CN112831640B - Production method of austenitic stainless steel with yield strength of more than or equal to 980MPa - Google Patents
Production method of austenitic stainless steel with yield strength of more than or equal to 980MPa Download PDFInfo
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- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- 238000005121 nitriding Methods 0.000 claims abstract description 45
- 238000000137 annealing Methods 0.000 claims abstract description 35
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 23
- 239000010935 stainless steel Substances 0.000 claims abstract description 21
- 238000005097 cold rolling Methods 0.000 claims abstract description 11
- 238000005096 rolling process Methods 0.000 claims abstract description 8
- 238000001816 cooling Methods 0.000 claims abstract description 5
- 230000009467 reduction Effects 0.000 claims description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract description 26
- 229910001566 austenite Inorganic materials 0.000 abstract description 19
- 229910000734 martensite Inorganic materials 0.000 abstract description 18
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 14
- 238000000034 method Methods 0.000 description 26
- 230000008569 process Effects 0.000 description 19
- 239000007789 gas Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 6
- 238000009792 diffusion process Methods 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 5
- 230000008859 change Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 230000007246 mechanism Effects 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 2
- 230000008595 infiltration Effects 0.000 description 2
- 238000001764 infiltration Methods 0.000 description 2
- 125000004433 nitrogen atom Chemical group N* 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
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- C23C8/24—Nitriding
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Abstract
一种屈服强度≥980MPa奥氏体不锈钢的生产方法：对厚度为3mm的不锈钢热轧板在室温下进行冷轧，轧制道次不低于4道次；进行渗氮，渗氮温度控制在456～628℃；进行高温退火：退火温度在989～1113℃；在冷却速度为3～24℃/s下冷却至室温。本发明不仅金相组织为全奥氏体，且不锈钢板厚度在0.39～0.6mm，屈服强度在980～1290MPa，抗拉强度在1112～1452MPa，延伸率在13.0～15.5%；冷轧是在室温下进行，在保持体心立方的马氏体结构情况下进行渗氮使氮含量提到最高；高温退火使马氏体组织切变为全奥氏体组织的同时仍然保持超细结构。
A production method of austenitic stainless steel with yield strength ≥980MPa: cold-rolling a stainless steel hot-rolled plate with a thickness of 3mm at room temperature, and the rolling passes are not less than 4 passes; nitriding is carried out, and the nitriding temperature is controlled at 456-628°C; high temperature annealing: annealing temperature is 989-1113°C; cooling to room temperature at a cooling rate of 3-24°C/s. In the present invention, not only the metallographic structure is full austenite, but also the thickness of the stainless steel plate is 0.39-0.6 mm, the yield strength is 980-1290 MPa, the tensile strength is 1112-1452 MPa, and the elongation is 13.0-15.5%; cold rolling is performed at room temperature Nitriding is carried out under the condition of maintaining the body-centered cubic martensite structure to increase the nitrogen content to the highest; high-temperature annealing makes the martensite structure shear into a full austenite structure while still maintaining an ultra-fine structure.
Description
技术领域technical field
本发明涉及不锈钢的生产方法，具体涉及一种屈服强度≥980MPa奥氏体不锈钢的生产方法。The invention relates to a production method of stainless steel, in particular to a production method of austenitic stainless steel with a yield strength of ≥980 MPa.
背景技术Background technique
奥氏体不锈钢占世界不锈钢总产量的70％以上，该钢具有良好的耐腐蚀性能和高的塑韧性。然而，其晶粒为粗大的面心立方结构，导致应力作用下极易发生变形，屈服强度仅为200-300MPa。随着世界资源消耗等问题日趋突出，急需开发超高强度的奥氏体不锈钢，通过薄规格的超高强度奥氏体不锈钢替代低强度级别的厚钢板，已成为发展趋势，也是社会发展的必然选择。Austenitic stainless steel accounts for more than 70% of the world's total stainless steel production. The steel has good corrosion resistance and high plastic toughness. However, its grains have a coarse face-centered cubic structure, which leads to easy deformation under the action of stress, and the yield strength is only 200-300MPa. With the increasingly prominent problems of resource consumption in the world, there is an urgent need to develop ultra-high-strength austenitic stainless steel. It has become a development trend to replace low-strength thick steel plates with ultra-high-strength austenitic stainless steels with thin specifications, and it is also inevitable for social development. choose.
