CN116829756A - 卷取温度影响的冷轧带或钢 - Google Patents

卷取温度影响的冷轧带或钢 Download PDF

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CN116829756A
CN116829756A CN202180093332.7A CN202180093332A CN116829756A CN 116829756 A CN116829756 A CN 116829756A CN 202180093332 A CN202180093332 A CN 202180093332A CN 116829756 A CN116829756 A CN 116829756A
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strip
temperature
steel
range
slab
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M·施瓦岑布伦纳
K·施坦德
M·格鲁伯
T·莫尔鲍尔
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Voestalpine Stahl GmbH
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Abstract

本发明涉及冷轧带或板，其包含以(重量％)计：C 0.12‑0.20；Mn 1.9‑2.6；Cr 0.15‑0.3；Si 0.3‑0.8；Al 0.8‑1.2；Mn+Cr 1.8‑5；Nb≤0.008；Ti≤0.02；Mo≤0.08；Ca≤0.005；V≤0.02；以及除杂质以外的余量Fe。在将Ri/t(y轴)相对于TS(MPa)/YR(x轴)作图的情况下，钢在由坐标A、B、C、D限定的区域内，并且其中A为[2200，3.5)，B为[2600，4.5]，C为[2600，3]，和D为[2200，2]。

Description

卷取温度影响的冷轧带或钢
技术领域
本发明涉及适合于汽车(机动车，automobile)中应用的高强度钢带和板。
背景技术
对于各种各样的应用，增加的强度水平是轻质构造体的先决条件，特别是在汽车工业中，因为车身质量降低导致降低的燃料消耗。
汽车车身零件经常由钢板(sheet steel)冲压而成，从而形成复杂的薄板结构构件。然而，这种零件不能由常规的高强度钢生产，因为该复杂的结构零件的可成形性过低。由于该原因，多相相变诱导塑性辅助钢(TRIP钢)在过去几年中获得了相当大的关注，特别是对于用于汽车车身结构零件中和作为座椅框架材料。
TRIP钢具有多相微观结构，其包括能够产生TRIP效应的亚稳定的残余奥氏体相。当所述钢变形时，所述奥氏体转变成马氏体，这导致显著的加工硬化。这种硬化效应起到抵抗材料中的颈缩的作用并延缓板成形操作中的失效。TRIP钢的微观结构可极大地改变其机械性质。
TRIP钢长期以来是已知的并且引起了许多关注，主要是因为贝氏体铁素体基体允许优异的拉伸翻边性(stretch flangability)。此外，由亚稳定的残余奥氏体岛向马氏体的应变诱导转变确保的TRIP效应显著改善了它们的可拉性。
当生产经冷轧的TRIP钢板时，最初提供板坯。将板坯在奥氏体温度范围内热轧成经热轧的带。其后将经热轧的带卷取。卷取阻力随升高的温度而降低。通常采用600℃的卷取温度。其后将经卷取的带分批退火，随后冷轧。其后将经冷轧的带连续退火。
WO 2019/122963 A1和WO2019123043 A1均公开了具有改善的磷化(phosphatation)覆盖率的TRIP钢。能够实现良好的磷化覆盖率。通过控制合金元素和工艺参数(其一为具有低的卷取温度)来实现改善的磷化覆盖率。所有该发明的实施例具有450℃的卷取温度。具有更高卷取温度的参考实施例没有提供足够的磷化覆盖率。低的卷取温度增加了冷轧力。
EP 2707514 B1公开了一种具有包含如下的微观结构的TRIP钢：5-20％多边形铁素体、10-15％残余奥氏体、5-15％马氏体、以及余量贝氏体。根据该文献，在5和20％之间的多边形铁素体的存在使得可超过90°的V弯曲角度而不发生开裂。
