CN107614729B - 高强度钢板及其制造方法 - Google Patents
高强度钢板及其制造方法 Download PDFInfo
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- CN107614729B CN107614729B CN201680031531.4A CN201680031531A CN107614729B CN 107614729 B CN107614729 B CN 107614729B CN 201680031531 A CN201680031531 A CN 201680031531A CN 107614729 B CN107614729 B CN 107614729B
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- steel sheet
- strength steel
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 136
- 239000010959 steel Substances 0.000 title claims abstract description 136
- 238000004519 manufacturing process Methods 0.000 title claims description 32
- 239000000126 substance Substances 0.000 claims abstract description 63
- 239000013078 crystal Substances 0.000 claims abstract description 40
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 33
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 16
- 229910001567 cementite Inorganic materials 0.000 claims abstract description 13
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims abstract description 13
- 239000002245 particle Substances 0.000 claims abstract description 12
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 10
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 239000000203 mixture Substances 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 4
- 238000000137 annealing Methods 0.000 claims description 46
- 238000002791 soaking Methods 0.000 claims description 23
- 238000000034 method Methods 0.000 claims description 19
- 238000007598 dipping method Methods 0.000 claims description 17
- 238000011282 treatment Methods 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 16
- 238000005246 galvanizing Methods 0.000 claims description 15
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 14
- 239000001257 hydrogen Substances 0.000 claims description 14
- 229910052739 hydrogen Inorganic materials 0.000 claims description 14
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 8
- 239000010960 cold rolled steel Substances 0.000 claims description 8
- 229910052725 zinc Inorganic materials 0.000 claims description 8