目前，能提高不锈钢强度的同时保持奥氏体结构及高的塑韧性和耐腐蚀性能的有效方法很少。间隙原子氮的固溶能有效提高奥氏体不锈钢强度的同时保持高的塑韧性和耐腐蚀性能，然而氮在奥氏体不锈钢冶炼时难以添加，且奥氏体不锈钢渗氮过程氮元素在面心立方结构中扩散非常慢，制备的加氮奥氏体不锈钢中氮含量大多为0.6％以下，加氮的奥氏体不锈钢屈服强度通常小于450MPa。At present, there are few effective methods to improve the strength of stainless steel while maintaining the austenitic structure and high plastic toughness and corrosion resistance. The solid solution of interstitial nitrogen can effectively improve the strength of austenitic stainless steel while maintaining high plasticity, toughness and corrosion resistance. However, nitrogen is difficult to add during the smelting of austenitic stainless steel, and nitrogen is present in the surface of austenitic stainless steel during nitriding. Diffusion is very slow in the centered cubic structure, the nitrogen content in the prepared nitrogen-added austenitic stainless steel is mostly below 0.6%, and the yield strength of nitrogen-added austenitic stainless steel is usually less than 450MPa.
大冷变形结合退火工艺也是一种提高奥氏体不锈钢强度的有效方法，利用大冷变形产生形变马氏体，随后退火发生逆相变获得超细晶奥氏体不锈钢。细晶强化在提高强度的同时还能保持良好的塑韧性和耐腐蚀性能。然而，大冷变形结合退火工艺制备的不锈钢难以同时获得超高强度和全奥氏体结构。这是因为短时退火获得超细晶粒的不锈钢具有超高强度，但也保留部分马氏体结构；退火时间延长会促使马氏体完全逆转变为奥氏体，此时也导致晶粒逐渐长大，对应的屈服强度迅速下降，该方法获得的具有全奥氏体结构的细晶不锈钢屈服强度难以超过700MPa。屈服强度级别在900MPa以上、全奥氏体结构、高的塑韧性和耐腐蚀性能的不锈钢尚无法制备。The large cold deformation combined with annealing process is also an effective method to improve the strength of austenitic stainless steel. The large cold deformation is used to generate deformed martensite, and then the reverse transformation occurs during annealing to obtain ultra-fine-grained austenitic stainless steel. Fine-grain strengthening can maintain good plastic toughness and corrosion resistance while increasing the strength. However, it is difficult for stainless steel prepared by large cold deformation combined with annealing process to obtain ultra-high strength and full austenite structure at the same time. This is because the stainless steel with ultra-fine grains obtained by short-time annealing has ultra-high strength, but also retains part of the martensite structure; prolonging the annealing time will cause the martensite to be completely reversed into austenite, which also causes the grains to gradually gradually change. The yield strength of the fine-grained stainless steel with full austenite structure obtained by this method is difficult to exceed 700MPa. Stainless steels with yield strength levels above 900 MPa, full austenitic structure, high plastic toughness and corrosion resistance are not yet available.
中国专利公开号为CN104451082的文献中，公开了《一种晶粒尺寸小于100nm的304奥氏体不锈钢的制备方法》。该文献中采用三阶段冷轧-退火工艺处理，25-35％的压下量进行冷轧，随后在800-900℃保温5-20min后，多次重复后制备了晶粒尺寸小于100nm的304不锈钢。该方法制备的不锈钢屈服强度为1100-1200MPa，抗拉强度为1250-1350MPa。但是该工艺在800-900℃保温5-20min后，仍然会有部分应变诱导马氏体组织残留，不能算全奥氏体结构。如果继续退火消除马氏体结构，这期间必然导致奥氏体晶粒粗大，屈服强度则会急剧下降，难以得到屈服强度大于980MPa的全奥氏体结构不锈钢。The Chinese Patent Publication No. CN104451082 discloses "a preparation method of 304 austenitic stainless steel with grain size less than 100 nm". In this document, a three-stage cold rolling-annealing process is used, cold rolling is carried out with a reduction of 25-35%, and then after holding at 800-900 ° C for 5-20 min, 304 with a grain size less than 100 nm is prepared after repeated repetitions. Stainless steel. The yield strength of the stainless steel prepared by the method is 1100-1200 MPa, and the tensile strength is 1250-1350 MPa. However, after the process is kept at 800-900℃ for 5-20min, there will still be some strain-induced martensite structure remaining, which cannot be regarded as a full austenite structure. If annealing is continued to eliminate the martensitic structure, the austenite grains will inevitably become coarse during this period, and the yield strength will drop sharply, making it difficult to obtain a fully austenitic stainless steel with a yield strength greater than 980MPa.
