CN111433379A - 冷轧热处理钢板及其制造方法 - Google Patents
冷轧热处理钢板及其制造方法 Download PDFInfo
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- CN111433379A CN111433379A CN201880072415.6A CN201880072415A CN111433379A CN 111433379 A CN111433379 A CN 111433379A CN 201880072415 A CN201880072415 A CN 201880072415A CN 111433379 A CN111433379 A CN 111433379A
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- Heat Treatment Of Steel (AREA)
Abstract
一种冷轧热处理钢板,具有包含以重量%表示的以下元素的组成:0.10%≤碳≤0.5%、1%≤锰≤3.4%、0.5%≤硅≤2.5%、0.03%≤铝≤1.5%、硫≤0.003%、0.002%≤磷≤0.02%、氮≤0.01%,以及可以包含以下任选的元素中的一者或更多者:0.05%≤铬≤1%、0.001%≤钼≤0.5%、0.001%≤铌≤0.1%、0.001%≤钛≤0.1%、0.01%≤铜≤2%、0.01%≤镍≤3%、0.0001%≤钙≤0.005%、钒≤0.1%、硼≤0.003%、铈≤0.1%、镁≤0.010%、锆≤0.010%,余量组成由铁和因加工而引起的不可避免的杂质构成,以及所述轧制钢板的显微组织以面积分数计包含10%至30%的残余奥氏体、5%至50%的退火贝氏体、10%至40%的贝氏体、1%至20%的淬火马氏体和少于30%的回火马氏体,其中贝氏体和残余奥氏体的组合存在应该为30%或更大。
Description
本发明涉及适合于用作汽车用钢板的冷轧热处理钢板。
汽车部件需要满足两个不一致的需求,即易于成形和强度,但是近年来,考虑到全球环境问题,还给予汽车改善燃料消耗的第三个要求。因此,现在汽车部件必须由具有高成形性的材料制成,以便符合复杂汽车组装中的易于装配的标准,并且同时必须在减轻车辆的重量以改善燃料效率的同时改善对于车辆抗撞性和耐久性的强度。
因此,进行了认真的研究和开发努力以通过增加材料的强度来减少汽车中使用的材料的量。相反地,钢板强度的增加降低成形性,因此需要开发不仅具有高强度而且具有高成形性的材料。
高强度高成形性钢板领域中的较早的研究和开发已经实现了多种用于制造高强度高成形性钢板的方法,本文列举了其中一些以便对本发明作出最终理解:
EP3144406专利要求保护具有优异的延展性的高强度冷轧钢板,其以重量%计包含:碳(C):0.1%至0.3%、硅(Si):0.1%至2.0%、铝(Al):0.005%至1.5%、锰(Mn):1.5%至3.0%、磷(P):0.04%或更少(不包括0%)、硫(S):0.015%或更少(不包括0%)、氮(N):0.02%或更少(不包括0%)、以及余量的铁(Fe)和不可避免的杂质,其中硅和铝之和(Si+Al)(重量%)满足1.0%或更大,以及其中显微组织以面积分数计包含:5%或更少的短轴与长轴之比为0.4或更大的多边形铁素体、70%或更少(不包括0%)的短轴与长轴之比为0.4或更小的针状铁素体、25%或更少(不包括0%)的针状残余奥氏体、以及余量的马氏体。此外,EP3144406设想了具有780MPa或更大的抗拉强度的高强度钢。
