CN113166828A - 经冷轧和热处理的钢板及其制造方法 - Google Patents

经冷轧和热处理的钢板及其制造方法 Download PDF

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CN113166828A
CN113166828A CN201980075856.6A CN201980075856A CN113166828A CN 113166828 A CN113166828 A CN 113166828A CN 201980075856 A CN201980075856 A CN 201980075856A CN 113166828 A CN113166828 A CN 113166828A
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steel sheet
cold rolled
heat treated
treated steel
rolled
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CN113166828B (zh
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帕特里斯·亚历山大
马加利·布扎
阿尼尔班·查克拉博蒂
哈桑·卡西米-阿马基
奥尔加·吉里娜
罗南·雅科洛
阿列克谢·科利佐夫
奥德·纳德勒
达蒙·帕纳希
米歇尔·索莱尔
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ArcelorMittal SA
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ArcelorMittal SA
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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  • Chemical Kinetics & Catalysis (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

本发明涉及经冷轧和热处理的钢板，所述经冷轧和热处理的钢板具有以下组成：按重量百分比计，C 0.3％至0.4％、Mn 2.0％至2.6％、Si：0.8％至1.6％、Al 0.01％至0.6％、Mo 0.15％至0.5％、Cr 0.3％至1.0％、Nb≤0.06％、Ti≤0.06％、Ni≤0.8％、S≤0.010％、P≤0.020％以及N≤0.008％，组成的剩余部分为铁和由熔炼产生的不可避免的杂质，以及具有由以下组成的显微组织：按表面分数计，15％至30％的残余奥氏体，所述残余奥氏体的碳含量为至少0.7％；70％至85％的回火马氏体；至多5％的新鲜马氏体和至多5％的贝氏体。本发明还涉及经冷轧和热处理的钢板的制造方法。

Description

经冷轧和热处理的钢板及其制造方法
本发明涉及具有高延性和可成形性的高强度钢板并且涉及获得这样的钢板的方法。
为了制造各种零件例如用于机动车辆的车身结构构件和车身板件的部件，已知使用由DP(双相)钢或TRIP(相变诱导塑性)钢制成的板。
考虑到全球环境保护，为了减轻汽车的重量以提高其燃料效率，期望具有改善的屈服强度和拉伸强度的板。但是这样的板还必须具有良好的延性和良好的可成形性，更特别地具有良好的延伸凸缘性。
