CN108779524A - 高强度镀锌退火钢板和制造这样的钢板的方法 - Google Patents

高强度镀锌退火钢板和制造这样的钢板的方法 Download PDF

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CN108779524A
CN108779524A CN201680073111.2A CN201680073111A CN108779524A CN 108779524 A CN108779524 A CN 108779524A CN 201680073111 A CN201680073111 A CN 201680073111A CN 108779524 A CN108779524 A CN 108779524A
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zinc
steel
steel plate
high intensity
terms
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CN108779524B (zh
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T.赫贝斯伯杰
F.温克尔霍弗
M.安曾伯杰
E.O.阿尔曼
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Voestalpine Stahl GmbH
Toyota Motor Europe NV SA
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Voestalpine Stahl GmbH
Toyota Motor Europe NV SA
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Abstract

高强度镀锌退火钢板，其具有：a)由以下元素构成的组成(以重量％计)：C 0.10‑0.2、Mn 2.0‑3.0、Si 0.2‑0.5、Cr 0.1‑0.7、Ti 0.01‑0.07、Al≤0.2、Nb<0.05、Mo<0.1、任选的B 0.001‑0.005、除杂质以外余量的铁，b)包含如下的多相微观结构(以体积％计)：残留奥氏体4–20、马氏体5–25、贝氏体铁素体≤10、多角形铁素体≤10、余量的贝氏体+回火马氏体50‑90，c)以下机械性质的至少之一：抗张强度(Rm)1180‑1300MPa、屈服强度(Rp0.2)800‑970MPa、伸长率(A50)≥8％、伸长率(A80)≥6％，以及d)对于具有35mm x 100mm尺寸的样品，≤4的根据90°V形弯曲试验值Ri/t的弯曲性，其中对于所述钢板，Ri为以mm计的弯曲半径和t为以mm计的厚度。

Description

高强度镀锌退火钢板和制造这样的钢板的方法
技术领域
本发明涉及适合于在汽车、建筑材料等中应用的高强度镀锌退火(镀锌层退火的，galvannealed)钢板。具体而言，本发明涉及具有至少1180MPa的抗张强度和优异的弯曲性的冷轧的镀锌退火钢板。
背景技术
对于许多种应用而言，提高的强度水平是轻重量构造的先决条件，在汽车工业中尤其如此，因为车身质量减小导致减少的燃料消耗。
汽车身零件常由钢板冲压出，形成复杂的薄板结构部件。然而，这样的零件无法由常规的高强度板制造，因为对于复杂的结构零件而言成形性太低。由于该原因，多相转变诱发塑性(Transformation Induced Plasticity)辅助的钢(TRIP钢)在过去多年已经赢得大量兴趣。
TRIP钢拥有多相微观结构(显微结构)，其包括能够产生TRIP效果的金属稳定的残留奥氏体(残余奥氏体)相。当所述钢变形时，所述奥氏体转变为马氏体，其导致显著的加工硬化。这种硬化效果起到抵抗材料中的缩颈(necking)和推迟板成形操作失败的作用。TRIP钢的微观结构可大大地改变其机械性质。TRIP钢微观结构的最重要的方面是残留奥氏体相的体积百分比、尺寸和形态，因为这些性质在钢变形时直接影响奥氏体向马氏体的转变。存在若干种使奥氏体在室温下化学稳定化的方式。在低合金TRIP钢中，奥氏体是通过其碳含量和小尺寸的奥氏体晶粒而稳定化的。使奥氏体稳定化所需的碳含量为近似1wt％。然而，钢中高的碳含量由于损害焊接性而在许多应用中都不能使用。