WO2018116155公开了一种TRIP钢。该发明的实施例公开了450℃的较低卷取温度分别与620℃或650℃的较高分批退火温度组合，以及560℃的较高卷取温度与460℃的较低分批退火温度组合。
尽管这些钢公开了多种有吸引力的性质，但仍需要在先进的成形操作方面具有改善的性质曲线、特别是弯曲性质的>950MPa的钢板或带。特别是与强度和韧性相关的弯曲性质。进一步期望的性质为：减少的晶界氧化、降低的对液体(液态)金属脆化的敏感性、降低的对氢脆化的敏感性和良好的可磷化性(phosphatability)。
发明内容
本发明涉及具有至少950MPa的拉伸强度和优异的可成形性的经冷轧的钢(冷轧钢)，其中将可在连续退火线(CAL)中和在热浸镀锌线(HDGL)中以工业规模生产钢板/带。
本发明旨在提供具有可加工成复杂的高强度结构构件的组成和微观结构的钢，其中弯曲性质是重要的。
对合金元素和工艺参数的仔细选择减少了晶界氧化。减少的晶界氧化改善了弯曲性并降低了液体金属脆化的风险以及对氢脆化的敏感性。它进一步促进了良好的可磷化性。
附图说明
图1显示了本发明的样品在虚线内的图。
具体实施方式
在声明中描述本发明。
钢板具有(以重量％计)由如下合金元素构成的组成：
C 0.08-0.28
Mn 1.5-4.5
Cr 0.01-0.5
Si 0.01-2.5
Al 0.5-2.0
Si+Al ≥0.5
Mn+Cr 1.8-5
Nb ≤0.1
Ti ≤0.1
Mo ≤0.5
Ca ≤0.05
V ≤0.1
除杂质以外的余量Fe。
下文中简要解释了所声明的合金的单独的元素的重要性及其与彼此的相互作用以及化学成分的限制。用于钢的化学组成的所有百分比贯穿描述以重量％(wt.％)给出。各个元素的上限和下限可在权利要求中阐述的限度内自由组合。对于本申请中给出的所有值，数值的算术精度可增加一位或两位。因此，作为例如0.1％给出的值也可表示为0.10或0.100％。微观结构成分的量以体积％(vol.％)给出。
C：0.08-0.28％
C使奥氏体稳定，并且对于在残余奥氏体相内获得足够的碳是重要的。C对于获得期望的强度水平也是重要的。一般地，可预期拉伸强度以100MPa/0.1％C的数量级增加。当C低于0.08％时，难以获得950MPa的拉伸强度。如果C超过0.28％，则焊接性受损。因此，上限可为0.26、0.24或0.22％、0.20或0.18％。下限可为0.10、0.12、0.14或0.16％。
Mn：1.5-4.5％
锰是固溶强化元素，其通过降低Ms温度来稳定奥氏体并防止在冷却期间形成铁素体和珠光体。此外，Mn降低Ac3温度并且对于奥氏体稳定性是重要的。在小于1.5％的含量下，可能难以获得期望的量的残余奥氏体、950MPa的拉伸强度，并且奥氏体化温度对于常规工业退火线可能过高。然而，如果Mn的量高于4.5％，则可能发生偏析问题，因为Mn在液相中累积并造成带状化(banding)，导致潜在地劣化的可加工性。因此，上限可为4.2、4.0、3.8、3.6、3.4、3.2、3.0、2.8、2.6或2.4％。下限可为1.5、1.7、1.9、2.1、2.3或2.5％。
Cr：0.01-0.5％
Cr在提高钢板的强度上是有效的。Cr为形成铁素体并延迟珠光体和贝氏体形成的元素。Ac3温度和Ms温度随着Cr含量增加仅略微降低。Cr导致稳定化的残余奥氏体的量增加。当高于0.5％时，其可能损害钢的表面光洁度，因此Cr的量限制为0.5％。上限可为0.45或0.40、0.35、0.30或0.25％。下限可为0.01、0.03、0.05、0.07、0.10、0.15、0.20或0.25％。优选地，根据本发明不进行故意添加Cr。
Si：0.01-2.5％
Si充当固溶强化元素，并且对于确保薄钢带的强度是重要的。Si抑制渗碳体析出，并且对于奥氏体稳定化是必需的。然而，如果含量过高，则在带表面上将形成过多的硅氧化物，这可能导致CAL中的辊上的覆盖层，并且因此导致随后生产的钢板上的表面缺陷。因此，上限为2.5％，并且可限制为2.4、2.2、2.0、1.8、1.6、1.4、1.2、1.0或0.8％。下限可为0.01、0.05、0.1、0.2、0.4、0.60、0.80或1.0％。