- 239000011701 zinc Substances 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 238000005275 alloying Methods 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 238000010792 warming Methods 0.000 claims description 3
- 238000012545 processing Methods 0.000 abstract description 30
- 230000000717 retained effect Effects 0.000 abstract description 7
- 238000005096 rolling process Methods 0.000 description 26
- 238000006243 chemical reaction Methods 0.000 description 19
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- 238000010438 heat treatment Methods 0.000 description 14
- 230000009467 reduction Effects 0.000 description 11
- 238000012360 testing method Methods 0.000 description 10
- 230000007704 transition Effects 0.000 description 7
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- 229910001335 Galvanized steel Inorganic materials 0.000 description 3
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- 229910052804 chromium Inorganic materials 0.000 description 3
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- 238000005336 cracking Methods 0.000 description 3
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- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 3
- 239000010452 phosphate Substances 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
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- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- UGFAIRIUMAVXCW-UHFFFAOYSA-N Carbon monoxide Chemical compound [O+]#[C-] UGFAIRIUMAVXCW-UHFFFAOYSA-N 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 229910002091 carbon monoxide Inorganic materials 0.000 description 2
- 230000008859 change Effects 0.000 description 2
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- 210000000981 epithelium Anatomy 0.000 description 2
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 206010011376 Crepitations Diseases 0.000 description 1
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- 229910052787 antimony Inorganic materials 0.000 description 1
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- 229910001563 bainite Inorganic materials 0.000 description 1
