CN114630914A - 高强度钢产品和用于制备所述高强度钢产品的退火方法 - Google Patents
高强度钢产品和用于制备所述高强度钢产品的退火方法 Download PDFInfo
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- CN114630914A CN114630914A CN202080066399.7A CN202080066399A CN114630914A CN 114630914 A CN114630914 A CN 114630914A CN 202080066399 A CN202080066399 A CN 202080066399A CN 114630914 A CN114630914 A CN 114630914A
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- steel sheet
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Abstract
本发明提供具有受控组成的钢片产品,其经历两步退火过程以制备具有期望的显微组织和有利的机械性质例如高强度和超高成形性的片材产品。该钢片产品可为冷轧或热轧的。按照本发明加工的钢材表现出有利的极限拉伸强度和总延伸率(UTS·TE)组合性质,并可落入第三代先进高强度钢材的范畴,在包括汽车制造商的各种行业中是期望的。
Description
相关申请的交叉引用
本申请是要求2016年5月10日提交的美国临时申请号62/334,189和2016年9月19日提交的美国临时申请号62/396,602的优先权的2017年5月10日提交的美国专利申请号15/591,344,现为美国专利号10,385,419的部分继续。本申请还是2019年7月2日提交的美国专利申请号16/459,757的部分继续,所述美国专利申请号16/459,757是美国专利申请号15/591,344的部分继续。全部前述申请通过引用并入本文。
发明领域
本发明涉及具有有利性质的高强度钢产品,并且涉及制备这样产品的退火方法。
背景技术
在过去的几年间,全球钢铁行业关注于用于汽车市场的第三代先进高强度钢(AHSS)的开发。这种三代钢材具有拉伸强度和延伸率的有利平衡,典型地在约20000MPa%或更大的UTS·TE范围中。然而,由于大多数方法需要高合金含量,例如典型地大于4重量%的锰,这导致当用常规制钢设备制造这种钢材时的困难,使钢铁行业处于商业化第3代AHSS的困难时期。另外,目前可得的AHSS难以通过例如点焊的技术焊接,难以用基于锌的电镀涂层涂覆,并且难以制造成大规模应用所需的薄规格片材。
发明内容
本发明提供具有受控组成的钢片产品,其经历两步退火过程以制备具有期望的显微组织和有利的机械性质例如高强度和超高成形性的片材产品。该钢片产品可为冷轧或热轧的。按照本发明加工的钢材表现出有利的极限拉伸强度和总延伸率(UTS·TE)组合性质,例如当使用标准小尺寸(subsize)ASTM或全尺寸JIS拉伸测试工序测试时大于25000MPa-%。另外,按照本发明制备的钢材表现出TE和扩孔的有利组合,即全局成形性和局部成形性都好。具有这些性质的钢材落入第三代先进高强度钢材的范畴,并且是包括汽车制造商的各行业高度期望的。
本发明的一方面是提供高强度轧制钢片产品,其包含0.12-0.5重量%的C、1-3重量%的Mn和0.8-3重量%的Si与Al的组合,其中该钢片产品经历了两步退火过程,包含铁素体和平均纵横比小于3:1的基本上等轴的残余奥氏体晶粒,并具有大于25000MPa%的极限拉伸强度和总延伸率的组合UTS·TE。