Al：0.5-2.0％
Al促进铁素体形成，并且还通常用作脱氧剂。与Si一样，Al不溶于渗碳体中，因此它在贝氏体形成期间显著延迟渗碳体形成。此外，可改善镀锌和降低的对液体金属脆化的敏感性。Al的添加导致残余奥氏体中的碳含量显著增加。Al的主要缺点是其在铸造期间的偏析行为。在铸造期间，Mn在板坯中间富集，并且Al含量降低。因此，在板坯的中间可形成显著的奥氏体稳定化区或带状物。这导致在加工结束时的马氏体带状化，并且在马氏体带状物中形成低应变内部裂纹。另一方面，Si和Cr在铸造期间也富集。因此，马氏体带状化的倾向可通过用Si和Cr合金化来降低，因为由于Mn富集而引起的奥氏体稳定化被这些元素抵消。由于这些原因，优选限制Al含量。上限水平可为2.0、1.8、1.7、1.6、1.5、1.4、1.3、1.2或1.1％。下限可设定为0.5、0.6、0.7、0.8或0.9％。
Si+Al≥0.5％
Si和Al抑制贝氏体形成期间的渗碳体析出。因此，它们的合并含量优选为至少0.5％。下限可为0.7、0.8、0.9、1.0、1.1％、1.2或1.3％。
Mn+Cr 1.8-5
锰和铬影响钢的淬透性(可硬化性，hardenability)。它们的合并含量优选在1.8-5.0％的范围内。
任选的元素
Mo≤0.5％
钼为强的淬透性试剂。其可通过降低碳化物粗化动力学来进一步增强NbC析出物的益处。因此，钢可含有最高达0.5％的量的Mo。上限可限制为0.4、0.3、0.2或0.1％。然而，根据本发明，故意添加Mo不是必需的。因此，上限可限制为≤0.01％。
Nb：≤0.1％
Nb由于其对晶粒尺寸的影响而通常用于低合金钢中以改善强度和韧性。Nb通过由于NbC的析出而细化基体微观结构和残余的奥氏体相来增加强度伸长率平衡。钢可含有≤0.1％的量的Nb。上限可限制为0.09、0.07、0.05、0.03或0.01％。根据本发明，故意添加Nb不是必需的。因此，上限可限制为≤0.004％。
V：≤0.1％
V的功能类似于Nb的功能，因为它有助于析出硬化和晶粒细化。钢可含有≤0.1％的量的V。上限可限制为0.09、0.07、0.05、0.03或0.01％。根据本发明，故意添加V不是必需的。因此，上限可限制为≤0.01％。
Ti：≤0.1％
Ti由于其通过形成碳化物、氮化物或碳氮化物对晶粒尺寸的影响而通常用于低合金钢中以改善强度和韧性。具体地，Ti为强的氮化物形成剂，并且可用于结合钢中的氮。然而，效果在0.1％以上时趋于饱和。上限可限制为0.09、0.07、0.05、0.03或0.01％。根据本发明，故意添加Ti不是必需的。因此，上限可限制为≤0.005％。
Ca≤0.05％
Ca可用于非金属夹杂物(inclusion)的改性。上限为0.05％，并且可设定为0.04、0.03、0.01％。根据本发明，故意添加Ca不是必需的。因此，上限可限制为≤0.005％。
杂质
Cu：≤0.06％
Cu为不期望的杂质元素，通过仔细选择所使用的废料将其限制为≤0.06％。
Ni：≤0.08％
Ni也为不期望的杂质元素，通过仔细选择所使用的废料将其限制为≤0.08％。
B：≤0.0006％
B为不期望的杂质元素，通过仔细选择所使用的废料将其限制为≤0.0006％。B增加硬度，但可能以降低的弯曲性为代价，并且因此在本发明建议的钢中不是期望的。B可能进一步使废料再循环更加困难，并且B的添加还可能劣化可加工性。因此，根据本发明，故意添加B不是期望的。
其它杂质元素可以正常出现的量包含在钢中。然而，优选将P、S、As、Zr、Sn的量限制为如下任选的最大含量：
P：≤0.02％
S：≤0.005％
As≤0.010％
Zr≤0.006％
Sn≤0.015％
还优选控制氮含量至如下范围：
N：≤0.015％，优选0.003-0.008％
在该范围内，可实现氮的稳定固定。
氧和氢可进一步限制为
O：≤0.0003
H：≤0.0020
微观结构成分在下文中以体积％(vol.％)表示。
本发明的经冷轧的钢板(冷轧钢板)具有包含至少40％经回火的马氏体(TM)和贝氏体(B)的微观结构。