除了这些机械要求之外，这样的钢板还必须表现出良好的抗液态金属脆化性(LME)。经锌或锌合金涂覆的钢板对于抗腐蚀性非常有效，因此被广泛用于汽车工业。然而，经验表明，对某些钢进行电弧焊或电阻焊可能由于称为液态金属脆化(Liquid MetalEmbrittlement，“LME”)或液态金属辅助开裂(Liquid Metal Assisted Cracking，“LMAC”)的现象而导致特定裂纹的出现。这种现象的特征在于，在施加的应力或者由约束、热膨胀或相变引起的内部应力下，液态Zn沿着下面的钢基体的晶界渗入。已知添加例如碳或硅的元素对LME裂纹有害。
汽车工业通常通过限制根据以下方程式计算的所谓的LME指数的上限值来评估这种抗性：
LME指数＝％C+％Si/4，
其中％C和％Si分别代表钢中碳和硅的重量百分比。
公开WO2010029983描述了一种获得拉伸强度高于980MPa，甚至高于1180MPa的高强度钢板的方法。然而，由于在拉伸强度高于1470MPa的本发明的钢组成中使用大量的硅，钢的抗液态金属脆化性将降低。
在公开WO2018073919中，描述了一种高强度经镀锌和镀锌扩散退火的钢板。需要大量的锰和硅以获得高于1470MPa的拉伸强度。高水平的锰可能产生对延性有害的偏析问题以及高水平的硅将降低抗液态金属脆化性。
在公开WO2009099079中，生产了一种拉伸强度高于1200MPa、总延伸率高于13％以及扩孔率高于50％的高强度镀锌钢板。该钢板的显微组织包含0％至10％的铁素体、0％至10％的马氏体、60％至95％的回火马氏体，并且包含5％至20％的残余奥氏体。为了使拉伸强度的值增加至大于1470MPa，该钢板的显微组织包含大量的回火马氏体和非常少量的残余奥氏体，这大大降低了钢板的延性。
因此，本发明的目的是提供一种达到至少1100MPa的屈服强度、至少1470MPa的拉伸强度、至少13％的总延伸率、至少15％的扩孔率和LME指数小于0.70的钢板。
本发明的目的通过提供根据权利要求1的钢板来实现。所述钢板还可以包括权利要求2至13中任一项的特征。另一个目的通过提供根据权利要求14的方法来实现。所述方法还可以包括权利要求15至17中任一项的特征。
现在将通过实例详细描述和举例说明本发明而不引入限制。
在下文中，Ac3表示转变温度，高于该温度奥氏体是完全稳定的，Ar3表示冷却时直至显微组织保持完全奥氏体的温度，Ms表示马氏体起始温度，即，冷却时奥氏体开始转变为马氏体的温度。
除非另外指出，否则所有的组成百分比均以重量百分比(重量％)给出。
根据本发明的钢的组成包含：按重量百分比计，
-0.3％≤C≤0.4％，以确保令人满意的强度，并改善残余奥氏体的稳定性(其是获得足够的延伸率所必须的)。如果碳含量大于0.4％，则热轧板太硬而不能冷轧并且可焊接性不足。如果碳含量低于0.3％，则拉伸强度和总延伸率将达不到目标值。
-2.0％≤Mn≤2.6％，以确保令人满意的强度并实现至少部分奥氏体的稳定化，以获得足够的延伸率。低于2.0％，最终组织包含不足的残余奥氏体分数，因此不能实现期望的延性和强度的组合。限定最大值以避免产生对拉伸成形性有害的偏析问题并且限制可焊接性问题。
-0.8％≤Si≤1.6％，因为硅延迟了渗碳体的析出。因此，至少0.8％的硅添加有助于使足够量的残余奥氏体稳定。硅进一步提供了固溶强化并且阻碍在从马氏体到奥氏体的碳再分配(其由在部分马氏体转变后立即进行再加热和保持步骤造成)期间碳化物的形成。含量太高时，在表面处形成硅氧化物，这损害了钢的可涂覆性。此外，硅对于抗液态金属脆化性是有害的。因此，Si含量小于或等于1.6％。在一个优选的实施方案中，硅含量低于1.5％以进一步增强抗液态金属脆化性。在另一个优选的实施方案中，硅含量低于1.4％，以及在另一个优选的实施方案中，硅含量低于1.3％。