本发明的另一方面是提供制备高强度轧制钢片产品的方法,所述产品包含0.12-0.5重量%的C、1-3重量%的锰和0.8-3重量%的Si与Al的组合。该方法包括使钢片产品经历第一步退火过程以实现主要是马氏体的显微组织,并使钢片产品经历第二步方法,所述第二步方法包括将临界状态下的片材产品在720-850℃的温度下均热,之后将片产品保持在370-445℃的温度下。
本发明的这些和其它方面将从以下描述变得更加明显。
附图简要描述
图1包括温度相对时间的曲线,说明按照本发明实施方案的两步退火方法。
图2包括温度相对时间的曲线,说明按照本发明另一实施方案的两步退火方法。
图3是温度相对时间的曲线,说明将两步热过程与任选的基于锌的热浸涂覆操作结合在单一生产设备中的两步退火方法。
图4是在按照本发明实施方案的热循环中限定均热和保温区域的退火过程的第二步骤的温度相对时间的曲线。
图5和6是电子背散射衍射(EBSD)显微照片,说明按照本发明实施方案的高强度钢片产品的显微组织。
图7是图1中显示的经历热过程的钢片产品的光学显微照片,显示较暗的铁素体晶粒和较亮的奥氏体晶粒。
图8是说明图7中显示的奥氏体晶粒的纵横比的柱状图。
图9和10是高强度钢片产品的图,显示按照本发明实施方案的奥氏体和铁素体晶粒尺寸分布。
图11是EBSD显微照片,说明如图1中显示加工的高强度钢片产品的显微组织。
图12和13是EBSD显微照片,显示如图2中显示加工的钢片产品。
图14是如图3中显示加工的钢片产品的EBSD显微照片。
图15是与本发明范围外加工的其它钢片产品相比本发明的高强度钢片产品的总延伸率相对极限拉伸强度的图。
图16是按照本发明实施方案在工厂试验中制备的高强度钢产品的总延伸率相对极限拉伸强度的图。
图17是使用按照本发明实施方案的热循环加工的冷轧和热轧基材的温度相对时间的曲线。
图18是图17中显示的经历热过程的冷轧钢片基材的EBSD显微照片,显示较暗的铁素体晶粒和较亮的残余奥氏体晶粒。
图19是图17中显示的经历热过程的热轧钢片基材的EBSD显微照片,显示较暗的铁素体晶粒和较亮的残余奥氏体晶粒。
详述
本发明的高强度钢片产品具有受控的组成,其与受控的退火过程一起产生期望的显微组织和包括高强度和超高成形性的有利机械性质。在一些实施方案中,钢组成可包括碳、锰和硅,以及本领域技术人员已知的任何其它合适的合金化添加。以下表1中列出了包括C、Mn、Si、Al、Ti和Nb的范围的钢组成的实例。
表1
钢组成(重量%)
实施例 | C | Mn | Si | Al | Si+AL | Ti | Nb |
A | 0.12-0.5 | 1-3 | 0-2 | 0-2 | 0.8-3 | 0-0.05 | 0-0.05 |
B | 0.15-0.4 | 1.3-2.5 | 0.2-1.8 | 0-1.5 | 0.9-2.5 | 0-0.03 | 0-0.03 |
C | 0.17-0.35 | 1.5-2.3 | 0.4-1.5 | 0-1 | 1-2 | 0-0.02 | 0-0.02 |
除了表1中所列的C、Mn、Si、Al、Ti和Nb的量之外,钢组成还可包括微量或杂质量的其它元素,例如最大0.015的S、最大0.03的P、最大0.2的Cu、最大0.02的Ni、最大0.2的Cr、最大0.2的Mo、最大0.1的Sn、最大0.015的N、最大0.1的V和最大0.004的B。当提及钢片产品的组成时,如本文使用的术语“基本上不含”意为特定元素或材料没有被有意地添加至该组成,并且仅作为杂质或以痕量存在。
在本发明的钢片产品中,C提供提高的强度并促进残余奥氏体的形成。Mn提供硬化并充当固溶增强剂。Si抑制热处理过程中铁碳化物析出,并提高奥氏体保留。Al抑制热处理过程中铁碳化物析出,并提高奥氏体保留。Ti和Nb可充当强度增强晶粒细化剂。