以及进一步的，10％-30％的新鲜马氏体(FM)。上限可限制为28、26、24或22％。下限可限制为12、14、16或18％。新鲜马氏体可改善边缘翻边性和局部延展性。这些未回火的马氏体颗粒经常与残余奥氏体颗粒紧密接触，并且因此它们经常被称为马氏体-奥氏体(MA)颗粒。
残余奥氏体是获得期望的TRIP效应的先决条件。因此，残余奥氏体的量应当在2-20％、优选5-15％的范围内。残余奥氏体的量借助于在Proc.Int.Conf.on TRIP-aidedhigh strength ferrous alloys(2002)，Ghent，Belgium，第61-64页中详细描述的饱和磁化法测量。
以及进一步的10％-35％的多边形铁素体(PF)。上限可为30％或25％。下限可为15％或20％。
所声明的钢的机械性质是重要的，并且应当满足如下要求：
TS拉伸强度(Rm)950-1350MPa
YS屈服强度(Rp0.2)350-1150MPa
弯曲性(Ri/t)≤4
YR屈服比(Rp0.2/Rm)≥0.35
Rm、Rp0.2值根据欧洲标准EN 10002第1部分得到，其中在带的纵向方向上取样。总伸长率(A50)根据日本工业标准JIS Z 2241:2011得到，其中在带的横向方向上取样。
屈服强度的下限可为350、360、370、380、390或400MPa。
弯曲性通过极限弯曲半径(Ri)(其定义为在没有出现裂纹的情况下的最小弯曲半径)与板厚度(t)的比来评估。为此，根据JIS Z2248，使用90°V-形块来使钢板弯曲。通过将极限弯曲半径除以厚度而获得的值(Ri/t)应当小于4、优选小于3.5。
Ri/t的上限可为4.0、3.9、3.8、3.7、3.6或3.5。下限可为2.0、2.5或3.0。
屈服比YR通过将屈服强度YS除以拉伸强度TS来定义。
YR的下限可为0.35、0.36、0.37、0.38、0.39或0.40。
在将Ri/t(y轴)相对于TS(MPa)/YR(x轴)作图的情况下，钢应当进一步在图1的由坐标A、B、C、D限定的区域内，并且其中A为[2200，3.5)，B为[2600，4.5]，C为[2600，3]，和D为[2200，2]。上面的虚线可在数学上表示为y＝0.0025*x-2，并且下面的虚线可表示为y＝0.0025*x-3.5。这提供了标准2≤0.0025*TS/YR-Ri/t≤3.5。已经发现满足该标准的钢在强度和弯曲性之间具有良好的平衡。下限可为2.2、2.4或2.6，并且上限可为3.5、3.3或3.1。
可进一步限制TS/YR比，使得TS/YR在2000-2800MPa内。下限可为2100、2200或2300。上限可为2700、2600或2500。优选的范围可为2400-2600。
本发明的经冷轧的热处理钢板可任选地涂布有锌或锌合金、或铝或铝合金以改善其耐腐蚀性。
所建议的钢可在具有以上建议组成的情况下通过经由转炉熔炼(convertermelting)和二次冶金制造常规冶金的钢板坯来生产。将板坯在奥氏体范围内热轧成经热轧的带。优选地，通过将板坯再加热至1000℃和1280℃之间的温度，在奥氏体范围内完全轧制所述板坯以获得经热轧的钢带，其中热轧终轧温度大于或等于850℃。其后，将所述经热轧的带在500-540℃范围内的卷取温度下卷取。任选地使所述经卷取的带经受除垢过程，例如酸洗。其后将经卷取的带在500-650℃、优选550-650℃范围内的温度下分批退火，持续时间5-30小时。其后以在35和90％之间的压下量、优选约40-60％的压下量冷轧经退火的钢带。在连续退火线(CAL)中或在热浸镀锌线(HDGL)中进一步处理所述经冷轧的钢带，其中微观结构得到微调。两条线都包括使钢经受800-1000℃、优选830-900℃的均热温度，优选随后快速慢速喷射和快速喷射冷却至350-450℃的保持温度150至1000秒的时间，之后冷却至室温。均热时间可为例如40秒至180秒。
在一种实施方式中，钢可具有如下特征：
冷轧带或板，其具有(以重量％计)包含如下的组成：
除杂质以外的余量Fe；并且
满足如下条件中的至少一个：
实施例
钢I1和参照钢R1通过经由转炉熔炼和二次冶金的常规冶金生产。组成显示在表1中，进一步的元素仅作为杂质存在，并且在本说明书中指定的最低水平以下。所有钢都具有大致相同的组成。