EP3128023提及具有优异的延伸率、扩孔性、耐延迟断裂性和高屈服比的高强度冷轧钢板以及用于制造该钢板的方法。高屈服比高强度冷轧钢板具有以质量%计包含以下的组成:C:0.13%至0.25%、Si:1.2%至2.2%、Mn:2.0%至3.2%、P:0.08%或更少、S:0.005%或更少、Al:0.01%至0.08%、N:0.008%或更少、Ti:0.055%至0.130%、以及余量的Fe和不可避免的杂质。该钢板具有如下显微组织:包含以体积分数计2%至15%的平均晶粒直径为2.0μm或更小的铁素体、以体积分数计5%至20%的平均晶粒直径为0.3μm至2.0μm的残余奥氏体、以体积分数计10%或更少(包括0%)的平均晶粒直径为2μm或更小的马氏体、以及余量的贝氏体和回火马氏体,并且贝氏体和回火马氏体的平均晶粒直径为5μm或更小。
EP3009527提供了具有优异的延伸率、优异的延伸凸缘性和高屈服比的高强度冷轧钢板及其制造方法。该高强度冷轧钢板具有组成和显微组织。组成基于质量包含0.15%至0.27%的C、0.8%至2.4%的Si、2.3%至3.5%的Mn、0.08%或更少的P、0.005%或更少的S、0.01%至0.08%的Al和0.010%或更少的N、余量的铁和不可避免的杂质。显微组织包含:平均晶粒尺寸为5μm或更小且体积分数为3%至20%的铁素体、体积分数为5%至20%的残余奥氏体、以及体积分数为5%至20%的马氏体、余量的贝氏体和/或回火马氏体。晶粒尺寸为2μm或更小的残余奥氏体、晶粒尺寸为2μm或更小的马氏体、或其混合相的总数量为每2,000μm2平行于钢板的轧制方向的厚度截面150个或更多。
本发明的目的是通过提供同时具有以下的冷轧热处理钢板来解决这些问题:
-大于或等于950MPa,优选地高于980MPa的极限抗拉强度,
-大于或等于20%,优选地高于21%的总延伸率。
在一个优选实施方案中,根据本发明的钢板具有0.60以上或更大的屈服强度/抗拉强度之比。
在一个优选实施方案中,根据本发明的钢板还可以表现出屈服强度等于或大于600MPa。
优选地,这样的钢还可以具有良好的成形适合性(对于轧制尤其如此)以及良好的焊接性和涂覆性。
本发明的另一个目的还在于提供与常规工业应用相容同时对于制造参数改变是稳健的用于制造这些板的方法。
本发明的冷轧热处理钢板可以任选地涂覆有锌或锌合金,或者涂覆有铝或铝合金以改善其耐腐蚀性。
碳以0.10%至0.5%存在于钢中。碳是通过产生低温转变相例如马氏体来增加本发明的钢的强度所必需的元素,此外,碳在奥氏体稳定化中也起着关键作用,因此是用于确保残余奥氏体所必需的元素。因此,碳起着两个关键作用,一个是增加强度,另一个是保持奥氏体以赋予延展性。但是碳含量小于0.10%将不能以本发明的钢所需的足够量使奥氏体稳定化。另一方面,在碳含量超过0.5%时,钢表现出差的点焊性,这限制其用于汽车部件的应用。
本发明的钢的锰含量为1%至3.4%。该元素为γ的。添加锰的目的实质上是为了获得包含奥氏体的组织。锰是使奥氏体在室温下稳定以获得残余奥氏体的元素。为了向本发明的钢提供强度和淬透性以及使奥氏体稳定,锰的至少约1重量%的量是强制的。因此,本发明优选较高百分比的锰,例如3.4%。但是当锰含量大于3.4%时,其产生不利的影响例如其在用于贝氏体转变的等温保温期间阻碍奥氏体向贝氏体的转变。此外,锰含量高于3.4%还会使本发明的钢的焊接性劣化,以及可能会无法实现延展性目标。锰的优选范围为1.2%至2.3%,并且更优选的范围为1.2%至2.2%。
本发明的钢的硅含量为0.5%至2.5%。硅是可以在过时效期间阻止碳化物的析出的成分,因此,由于硅的存在,富含碳的奥氏体在室温下是稳定的。此外,由于硅在碳化物中的溶解度差,其有效地抑制或阻止碳化物的形成,因此还促进在贝氏体组织中形成低密度碳化物,根据本发明这是所寻求的以赋予本发明的钢以其基本机械特性。然而,不成比例的硅含量不会产生所提及的效果并且导致诸如回火脆化的问题。因此,将浓度控制在2.5%的上限以内。
铝的含量为0.03%至1.5%。在本发明中,铝除去钢水中存在的氧从而防止氧在凝固过程期间形成气相。铝还使钢中的氮固定从而形成铝氮化物以便减小晶粒的尺寸。高于1.5%的较高铝含量使Ac3点升高至高温,从而降低生产率。当添加高的锰含量时,可以使用1.0%至1.5%的铝含量,以平衡锰对转变点和随温度的奥氏体形成演变的影响。