在一些实施方案中,Al可以至少0.1重量%或至少0.2重量%的量存在。例如,在一些实施方案中,Al可以0.5-1.2重量%、或0.7-1.1重量%的量存在。供选择地,钢片产品可基本上不含Al。
具有如以上描述组成的钢片产品经历如以下更全面描述的两步退火方法。发现产生的钢产品具有有利的机械性质,包括期望的极限拉伸强度、高延伸率、高λ值、高弯曲性和高屈服比(YS/UTS)。
在一些实施方案中,钢片产品的极限拉伸强度(UTS)范围为700-1100MPa或更大。在一些实施方案中,钢片产品具有大于700MPa、例如720-1100MPa或750-1050MPa的极限拉伸强度。
在一些实施方案中,钢片产品具有典型地大于22%,例如大于27%或大于33%的总延伸率(TE)。例如,钢片产品可具有至少20%、或至少25%、或至少27%,例如22-45%、或25-40%的总延伸率。
钢片产品可具有如通过标准扩孔测试测量的典型地大于20%,例如大于25%、或大于30%、或大于35%的λ(lambda)值。扩孔比或λ可大于20%,例如22-80%或25-60%。
在一些实施方案中,总延伸率(TE)和扩孔(λ)两者提高的值导致钢片产品表现出好的全局成形性和局部成形性。
本钢片产品观察到大于25,000的强度延伸率平衡(UTS·TE),使它们落入例如汽车行业的多个行业高度需要的第三代钢材的范畴。在一些实施方案中,UTS·TE值可大于27000、或大于30000、或大于35000。
按照本发明的一些实施方案,钢片产品的最终显微组织可主要包含铁素体,例如至少50%直至80%或更高,与较少量的残余奥氏体,例如5-25%,和微量的新生马氏体,例如0-10%或15%。可通过标准EBSD技术来测定铁素体、奥氏体和马氏体的量。供选择地,可通过磁性饱和方法来测定残余奥氏体含量。除非本文另外规定,通过EBSD技术测定残余奥氏体的体积%。
在一些实施方案中,残余奥氏体占1-25体积%,例如5-20体积%。新生马氏体的量可占小于15体积%、或小于10体积%、或小于5体积%。在一些实施方案中,钢片产品基本上不含新生马氏体。发现了当新生马氏体量大于15%时,扩孔值明显降低,例如局部成形性明显降低。
如以下描述,可通过马氏体的回火和/或再结晶在加热段期间,或在第二退火过程的冷却和保温段期间通过奥氏体分解形成至少一部分铁素体。一些铁素体可以被认为是贝氏体铁素体。铁素体、奥氏体和马氏体相是细晶粒的,例如具有小于10微米,例如小于5微米、或小于3微米的平均晶粒尺寸。例如,铁素体晶粒尺寸可范围从小于10微米,例如小于8微米、或小于6微米。平均奥氏体晶粒尺寸可范围从小于2微米,例如小于1微米、或小于0.5微米。当存在时,马氏体晶粒尺寸可范围从小于10微米,例如小于8微米、或小于6微米。
奥氏体晶粒可基本上是等轴的,例如具有的平均纵横比小于3:1或小于2:1,例如约1:1。发现了小于约5%的残余奥氏体的量导致明显降低的总延伸率(TE)。还发现了可仅在非常高的碳水平下获得大于25%的残余奥氏体的量,这导致差的焊接性。
在本发明的一些实施方案中,使用两步退火方法来制备具有有利机械性质例如以上描述那些的先进高强度钢产品。在每个第一和第二退火步骤内,可使用多种进行热处理的方法。在图1-3中显示并在下面描述两步退火方法的实例。图1呈现连续退火生产线(CAL),之后是连续退火生产线(CAL)制备路线。图2呈现CAL加上连续电镀生产线(CGL)制备路线。图3呈现允许在单个设备中发生CAL+CAL或CAL+CGL步骤的专门设计的生产线。虽然在图3中显示了直接火焰炉(DFF)之后辐射管(RT)炉实施方案,但是可使用其它实施方案例如全部辐射管、电辐射加热等来实现期望的热循环。
步骤1