中国专利公开号为CN103088283A的文献中，公开了《一种奥氏体不锈钢分段加压固溶氮化催渗方法》。该文献中对奥氏体不锈钢采用500-700℃氮化预处理5-10小时，随后升温到900-1200℃进行固溶氮化处理1-20小时，得到渗氮层厚度约为90-311微米的奥氏体不锈钢。然而，该工艺制备的产品并没有给出N含量、强度和塑性的数据。根据工艺可知渗氮前奥氏体不锈钢组织为粗大奥氏体晶粒，在500-700℃区间渗氮，氮在奥氏体结构中扩散系数太小导致钢中氮含量并不会太高；此外该方法还要对不锈钢在900-1200℃保温1-20小时，高温条件下长时间退火会导致奥氏体不锈钢晶粒尺寸异常粗大，材料的屈服强度和抗拉强度会急剧下降，难以得到屈服强度大于980MPa的全奥氏体结构不锈钢。In the document with the Chinese Patent Publication No. CN103088283A, "a method for catalyzing the infiltration of austenitic stainless steel by segmented pressure solid solution nitriding" is disclosed. In this document, the austenitic stainless steel is pretreated by nitriding at 500-700 °C for 5-10 hours, and then heated to 900-1200 °C for solution nitriding for 1-20 hours, and the thickness of the nitrided layer is about 90-311 Micron austenitic stainless steel. However, data on N content, strength and plasticity are not given for products produced by this process. According to the process, the microstructure of austenitic stainless steel before nitriding is coarse austenite grains. When nitriding in the range of 500-700 °C, the diffusion coefficient of nitrogen in the austenitic structure is too small, so the nitrogen content in the steel is not too high; In addition, this method also needs to keep the stainless steel at 900-1200 ℃ for 1-20 hours. Long-term annealing at high temperature will lead to abnormally large grain size of austenitic stainless steel, and the yield strength and tensile strength of the material will drop sharply, which is difficult to obtain. Full austenitic structural stainless steel with yield strength greater than 980MPa.
发明内容SUMMARY OF THE INVENTION
本发明的目的在于解决现有技术存在的强度级别与不锈钢为全奥氏体组织不能同时满足要求，且强度级别低的不足，提供一种厚度在0.39～0.60mm，屈服强度在980～1290MPa，抗拉强度在1112～1452MPa，延伸率在13.0～15.5％的奥氏体不锈钢的生产方法。The purpose of the present invention is to solve the problem that the strength level in the prior art cannot meet the requirements at the same time as the stainless steel is a full austenite structure, and the strength level is low, and to provide a thickness of 0.39-0.60mm, a yield strength of 980-1290MPa, A production method of austenitic stainless steel with tensile strength of 1112-1452MPa and elongation of 13.0-15.5%.
