CN111315909B - 冷成型性优异的超高强度高延展性钢板及其制造方法 - Google Patents

冷成型性优异的超高强度高延展性钢板及其制造方法 Download PDF

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CN111315909B
CN111315909B CN201880072833.5A CN201880072833A CN111315909B CN 111315909 B CN111315909 B CN 111315909B CN 201880072833 A CN201880072833 A CN 201880072833A CN 111315909 B CN111315909 B CN 111315909B
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steel sheet
less
temperature
ultra
cold
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CN111315909A (zh
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柳朱炫
李圭荣
李世雄
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Posco Holdings Inc
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Posco Co Ltd
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Abstract

本发明涉及一种车辆用钢板，更详细地，涉及一种在确保超高强度和高延展性的同时，由于高屈服强度比而具有优异的冷成型性，并且碰撞特性提高的超高强度高延展性钢板及其制造方法。

Description

冷成型性优异的超高强度高延展性钢板及其制造方法
技术领域
本发明涉及一种车辆用钢板，更详细地，涉及一种冷成型性优异的超高强度高延展性钢板及其制造方法。
背景技术
为了在车辆碰撞时确保乘客的安全性，正在加强车辆的安全标准。为此，需要提高车辆用钢板的强度或厚度，但是，为了提高由于环境问题而被加强的车辆的燃油效率，车辆公司持续地要求车体的轻量化。
为了同时确保车辆的碰撞稳定性和轻量化，需要进行钢板的高强度化。但是，在如上所述提高钢板的强度时，通常会存在钢板的延展性降低的倾向，因此，高强度钢对要求成型性的部件存在使用限制。
为了克服所述高强度钢的缺点，在成型性良好的高温中成型部件后快速冷却至常温以确保低温组织，从而最终开发出了实现高屈服强度和高拉伸强度的热压成型(HotPress Forming，HPF)钢。但是，车辆部件制造公司对热压成型设备的新投资和高温热处理引起的工艺费用的增加最终会导致车辆部件成本的增加。
因此，对具有高强度的同时，延伸率优异且可进行冷压成型(Cold PressForming)的钢材持续地进行研究。
作为一个示例，专利文献1公开了一种通过添加0.5～1.5重量％的碳(C)和10～25重量％的锰(Mn)来获得具有700～900MPa的拉伸强度和50～90％水平的高延展性的超高张力钢板。
专利文献2公开了一种通过添加0.4～0.7％的C、12～24％的Mn获得具有1300MPa以上的拉伸强度、1000MPa以上的屈服强度的同时，还具有优异的碰撞特性的超高强度钢板。
但是，与热压成型钢相比，专利文献1的钢板的屈服强度和拉伸强度低，从而碰撞特性差，因此，在将其作为车辆用结构部件来使用时，其应用受到限制。另外，专利文献2的钢板的延伸率为10％左右且为较低水平，因此，在通过冷压成型来应用于复杂形状的部件时，受到限制，并且由于在退火之后通过再轧制来确保高水平的强度，因此，存在附加工艺导致的制造成本增加的缺点。