-0.01％≤Al≤0.6％，因为铝是精炼期间对处于液相的钢脱氧非常有效的元素。此外，铝阻碍在从马氏体到奥氏体的碳再分配(其由在部分马氏体转变后立即进行再加热和保持步骤造成)期间碳化物的形成。铝含量不高于0.6％以避免出现夹杂物、避免氧化问题以及限制Ac3温度的升高(其使得更难以形成完全的奥氏体组织)。在一个优选的实施方案中，铝含量为0.2％至0.5％。
在一个优选的实施方案中，硅和铝Si+Al的累积量等于或大于1.6％。
-0.15％≤Mo≤0.5％。钼提高淬透性，使残余奥氏体稳定，从而在配分期间减少奥氏体分解。此外，钼与铬一起有助于抑制在卷取期间热轧钢板表面处的晶界氧化，晶界氧化必须在冷轧之前被去除。考虑到所追求的特性，超过0.5％，钼的添加是昂贵且无效的。在一个优选的实施方案中，钼含量为0.20％至0.40％。
-0.3％≤Cr≤1.0％。铬提高淬透性并延缓马氏体回火。铬与钼一起有助于抑制在卷取之后热轧钢板表面处的晶界氧化，晶界氧化必须在冷轧之前被去除。允许最大1.0％的铬，注意高于饱和效应，添加铬既无用又昂贵。较高的铬在酸洗处理期间引起表面清洁问题，结果影响钢的可涂覆性。在一个优选的实施方案中，铬含量为0.6％至0.8％。
-可以添加Nb≤0.06％以在热轧期间精炼奥氏体晶粒并提供析出强化。优选地，添加的铌的最小量为0.0010％。大于0.06％的添加，不能确保屈服强度、延伸率和扩孔率处于期望的水平。优选地，添加的铌的最大量为0.04％。
-可以添加Ti≤0.06％以提供析出强化。优选地，添加的钛的最小量为0.0010％。然而，当其量大于或等于0.06％时，不能确保屈服强度、延伸率和扩孔率处于期望的水平。优选地，添加的钛的最大量为0.04％。
优选地，铌和钛Nb+Ti的累积量高于0.01％。
-Ni≤0.8％。镍可以是铬或钼的替代元素并且可以被添加以使残余奥氏体稳定。优选地，添加的镍的最小量为0.0010％。
可以任选地将一些元素添加至根据本发明的钢的组成中：
-可以添加V≤0.2％以提供析出强化。优选地，添加的钒的最小量为0.0010％。然而，当其量大于或等于0.2％时，不能确保屈服强度、延伸率和扩孔率处于期望的水平。
-可以添加B：0.0003％至0.005％以提高钢的淬火性。
钢的组成的剩余部分是铁和由熔炼产生的杂质。在这方面，至少Cu、S、P和N被认为是残余元素，它们是不可避免的杂质。因此，它们的含量为Cu小于0.03％，S小于0.010％，P小于0.020％，以及N小于0.008％。
优选地，钢的组成为使得钢的碳当量Ceq低于或等于0.55％，碳当量定义为Ceq＝％C+％Mn/20+％Si/28+2＊％P。
现在将描述根据本发明的经冷轧和热处理的钢板的显微组织。
经冷轧和热处理的钢板具有由以下组成的显微组织：按表面分数计，
-15％至30％的残余奥氏体，所述残余奥氏体的碳含量为至少0.7％，
-70％至85％的回火马氏体，和
-至多5％的新鲜马氏体，以及
-至多5％的贝氏体。
表面分数通过以下方法确定：切割经冷轧和热处理的试样，并使用本身已知的试剂进行抛光和蚀刻，以露出显微组织。然后，通过联接至电子背散射衍射(“EBSD”)装置并联接至透射电子显微镜(TEM)的光学或扫描电子显微镜例如用放大倍率大于5000×的带有场发射枪的扫描电子显微镜(“FEG-SEM”)对截面进行检查。
通过本身已知的方法利用图像分析来进行各构成要素的表面分数的确定。残余奥氏体分数例如通过X射线衍射(XRD)确定。
经冷轧和热处理的钢板的显微组织包含至少15％的奥氏体(其在室温下为残余奥氏体)。当以至少15％的表面分数存在时，残余奥氏体有助于提高延性。大于30％，根据ISO16630:2009要求的扩孔率HER的水平低于15％，因为奥氏体中的碳含量太低而无法使奥氏体稳定。
残余奥氏体的碳含量大于0.7％以确保根据本发明的钢板可以达到目标的扩孔率和强度以及延伸率。
经冷轧和热处理的钢板的显微组织包含表面分数为70％至85％的量的回火马氏体。