实现上述目的的措施：Measures to achieve the above objectives:
一种屈服强度≥980MPa奥氏体不锈钢的生产方法，其步骤：A production method of austenitic stainless steel with yield strength ≥980MPa, comprising the steps of:
1)对厚度为3mm的不锈钢热轧板在室温下进行冷轧，轧制道次不低于4道次，轧制至0.39～0.6mm厚度；每道次压下率控制在33～43％；1) Cold-rolling the hot-rolled stainless steel sheet with a thickness of 3mm at room temperature, the number of rolling passes is not less than 4 times, and rolling to a thickness of 0.39-0.6mm; the reduction rate of each pass is controlled at 33-43% ;
2)进行渗氮，渗氮温度控制在456～628℃，渗氮时间在22～60min，渗氮气氛为10％NH3+60％N2+30％H2混合气，混合气流量在1.6～2.3L/min；2) Carry out nitriding, the nitriding temperature is controlled at 456～628℃, the nitriding time is 22～60min, the nitriding atmosphere is 10% NH3 +60% N2 +30% H2 mixed gas, and the mixed gas flow rate is 1.6 ~2.3L/min;
3)进行高温退火：退火温度在989～1113℃，并在此温度下保温28～58秒；3) High-temperature annealing: the annealing temperature is 989-1113°C, and the temperature is kept at this temperature for 28-58 seconds;
4)进行冷却，在冷却速度为3～24℃/s下冷却至室温。4) It is cooled to room temperature at a cooling rate of 3 to 24° C./s.
优选地：所述渗氮温度控制在496～592℃，渗氮时间在29～53min，混合气流量在1.8～2.1L/min。Preferably: the nitriding temperature is controlled at 496-592° C., the nitriding time is 29-53 min, and the mixed gas flow rate is 1.8-2.1 L/min.
优选地：所述高温退火温度控制在989～1016℃，退火时间在38～58秒。Preferably, the high temperature annealing temperature is controlled at 989-1016° C., and the annealing time is 38-58 seconds.
本发明主要工艺的机理及作用The mechanism and function of the main process of the present invention
本发明之所以控制冷轧每道次压下率在33～43％，是由于控制冷轧过程中的压下率和冷轧后的厚度，若每道次压下率过小，难以得到由大量形变马氏体构成的冷轧板，导致后续退火过程中氮原子渗入量较低，且退火后难以得到超细晶粒的奥氏体不锈钢；若每道次压下率过大，易损伤设备；若每道次压下率不均衡，易导致冷轧板中产生的形变马氏体分布不均，在后续退火过程中不锈钢组织的部分区域易残留马氏体或者奥氏体晶粒粗大。The reason why the present invention controls the reduction ratio of each pass of cold rolling to be 33-43% is because the reduction ratio in the cold rolling process and the thickness after cold rolling are controlled. If the reduction ratio of each pass is too small, it is difficult to obtain The cold-rolled sheet composed of a large amount of deformed martensite leads to a low infiltration amount of nitrogen atoms in the subsequent annealing process, and it is difficult to obtain austenitic stainless steel with ultra-fine grains after annealing; if the reduction rate per pass is too large, it is easy to be damaged. Equipment; if the reduction ratio of each pass is not balanced, it is easy to cause uneven distribution of deformed martensite in the cold-rolled sheet, and in the subsequent annealing process, some areas of the stainless steel structure are prone to residual martensite or coarse austenite grains .
本发明之所以进行渗氮，且控制渗氮温度在456～628℃，渗氮时间在22～60min，渗氮气氛为10％NH3+60％N2+30％H2混合气，混合气流量在1.6～2.3L/min，优选地渗氮温度控制在496～592℃，渗氮时间在29～53min混合气流量在1.8～2.1L/min，是由于若渗氮采用低的温度，使得钢中氮的扩散系数较小，难以获得较高的渗氮量；若渗氮采用高的温度，可导致马氏体结构通过逆相变为奥氏体组织，奥氏体中氮扩散系数太小，导致氮难以渗入到钢中。若渗氮采用短的时间，马氏体和奥氏体中静态再结晶效果不明显；若渗氮采用长的时间，极易导致再结晶结束后发生晶粒长大，获得的晶粒迅速粗化。若渗氮气氛中NH3的体积百分含量小于10％，难以达到最佳渗氮效果；若渗氮气氛中NH3的体积百分含量大于10％，渗氮效果变化幅度不大，且不经济环保。这都不利于得到高的氮含量和超细奥氏体结构。恰当的渗氮工艺能使得奥氏体不锈钢得到高的氮含量。The reason why the present invention carries out nitriding is to control the nitriding temperature at 456-628° C., the nitriding time at 22-60 min, and the nitriding atmosphere as a mixed gas of 10% NH 3 +60% N 2 +30% H 2 , and the mixed gas The flow rate is 1.6~2.3L/min, preferably the nitriding temperature is controlled at 496~592℃, and the nitriding time is 29~53min, and the mixed gas flow is 1.8~2.1L/min. This is because if the nitriding temperature is low, the The diffusion coefficient of nitrogen in the steel is small, so it is difficult to obtain a high nitriding amount; if a high temperature is used for nitriding, the martensite structure can be transformed into austenite through reverse phase transformation, and the nitrogen diffusion coefficient in austenite is too high. small, making it difficult for nitrogen to penetrate into the steel. If the nitriding time is short, the effect of static recrystallization in martensite and austenite is not obvious; if the nitriding time is long, it is easy to cause grain growth after recrystallization, and the obtained grains are rapidly coarse. change. If the volume percentage of NH 3 in the nitriding atmosphere is less than 10%, it is difficult to achieve the best nitriding effect; if the volume percentage of NH 3 in the nitriding atmosphere is greater than 10%, the nitriding effect does not change much and does not change much. Economical and environmentally friendly. This is not conducive to obtaining high nitrogen content and ultrafine austenite structure. Proper nitriding process can make austenitic stainless steel get high nitrogen content.