因此，需要开发一种可以代替现有的热压成型钢且冷成型性优异的超高强度高延展性钢板。
现有技术文献
(专利文献1)国际公开专利公报WO2011-122237
(专利文献2)韩国公开专利公报第2013-0138039号
发明内容
(一)要解决的技术问题
本发明的一个方面提供一种在确保超高强度和高延展性的同时，由于高屈服强度比而具有优异的冷成型性，并且冲撞特性提高的超高强度高延展性钢板及其制造方法。
(二)技术方案
本发明的一个方面提供一种冷成型性优异的超高强度高延展性钢板，以重量％计，所述钢板包含碳(C)：0.1～0.3％、锰(Mn)：6～10％、磷(P)：0.05％以下、硫(S)：0.02％以下、氮(N)：0.02％以下、铝(Al)：0.5％以下(0％除外)以及选自钛(Ti)：0.1％以下、铌(Nb)：0.1％以下、钒(V)：0.2％以下以及钼(Mo)：1％以下中的1种以上、余量的Fe和其他不可避免的杂质，并且微细组织由体积分数为20％以上的残余奥氏体和60％以上的退火马氏体组成，所述钢板包含1013个/m2以上的具有30nm以下尺寸的析出物。
本发明的另一个方面提供一种冷成型性优异的超高强度高延展性钢板的制造方法，包括以下步骤：以1050～1300℃的温度范围对满足上述合金组成的钢坯进行再加热；在800～1000℃的温度范围内，对再加热的所述钢坯进行热精轧，以制造热轧钢板；在50～750℃的温度范围内收卷所述热轧钢板；在所述收卷后，进行酸洗和冷轧，以制造冷轧钢板；第一次退火热处理，在750～870℃的温度范围内将所述冷轧钢板保持10～3600秒后，冷却至常温～Ms，然后在Ms～500℃的温度范围内进行再加热，并保持10～3600秒，然后冷却至常温；以及第二次退火热处理，在所述第一次退火热处理后，在550～750℃的温度范围内保持10～3600秒后，进行冷却。
(三)有益效果
根据本发明，可以提供一种可以同时满足冷成型用钢板所需的成型性和碰撞稳定性的超高强度钢板。
所述超高强度钢板可以代替现有的热压成型钢，因此具有可以节省制造成本的效果。
附图说明
图1是示出根据本发明的一个实施例的退火工艺的一个示例的图。
图2是示出根据本发明的一个实施例的在第一次退火热处理时，根据退火后的冷却温度的残余奥氏体分数的图表。
图3是观察根据本发明的一个实施例的发明例13的最终微细组织的照片。
最佳实施方式
本发明人为了开发能够替代现有热压成型钢，并且具有同等以上的机械物理性质且可节省部件制造成本的冷压成型用钢板而进行了深入研究。结果，确认可以通过将合金组成、制造条件等最佳化来提供具有适于冷压成型的机械物理性质和微细组织的钢板，并完成了本发明。
下面，对本发明进行详细说明。
优选地，以重量％计，根据本发明的一个方面的冷成型性优异的超高强度高延展性钢板包含碳(C)：0.1～0.3％、锰(Mn)：6～10％、磷(P)：0.05％以下、硫(S)：0.02％以下、氮(N)：0.02％以下、铝(Al)：0.5％以下(0％除外)以及选自钛(Ti)：0.1％以下、铌(Nb)：0.1％以下、钒(V)：0.2％以下以及钼(Mo)：1％以下中的一种以上。
下面，对如上所述限制本发明中提供的超高强度钢板的合金成分的理由进行详细说明。此时，除非有特别说明，各成分的含量表示重量％。
C：0.1～0.3％
碳(C)是用于强化钢的有效元素。在本发明中，为了确保奥氏体的稳定化和强度而添加碳。
为了获得上述效果，优选地，添加0.1％以上的C，但是当C的含量超过0.3％时，存在焊接性降低的可能性。
因此，在本发明中，优选地，将所述C的含量控制在0.1～0.3％。更优选地，可以控制在0.12～0.20％。
Mn：6～10％
锰(Mn)是抑制铁素体的转变且使残留奥氏体形成和稳定化的有效元素。