回火马氏体是在退火之后的冷却时形成然后在配分步骤期间回火的马氏体。
经冷轧和热处理的钢板的显微组织包含至多5％的新鲜马氏体和至多5％的贝氏体。
新鲜马氏体是可以在配分步骤之后冷却时形成的马氏体。
在一个优选的实施方案中，根据本发明的经冷轧和热处理的钢板为使得新鲜马氏体的表面分数低于2％并且贝氏体的表面分数低于2％。
在另一个实施方案中，根据本发明的经冷轧和热处理的钢板为使得不包含新鲜马氏体、贝氏体。
根据本发明的经冷轧和热处理的钢板的显微组织不包含铁素体和珠光体。
可以通过任何合适的制造方法来制造根据本发明的钢板，并且本领域技术人员可以限定方法。然而，优选使用根据本发明的方法，该方法包括以下步骤：
可以通过以下制造厚度为例如1.8mm至6mm的热轧板：铸造具有如上所述的组成的钢以获得板坯，在1150℃至1300℃的温度T再加热下对板坯进行再加热，对经再加热的板坯进行热轧，最终轧制温度高于Ar3，以获得经热轧的钢。
为了避免奥氏体晶粒粗化，最终轧制温度优选为至多1000℃。
然后以例如1℃/秒至120℃/秒的冷却速率对经热轧的钢进行冷却，并且在200℃至700℃的温度T卷取下进行卷取。在一个优选的实施方案中，T卷取为450℃至650℃。
卷取之后的经热轧的钢板包括最大厚度为5μm的晶界氧化层。
卷取之后，可以对板进行酸洗。
然后，对经热轧的钢板进行退火，以改善经热轧的钢板的可冷轧性和韧性，以及提供适用于制造具有高机械特性特别是高强度和高延性的经冷轧和热处理的钢板的经热轧和退火的钢板。
在一个优选的实施方案中，对经热轧的钢板进行的退火是在1000秒至108000秒期间在500℃至800℃的温度下进行的分批退火。
然后任选地对经热轧和退火的钢板进行酸洗。
然后对经热轧和退火的钢板进行冷轧以获得厚度可以为例如0.7mm至3mm或甚至更好地在0.8mm至2mm的范围内的经冷轧的钢板。
冷轧压下率优选为20％至80％。低于20％，不利于在随后的热处理期间的再结晶，这可能损害经冷轧和热处理的钢板的延性。大于80％，在冷轧期间存在边缘开裂的风险。
然后在连续退火线上对经冷轧的钢板进行热处理。
热处理包括以下步骤：
-将经冷轧的钢板再加热至Ac3至Ac3+100℃的退火温度，并将经冷轧的钢板在所述退火温度下保持30秒至600秒的保持时间，以在退火时获得完全的奥氏体组织，
到达退火温度的再加热速率优选为1℃/秒至200℃/秒。
-以优选为0.1℃/秒至200℃/秒的冷却速率将经冷轧的钢板淬火至(Ms-140℃)至(Ms-75℃)，优选为150℃至215℃的淬火温度Tq，并且将其在所述淬火温度下保持1秒至200秒的保持时间。
选择冷却速率以避免在冷却时珠光体的形成。
在该淬火步骤期间，奥氏体部分地转变为马氏体。
如果淬火温度低于(Ms-140℃)，则最终组织中的回火马氏体的分数太高，导致最终奥氏体分数低于15％，这对钢的总延伸率是有害的。此外，如果淬火温度高于(Ms-75℃)，则不能实现所需的扩孔率。
-任选地将经淬火的板在淬火温度下保持1秒至200秒，优选3秒至30秒的保持时间，以避免在马氏体中形成ε碳化物(这将导致钢的延伸率降低)。
-将经冷轧的钢板再加热至350℃至500℃的配分温度，并且将经冷轧的钢板在所述配分温度下保持30秒至2000秒，以及更优选30秒至800秒的配分时间。
-任选地对板进行热浸涂。可以使用任何种类的涂层，特别是锌或锌合金例如锌-镍、锌-镁或锌-镁-铝合金，铝或铝合金例如铝-硅。
-紧接在配分步骤之后或紧接在热浸涂步骤(如果进行的话)之后，将经冷轧的钢板冷却至室温，以获得经冷轧和热处理的钢板。冷却速率优选高于1℃/秒，例如为2℃/秒至20℃/秒。
-任选地，在冷却至室温之后，如果尚未进行热浸涂步骤，则可以通过电化学方法例如电镀，或者通过任何真空涂覆法例如PVD或射流气相沉积来涂覆板。可以使用任何种类的涂层，特别是锌或锌合金例如锌-镍、锌-镁或锌-镁-铝合金。任选地，在通过电镀涂覆之后，可以使板经受脱气。