本发明的钢的铬含量为0.05%至1%。铬是为钢提供强度和硬化的必需元素,但是当高于1%使用时,损害钢的表面光洁度。此外,低于1%的铬含量会使碳化物在贝氏体组织中的分散模式粗化,并因此,保持碳化物的密度在贝氏体中是低的。
铌以0.001%至0.1%存在于本发明的钢中,并且适合于形成碳氮化物从而通过析出硬化赋予本发明的钢的强度。铌还会通过其析出为碳氮化物以及通过阻止加热过程期间的再结晶而影响显微组织组分的尺寸。因此,在保温温度结束时并因此在退火完成之后形成的更细的显微组织使产品硬化。然而,铌含量高于0.1%在经济上得不到关注,因为观察到其影响的饱和作用,这意味着额外量的铌不会产生产品的任何强度改善。
钛与铌一样以0.001%至0.1%被添加到本发明的钢中,其包含在碳氮化物中,因此在硬化方面起作用。但是其还形成在铸造产品的凝固期间出现的钛氮化物。因此将钛的量限制为0.1%以避免形成对成形性不利的粗大钛氮化物。如果钛含量低于0.001%,则对本发明的钢不会赋予任何作用。
本发明的钢的磷成分为0.002%至0.02%。磷降低点焊性和热延展性,特别是由于其倾向于在晶界处偏析或与锰共偏析。由于这些原因,将其含量限制为0.02%,并且优选低于0.013%。
硫不是必需元素但是可能作为杂质包含在钢中,并且从本发明的观点出发,优选硫含量尽可能低,但是从制造成本的观点出发为0.003%或更少。此外,如果钢中存在较高的硫,则其尤其与锰结合以形成硫化物并且降低其对本发明的有益影响。
本发明的钢中的钙含量为0.001%至0.005%。钙作为任选的元素被添加到本发明的钢中,在夹杂物处理期间尤其如此。钙通过捕获呈球状形式的有害硫内容物从而阻止硫的有害影响而有助于钢的精炼。
氮被限制为0.01%,以避免材料老化并使在凝固期间对钢的机械特性不利的铝氮化物的析出最小化。
钼是任选的元素,构成本发明的钢的0%至0.5%;钼在改善淬透性和硬度方面起着有效作用,延缓贝氏体的出现并且避免在贝氏体中析出碳化物。然而,过量添加钼会增加合金元素的添加成本,使得出于经济原因,将其含量限制为0.5%。
铜可以作为任选的元素以0.01%至2%的量被添加以增加钢的强度并改善其耐腐蚀性。为了获得这样的效果,需要最少0.01%。然而,当其含量高于2%时,其可能使表面方面劣化。
镍可以作为任选的元素以0.01%至3%的量被添加以增加钢的强度并改善其韧性。为了获得这样的效果,需要最少0.01%。然而,当其含量高于3%时,镍导致延展性劣化。
钒有效于通过形成碳化物或碳氮化物来提高钢的强度并且从经济角度出发,上限为0.1%。其他元素例如铈、硼、镁或锆可以以以下比例单独添加或以组合添加:铈≤0.1%、硼≤0.003%、镁≤0.010%和锆≤0.010%。多至所指出的最大含量水平,这些元素使得可以在凝固期间使晶粒细化。钢的组成的剩余部分由铁和加工中产生的不可避免的杂质组成。
本发明要求保护的板的显微组织由以下组成:
贝氏体,其以面积分数计构成本发明的钢的显微组织的10%至40%。在本发明中,本发明的贝氏体累积由板条贝氏体和粒状贝氏体组成。为了确保20%的总延伸率,具有10%的贝氏体是强制的。
残余奥氏体,其以面积分数计构成钢的10%至30%。已知残余奥氏体具有比贝氏体更高的碳溶解度,并因此充当有效的碳捕集器(Carbon trap),从而阻止在贝氏体中形成碳化物。本发明的残余奥氏体内的碳百分比优选高于0.9%,并且优选低于1.1%。根据本发明的钢的残余奥氏体赋予增强的延展性。
退火贝氏体,其以面积分数计构成本发明的钢的显微组织的5%至50%。退火贝氏体赋予本发明的钢强度和成形性。退火贝氏体在T均热至Ac3的温度下进行第二退火期间形成。需要具有5%的退火贝氏体以达到本发明的钢的目标延伸率,但是当退火贝氏体的量超过50%时,本发明的钢无法达到强度。