因此需要特定的加工路径以将碳富集到奥氏体中以使其在室温下稳定化。普通的TRIP钢化学还含有少量添加的其它元素以帮助使奥氏体稳定化以及辅助将碳分配到奥氏体中的微观结构的生成。最普通的添加是1.5wt％的Si和Mn两者。为了抑制奥氏体在贝氏体转变期间分解，通常认为必要的是硅含量应为至少1wt％。钢的硅含量是重要的，因为硅不溶于渗碳体中。US 2009/0238713公开了这样的TRIP钢。然而，高的硅含量可为造成热轧钢差的表面品质和冷轧钢差的涂覆性的原因。因此，一直在研究将硅用其它元素部分或完全代替，且已经报道了基于Al的合金设计的有希望的结果。然而，使用铝的缺点是转变温度(AC3)的上升，其使得常规工业退火线中的全奥氏体化非常困难或甚至不可行。
取决于基体相，引用以下主要类型的TRIP钢：
TPF，具有多角形铁素体基体的TRIP钢
TPF钢，如先前已经提及的，包含来自相对软的多角形铁素体的基体以及来自贝氏体和残留奥氏体的夹杂物。在变形时残留奥氏体转变为马氏体，得到期望的TRIP效果，其容许钢实现优异的强度和拉延性(可拉性，drawability)组合。然而，它们的拉伸翻边性(凸缘性，flangability)与具有更均匀的微观结构和更强的基体的TBF、TMF和TAM钢相比较低。
TBF，具有贝氏体铁素体基体的TRIP钢
TBF钢已经知晓了很久且吸引了很多兴趣，因为贝氏体铁素体基体容许优异的拉伸翻边性。而且，与TPF钢类似，由应变诱发的亚稳定的残留奥氏体岛向马氏体的转变所确保的TRIP效果显著改善了它们的拉延性。
TMF，具有马氏体铁素体基体的TRIP钢
TMF钢也包含嵌入到强的马氏体基体中的亚稳定的残留奥氏体的小岛，其使得这些钢与TBF钢相比实现甚至更好的拉伸翻边性。虽然这些钢也呈现出TRIP效果，但是它们的拉延性与TBF钢相比较低。
TAM，具有退火马氏体基体的TRIP钢
TAM钢包含通过新鲜马氏体的再退火而获得的来自针状铁素体的基体。通过在应变时亚稳定的残留奥氏体夹杂物向马氏体的转变而再次实现了明显的TRIP效果。尽管它们有望(获得)强度、拉延性和拉伸翻边性组合，但是这些钢由于它们复杂和昂贵的双热循环而尚未赢得显著的工业兴趣。
TRIP钢的成形性主要受到残留奥氏体相的转变特性的影响，所述转变特性进而受到奥氏体化学、其形态和其它因素的影响。在ISIJ International Vol.50(2010),No.1，p.162-168中，讨论了影响具有至少980MPa的抗张强度的TBF钢的成形性的方面。然而，在该文献中考查的冷轧材料在盐浴中在950℃退火和在300-500℃奥氏体回火(austemper)200秒。因此，由于高的退火温度，这些材料不适合于在常规的工业退火线中制造。
汽车身零件具有高的强度和加工性(workability)，但存在使用经涂覆的钢以提高耐腐蚀性的趋势。因此，存在对用于结构零件如侧部件、侧梁和柱的具有良好的弯曲性的高强度镀锌和镀锌退火(GA)钢板的需求。
WO2015/093043公开了具有至少1180MPa的抗张强度的镀锌退火钢板。EP2881481、US 2013/0040165和WO2015/092987各自公开了具有至少1180MPa的抗张强度的镀锌钢板。EP 2785889公开了具有至少1180MPa的抗张强度的双相(DP)钢。
发明内容
本发明涉及具有至少1180MPa的抗张强度和具有优异的弯曲性的高强度镀锌退火(GA)钢板以及以工业规模制造其的方法。具体而言，本发明的目的在于提供可在设置有感应(加热)镀锌退火感应器(inductor)的工业镀锌退火设备中加工的钢组成。
具体实施方式
发明描述在权利要求中。
所述钢板具有由以下元素构成的组成(以重量％计)：
任选地
B 0.001–0.005
除杂质以外余量的铁。
下面简要地解释所主张的合金的单独元素的重要性和它们彼此的相互作用以及化学成分的限制。所述钢的化学组成的全部百分比在整个说明书中以重量％(wt％)给出。硬质相的量以体积％(vol％)给出。各个元素的上限和下限可在权利要求中所述的界限内自由地组合。