本发明之所以进行高温退火，且温度控制在989～1113℃，退火时间在28～58秒，优选地退火温度控制在989～1016℃，退火时间在38～58秒，此温度段退火能使形变马氏体组织通过切变机制快速逆转变为超细奥氏体结构。若退火温度过低，难以通过切变机制快速转变为奥氏体；若退火温度过高或保温时间过长，极易导致获得的奥氏体晶粒迅速粗化。这都不利于得到组织为超细全奥氏体晶粒的钢板。The reason why the present invention performs high-temperature annealing, and the temperature is controlled at 989-1113°C, the annealing time is 28-58 seconds, preferably the annealing temperature is controlled at 989-1016°C, and the annealing time is 38-58 seconds. The deformed martensitic structure is rapidly reversed into an ultrafine austenite structure by a shear mechanism. If the annealing temperature is too low, it is difficult to rapidly transform into austenite through the shear mechanism; if the annealing temperature is too high or the holding time is too long, the obtained austenite grains will be easily coarsened rapidly. This is not conducive to obtaining a steel plate with ultra-fine full austenite grains.
本发明与现有技术相比，其特点：不仅金相组织为全奥氏体，且不锈钢板厚度在0.39～0.6mm，屈服强度在980～1290MPa，抗拉强度在1112～1452MPa，延伸率在13.0～15.5％，还在于：Compared with the prior art, the invention has the following characteristics: not only the metallographic structure is full austenite, but also the thickness of the stainless steel plate is 0.39-0.6mm, the yield strength is 980-1290MPa, the tensile strength is 1112-1452MPa, and the elongation is 13.0 to 15.5%, but also in:
1.本发明所述的冷轧是在室温下进行，而目前国内外利用冷轧—退火工艺制备纳米级奥氏体不锈钢，冷轧大多是低温或者是超低温进行。本发明更易于工业化生产。1. The cold rolling of the present invention is carried out at room temperature, and the cold rolling-annealing process is used to prepare nano-scale austenitic stainless steel at home and abroad, and the cold rolling is mostly carried out at low temperature or ultra-low temperature. The present invention is easier for industrial production.
2.本发明采用中温渗氮工艺，在保持体心立方的马氏体结构情况下进行渗氮，中温阶段体心立方的马氏体结构中氮原子扩散系数大，扩散速度快，可将不锈钢中氮含量提到最高。2. The present invention adopts the medium-temperature nitriding process to carry out nitriding under the condition of maintaining the body-centered cubic martensite structure. In the middle-temperature stage, the body-centered cubic martensite structure has a large diffusion coefficient of nitrogen atoms and a fast diffusion rate, which can make stainless steel. The nitrogen content is mentioned to be the highest.