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- 238000000748 compression moulding Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
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- 229920006395 saturated elastomer Polymers 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052712 strontium Inorganic materials 0.000 description 1
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- 229910052718 tin Inorganic materials 0.000 description 1
- 239000004408 titanium dioxide Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
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- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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Abstract
得到高屈强比、且同时具有优异的拉伸凸缘性和耐二次加工脆性的高强度钢板。化学转化处理性优异的高强度钢板,其具有下述成分组成和钢组织,所述成分组成以质量%计,含有C:0.02%以上且小于0.10%、Si:小于0.3%、Mn:小于1.0%、P:0.10%以下、S:0.020%以下、Al:0.01~0.10%、N:0.010%以下、Nb:0.003%以上且小于0.070%,余部由Fe及不可避免的杂质构成,所述钢组织为:(i)以面积百分数计,包含铁素体:90%以上,珠光体、马氏体、残余奥氏体及渗碳体的总计:0~10%;(ii)所述铁素体的平均晶体粒径为15.0μm以下;(iii)所述铁素体的平均纵横比为1.2以上,高强度钢板的拉伸强度为500MPa以下。
Description
技术领域
本发明涉及适用于汽车部件等的高强度钢板及其制造方法。
背景技术
在汽车中,具有590MPa以上的拉伸强度的钢板的使用正在扩大,另一方面,当前也大量使用拉伸强度为400MPa级别(class)的钢板。
该400MPa级别的钢板在成型为汽车部件时被加工成复杂的形状,因此,需要具有优异的拉伸凸缘性(Stretch flangeability)。另外,对于该强度级别而言,由于拉伸强度与拉伸凸缘性是相反的,因此,为了得到优异的成型性,拉伸强度优选为500MPa以下。另一方面,从确保部件强度的观点考虑,优选屈服强度较高,具体而言,屈服强度与拉伸强度之比即屈强比优选为0.7以上。此外,对于汽车部件而言,作为涂装的前处理,对钢板表面实施析出磷酸化合物的化学转化处理,因此,需要优异的化学转化处理性。针对这种要求,迄今为止公开了各种钢板及其制造技术。
专利文献1中公开了添加Nb、Ti,并且以原子数比计Ti量大于N的方式添加,主相的多边形铁素体、贝氏体中的一者或两者的总计面积百分数为98%以上的、扩孔性优异的高杨氏模量钢板及其制造方法。
专利文献2中公开了,总计添加0.04质量%以上的Nb、Ti的一者或两者,含有以面积百分数计为20~50%的未再结晶铁素体作为钢组织的、耐冲击特性优异的高强度钢板及其制造方法。
专利文献3中公开了以质量%计、Cr含有量为0.3%以上,并且,含有确保耐常温时效性(其由钢中N量算出)而所需的量的Cr,铁素体为主相,铁素体粒径为25μm以下的、涂装烘烤固化性能和耐常温时效性优异的高强度钢板及其制造方法。
现有技术文献
专利文献
专利文献1:日本专利第5037415号公报
专利文献2:日本专利第4995109号公报
专利文献3:日本特开2007-31771号公报
发明内容
发明要解决的课题
为得到高屈强比且拉伸凸缘性优异的高强度钢板,利用借助Nb、Ti、V碳化物的颗粒弥散强化是有效的。另一方面,对于这种高强度钢板而言,钢板由于模压成型时蓄积的应变而发生脆化,在移除压模时、运输成型品时产生裂纹的二次加工脆性有时成为问题。
在专利文献1记载的技术中,由于未对热轧钢板实施冷轧,因此,据认为得不到在本发明中作为重要要件的微细铁素体的平均晶体粒径。因此,即便通过添加Nb、Ti而实现了高屈强比和优异的拉伸凸缘性,也得不到同时具有耐二次加工脆性的高强度钢板。
在专利文献2记载的技术中,由于在连续退火生产线中实施退火,因此升温时的加热速度未被适当地控制,均热温度也为800℃以上,因此,得到高屈强比、且同时具有优异的拉伸凸缘性和耐二次加工脆性的高强度钢板。