C：0.10-0.2％
C是使奥氏体稳定化的元素，且对在残留奥氏体相内获得充足的碳是重要的。C对于获得期望的强度水平也是重要的。通常，可预期每0.1％C大约100MPa的抗张强度的提高。当C低于0.1％时，则难以达到1180MPa的抗张强度。如果C超过0.2％，则焊接性受损。上限可为0.19、0.18或者0.17％。下限可为0.11、0.12、0.12、0.14或者0.15％。优选的范围为0.14-0.19％。
Mn：2.0-3.0％
锰是固溶体强化元素，其通过降低Ms温度而使奥氏体稳定化，和防止在冷却期间形成铁素体和珠光体。此外，Mn降低Ac3温度。在小于2％的含量下，可能难以获得1180MPa的抗张强度，并且对于常规的工业退火线而言，奥氏体化温度可能太高。然而，如果Mn的量高于3％，可能出现偏析问题并且加工性可能劣化。上限可为2.99、2.9、2.7、2.6或者2.5％％。下限可为2.1、2.2、2.3或者2.4％。优选的范围为2.3-2.7％。
Si：0.2-0.5
Si充当固溶体强化元素，并且对于确保薄钢板的强度是重要的。然而，如果含量太高，则钢板的涂覆性劣化。因此，上限为0.5％和且可限制到或者0.45％。下限可为0.20、0.25、0.30、0.35或者0.40％。优选的范围为0.25-0.45％。
Cr：0.1-0.7
Cr在提高钢板的强度方面是有效的。Cr是形成铁素体的元素并且减缓珠光体和贝氏体的形成。增加Cr含量仅轻微地降低Ac3温度和Ms温度。预料不到的是，添加Cr导致稳定化的残留奥氏体量的明显增加。Cr的量限制到0.7％。上限可为0.65、0.60、0.55或者0.50％。下限可为0.15、0.20、0.25、0.30、0.35或者0.40％。优选的范围为0.2-0.6％.
Si+Cr：0.5-1.1
Si和Cr在组合添加时对增加残余奥氏体的量具有协同和完全预料不到的效果，其进而导致改善的延展性和弯曲性。由于这些原因，Si+Cr的量优选限制到0.5-1.1％。较低的量可为0.55、0.60、0.65、0.70或者0.75％。上限可为1.05、1.0、0.95、0.90或者0.85％.
Ti：0.01-0.07
Ti由于其通过形成碳化物、氮化物或碳氮化物而对晶粒尺寸的影响，常用在低合金钢中以改善强度和韧性。然而，该效果在高于0.07％时趋于饱和。因此，Ti的最低限为0.01％，且可设定为0.02或者0.04％。上限为0.07％且可设定为0.06、0.05或者0.04％。优选的范围为0.03-0.04％。
Al：≤0.2
Al促进铁素体形成且还常用作脱氧剂。Ms温度随着Al含量增加而提高。Al的进一步的缺陷在于其导致AC3温度的显著提高。由于这些原因，Al含量优选地限制到小于0.1％，最优选地小于0.06％。
Nb：<0.05
Nb由于其对晶粒尺寸的影响而常用在低合金钢中以改善强度和韧性。Nb由于NbC的沉淀而通过细化(refine)基体微观结构和残留奥氏体相提高强度伸长率平衡。所述钢可以≤0.05％、优选地≤0.03％的量包含Nb。根据本发明，故意添加Nb不是必须的。因此上限可限制到≤0.01％。
Mo：<0.1
Mo可添加以改善强度。然而，Mo一般不故意添加。因此上限可为0.05或0.03％。
B：0.001-0.005
B可任选地添加。B抑制铁素体的形成和改善钢板的焊接性。为了具有明显的效果，应添加至少0.001％。然而，过量使加工性劣化。优选的范围为0.002-0.005％和0.0002-0.005％。
所述镀锌退火钢板具有包含如下的多相微观结构(以体积％计)：
残留奥氏体(RA)的量为4-20％，优选为5-10％。由于TRIP效果，残留奥氏体在需要高伸长率时是先决条件。大量的残余奥氏体使拉伸翻边性降低。较低的量可设定为5、5.5、6.0、6.5或7％。
马氏体可以5-25％的量存在于最终的微观结构中。这些马氏体颗粒经常与残留奥氏体颗粒密切接触且因此称为马氏体-奥氏体(MA)颗粒。残留奥氏体的量借由在如下中详细描述的饱和磁化方法来测量：Proc.Int.Conf.，TRIP-辅助的高强度亚铁合金(TRIP-aided high strength ferrous alloys)(2002)，Ghent，Belgium，p.61-64.