当所述Mn的含量小于6％时，残余奥氏体的稳定性不足，从而导致机械物理性质的降低。但是，当所述Mn的含量超过10％时，合金成本增加，并且导致焊接性降低，因此不是优选的。
因此，在本发明中，优选地，将所述Mn的含量控制在6～10％。更优选地，可以控制在7～9％。
P：0.05％以下
磷(P)是具有固溶强化效果的元素，但是，当所述P的含量超过0.05％时，焊接性降低，并且引发钢的脆性的危险性增加。
因此，在本发明中，优选地，将所述P的含量控制在0.05％以下，更优选地，可以控制在0.02％以下。但是，考虑到制钢时生产性等降低而排除0％。
S：0.02％以下
硫(S)是不可避免地包含在钢中的元素，并且S是阻碍钢板的延展性和焊接性的元素。
尤其，当所述S的含量超过0.02％时，阻碍钢板的延展性和焊接性的可能性变高，因此，优选控制在0.02％以下。但是，考虑到制钢时生产性等降低而排除0％。
N：0.02％以下
氮(N)是具有固溶强化效果的元素，但是，当所述N的含量超过0.02％时，发生脆性的危险性增加，并且由于与Al结合而析出过量的AlN，从而存在阻碍连铸质量的可能性。
因此，在本发明中，优选将所述N的含量控制在0.02％以下，但是，考虑到制钢时生产性等降低而排除0％。
Al：0.5％以下(0％除外)
铝(Al)是在铁素体内抑制碳化物的生成从而有助于残余奥氏体的稳定化且为了钢的脱氧而添加的元素。
当所述Al的含量超过0.5％时，钢的拉伸强度降低，在铸造时，由于与保护渣的反应，难以制造完好的板坯，并且由于形成表面氧化物而阻碍镀覆性。
因此，在本发明中，优选地，将所述Al的含量控制在0.5％以下。更优选地，可以包含0.3％以下的Al，并且排除0％。
除了上述的合金元素之外，本发明的钢板还可以包含析出物形成元素，具体地，优选包含选自由Ti、Nb、V以及Mo组成的组中的一种以上。
Ti：0.1％以下
钛(Ti)是微细碳化物形成元素，并且Ti有助于屈服强度和拉伸强度的提高。另外，Ti是氮化物形成元素，并且Ti通过将钢中的N析出为TiN来抑制AlN的析出，从而具有在连铸时降低产生裂纹的危险的效果。
当所述的Ti的含量超过0.1％时，析出粗大的碳化物，并且由于钢中碳含量的减少而存在强度和延伸率变差的可能性，并且可能会在连铸时导致喷嘴堵塞。
因此，在本发明中，优选将所述Ti的含量控制在0.1％以下。
Nb：0.1％以下
铌(Nb)是偏析在奥氏体晶界以在退火热处理时抑制奥氏体晶粒的粗大化，并且通过形成微细的碳化物来助于提高强度的元素。
当所述Nb的含量超过0.1％时，析出粗大的碳化物，由于钢中碳含量的减少而存在强度和延伸率降低的可能性，并且存在制造成本增加的问题。
因此，在本发明中，优选将所述Nb的含量控制在0.1％以下。
V：0.2％以下
钒(V)是与碳或氮反应而形成碳氮化物的元素，并且是在低温中形成微细的析出物来增加钢的屈服强度时起到重要作用的元素。
当所述V的含量超过0.2％时，析出粗大的碳化物，由于钢中碳含量的减少而存在强度和延伸率变差的可能性，并且存在制造成本增加的问题。
因此，在本发明中，优选将所述V的含量控制在0.2％以下。
Mo：1％以下
钼(Mo)是形成碳化物的元素，并且在与Ti、Nb、V等复合添加时，具有通过保持析出物的微细的尺寸来提高屈服强度和拉伸强度的效果。
当所述Mo的含量超过1％时，会使上述效果饱和，并且存在反而使制造成本增加的问题。
因此，在本发明中，优选将所述Mo的含量控制在1％以下。
本发明的其余成分是铁(Fe)。但是，在通常的制造过程中，可从原料或周围环境中不可避免地混入不期望的杂质，因此无法排除这些杂质。对本领域的普通技术人员而言，这些杂质是公知的，因此，在本说明书中不对该内容进行特别说明。
另一方面，本发明的钢板还可以包含1.0％以下的硅(Si)。
硅(Si)是固溶强化元素，并且可以以增加钢板的强度为目的添加Si，但是当添加过多时，可能因退火氧化物的生成而发生钢板的镀覆性变差的问题。因此，在添加所述Si时，优选添加1.0％以下的Si。
