temperature in the range of1000-1250℃, RA in slab decreased rapidly with temperature. Analysis suggested that, the as-cast microstructure and its deformation characters induce the cracking problem during hot deformation. Through the comparison of cracking in hot working and ductility-dip cracking in welding, it is found that they have the same characters and induced by the same mechanism. The concept of ductility-dip temperature range (DDTR) during hot deformation was proposed in this article. As the strain rate is0.1s-1, the cracking tendency of each microstructure from high to low is1#,3#,4#,2#, respectively.
The influence of strain rate on hot ductility, cracks nucleating positions and DDTR were analyzed. As the strain rate is lower, RA in1#and3#microstructure is high, while increasing the strain rate would decrease the hot ductility and the positions of crack nucleuses were changed from δ ferrite dendrites to austenite GB. In2#microstructure, RA increases with strain rate, and the positions of cracks nucleuses are changed from GB ferrite to the co-existence of GB ferrite and austenite GB. As the materials deformation at higher strain rate, the strength can be improved both in austenite and ferrite, which will decrease the stress concentration on ferrite and transfer the weak location from ferrite to austenite GB, then induce the change of nucleating positions of cracks. As increasing the strain rate from0.1to10s-1will enlarge the DDTR in1#and4#microstructure, move the DDTR50℃to the low temperature side in3#microstructure, decrease the DDTR in2#microstructure.
According to the hot rolling experiment results, in the range of1000-1250℃, in the two steels, the critical cracking strain deceases rapidly with deformation temperature, In multi-pass hot rolling, the microstructure in Cr15Mn9Cu2NiN slab easier suffer from cracking than the equiaxed grains which from recrystallization, all of this is consistent with the results from tensile tests.
According to the above results, the cracking mechanism of as-cast austenitic stainless steel during hot working is proposed. The reason that as-cast ASSs are easier suffer from cracking problems during hot working, mainly due to the as-cast microstructure and its deformation characters. The as-cast microstructure is consisting of coarse columnar grains, which has obviously crystal orientation. During deformation, as decreasing deformation temperature, the columnar grains are easy to strengthen, leading to higher yield strength, the deformation coordination ability is poor, and under a small deformation amount, the cracks will nucleate at the boundaries of columnar grains. The majority of columnar grains boundaries are high angle GB. During deformation, once the cracks nucleate on columnar GBs, they will grow and propagate along them. The stacking faults energy in ASSs is low, and the soften mechanism in which is dynamic recrystallization during elevated-temperature deformation. As the strain lower than the critical strain that needed for dynamic recrystallization, and the dynamic recovery is suppressed, such as at lower deformation temperature or higher strain rate, the cracks will nucleate quickly.
In the practical hot rolling produce of Cr15Mn9Cu2NiN, increasing the time in the furnace, preheating temperature and roughing rolling start temperature or adjusting the content of B will reduce the proportion of edge-cracking in strip. But increasing the content of N will deteriorate the hot ductility in slab, and increase the proportion of edge-cracking in strip.
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