淬火马氏体,其以面积分数计构成显微组织的1%至20%。淬火马氏体赋予本发明强度。淬火马氏体在第二退火的冷却期间形成。不需要最小量,但是当淬火马氏体超过20%时,其赋予过高的强度,但是使其他机械特性劣化,超出可接受的限制。
回火马氏体,其以面积分数计构成显微组织的0%至30%。当将钢在Tcmin至Tcmax下冷却并在过时效保温期间进行回火时,可以形成马氏体。回火马氏体赋予本发明延展性和强度。当回火马氏体超过30%时,其赋予过高的强度,但是减小延伸率,超过可接受的限制。
除了上述显微组织之外,在不损害钢板的机械特性的情况下,冷轧热处理钢板的显微组织不含诸如珠光体、铁素体和渗碳体的显微组织组分。
根据本发明的钢板可以通过任何合适的方法来制造。一种优选方法在于提供具有根据本发明的化学组成的钢的半成品铸件。铸件可以被制成锭料或者连续地呈薄板坯或薄带的形式,即厚度范围从对于板坯为约220mm到对于薄带为数十毫米。
例如,具有上述化学组成的板坯通过连续铸造而制造,其中板坯任选地在连续铸造过程期间经历直接轻压下以避免中心偏析并确保局部碳与标称碳之比保持低于1.10。通过连续铸造过程提供的板坯可以在连续铸造之后在高温下直接使用,或者可以首先冷却至室温,然后再加热以进行热轧。
经受热轧的板坯的温度优选为至少1200℃并且必须低于1280℃。如果板坯的温度低于1200℃,则对轧机施加过大的负荷,此外,钢的温度可能在精轧期间降低至铁素体转变温度,由此钢会在组织中包含转变铁素体的状态下被轧制。因此,板坯的温度优选足够高,使得可以在Ac3至Ac3+100℃的温度范围内完成热轧并且最终轧制温度保持高于Ac3。必须避免在高于1280℃的温度下进行再加热,原因是这在工业上是昂贵的。
优选Ac3至Ac3+100℃的最终轧制温度范围以具有有利于再结晶和轧制的组织。必需使最终轧制道次在高于Ac3的温度下进行,原因是低于该温度,钢板表现出显著的可轧制性下降。然后将以这种方式获得的板以高于30℃/秒的冷却速率冷却至卷取温度,卷取温度必须低于600℃。优选地,冷却速率小于或等于200℃/秒。
在低于600℃的卷取温度下对热轧钢板进行卷取以避免热轧钢板的椭圆化并且优选低于570℃以避免氧化皮形成。卷取温度的优选范围为350℃至570℃。经卷取的热轧钢板在使其经受任选的热带退火之前被冷却至室温。
可以使热轧钢板经受任选的氧化皮去除步骤以去除在热轧期间形成的氧化皮。然后可以使热轧板在400℃至750℃的温度下经受任选的热带退火至少12小时且不长于96小时,但是应该使温度保持低于750℃以避免使经热轧的显微组织部分转变并因此丧失显微组织均匀性。其后,可以例如通过对这样的钢板进行酸洗来进行任选的氧化皮去除步骤以去除氧化皮。以35%至90%的厚度压下率对该热轧钢板进行冷轧。然后使由冷轧过程获得的冷轧钢板经受两个退火步骤以赋予本发明的钢以显微组织和机械特性。
在冷轧钢板的第一退火中,以大于3℃/秒的加热速率将冷轧钢板加热至Ac3至Ac3+100℃的均热温度,其中本发明的钢的Ac3通过使用下式来计算:
Ac3=901-262*C-29*Mn+31*Si-12*Cr-155*Nb+86*Al
其中元素含量以重量%表示。
将钢板在均热温度下保温10秒至500秒以确保强加工硬化初始组织完全再结晶并完全转变成奥氏体。然后以大于25℃/秒的冷却速率将板冷却至380℃至480℃的范围,并且优选冷却至380℃至450℃的范围,并将冷轧钢板保温10秒至500秒,然后将冷轧钢板冷却至室温以获得退火冷轧钢板。
以大于3℃/秒的加热速率将冷轧退火钢板的第二退火加热至T均热至Ac3的均热温度,其中:
T均热=830-260*C-25*Mn+22*Si+40*Al
其中元素含量以重量%表示。
持续10秒至500秒以确保充足的再结晶和转变从而获得最少50%的奥氏体显微组织。然后以大于20℃/秒的冷却速率将板冷却至Tcmax至Tcmin范围内的温度。这些Tcmax和Tcmin如下限定:
Tcmax=565-601*(1-Exp(-0.868*C))-34*Mn-13*Si-10*Cr+13*Al-361*Nb