另外，为了提高机械物理性质等，除了上述的合金元素之外，本发明的钢板还可以包含1％以下的镍(Ni)、0.5％以下的铜(Cu)以及1％以下的铬(Cr)中的一种以上。
所述Ni、Cu以及Cr是有助于残余奥氏体的稳定化的元素，并且通过与C、Si、Mn、Al等的复合作用，可以进一步提高奥氏体的稳定化。
但是，当所述Ni、Cu以及Cr的含量分别超过1％、0.5％、1.0％时，制造成本过度增加，因此不是优选的。
并且，在热轧时，所述Cu可能会引起脆性，因此优选与Ni一起添加。
优选地，满足上述合金组成的本发明的钢板的微细组织包含体积分数为20％以上的残余奥氏体和60％以上的退火马氏体。
当所述残余奥氏体相的分数小于20％，或者退火马氏体相的分数小于60％时，不仅难以确保超高强度，而且难以稳定地确保高延展性和扩孔性。
除所述残余奥氏体相和退火马氏体相之外的余量的组织可以包括ε马氏体和α马氏体相，此时，优选地，包含体积分数为20％以下(包括0％)的所述组织。
本发明的退火马氏体相是指在将高温的奥氏体冷却至马氏体转变温度(Ms)以下时，转变的体心立方结构(BCC)的α马氏体在加热过程中通过恢复减少位错，但是，由于没有发生再结晶而保持针状的状态的相(phase)。马氏体相根据其种类而具有不同的物理性质，因此，本发明的退火马氏体与一般的马氏体相不同。
本发明的钢板包含Ti、Nb、V以及Mo中的一种以上的析出物，具体地，优选包含1013个/m2以上的具有30nm以下的尺寸的析出物。
如果存在大量的尺寸超过30nm的析出物，则由于析出物的粗大化，使得无法获得充分的根据微细析出物的效果，即，提高强度等效果。同样地，当所述微细析出物的数量小于1013个/m2时，也无法获得提高强度的效果。
在本发明中，所述析出物包含碳化物、氮化物以及复合碳氮化物中的一种以上。
如上所述，本发明的钢板的微细组织充分包含残余奥氏体相和退火马氏体相，并且本发明的钢板可通过形成微细析出物来获得1000MPa以上的屈服强度、1250MPa以上的拉伸强度。
进一步地，由于可确保高延展性，拉伸强度和延伸率的乘积为22000MPa％以上，并且扩孔性(HER)为10％以上，因此可以提高冲击特性。
另一方面，在本发明中说明的钢板可以是冷轧钢板，并且还可以是通过镀覆所述冷轧钢板来获得的热浸镀锌钢板或合金化热浸镀锌钢板。
作为一个示例，所述热浸镀锌钢板可以在冷轧钢板的至少一面包括镀锌层，也可以形成有镀锌合金层。
另外，所述合金化热浸镀锌钢板可以是对所述热浸镀锌钢板进行合金化热处理的钢板。
下面，对本发明的另一方面的冷成型性优异的超高强度高延展性钢板的制造方法进行详细说明。
首先，下面，对根据本发明的冷轧钢板的制造方法进行具体说明。
根据本发明的冷轧钢板可在准备满足上述的合金组成的钢坯之后，通对其进行再加热-热轧-收卷-冷轧-退火热处理工艺来制造，下面将对各工艺条件进行详细说明。
[钢坯再加热]
在本发明中，优选地，在进行热轧之前，经过再加热预先准备的钢坯以进行均质化处理的工艺，此时，优选在1050～1300℃下进行再加热工艺。
当所述再加热温度小于1050℃时，在后续的热轧时存在负荷急剧增加的问题，但是，当所述再加热温度超过1300℃时，不仅能量成本增加，还会因表面氧化皮的量的增加而导致材料损失，并且，在含有大量的Mn时，可能存在液体。
因此，优选在1050～1300℃的温度范围内对钢坯进行再加热。
[热轧]
优选地，对再加热的所述钢坯进行热精轧以制造热轧钢板，此时，优选在800～1000℃的温度范围内执行热精轧。
当所述热精轧温度小于800℃时，存在轧制负荷大幅增加的问题，但是，当所述热精轧温度超过1000℃时，引发由氧化皮导致的表面缺陷和轧辊的寿命缩短。
因此，优选在800～1000℃的温度范围内进行热精轧。
[收卷]