表1
钢 C N Mn Cr Si Al
I1 0.17 0.0033 2.33 0.23 0.464 0.96
R1 0.17 0.0033 2.33 0.23 0.464 0.96
所述钢是连续地铸造并切割成板坯的。
将板坯再加热并在奥氏体范围内热轧至约3.2mm的厚度。热轧终轧温度为约900℃。
其后将经热轧的钢带卷取，钢I1在530℃的卷取温度下卷取，并且参照钢R1在约630℃下卷取。
将经卷取的经热轧的带酸洗并在约624℃下分批退火10小时以降低经热轧的带的拉伸强度，从而降低冷轧力。
其后将带在五机架冷轧机中冷轧至约1.5mm的最终厚度，并最终输送到热浸镀锌线(HDGL)。在HDGL中，将带加热至约850℃的均热温度并在此保持约120秒。在退火后，将带缓慢喷射冷却至约750℃(SJC)，然后快速喷射冷却至约400℃(RJC)的保持温度并保持约180秒。对所述带进行热浸镀锌以施加Zn涂层。
将所述带在Ac3＝778℃以上均热。Ac3通过下式确定：
Ac3＝910-203*C1/2-15.2Ni-30Mn+44.7Si+104V+31.5Mo+13.1W。
工艺参数显示在表2中。
表2
屈服强度YS和拉伸强度TS根据欧洲标准EN 10002第1部分得到。在带的纵向方向上取样。
使所生产的带的样品经受根据JIS Z2248的V弯曲测试以找出极限弯曲半径(Ri)。通过肉眼和在25倍放大倍率的光学显微镜下检查样品以研究裂纹的发生。通过将极限弯曲半径(Ri)除以经冷轧的带的厚度t来确定Ri/t。Ri为其中材料在三次弯曲测试后显示没有裂纹的最大半径。
在530℃下卷取的钢I1的极限弯曲半径(Ri)小于在630℃下卷取的R1的极限弯曲半径。
机械性质显示在表3中。
表3
I1的微观结构确定为：
在图1中，已经将除以厚度的极限弯曲半径(Ri)对除以屈服比的拉伸强度TS/YR作图。在较高温度下卷取的参考钢R1在由如下定义的上部虚线以上：
Ri/t＝0.0025*TS/YR-2
本发明的钢I1在该线以下。
下部虚线由如下定义
Ri/t＝0.0025*TS/YR-3.5
本发明的钢I1在该线以上。在这些边界内，实现了与强度和韧性相关的良好弯曲性质。

Claims (4)

1.经冷轧的钢带或板
a)具有(以重量％计)由如下构成的组成：
除杂质以外的余量Fe，
b)满足如下条件：
c)在将Ri/T(y轴)相对于TS/YR(x轴)作图的情况下，在由坐标A、B、C、D限定的区域内，并且其中A为[2200，3.5)，B为[2600，4.5]，C为[2600，3]，并且D为[2200，2]；
d)具有(以体积％计)包含如下的多相微观结构
回火的马氏体+
2.根据权利要求1所述的冷轧带或板，其中所述组成包含(以重量％计)：
除杂质以外的余量Fe；并且
b)满足如下条件中的至少一个：
3.经热处理的和经冷轧的根据权利要求1或2所述的钢带或板的制造方法，包括如下步骤：
a)提供具有根据前述权利要求任一项的组成的钢板坯；
b)将所述板坯在奥氏体范围内热轧为经热轧的带；
c)将所述经热轧的带在500-540℃范围内的卷取温度下卷取；
d)任选地对经卷取的钢带进行除垢过程；
e)将经卷取的带在500-650℃范围内的温度下分批退火，持续时间5-30小时；
f)以35和90％之间的压下量冷轧经退火的钢带；
g)在连续退火线中或在热浸镀锌线中进一步处理经冷轧的钢带；和
h)进一步冷却所述钢带至室温。
4.根据权利要求3所述的方法，满足如下条件中的至少一个：
-在步骤b)中，将所述板坯再加热至1000℃和1280℃之间的温度，将所述板坯完全在奥氏体范围内轧制以获得经热轧的钢带，其中热轧终轧温度大于或等于850℃；
-在步骤f)中，在550-650℃的范围内进行分批退火；
-在步骤g)中，均热温度为800-1000℃、优选830-90℃；和
-在步骤g)中，保持温度为350-450℃，时间150至1000秒。
CN202180093332.7A 2020-12-23 2021-12-23 卷取温度影响的冷轧带或钢 Pending CN116829756A (zh)

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