在专利文献3记载的技术中,若考虑到工业生产上钢中含有的N量,则实质上,需要含有0.4%以上的Cr。为了通过上述的钢来确保优异的化学转化处理性,需要控制退火时的气氛,以使得在退火时不在表面生成Cr氧化物等。但是,在专利文献3中,关于化学转化处理性没有任何考虑,可想到,在钢板表层大量地生成氧化物量。因此,在专利文献3中,得不到化学转化处理性优异的高强度钢板。另外,由于专利文献3是用于在连续退火生产线中制造的技术,可想到,得不到与箱式退火同样的效果。
本发明鉴于上述情况、为解决上述问题而做出的,本发明的目的在于,得到高屈强比、且拉伸凸缘性、耐二次加工脆性及化学转化处理性优异的高强度钢板。
另外,与连续退火炉比较,箱式退火炉具有设备设置成本低的优点。本发明的目的还在于,通过箱式退火炉来制造具有上述的优异特性的高强度钢板。
用于解决上述问题的手段
为解决上述课题,本申请的发明人进行了深入研究。结果发现,重要的是:在以铁素体为主体的钢组织中,使由铁素体的当量圆直径规定的平均粒径微细化至一定以下,进而在垂直于轧制宽度方向(轧制垂直方向)的截面中,与铁素体晶粒的轧制方向的晶粒长度相比,减小板厚方向的晶粒长度,即增大纵横比,并且发现:为形成所期望的钢组织,有效的是,设为规定的成分组成,并且将退火时的升温速度和均热温度控制在适当的范围。
此外,发明人还发现,为了确保本发明要实现的优异的化学转化处理性,重要的是,将箱式退火时的气氛中的氢浓度设为5体积%以上。
本发明是基于上述发现而做出的,其主要内容如下所述。
[1]化学转化处理性优异的高强度钢板,其特征在于,所述高强度钢板具有下述成分组成和钢组织,
所述成分组成以质量%计,含有C:0.02%以上且小于0.10%、Si:小于0.3%、Mn:小于1.0%、P:0.10%以下、S:0.020%以下、Al:0.01~0.10%、N:0.010%以下、Nb:0.003%以上且小于0.070%,余部由Fe及不可避免的杂质构成,
所述钢组织为:(i)以面积百分数计,包含铁素体:90%以上,珠光体、马氏体、残余奥氏体及渗碳体的总计:0~10%;(ii)所述铁素体的平均晶体粒径为15.0μm以下;(iii)所述铁素体的平均纵横比为1.2以上,
拉伸强度为500MPa以下。
[2]如[1]中记载的化学转化处理性优异的高强度钢板,其特征在于,以质量%计,进一步含有Cr:小于0.5%、Mo:0.3%以下、B:0.005%以下、Cu:0.3%以下、Ni:0.3%以下中的任意1种或2种以上。
[3]如[1]或[2]中记载的化学转化处理性优异的高强度钢板,其特征在于,在表面具有热浸镀锌层。
[4]如[3]中记载的化学转化处理性优异的高强度钢板,其特征在于,所述热浸镀锌层为合金化热浸镀锌层。
[5]如[1]或[2]中记载的化学转化处理性优异的高强度钢板,其特征在于,在表面具有电镀锌层。
[6]化学转化处理性优异的高强度钢板的制造方法,其特征在于,所述高强度钢板的制造方法为[1]或[2]中记载的高强度钢板的制造方法,在通过箱式退火炉将冷轧钢板退火的过程中,
将炉内气氛中的氢浓度设为5~100体积%,
以120℃/小时以下的速度升温至550℃,
在550~750℃的温度区域中均热。
[7]如[6]中记载的化学转化处理性优异的高强度钢板的制造方法,其特征在于,在所述退火后,实施热浸镀锌。
[8]如[7]中记载的化学转化处理性优异的高强度钢板的制造方法,其特征在于,在实施所述热浸镀锌后,对热浸镀锌实施合金化处理。
[9]如[6]中记载的化学转化处理性优异的高强度钢板的制造方法,其特征在于,在所述退火后,实施电镀锌。
发明效果
通过本发明,适当地控制成分组成、退火时的升温速度及均热温度,由此可得到本发明要实现的钢组织,因此,可得到适用于汽车部件用途,高屈强比,并且拉伸凸缘性、耐二次加工脆性及化学转化处理性优异的高强度钢板。
当将本发明的高强度钢板用作汽车部件的原料时,能够实现汽车的进一步的轻量化。本发明的利用价值在汽车、铁钢业界极大。
另外,高强度是指拉伸强度为300MPa以上且500MPa以下,高屈强比是指屈强比为0.70以上,优异的拉伸凸缘性是指扩孔率为100%以上,优异的耐二次加工脆性是指脆性转变温度为-60℃以下,化学转化处理性优异是指未生成磷酸化合物的微小区域(未覆盖区域(a lack of hiding))以面积百分数计为5%以下。
如上所述,本发明的钢板形成优异的汽车用部件。作为汽车用部件的原料的钢板的厚度通常为0.5~2.0mm。
附图说明
[图1]为示出作为钢板的二次加工脆性的指标的转变温度的测定方法的图。
具体实施方式
以下,对本发明的实施方式进行说明。需要说明的是,本发明不限于以下的实施方式。
为得到高屈强比、且具有优异的拉伸凸缘性和耐二次加工脆性的高强度钢板,本申请的发明人进行了深入研究。结果发现,在成分组成中,将Nb含有量设为以质量%计为0.003%以上且小于0.070%,将钢组织的主相设为铁素体,进行控制以使得在垂直于轧制宽度方向的截面中,该铁素体的平均粒径为15.0μm以下,由铁素体晶粒的轧制方向的平均晶粒长度与板厚方向的平均晶粒长度之比表示的平均纵横比成为1.2以上,由此可得到高屈强比、且具有优异的拉伸凸缘性和耐二次加工脆性的高强度钢板。