优选地，在50～750℃的温度范围内对根据上述方式制造的热轧钢板进行收卷。
当所述收卷温度超过750℃时，钢板表面的氧化皮形成过多，从而引起缺陷，并且这将成为镀覆性变差的原因。另一方面，当钢的组成成分中含有6％以上的Mn时，淬透性大幅增加，因此即使在热轧收卷后冷却至常温，也不会发生铁素体的转变。因此，不需要特别限制收卷温度的下限。但是，当所述收卷温度小于50℃时，为了降低钢板的温度，需要通过喷射冷却水来进行冷却，这会导致不必要的工艺成本的增加，因此，优选地，将收卷温度限制在50℃以上。
另一方面，在根据钢的合金组成中Mn的添加量马氏体的转变开始温度为常温以上时，可能在常温下生成马氏体。在这种情况下，马氏体的组织使得热轧板的强度非常高，因此，可以在冷轧之前进行额外的热处理，以降低在后续冷轧时的负荷。此时，优选地，在可降低热轧材料的强度的500～700℃的温度范围内进行热处理。此时，对热处理时间不进行特别地限定，可根据热轧板的强度水平来适当地选择。
[酸洗和冷轧]
在通过对如上所述收卷的热轧钢板进行传统的酸洗处理去除氧化层后，为了确保钢板的形状和客户要求的厚度，优选执行冷轧。
在所述冷轧时，对压下率不作特别的限制，但是，为了在后续的退火热处理工艺中，抑制再结晶时的粗大铁素体晶粒的生成，优选以15％以上的冷压下率执行。另外，当所述压下率小于15％时，可能难以确保目标水平的强度。
另一方面，当根据钢中Mn的添加量马氏体的转变开始温度为常温以上时，制造的热轧钢板内强度会提高，因此，在进行所述酸洗和冷轧之前，可以进行额外的热处理。其相当于用于降低冷轧时的负荷的工艺。在所述热处理时，只要是能够降低冷轧时的负荷的工艺条件，便对其不作特别的限制，例如，可以在600℃中进行10小时左右的热处理。
[退火]
本发明用于制造具有优异的强度、延伸率以及扩孔性的超高强度钢板，为了获取所述钢板，重要的是根据下述条件来进行退火热处理。尤其，复合残余奥氏体和退火马氏体相来确保最终微细组织，并且为了以此来获得目标物理性质，优选需要阶段性地执行所述退火热处理(图1)。
第一次退火热处理
优选地，进行第一次退火热处理，具体地，将通过完成所述冷轧来获得的冷轧钢板在750～870℃的温度范围内保持10～3600秒后，冷却至常温～Ms，接下来，以Ms～500℃的温度范围进行再加热，并保持10～3600秒，然后重新冷却至常温。
所述最初保持温度(750～870℃)相当于本发明的成分系统中奥氏体的单相区，并且，考虑到退火时相转变活动(kinetic)，优选进行热处理10秒以上。随着退火时间的增加，更接近于平衡相，从而可获得均匀的组织，但是存在工艺成本增加的缺点，因此，优选将其时间限制为3600秒以下。
优选地，在所述温度范围内进行退火后，冷却至常温～Ms(马氏体转变开始温度)的温度范围，之后，优选以Ms～500℃的温度范围进行再加热，然后保持10～3600秒。
在所述退火后冷却至Ms以下时，马氏体的变态转变量随着温度的降低而增加，并且在常温中也可以存在未转变的奥氏体。因此，在经过冷却至Ms以下的冷却过程后，可以由马氏体和奥氏体来组成钢板的组织。
将其再加热至Ms以上的温度时，由于马氏体内的碳固溶度低，因此使马氏体内的碳被分配至周边的奥氏体，从而使得奥氏体的稳定度提高。将其再次冷却至常温时，形成大量的残余奥氏体相，并且余量为马氏体。
将退火后冷却的钢板以Ms以上进行再加热时，马氏体内的碳需要扩散至奥氏体，因此优选保持10秒以上。如果保持时间超过3600秒或者再加热温度超过500℃，则碳在相(phase)之间进行再分配，并且还会析出碳化铁(cementite)，因此反而存在奥氏体的稳定性减小、残余奥氏体相分数降低的可能性。
其中，Ms可以通过下述关系式来导出，常温是指25℃左右的温度。
Ms＝539-423[C]-30.4[Mn]-7.5[Si]+30[Al](各元素指重量含量)