3.本发明所述的高温退火工艺，在中温渗氮过程中形变马氏体发生回复再结晶，减少马氏体晶粒内部的位错，形成大量的亚晶界，获得晶粒尺寸在亚微米级的超细结构；随后的高温退火使得马氏体组织切变为全奥氏体组织的同时仍然保持超细结构。3. In the high-temperature annealing process of the present invention, the deformed martensite undergoes recovery and recrystallization during the medium-temperature nitriding process, which reduces the dislocation inside the martensite grains, forms a large number of sub-grain boundaries, and obtains the grain size in the sub-grain size. Micron-scale ultra-fine structure; subsequent high temperature annealing allows the martensite structure to be sheared into a fully austenitic structure while still maintaining the ultra-fine structure.
附图说明Description of drawings
图1为不锈钢经本发明渗氮后的组织形貌图；Fig. 1 is the microstructure diagram of stainless steel after nitriding of the present invention;
图2为不锈钢经本发明高温退火后组织形貌图。Fig. 2 is the microstructure diagram of stainless steel after high temperature annealing of the present invention.
具体实施方式Detailed ways
下面结合具体实施例对本发明进行进一步描述：The present invention is further described below in conjunction with specific embodiment:
表1为本发明各实施例及对比例工艺主要参数控制列表；Table 1 is the main parameter control list of each embodiment of the present invention and the comparative example process;
表2为本发明各实施例及对比例力学性能检测情况列表。Table 2 is a list of the mechanical properties detection of each embodiment of the present invention and the comparative example.
本发明各实施例均按照以下步骤生产：Each embodiment of the present invention is produced according to the following steps:
1)对不锈钢热轧板在室温下进行冷轧，轧制道次不低于4道次，轧制至0.39～0.6mm厚度；每道次压下率控制在33～43％；1) Cold-rolling the hot-rolled stainless steel sheet at room temperature, the number of rolling passes is not less than 4 passes, and the rolling is to a thickness of 0.39-0.6mm; the reduction rate of each pass is controlled at 33-43%;
2)进行渗氮，渗氮温度控制在456～628℃，渗氮时间在22～60min，渗氮气氛为10％NH3+60％N2+30％H2混合气，混合气流量在1.6～2.3L/min；2) Carry out nitriding, the nitriding temperature is controlled at 456～628℃, the nitriding time is 22～60min, the nitriding atmosphere is 10% NH3 +60% N2 +30% H2 mixed gas, and the mixed gas flow rate is 1.6 ~2.3L/min;
3)进行高温退火：退火温度在989～1113℃，并在此温度下保温28～58秒；3) High-temperature annealing: the annealing temperature is 989-1113°C, and the temperature is kept at this temperature for 28-58 seconds;
4)进行冷却，在冷却速度为3～24℃/s下冷却至室温。4) It is cooled to room temperature at a cooling rate of 3 to 24° C./s.
表1本发明各实施例及对比例工艺主要参数控制列表Table 1 Control list of main parameters of each embodiment of the present invention and comparative example process
表2本发明各实施例及对比例力学性能检测情况列表Table 2 List of mechanical properties testing of each embodiment of the present invention and comparative example
由上述表2可以看出，本发明实施例中的奥氏体不锈钢热轧板坯经过一系列轧制热处理，由本发明实施例1～6中产品相对于不同冷轧压下量的对比例7和改变退火温度工艺的对比例8和退火时间工艺的对比例9，在屈服强度、抗拉强度方面均具有良好的表现，尤其是屈服强度、抗拉强度等明显高于对比例，本发明实施例1～6中产品的屈服强度为980～1290MPa，抗拉强度为1112～1452MPa，延伸率为13.0～15.5％，成品厚度为0.39～0.48mm。It can be seen from the above Table 2 that the hot-rolled austenitic stainless steel slab in the embodiment of the present invention has undergone a series of rolling heat treatments. And the comparative example 8 of changing the annealing temperature process and the comparative example 9 of the annealing time process have good performance in terms of yield strength and tensile strength, especially the yield strength and tensile strength are obviously higher than those of the comparative example, the present invention implements The yield strength of the products in Examples 1-6 is 980-1290 MPa, the tensile strength is 1112-1452 MPa, the elongation is 13.0-15.5%, and the thickness of the finished product is 0.39-0.48 mm.
本发明的实施例仅为最佳例举，并非对技术方案的限定性实施。The embodiments of the present invention are only the best examples, and are not restrictive implementations of the technical solutions.
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