退火方法的第一步骤的目的是在冷轧或热轧钢片产品中实现马氏体显微组织。在第一步骤的第一退火阶段中,可典型地使用大于A3温度的退火温度,例如可使用至少820℃的退火温度。在一些实施方案中,第一阶段退火温度可典型地范围为830-980℃,例如830-940℃、或840-930℃、或860-925℃。在一些实施方案中,可典型地保持峰值退火温度至少20秒,例如20-500秒,或30-200秒。可通过常规技术例如非氧化或氧化直接火焰炉(DFF)、富氧DFI、感应、气体辐射管加热、电辐射加热等来实现加热。可适合于在本发明的方法中使用的加热***的实例公开于归于Fives Stein的美国专利号5,798,007、7,368,689、8,425,225和8,845,324,美国专利申请号2009/0158975和已公开PCT申请号WO/2015083047。可适合于在本发明的方法中使用的加热***的额外的实例包括归于Drever International的美国专利号7,384,489,和归于Nippon Steel和Sumitomo Metal Corporation的美国专利号9,096,918。任何其它的合适的已知类型的加热***和方法可适合于使用在步骤1和步骤2中。
在第一阶段中,在达到峰值退火温度并保持期望的时间段之后,将冷轧或热轧的钢片淬火至室温,或至大于室温的受控温度,如以下更全面描述。淬火温度可不必为室温,但应低于马氏体开始温度(Ms)并优选低于马氏体结束温度(MF),从而形成主要是马氏体的显微组织。在一些实施方案中,在第一步骤过程和第二步骤过程之间,可将该钢片产品冷却至低于300℃例如低于200℃的温度。
淬火可通过常规技术来实现,例如水淬火,浸入式刀/喷嘴水淬火,气体冷却,使用冷的、温的或热的水和气体的组合的快速冷却,水溶液冷却,其它液体或气体流体冷却,急冷辊淬火,水雾喷雾,湿式瞬时冷却,非氧化湿式瞬时冷却等。可典型地使用30-2000℃/秒的淬火速率。
本领域技术人员已知的各种类型的冷却和淬火***和方法可适合于在本发明的方法中使用。在商购基础上常规使用的合适的冷却/淬火***和方法可包括水淬火、水雾冷却、干式瞬时和湿式瞬时、氧化和非氧化冷却、烷烃流体至气体相变冷却、热水淬火(包括两步水淬火)、辊淬火、高百分比氢或氦气喷射冷却等。例如,可使用干式瞬时和/或湿式瞬时氧化和非氧化冷却/淬火例如Fives Stein的已公开PCT申请号WO2015/083047中公开的。描述可适合于在本发明的方法中使用的冷却/淬火***和方法的其它Fives Stein专利文件包括美国专利号6,464,808B2、6,547,898B2和8,918,199B2,和美国专利申请公开号US2009/0158975A1、US2009/0315228A1和US2011/0266725A1。可适合于在本发明的方法中使用的冷却/淬火***和方法的其它实例包括在美国专利号8,359,894B2、8,844,462B2和7,384,489B2,和美国专利申请公开号2002/0017747A1和2014/0083572A1中公开的那些。
在一些实施方案中,在达到第一阶段峰值退火温度并且将钢淬火以形成马氏体之后,可任选使马氏体回火以稍微软化钢以使进一步加工更可行。回火通过升高钢的温度在室温至约500℃的范围中并保持至多600秒发生。如果使用回火,回火温度可保持恒定,或可在这个优选的范围内变化。
在回火之后,温度倾斜下降至室温。这样的倾斜下降的速率可典型地范围为1-40℃/秒,例如2-20℃/秒。在单一道次设备炉的情况下,如图3中,回火可以不是必要的。
步骤2
退火方法的第二步骤可包括在相对高的退火温度下进行的第一阶段和在相对低的温度下进行的第二阶段。如图4中描述,这些阶段定义为第二退火的“均热”和“保温”区域。控制温度以便促进最终产品中期望显微组织的形成。