贝氏体铁素体和多角形铁素体不是想要的微观结构成分。因此将它们各自限制到10％。
微观结构的主要部分由贝氏体和回火马氏体构成。这些成分可能难以彼此区分。因此，将两种成分的总含量限制到50-90％。该量常在60-80％的范围内。
请求保护的钢的机械性质是重要的且应满足以下要求的至少之一：
以及
对于具有30-50mm、优选地35mm宽度和100mm长度的样品，在带的轧制和横向方向上90°V形弯曲试验值Ri/t≤4(特别是准静态)，其中Ri为以mm计的弯曲半径和t为所述钢板的以mm计的厚度。
优选地，同时满足所有这些要求。屈服强度的下限可设定为810、820、830、840、850、860或870MPa。
Rm、Rp0.2和A80值根据欧洲标准EN 10002第1部分得到，其中在带的纵向方向截取样品。伸长率(A50)根据日本工业标准JIS Z 2241：2011得到。
弯曲性由极限弯曲半径(Ri)(其定义为未出现裂纹时的最小弯曲半径)与板厚度(t)的比率而评价。为此目的，使用90°V形状的块将钢板样品在准静态条件(15mm/分钟)下弯曲。优选的样品尺寸为35mm x 100mm x t mm。将所述样品通过眼睛和在具有25倍放大倍率的光学显微镜下两者进行检查，以研究裂纹的出现。
该试验方法的进一步的信息可在如下向公众开放的硕士论文文献中找到：Bendability of Dual Phase Steels(DP)and V Bend Test Parameter Optimization,A.Ugar Tuna,Politecnico di Milano:Reference:Matr.758811,Milan,2011/2012；2012学年；网络链接：https://www.politesi.polimi.it/bitstream/10589/42761/l/2012_04_Tuna.pdf
本发明钢板的机械性质很大程度上可通过合金化组成和微观结构进行调节。
本发明的钢板可在常规的工业退火线中制造。加工包括如下步骤：
a)提供具有如前述权利要求任一项中所述的组成的热轧钢板，
b)对热轧板进行酸洗，
c)将经酸洗的板在450-620℃的温度下间歇退火5-20小时的时间，
d)将经退火的钢板冷轧以获得至少50％的厚度减小量(减薄量，thicknessreduction)，
e)将经冷轧的钢板在连续退火线中在780-870℃的温度退火30-120秒的时间，
f)将所述钢板冷却至350-460℃的温度，冷却速率≤150℃/s，
g)任选地，将所述钢板再加热至400-500℃，
h)将所述钢板热浸镀锌，
i)将所述钢板在500-600℃的温度镀锌退火，
j)将所述经镀锌退火的钢板冷却至环境温度。
所述方法应优选地包括以下步骤：
在步骤c)中，间歇退火温度可设定为500-610℃、520-610℃或者550-600℃和保持时间可为7-15小时或者8-12小时，
在步骤d)中，厚度减小量可为55、60、65、70或者75％，
在步骤e)中，退火温度可为800-870、820-860或者830-860℃和保持时间可为30-110、35-100、40-90、40-80或者40-70秒，
在步骤f)中，冷却温度可为350-440、350-420或者350-400℃和冷却速率可为≤120、≤110、≤100、≤90或者≤70℃/s，
在步骤h)中，其可优选具有440-480或者450-470℃的锌浴温度，
以及
在步骤i)中，镀锌退火温度可为520-580或者540-560℃。