另外,对为了得到以铁素体为主体的上述钢组织的制造条件进行了深入研究,结果发现,重要的是,通过将退火时的直至550℃的升温速度设为120℃/小时以下,于550~750℃均热保持。据认为,这是由于,通过减慢退火中的升温速度,铁素体的再结晶能够在比较低的低温发生,因此再结晶的核生成变得微细,另外,通过将均热温度设为比较低的低温,由于NbC的钉扎效应而在铁素体晶粒的晶粒成长方向上产生各向异性。
另外,发明人还发现,为了确保本发明要实现的优异的化学转化处理性,重要的是,将箱式退火时的气氛中的氢浓度设为5体积%以上。据认为,这是由于,若在钢板表面生成Fe、Mn、Si、Cr等的氧化物,则当化学转化处理时,形成未生成磷酸化合物的微小区域(以降,有时称为未覆盖区域),化学转化处理性变差,但通过将炉内设为不易氧化的气氛,从而减少了钢板表面的氧化物。
需要说明的是,以拉伸方向垂直于轧制方向的方式,采集JIS5号拉伸试验片,利用基于JIS Z 2241的拉伸试验,来求出屈服强度和拉伸强度。作为拉伸凸缘性的指标的扩孔率利用JIS Z 2256中记载的扩孔试验求出。关于作为耐二次加工脆性的指标的脆化转变温度,如图1所示,使用以拉深比为1.8进行深拉深成型而得到的直径50mm、高度35mm的圆筒深拉深成型材料,测定不发生纵向裂纹失效的最低温度(转变温度),从而将作为能够适于在寒冷地区使用的温度为-60℃以下的情况,判定为特性良好。
另外,关于化学转化处理性的评价,首先,进行下述化学转化处理:使用NihonParkerizing Co.,Ltd.;制的脱脂液FINECLEANER2000系列(注册商标)通过喷雾方式而在处理温度40℃、处理时间120秒的条件下脱脂,然后,水洗,用Nihon Parkerizing Co.,Ltd.;制的表面调节液PREPALENE X(注册商标)在20秒、25℃的条件下进行表面调节,在40℃的化学转化处理液(PB-SX35(注册商标))中浸渍120秒,然后,水洗,进行热风干燥。接下来,使用扫描型电子显微镜(SEM)以500倍的倍率对化学转化处理后的供试验材料任意地观察5个视野,利用ASTM E 562-05中记载的样点法测定化学转化处理皮膜的未覆盖区域面积百分数,将未覆盖区域面积百分数为5%以下的情况判定为化学转化处理性良好。
基于以上发现而完成的本发明的高强度钢板具有应用于汽车内板时所必须的、高屈强比、且优异的拉伸凸缘性、耐二次加工脆性及化学转化处理性。
<高强度钢板>
本发明的高强度钢板具有特定的成分组成和特定的钢组织。首先,按照成分组成、钢组织的顺序进行说明。
本发明的高强度钢板的成分组成以质量%计,含有C:0.02%以上且小于0.10%、Si:小于0.3%、Mn:小于1.0%、P:0.10%以下、S:0.020%以下、Al:0.01~0.10%、N:0.010%以下、Nb:0.003%以上且小于0.070%。在本说明书中,表示成分的含有量的“质量%”记载为“%”。
C:0.02%以上且小于0.10%
C与Nb键合从而析出NbC,从而屈服强度和拉伸强度增加。当C含有量小于0.02%时,NbC的析出量不足,因此得不到所期望的屈强比、拉伸强度。若C含有量为0.10%以上,则渗碳体发生粗大化,珠光体、马氏体过度地生成,因此屈强比、拉伸凸缘性降低。因此,C含有量设为0.02%以上且小于0.10%。对于下限而言,优选的C含有量为0.02%以上。对于上限而言,优选的C含有量为0.06%以下。
Si:小于0.3%
通常,Si对于通过使铁素体固溶强化从而增加屈服强度和拉伸强度而言是有效的,但由于Si具有将铁素体晶粒内的C驱逐至晶界的效果,因此,通过含有Si,从而在晶界形成粗大的渗碳体,拉伸凸缘性变差。此外,Si在退火时在钢板表层形成氧化物,从而导致化学转化处理性变差。因此,优选尽可能地降低Si含有量,上限设为小于0.3%。优选设为小于0.1%。另一方面,由于为了将Si含有量设为小于0.001%,需要高额的设备投资和长时间的精炼处理,因此对于下限而言,优选的Si含有量为0.001%以上。
Mn:小于1.0%
Mn通过铁素体的固溶强化从而对于增加屈服强度和拉伸强度而言是有效的。另外,Mn易于固溶于渗碳体,通过固溶从而抑制渗碳体的粗大化,因此对得到优异的拉伸凸缘性而言也是有效的。然而,若Mn含有量为1.0%以上,则在Mn偏析部局部地生成马氏体,因此拉伸凸缘性变差。另外,从化学转化处理性的观点考虑,由于Mn氧化物是酸可溶性的,因此,即便在退火时在钢板表层形成了氧化物,也能够在实施化学转化处理时从钢板表层除去。因此,大多情况下不会对化学转化处理性产生不良影响。但是,若过度地生成Mn氧化物,则不能完全地从表层除去,有时导致化学转化处理性变差,因此,Mn添加量优选较少。因此,Mn含有量设为小于1.0%。对于下限而言,优选的Mn含有量为0.2%以上。对于上限而言,优选的Mn含有量为0.8%以下。
P:0.10%以下