在第二步骤的第一退火阶段中,可使用在A1和A3之间的均热区域温度,例如可使用至少720℃的退火温度。在一些实施方案中,均热区域温度可典型地范围为720-850℃,例如760-825℃。在一些实施方案中,可典型地保持峰值退火温度至少15秒,例如20-300秒,或30-150秒。
在第二步骤的第一阶段期间,可通过从低于Ms的相对低的温度例如室温以0.5-50℃/秒的平均速率例如约2-20℃/秒加热钢来实现均热区域温度。在一些实施方案中,倾斜上升可进行25-800秒,例如100-500秒。可通过任何合适的加热***或方法,例如使用辐射加热、感应加热、直接火焰炉加热等来实现第二步骤的第一阶段加热。
在达到均热区域温度并保持期望的时间段之后,可将钢冷却至大于室温的受控温度到保温区域。在一些实施方案中,在第二步均热过程和第二步保温过程之间将该钢片产品维持在大于300℃的温度下。可通过常规技术例如水冷却、气体冷却等来实现从均热至保温区域的冷却。可典型地使用5-400℃/秒的平均冷却速率。任何合适类型的冷却和淬火***可适合于在从均热温度至保温温度的冷却中使用,包括以上描述的那些。
按照本发明的实施方案,在360-445℃的典型温度下,例如370-440℃进行保温区域步骤。保温区域可保持至多800秒,例如30-600秒。
保温区域温度可保持恒定,或可在优选的温度范围内稍微变化。在保温之后,如果钢待热浸涂覆,可例如通过感应或其它加热方法将钢再加热从而在用于获得良好涂覆结果的适当温度下进入热浸涂覆罐。
在一些实施方案中,在保温区域温度维持了期望的时间段之后,可将温度倾斜下降至室温。这样的倾斜下降可任选进行10-1000秒,例如约20-500秒。这样的倾斜下降的速率可典型地范围为1-1000℃/秒,例如2-20℃/秒。
按照一些实施方案,可在连续退火生产线(CAL)上进行第一步和第二步退火过程之一或两者。在经过CAL+CAL过程之后,可电镀钢以制备基于锌的涂覆的产品。
在一些实施方案中,在保温区域结束时热浸电镀该退火的钢片。电镀温度可典型地范围为440-480℃,例如450-470℃。在一些实施方案中,可在例如如图2中显示的连续电镀生产线(CGL)上进行电镀步骤作为第二步退火过程的一部分。可使用这种CAL+CGL过程来制备基于锌的或基于锌合金的热浸电镀产品或在涂覆之后再加热以制备电镀铁-锌镀层扩散退火类型的涂覆产品。任选的基于镍的涂覆步骤可发生在方法中的CAL和CGL步骤之间以改进锌涂层性质。第二步骤中使用连续电镀生产线相对使用CAL+CAL+EG路线提高了制备涂覆的GEN3产品的效率。
还可在专门设计的CGL上制成电镀产品或基于锌的合金的热浸涂覆产品,在专门设计的CGL中可在单一生产线中发生两步退火,如图3中显示。在这种情况下锌镀层扩散退火可也为选择。此外,还可专门设计和建造单一制备设备来结合两步热过程以制备如本发明中限定的未涂覆的第三代钢材。
以下实施例意图说明本发明的各方面,并不意图限制发明的范围。
实施例1
具有如表2中所列组成的冷轧钢片1号样品经历如图1中说明的两步退火方法。在图5和6中显示所得产物的显微组织。使用商购EDAX取向成像显微法软件的EBSD技术显示在图5中暗的铁素体晶粒和亮的奥氏体晶粒。
实施例2
具有如表2中所列组成的冷轧钢片2号样品经历如图1中说明的两步退火方法。在图11中显示所得产物的显微组织。在表2中列出2号样品的机械性质。在图9和10中分别显示奥氏体和铁素体的晶粒尺寸分布。平均奥氏体晶粒尺寸小于1微米且平均铁素体晶粒尺寸小于10微米。
显微组织包括约80体积%的具有约5微米的平均晶粒尺寸的铁素体,约10体积%的具有基本上等轴的晶粒和约0.5微米的平均晶粒尺寸的残余奥氏体,和约10体积%的具有约5微米的平均晶粒尺寸的新生马氏体。在以下表2中列出1号样品的机械性质。