实施例
将2个钢种(其组成汇总于表1中)铸造成半成品，并按照表2中汇总的工艺参数加工成钢板。
表1-组成
下表中汇总了测试的组成，其中元素含量以重量百分比表示。没有添加钒。
Figure BDA0003070355850000071
钢A为根据本发明的。
带下划线的值：不与本发明相对应。
对于给定的钢，本领域技术人员知晓如何通过膨胀测试和金相学分析来确定Ar3、Ac3和Ms。
Figure BDA0003070355850000081
分析了卷取之后的经热轧的板的一些样品以评估是否可能存在晶界氧化层，并将相应结果汇总在表3中。
然后分析了经冷轧和热处理的板的一些样品，并在表4和表5中分别汇总了对应的显微组织元素和机械特性。
表3-经热轧的钢板的晶界氧化
晶界氧化是晶间氧化，其特征在于经卷取的板的表面上的不连续性。在钢表面上的铁层中，氧化物分散在晶粒之间。与在基体中均匀扩散相比，最终显微组织的晶界自然地构成了对与铁相比更可氧化的元素的扩散短路。结果是在晶界水平更显著的氧化和更深的氧化。
确定卷取之后在经热轧的钢板上晶界氧化层(GBO)的存在：
试验 GBO层 厚度(μm)
1<sup>＊</sup> 否 0
2<sup>＊</sup> 否 0
3<sup>＊</sup> 是 1
5 是 <u>7</u>
6 是 <u>8</u>
7<sup>＊</sup> 是 1
*：根据本发明的试验。
由于钢组成和卷取温度范围的组合，试验1至3和试验7显示出对GBO生长的良好控制，试验1和2甚至显示出完全的抑制。由于高的卷取温度，试验5表现出差的结果，而试验6由于钢种中没有钼，因此未表现出良好的结果。
表4-经冷轧和退火的钢板的显微组织
确定所获得的经冷轧的钢板的显微组织的相百分比：
Figure BDA0003070355850000091
*：根据本发明的试验/带下划线的值：不与本发明相对应。
γ：代表残余奥氏体表面分数
γ中的C：代表奥氏体相的碳含量
TM：代表回火马氏体表面分数
FM：代表新鲜马氏体表面分数
B：代表贝氏体表面分数
F：代表铁素体表面分数
表5-经冷轧和退火的钢板的机械特性
确定测试的样品的机械特性并汇总在下表中：
试验 YS(MPa) TS(MPa) TE(％) HER(％)
1<sup>＊</sup> 1210 1524 16 20
2<sup>＊</sup> 1248 1517 15 16
3<sup>*</sup> 1340 1551 14 21
4 <u>1050</u> 1550 14 <u>5</u>
7<sup>＊</sup> 1248 1527 16 19
*：根据本发明的试验
带下划线的值：不匹配机械特性。
根据2009年10月公布的ISO标准ISO 6892-1测量了屈服强度YS、拉伸强度TS和均匀延伸率TE。根据ISO标准16630：2009测量了扩孔率HER。由于测量方法的差异，根据ISO标准16630：2009的扩孔率HER的值与根据JFS T 1001(日本钢铁联合会标准)的扩孔率λ的值非常不同，并且没有可比性。
实施例显示出根据本发明的钢板(即实施例1至3和实施例7)由于其特定的组成和显微组织，是仅有的表现出所有目标特性的钢板。实施例4的经冷轧和退火的钢板具有与本发明对应的化学组成，并且在等于225℃的温度Tq下淬火，这产生了更多的新鲜马氏体，导致低水平的扩孔率。

Claims (17)

1.一种经冷轧和热处理的钢板，由具有包含以下的组成的钢制成：按重量百分比计，
C：0.3％至0.4％
Mn：2.0％至2.6％
Si：0.8％至1.6％
Al：0.01％至0.6％
Mo：0.15％至0.5％
Cr：0.3％至1.0％