Tcmin=565-601*(1-Exp(-1.736*C))-34*Mn-13*Si-10*Cr+13*Al-361*Nb
其中元素含量以重量%表示。
其后,使冷轧退火钢板达到380℃至580℃的温度范围并保温10秒至500秒以确保形成足够量的贝氏体以及对马氏体进行回火从而赋予本发明的钢以目标机械特性。之后,以至少1℃/秒的冷却速率将冷轧退火钢板冷却至室温以形成淬火马氏体,从而获得冷轧热处理钢板。
然后可以任选地通过任何已知的工业方法(例如电镀锌、JVD、PVD、热浸(GI/GA)等)涂覆冷轧热处理钢板。电镀锌不会改变或修改所要求保护的冷轧热处理钢板的任何机械特性或显微组织。电镀锌可以通过任何常规的工业方法例如通过电镀完成。
本文提供的以下测试、实施例、图示和表本质上是非限制性的,并且必须仅为了举例说明的目的而考虑,并且将显示本发明的有利特征。
表1中列举并收集了由具有不同组成的钢制成的钢板,其中分别根据如表2中所记录的工艺参数制造钢板。其后,表3收集了在试验期间获得的钢板的显微组织,以及表4收集了所获得的特性的评估结果。
表1描绘了具有以重量%表示的组成的钢。钢组成I1至I5用于制造根据本发明的板,该表还说明了在表中由R1至R4指定的参照钢组成。
表1还用作本发明的钢与参照钢之间的比较表格。表1在此:
表2
表2收集了对表1的钢实施的退火工艺参数。钢组成I1至I5用于制造根据本发明的板,该表还说明了在表中由R1至R4指定的参照钢。表2还示出了Tcmin和Tcmax的表格。对于本发明的钢和参照钢,这些Tcmax和Tcmin如下限定:
Tcmax=565-601*(1-Exp(-0.868*C))-34*Mn-13*Si-10*Cr+13*Al-361*Nb
Tcmin=565-601*(1-Exp(-1.736*C))-34*Mn-13*Si-10*Cr+13*Al-361*Nb
此外,在对本发明的钢以及参照钢进行退火处理之前,将钢加热到1000℃至1280℃的温度,然后以高于850℃的最终温度进行热轧,其后在低于600℃的温度下进行卷取。然后按要求对热轧卷料进行加工,其后以30%至95%的厚度压下率进行冷轧。使本发明的钢和参照钢二者的这些冷轧钢板经受如本文表2中列举的热处理:
表3
表3例示了根据标准在不同显微镜(例如扫描电子显微镜)上进行的测试以确定本发明的钢和参照钢二者的显微组织组成的结果。
结果记录在此:
I=根据本发明;R=参照;带下划线的值:非根据本发明。
表4
表4例示了本发明的钢和参照钢二者的机械特性。为了确定抗拉强度、屈服强度和总延伸率,根据JIS Z2241标准进行拉伸测试。
在此之后根据标准进行的各机械测试的结果被制成表:
I=根据本发明;R=参照;带下划线的值:非根据本发明。
Claims (21)
1.一种冷轧热处理钢板,具有包含以重量%表示的以下元素的组成:
0.10%≤碳≤0.5%
1%≤锰≤3.4%
0.5%≤硅≤2.5%
0.03%≤铝≤1.5%
硫≤0.003%
0.002%≤磷≤0.02%
氮≤0.01%
可选择地包含以下元素中的一者或更多者:
0.05%≤铬≤1%
0.001%≤钼≤0.5%
0.001%≤铌≤0.1%
0.001%≤钛≤0.1%
0.01%≤铜≤2%
0.01%≤镍≤3%
0.0001%≤钙≤0.005%
钒≤0.1%
硼≤0.003%
铈≤0.1%
镁≤0.010%
锆≤0.010%
余量组成由铁和因加工而引起的不可避免的杂质构成,以及所述轧制钢板的显微组织以面积分数计包含10%至30%的残余奥氏体、5%至50%的退火贝氏体、10%至40%的贝氏体、1%至20%的淬火马氏体和少于30%的回火马氏体,其中贝氏体和残余奥氏体的组合存在应该为30%或更大。
2.根据权利要求1所述的冷轧热处理钢板,其中组成包含0.7%≤硅≤2.2%。
3.根据权利要求1至2所述的冷轧热处理钢板,其中组成包含1%≤硅≤2.2%。