通过所述第一次退火热处理工艺后残余的奥氏体相的分数越高，在后续的第二次退火热处理后最终在钢内的残余奥氏体量越增加，从而可以稳定地确保目标物理性质。
第二次退火热处理
优选地，在双相区温度范围内，对进行所述第一次退火热处理和冷却的冷轧钢板进行退火热处理，更优选地，在550～750℃范围中进行10～3600秒的第二次退火热处理。
在双相区进行退火时，如C、Mn的元素会富集在奥氏体，使得奥氏体的稳定性增加，从而在常温中残留，并且在此进一步施加变形时，残余奥氏体会转变为马氏体，使得钢板的颈缩(necking)现象延迟发生，因此有助于延伸率和强度的提高。
当所述第二次退火热处理在550～750℃的温度范围内进行时，在第一次退火热处理后获得的组织中发生奥氏体的逆转变，从而具有奥氏体分数增加的效果。
此时，考虑到相转变活动(kinetic)，优选进行热处理10秒以上。随着退火时间的增加，更接近于平衡相，从而可获得均匀的组织，但是存在工艺成本增加的缺点，并且存在因组织的粗大而导致物理性质变差的可能性，因此，优选将其时间限制为3600秒以下。
另一方面，本发明可以根据上述方式，阶段性地对退火热处理的冷轧钢板进行镀覆处理，以制造为镀覆钢板。
此时，可以使用电镀镀覆法、热浸镀覆法或者合金化热浸镀覆法，作为一个示例，可以将所述冷轧钢板沉积在镀锌浴中，从而制造出热浸镀锌钢板。进一步地，可以对所述热浸镀锌钢板进行合金化热处理，以制造为合金化热浸镀锌钢板。
对所述镀覆处理时的条件不作特别的限定，可通过通常进行的条件来执行。
下面，通过实施例对本发明进行更详细说明。但是，需要注意的是下述实施例仅是用于更详细地说明本发明的示例，而不是限定本发明的权利范围。这是因为本发明的权利范围由权利要求书中记载的内容和由此合理推导的内容所确定。
具体实施方式
(实施例)
将具有以下表1中的组成成分的钢真空溶解为30Kg的钢锭(ingot)后，在1200℃的温度中将其保持1小时。之后，通过在900℃中执行热精轧来制造热轧钢板，接下来，将所述热轧钢板装入预先加热至600℃的炉中并保持一小时后进行炉冷，从而模拟了热轧收卷。
另一方面，由于含有大量Mn的钢种的热轧钢板的强度高，因此，为了减小在后续的冷轧时的负荷，可以在冷轧之前进行额外的热处理。如果根据Mn的添加量马氏体转变开始温度为常温以上，热轧钢板内可能生成大量马氏体，此时，由于马氏体组织，导致热轧钢板的强度变得非常高。因此，在600℃中对根据上述方法冷却的各试片进行10小时热处理。
之后，将各试片冷却至常温后，通过酸洗和冷轧来制造冷轧钢板。所述冷轧以30％以上的冷压下率执行。对根据上述方法来制造的各个冷轧钢板以下表2示出的条件进行了阶段性退火热处理。
对根据如上所述的方法来制造的各个试片的机械物理性质进行测量，并通过观察微细组织，将各组织分数的测量结果示出在下表3中。
对于所述机械物理性质，以JIS5号规格加工拉伸试片后，通过使用万能拉伸试验机来执行拉伸试验。
对于微细组织分数，通过X射线衍射(XRD)来测量最终退火组织，从而计算出面心立方结构(FCC)的残余奥氏体、BCC的马氏体以及密排六方结构(HCP)的ε马氏体的相(phase)之间的分数。另外，退火马氏体和α马氏体均具有BCC结构，因此，通过使用电子扫描显微镜进行观察来区分所述两个相。
[表1]
Figure GDA0003192104550000141
[表2]
Figure GDA0003192104550000151
[表3]
Figure GDA0003192104550000161
(在[表3]中，筛选尺寸在30mm以下的所述析出物，并对其数量进行测量。在所述[表3]中，YS：屈服强度、TS：拉伸强度、El：延伸率、HER：扩孔性。)
如所述表1至表3所示，均满足本发明提出的合金组成和制造条件的发明例1至25不仅是具有1000MPa以上的屈服强度、1250MPa以上的拉伸强度的超高强度钢，而且由于具有优异的延伸率，可以确保22000MPa％以上的拉伸强度×延伸率的值，并且还可以确保10％以上的扩孔性。