Nb≤0.06％
Ti≤0.06％
Ni≤0.8％
S≤0.010％
P≤0.020％
N≤0.008％
Cu≤0.03％
以及任选地包含以下元素中的一者或更多者：按重量百分比计，
B：0.0003％至0.005％
V≤0.2％
所述组成的剩余部分是铁和由熔炼产生的不可避免的杂质，
所述钢板具有由以下组成的显微组织：按表面分数计，
-15％至30％的残余奥氏体，所述残余奥氏体的碳含量为至少0.7％，
-70％至85％的回火马氏体，和
-至多5％的新鲜马氏体，以及
-至多5％的贝氏体。
2.根据权利要求1所述的经冷轧和热处理的钢板，其中铬含量为0.6％至0.8％。
3.根据权利要求1或2所述的经冷轧和热处理的钢板，其中硅含量低于1.5％。
4.根据权利要求1至3中任一项所述的经冷轧和热处理的钢板，其中硅含量低于1.4％。
5.根据权利要求1至4中任一项所述的经冷轧和热处理的钢板，其中硅含量低于1.3％。
6.根据权利要求1至5中任一项所述的经冷轧和热处理的钢板，其中硅和铝的累积量等于或大于1.6％。
7.根据权利要求1至6中任一项所述的经冷轧和热处理的钢板，其中铝含量为0.2％至0.5％。
8.根据权利要求1至7中任一项所述的经冷轧和热处理的钢板，其中钼含量为0.20％至0.40％。
9.根据权利要求1至8中任一项所述的经冷轧和热处理的钢板，其中所述显微组织包含至多2％的新鲜马氏体。
10.根据权利要求1至9中任一项所述的经冷轧和热处理的钢板，其中所述显微组织包含至多2％的贝氏体。
11.根据权利要求1至10中任一项所述的经冷轧和热处理的钢板，其中所述显微组织不包含贝氏体和新鲜马氏体。
12.根据权利要求1至11中任一项所述的经冷轧和热处理的钢板，其中所述经冷轧和热处理的钢板涂覆有Zn或Zn合金或者Al或Al合金。
13.根据权利要求1至12中任一项所述的经冷轧和热处理的钢板，其中所述经冷轧和热处理的钢板的屈服强度YS为至少1100MPa，拉伸强度TS为至少1470MPa，总延伸率TE为至少13％，扩孔率HER为至少15％以及LME指数小于0.70。
14.一种用于制造经冷轧和热处理的钢板的方法，包括以下顺序步骤：
-铸造钢以获得板坯，所述钢具有根据权利要求1至8中任一项所述的组成，
-在1150℃至1300℃的温度T再加热下对所述板坯进行再加热，
-在高于Ar3的温度下对经再加热的板坯进行热轧以获得经热轧的钢板，
-在200℃至700℃的卷取温度T卷取下对经热轧的钢板进行卷取，
-任选地对所述经热轧的钢板进行酸洗，
-任选地对所述经热轧的钢板进行退火以获得经热轧和退火的钢板，
-任选地对所述经热轧和退火的钢板进行酸洗，
-对所述经热轧和退火的钢板进行冷轧以获得经冷轧的钢板，
-将所述经冷轧的钢板再加热至Ac3至Ac3+100℃的退火温度，并将所述经冷轧的钢板在所述退火温度下保持30秒至600秒的保持时间，以在退火时获得完全的奥氏体组织，
-以0.1℃/秒至200℃/秒的冷却速率将所述经冷轧的钢板淬火至(Ms-140℃)至(Ms-75℃)的淬火温度Tq，以及任选地将其在Tq下保持1秒至200秒的保持时间，
-将所述经冷轧的钢板再加热至350℃至500℃的配分温度，并将所述经冷轧的钢板在所述配分温度下保持30秒至2000秒的配分时间，
-将冷轧钢和热处理的板冷却至室温。
15.根据权利要求14所述的方法，其中所述卷取温度T卷取为450℃至650℃。
16.根据权利要求14至15中任一项所述的方法，其中卷取之后的所述经热轧的钢板包括最大厚度为5μm的晶界氧化层。
17.根据权利要求14至16中任一项所述的方法，其中在1000秒至108000秒期间在500℃至800℃的温度下对热带进行退火。
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