4.根据权利要求1至3所述的冷轧热处理钢板,其中组成包含0.03%≤铝≤1.0%。
5.根据权利要求1至4所述的冷轧热处理钢板,其中组成包含1.2%≤锰≤2.3%。
6.根据权利要求1至5所述的冷轧热处理钢板,其中组成包含0.05%≤铬≤0.5%。
7.根据权利要求1至6所述的冷轧热处理钢板,其中残余奥氏体和贝氏体相之和大于35%。
8.根据权利要求1至7所述的冷轧热处理钢板,其中退火贝氏体和贝氏体相之和大于45%。
9.根据权利要求1至8所述的冷轧热处理钢板,其中残余奥氏体为15%至30%。
10.根据权利要求1至9所述的冷轧热处理钢板,其中贝氏体为15%至40%。
11.根据权利要求1至10所述的冷轧热处理钢板,具有大于950MPa的抗拉强度和20%或更大的总延伸率。
12.根据权利要求1至11所述的冷轧热处理钢板,具有高于600MPa的屈服强度,以及屈服强度与抗拉强度之比为0.6或更大。
13.根据权利要求1至12所述的冷轧热处理钢板,具有1000MPa至1100MPa的抗拉强度和23%或更大的总延伸率。
14.根据权利要求1至13所述的冷轧热处理钢板,其中不包含铁素体。
15.一种制造根据权利要求1至14所述的冷轧热处理钢板的方法,包括以下步骤:
-提供根据权利要求1至6中任一项所述的钢组成;
-将所述半成品再加热至1200℃至1280℃的温度;
-在其中热轧终轧温度应该高于Ac3的奥氏体范围内对所述半成品进行轧制以获得热轧钢板;
-将所述板以高于30℃/秒的冷却速率冷却至低于600℃的卷取温度,并对所述热轧板进行卷取;
-将所述热轧板冷却至室温;
-可选择地包括:对所述热轧钢板进行氧化皮去除步骤;
-可选择地包括:在400℃至750℃的温度下对热轧钢板进行退火;
-任选地,对所述热轧钢板进行氧化皮去除步骤;
-以35%至90%的压下率对所述热轧钢板进行冷轧以获得冷轧钢板;
-然后通过将所述冷轧钢板以大于3℃/秒的速率加热至Ac3至Ac3+100℃的均热温度并保温10秒至500秒来进行第一退火;
-然后将所述板以大于25℃/秒的速率冷却至380℃至480℃的温度并将所述冷轧钢板保温10秒至500秒的时间;
-将所述冷轧钢板冷却至室温以获得冷轧退火钢板;
-然后通过将所述冷轧退火钢板以大于3℃/秒的速率加热至T均热至Ac3的均热温度并保温10秒至500秒来进行第二退火;
-然后将所述板以大于20℃/秒的速率冷却至Tcmax至Tcmin的温度范围,其中Tcmax至Tcmin如下限定:
Tcmax=565-601*(1-Exp(-0.868*C))-34*Mn-13*Si-10*Cr+13*Al-361*Nb
Tcmin=565-601*(1-Exp(-1.736*C))-34*Mn-13*Si-10*Cr+13*Al-361*Nb
其中C、Mn、Si、Cr、Al和Nb是以钢中的元素的重量%计;
-然后使所述冷轧退火钢板经5秒至500秒达到350℃至550℃的温度范围,并将所述退火冷轧钢板以高于1℃/秒的冷却速率冷却至室温以获得冷轧热处理钢板。
16.根据权利要求15所述的制造冷轧热处理钢板的方法,所述热轧钢板的卷取温度低于570℃。
17.根据权利要求15和16所述的制造冷轧热处理钢板的方法,其中在Ac3至Ac3+75℃的均热温度下对所述冷轧钢板进行10秒至500秒的第一退火。
18.根据权利要求15至17所述的制造冷轧热处理钢板的方法,其中在T均热至Ac3下对一次退火冷轧钢板进行10秒至500秒的连续退火,以使奥氏体与退火贝氏体之比为50:50至90:10。
19.根据权利要求1至14中任一项所述的钢板或根据权利要求15至18的方法制造的钢板用于制造车辆的结构或安全部件的用途。
20.一种根据权利要求19通过对所述钢板进行柔性轧制而获得的部件。
21.一种包括根据权利要求14至20中任一项获得的部件的车辆。
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