实施例3
具有如表2中所列组成的冷轧钢片3号样品经历如图2中说明的两步退火方法。在图12和13中显示所得产物的显微组织。在图13中,奥氏体颜色亮且铁素体颜色暗。在表2中列出3号样品的机械性质。
实施例4
具有如表2中所列组成的冷轧钢片4号样品经历如图3中说明的两步退火方法。在图14中显示所得产物的显微组织。在图14中,奥氏体颜色亮和铁素体颜色暗。在表2中列出4号样品的机械性质。
实施例5
具有如表2中所列组成的冷轧钢片5号样品经历如图1中说明的两步退火方法。在表2中列出5号样品的机械性质。
实施例6
具有如表2中所列组成的冷轧钢片6号样品经历如图1中说明的两步退火方法。在表2中列出6号样品的机械性质。图7是显示图2中显示的6号钢样品的显微组织的光学图像,所述6号样品经历图1中显示的两步退火方法。在图7中,显微照片的暗区域是铁素体晶粒,而亮区域是奥氏体晶粒。图8是说明图7中显示的奥氏体晶粒的纵横比的图。使用图7的光学图像来确定奥氏体晶粒的纵横比,其中使用可商购得到的软件的图像分析。图7显示奥氏体晶粒的平均纵横比小于3:1。
实施例7
具有如表2中所列组成的冷轧钢片7号样品经历如图2中说明的两步退火方法。在表2中列出7号样品的机械性质。
实施例8
具有如表2中所列组成的冷轧钢片8号样品经历如图3中说明的两步退火方法。在表2中列出8号样品的机械性质。
实施例1-8中的钢材表现出在700至1100MPa范围内的UTS水平。
比较例1-4
具有如表2中所列组成的冷轧钢片C1-C4号样品经历如图1中说明的两步退火方法。在表2中列出C1-C4号样品的机械性质。比较例1-4中的钢材表现出小于700MPa的UTS水平。
比较例5-8
具有如表2中所列组成的冷轧钢片C5-C8号样品经历如图1中说明的两步退火方法。在表2中列出C5-C8号样品的机械性质。比较例5-8中的钢材表现出大于1100MPa的UTS水平。
比较例9-11
具有如表2中所列组成的冷轧钢片C9-C11号样品经历与图1中说明的类似的两步退火方法,除了第二退火中的均热或保温温度在发明的优选范围外。在表2中列出C9-C11号样品的机械性质。
比较例12
具有表2中所列组成的冷轧片C12号样品经历与图2中说明的类似的两步退火方法,除了第二退火中的保温区域温度在发明的优选范围外。在表2中列出C12号样品的机械性质。
图15绘制实施例1-8的样品1-8以及比较例C1-C12的样品C1-C12的总延伸率(TE)和极限拉伸强度(UTS)。在图15中粗略地绘制与25000的UTS·TE对应的线。如可看出,按照本发明制备的高强度钢片样品相对于比较样品具有强度和延伸率的优异组合,即对于本发明实施例观察到在高UTS水平下高的总延伸率性质。样品1至样品8钢材落入第三代先进高强度钢材的范畴,其为汽车和其它产业高度期望的。
实施例9
使用CAL+CAL或CAL+CGL方法对于以下表3中标号M1-M5的样品进行工厂试验。对于样品M1、M2和M5,使用图1中显示的CAL+CAL加工时间和温度。对于样品M3和M4,使用图2中显示的CAL+CGL加工时间和温度。
表3
工厂试验结果
图16显示工厂试验材料的强度-延伸率平衡,全部满足25,000的最小UTS·TE。试验材料表现出λ值大于20%。
实施例10