本发明人已经意识到热轧板在冷轧之前需要经历间歇退火以获得厚度偏差窄的冷轧所需的微观结构。
实施例
通过如下来制备具有下列组成的钢：常规的炼钢法，连铸和进行热轧至3.8mm的厚度。
除杂质以外余量的铁。
将经热轧的带酸洗并在550℃的温度进行间歇退火10小时。之后将所述钢板以60％的厚度减小量冷轧至1.5mm的最终厚度。将钢板在连续镀锌退火设备中进行处理，其包括：在863℃退火52秒，冷却到390℃，在具有460℃温度的Zn-锅中镀锌，在540℃镀锌退火，和冷却至环境温度。
由此获得的钢板具有由如下构成的微观结构：6％残留奥氏体，16％马氏体以及78％贝氏体和回火马氏体。对所述镀锌退火钢板进行抗张试验和检查其弯曲性。获得以下结果：
因此，所述镀锌退火钢板具有高的强度和优异的弯曲性。
工业实用性
本发明的材料可广泛应用于汽车中的高强度结构零件。

Claims (10)

1.高强度镀锌退火钢板，其具有：
a)由以下元素构成的组成(以重量％计)
任选地
B 0.001–0.005
除杂质以外余量的铁，
b)包含如下的多相微观结构(以体积％计)
c)以下机械性质的至少之一
以及
d)对于具有35mmx100mm尺寸的样品，≤4的根据90°V形弯曲试验值Ri/t的弯曲性，其中Ri为以mm计的弯曲半径和t为所述钢板的以mm计的厚度。
2.根据权利要求1的高强度镀锌退火钢板，其满足如下的至少之一：
任选地
B 0.002-0.004
除杂质以外余量的铁。
3.根据权利要求1或2的高强度镀锌退火钢板，其具有满足如下的至少之一的多相微观结构：
和/或具有伸长率(A80)≥8％。
4.根据前述权利要求任一项的高强度镀锌退火钢板，其中以下限制适用于杂质含量：
5.根据前述权利要求任一项的高强度镀锌退火钢板，其中所述多相微观结构包含(以体积％计)：
6.根据前述权利要求任一项的高强度镀锌退火钢板，其中所述多相微观结构包含(以体积％计)：
7.根据前述权利要求任一项的高强度镀锌退火钢板，其满足以下要求：
a)钢组成包含(以重量％计)：
任选地
B 0.002-0.004
b)所述多相微观结构包含(以体积％计)：
残留奥氏体 5-15
马氏体 10-20
贝氏体+回火马氏体 60-80
c)机械性质
d)对于具有35mmx100mm尺寸的样品，≤4的根据丰田V形弯曲试验值Ri/t的弯曲性，其中Ri为以mm计的弯曲半径和t为所述钢板的以mm计的厚度。
8.制造高强度镀锌退火钢板的方法，其包括如下步骤：
k)提供具有如前述权利要求任一项中所述的组成的热轧钢板，
1)对热轧板进行酸洗，
m)将经酸洗的板在450-620℃的温度间歇退火5-20小时的时间，
n)将经退火的钢板冷轧以获得至少50％的厚度减小量，
o)将经冷轧的钢板在连续退火线中在780-870℃的温度退火30-120秒的时间，
p)将所述钢板冷却至350-460℃的温度，优选地以≤150℃/s的冷却速率进行，
q)任选地，将所述钢板再加热至400-500℃，
r)将所述钢板热浸镀锌，
s)将所述钢板在500-600℃的温度镀锌退火，
t)将经镀锌退火的钢板冷却至环境温度。
9.根据权利要求8的制造高强度镀锌退火钢板的方法，其中所述钢板满足权利要求1-7的一项或多项中所陈述的要求。
10.根据权利要求8或9的制造高强度镀锌退火钢板的方法，其中所述镀锌退火步骤是通过使用至少一个感应线圈而实施的。
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