这是由在第一次退火热处理时，在退火-冷却后以特定温度范围进行再加热处理，从而在第二次退火热处理后，最终残余奥氏体分数增加而引起的。
因此，可确认根据本发明的所述钢板作为可替代现有热压成型用钢板的冷压成型用钢板非常有利。
但是，即便满足本发明的成分组成，当制造条件不满足本发明时，难以确保目标机械物理性质。
具体地，在第一次退火热处理工艺中，退火后进行冷却时，在冷却终止温度超过Ms，即，退火-冷却后没有进行再加热工艺的情况下(比较例1至13)，最终残余奥氏体的分数低，从而目标强度、延伸率或者扩孔性变差。
另外，在第一次退火热处理工艺时再加热温度过高的比较例14中，没有形成充分的残余奥氏体相，因此扩孔性变差。并且，在第二次退火热处理时退火温度过高的比较例15中，没有形成充分的退火马氏体相和残余奥氏体相，因此强度和扩孔性变差。
进一步地，即便制造条件满足本发明，没有添加析出硬化元素的比较例16和17以及Mn含量不充分的比较例18和19无法确保目标水平的强度。
图2是示出使用发明钢8测量根据在第一次退火热处理时的退火后冷却温度的残余奥氏体分数的结果的图表。如图2所示，可确认在退火后冷却时，随着冷却温度降低至Ms以下，残余奥氏体相的分数增加(图2中，对于冷却温度为250℃、300℃、400℃的情况，没有示出在[表2]和[表3]中)。
图3是观察发明例13的最终微细组织的照片，可确认退火马氏体(a)和残余奥氏体(b)内形成析出物。

Claims (7)

1.一种冷成型性优异的超高强度高延展性钢板的制造方法，包括以下步骤：
以1050～1300℃的温度范围对钢坯进行再加热，以重量％计，所述钢坯包含碳(C)：0.1～0.3％、锰(Mn)：6～10％、磷(P)：0.05％以下、硫(S)：0.02％以下、氮(N)：0.02％以下、铝(Al)：0.5％以下且0％除外以及选自钛(Ti)：0.1％以下、铌(Nb)：0.1％以下、钒(V)：0.2％以下以及钼(Mo)：1％以下中的1种以上、余量的Fe和其他不可避免的杂质；
在800～1000℃的温度范围内，对再加热的所述钢坯进行热精轧，以制造热轧钢板；
在50～750℃的温度范围内收卷所述热轧钢板；
在所述收卷后，进行酸洗和冷轧，以制造冷轧钢板；
第一次退火热处理，在750～870℃的温度范围内将所述冷轧钢板保持10～3600秒后，冷却至常温～Ms，然后在Ms～500℃的温度范围内进行再加热，并保持10～3600秒，然后冷却至常温；以及
第二次退火热处理，在所述第一次退火热处理后，在550～750℃的温度范围内保持10～3600秒后，进行冷却。
2.根据权利要求1所述的冷成型性优异的超高强度高延展性钢板的制造方法，其中，
在所述酸洗前，还包括在500～700℃的温度范围内对收卷的热轧钢板进行热处理的步骤。
3.根据权利要求1所述的冷成型性优异的超高强度高延展性钢板的制造方法，其中，
以15％以上的压下率进行所述冷轧。
4.根据权利要求1所述的冷成型性优异的超高强度高延展性钢板的制造方法，还包括在进行所述第二次热处理后，将钢板浸渍在镀锌浴中，以制造热浸镀锌钢板的步骤。
5.根据权利要求4所述的冷成型性优异的超高强度高延展性钢板的制造方法，还包括对所述热浸镀锌钢板进行合金化热处理，以制造合金化热浸镀锌钢板的步骤。
6.根据权利要求1所述的冷成型性优异的超高强度高延展性钢板的制造方法，其中，
所述钢坯还包含1.0重量％以下的硅(Si)。
7.根据权利要求1所述的冷成型性优异的超高强度高延展性钢板的制造方法，其中，
所述钢坯进一步包含选自镍(Ni)：1重量％以下、铜(Cu)：0.5重量％以下以及铬(Cr)：1重量％以下中的1种以上。
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