对应于表4中9A-12B号样品的具有0.23重量%C、2.3重量%Mn、0.6重量%Si和0.8重量%Al的组成的冷轧和热轧钢片材经历如图17中显示的两阶段退火方法。在表4中,冷轧样品列为“CR”基材类型,且热轧样品列为“HR”基材类型。在表4中列出9A-12B号样品的机械性质。热轧基材样品显示可与冷轧样品比较的优异的YS、UTS、TE和扩孔性质,显示直接加工成两阶段退火方法的热轧基材可产生第三代AHSS性质。此外,如图18和19中显示的EBSD相分布(其中残余奥氏体晶粒比铁素体晶粒更亮)中表示,当与冷轧材料相比热轧材料观察到类似的奥氏体含量、分布和形态。图18显示冷轧样品11A的奥氏体含量且图19显示热轧样品12A的奥氏体含量。在两个显微组织中观察到奥氏体的细的主要是等轴的分布。
表4
如本文使用的,“包括”、“含有”和类似术语在本申请的上下文中应理解为与“包含”同义,并因此是开放式的且没有排除额外的未描述或未记载的元素、材料、相或方法步骤的存在。如本文使用的,“由...组成”在本申请的上下文中应理解为排除任何未规定的元素、材料、相或方法步骤的存在。如本文使用的,“基本上由...组成”在本申请的上下文中应理解为当适用时包括规定的元素、材料、相或方法步骤,并还包括没有实质上影响发明的基础或新颖特性的任何未规定的元素、材料、相或方法步骤。
尽管列出本发明的宽泛范围的数值范围和参数是近似值,但尽可能精确地报告在具体实施例中列出的数值。然而,任何数值固有地含有由在它们各自的测试测量中发现的标准变化所必然产生的一些误差。
此外,应理解本文记载的任何数值范围意图包括其中包括的全部子范围。例如,“1至10”的范围意图包括在记载的最小值为1和记载的最大值为10之间(并包括记载的最小值为1和记载的最大值为10)的全部子范围,即具有最小值等于或大于1和最大值等于或小于10的全部子范围。
在本申请中,单数的使用包括复数且复数包括单数,除非另外具体指出。另外,在本申请中,使用“或”意为“和/或”,除非另外具体指出,即使可在一些情况下明确地使用“和/或”。在本申请和所附权利要求书中,除非清楚和明确地限制为一个所指物,否则冠词“一个”、“一种”和“该”包括复数所指物。
尽管就说明的目的而言以上描述了本发明的特定实施方案,对本领域技术人员将明显的是可在不偏离本发明的情况下进行本发明的细节的数值变化。
Claims (33)
1.高强度轧制钢片产品,其包含0.12-0.5重量%的C、1-3重量%的Mn和0.8-3重量%的Si与Al的组合,其中该钢片产品经历了两步退火过程,包含铁素体和平均纵横比小于3:1的基本上等轴的残余奥氏体晶粒,并具有大于25000MPa%的极限拉伸强度和总延伸率的组合UTS·TE。
2.根据权利要求1所述的高强度轧制钢片产品,其中Si占至多2重量%,Al占至多2重量%,并且该轧制钢片产品还包含至多0.05重量%的Ti和至多0.05重量%的Nb。
3.根据权利要求2所述的高强度轧制钢片产品,其中C占0.15-0.4重量%,Mn占1.3-2.5重量%,Si占0.2-1.8重量%,Al占至多1.5重量%,Ti占至多0.03重量%,且Nb占至多0.03重量%。
4.根据权利要求1所述的高强度轧制钢片产品,其中铁素体占至少50体积%,残余奥氏体占5-25体积%,且残余奥氏体晶粒的平均纵横比小于2:1。
5.根据权利要求1所述的高强度轧制钢片产品,其中残余奥氏体具有小于10微米的平均晶粒尺寸。
6.根据权利要求5所述的高强度轧制钢片产品,其中残余奥氏体具有小于1微米的平均晶粒尺寸。
7.根据权利要求5所述的高强度轧制钢片产品,其中该轧制钢片产品包含小于15体积%的新生马氏体。
8.根据权利要求1所述的高强度轧制钢片产品,其中该轧制钢片产品具有720-1100MPa的极限拉伸强度并具有至少20%的总延伸率。
9.根据权利要求1所述的高强度轧制钢片产品,其中该轧制钢片产品具有大于20%的扩孔比。
10.根据权利要求1所述的高强度轧制钢片产品,其中UTS·TE为至少27000MPa%。
11.根据权利要求1所述的高强度轧制钢片产品,还包含在该轧制钢片产品上的基于锌的涂层。
12.根据权利要求1所述的高强度轧制钢片产品,其中该轧制钢片产品是热轧的。
13.制备高强度轧制钢片产品的方法,所述产品包含0.12-0.5重量%的C、1-3重量%的锰和0.8-3重量%的Si与Al的组合,该方法包括:
使钢片产品经历第一步退火过程以实现主要是马氏体的显微组织;并且
使钢片产品经历第二步过程,所述第二步过程包括将临界状态下的片材产品在720-850℃的温度下均热,之后将片材产品保持在360-445℃的温度下,其中该钢片产品包含铁素体和平均纵横比小于3:1的基本上等轴的残余奥氏体晶粒,并具有大于25000MPa%的极限拉伸强度和总延伸率的组合UTS·TE。
14.根据权利要求13所述的方法,其中在大于820℃的温度下进行第一步退火过程。
15.根据权利要求13所述的方法,其中在830-940℃的温度下进行第一步退火过程。
16.根据权利要求13所述的方法,其中在720-850℃的温度下进行第二步均热过程,且在370-440℃的温度下进行第二步保温过程。
17.根据权利要求13所述的方法,其中在第一步过程和第二步过程之间将该钢片产品冷却至低于300℃的温度。
18.根据权利要求13所述的方法,其中在第二步均热过程和第二步保温过程之间将该钢片产品维持在大于300℃的温度下。
19.根据权利要求13所述的方法,其中在连续退火生产线上进行第一步退火过程,且在连续退火生产线上进行第二步过程。
20.根据权利要求19所述的方法,其中对于第一步退火过程和第二步过程两者使用相同的连续退火生产线。
21.根据权利要求19所述的方法,其中对于第一步退火过程和第二步过程使用分别的连续退火生产线。
22.根据权利要求13所述的方法,其中在连续退火生产线上进行第一步退火过程,且在连续电镀生产线上进行第二步过程。
23.根据权利要求13所述的方法,还包括用基于锌的涂层电解涂覆该轧制钢片产品。
24.根据权利要求13所述的方法,其中Si占至多2重量%,Al占至多2重量%,并且该轧制钢片产品还包含至多0.05重量%的Ti和至多0.05重量%Nb。
25.根据权利要求25所述的方法,其中C占0.15-0.4重量%,Mn占1.3-2.5重量%,Si占0.2-1.8重量%,Al占至多1.5重量%,Ti占至多0.03重量%,且Nb占至多0.03重量%。
26.根据权利要求13所述的方法,其中在第一步退火过程前将轧制钢片产品热轧。
27.根据权利要求13所述的方法,其中铁素体占至少50体积%,残余奥氏体占5-25体积%,且残余奥氏体晶粒的平均纵横比小于2:1。
28.根据权利要求13所述的方法,其中残余奥氏体具有小于10微米的平均晶粒尺寸。
29.根据权利要求29所述的方法,其中残余奥氏体具有小于1微米的平均晶粒尺寸。
30.根据权利要求13所述的方法,其中该轧制钢片产品包含小于15体积%的新生马氏体。
31.根据权利要求13所述的方法,其中该轧制钢片产品具有720-1100MPa的极限拉伸强度并具有至少20%的总延伸率。
32.根据权利要求13所述的方法,其中该轧制钢片产品具有大于20%的扩孔比。
33.根据权利要求13所述的方法,还包括在该轧制钢片产品上施加基于锌的涂层。
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PCT/US2020/046847 WO2021034851A1 (en) | 2019-08-19 | 2020-08-18 | High strength steel products and annealing processes for making the same |
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