P在铁素体晶界偏析,从而使耐二次加工脆性变差。另外,P以带状偏析,因此也使拉伸凸缘性变差。因此,优选的是,尽可能地减少P含有量,上限设为0.10%。优选地设为0.04%以下。进一步优选为0.03%以下。需要说明的是,虽然优选不添加P,但从制造成本的观点考虑,优选为0.001%以上。
S:0.020%以下
S是即便不主动添加,有时也会作为杂质而不可避免地包含的元素。由于通过形成MnS等夹杂物,而拉伸凸缘性降低,因此,优选的是,尽可能地减少S含有量。因此,S含有量设为0.020%以下。优选的是,设为0.015%以下。需要说明的是,虽然优选不添加S,但从制造成本的观点考虑,优选为0.0001%以上。
Al:0.01~0.10%
Al是为了在精炼工序中脱氧、及将固溶N以AlN的形式固定而添加的。为了得到充分的效果,需要将Al含有量设为0.01%以上。然而,若Al含有量大于0.10%,则AlN粗大地析出,从而成为开裂的起点,因此拉伸凸缘性降低。另外,若Al含有量大于0.10%,则在退火时在钢板表层形成氧化物,从而化学转化处理性变差。因而,Al含有量设为0.01~0.10%。对于上限而言,优选的Al含有量设为0.07%以下。进一步优选的是,设为0.06%以下。
N:0.010%以下
N是直至铁水的精炼工序而不可避免地含有的元素,若N含有量大于0.010%,则在铸造时作为Nb碳氮化物析出后,即便加热板坯,也不会溶解而作为粗大的碳氮化物残留,在成型时成为开裂的起点,因此拉伸凸缘性变差。因而,N含有量设为0.010%以下。需要说明的是,虽然优选不添加N,但从制造成本的观点考虑,优选为0.0001%以上。
Nb:0.003%以上且小于0.070%
Nb是有助于通过铁素体晶粒的微细化、Nb碳化物的析出而带来的屈强比和拉伸强度的增加的重要元素。另外,通过适量含有Nb,而使铁素体粒径变得微细,因此,从改善耐二次加工脆性的观点考虑也是有效的。当Nb含有量小于0.003%时,不能充分地得到Nb碳化物的体积率,因此,由Nb带来的上述效果小。另外,当Nb含有量为0.070%以上时,Nb碳化物过剩地析出,在退火后仍残留延展性差的未再结晶铁素体,因此拉伸凸缘性变差。另外,当Nb含有量为0.070%以上时,有时在退火时在钢板表层形成氧化物,有时导致化学转化处理性变差。因此,Nb含有量设为0.003%以上且小于0.070%。对于下限而言,优选的Nb含有量为0.003%以上。对于上限而言,优选的Nb含有量为0.050%以下。
除上述成分以外,本发明的高强度钢板的成分组成以质量%计,也可以含有Cr:小于0.5%、Mo:0.3%以下、B:0.005%以下、Cu:0.3%以下、Ni:0.3%以下中的任意1种或2种以上。以下,对这些成分进行说明。
Cr:小于0.5%
作为不损害本发明的作用效果的微量元素,也可以含有Cr。然而,在较高地设定均热温度的情况下,若Cr含有量为0.5%以上,则由于淬火性的提高,导致过剩地生成马氏体,从而有时导致屈强比的降低。另外,若Cr含有量为0.5%以上,则在退火时在钢板表层形成氧化物,从而导致化学转化处理性变差。因而,当含有Cr时,其含有量设为小于0.5%。另外,从化学转化处理性的观点考虑,优选设为小于0.3%。更优选为0.2%以下,最优选为0.1%以下。
Mo:0.3%以下
作为不损害本发明的作用效果的微量元素,也可以含有Mo。然而,在较高地设定均热温度的情况下,若Mo含有量大于0.3%,则由于淬火性的提高,导致马氏体过剩地生成,从而有时导致屈强比的降低。另外,若Mo含有量大于0.3%,则化学转化处理时的化学转化晶体的形成速度降低,从而导致化学转化处理性变差。因而,当含有Mo时,其含有量设为0.3%以下。从化学转化处理性的观点考虑,进一步优选设为0.2%以下。
B:0.005%以下
作为不损害本发明的作用效果的微量元素,也可以含有B。另外,有时,由于含有B而铁素体晶界被强化,耐二次加工脆性进一步提高。为了得到该效果,B含有量优选为3质量ppm以上。然而,若B含有量大于0.005%,则由于淬火性的提高,马氏体过剩地生成,从而有时导致屈强比的降低。因而,当含有B时,其含有量设为0.005%以下。
Cu:0.3%以下
作为不损害本发明的作用效果的微量元素,也可以含有Cu。然而,若Cu含有量大于0.3%,则由于淬火性的提高,马氏体过剩地生成,从而有时导致屈强比的降低。另外,若Cu含有量大于0.3%,则在退火时在钢板表层形成有氧化物的情况下,化学转化处理性有时变差。因而,当含有Cu时,其含有量设为0.3%以下。
Ni:0.3%以下
作为不损害本发明的作用效果的微量元素,也可以含有Ni。然而,若Ni含有量大于0.3%,则由于淬火性的提高,马氏体过剩地生成,从而有时导致屈强比的降低。另外,若Ni含有量大于0.3%,则在退火时在钢板表层形成有氧化物的情况下,有时导致化学转化处理性变差。因而,当含有Ni时,其含有量设为0.3%以下。
上述以外的余部为Fe及不可避免的杂质。在不可避免的杂质中,不仅包含在制造时不可避免地混入的成分,还包括为了得到所期望的特性等而不可避免地添加的成分、不损害本发明的效果的成分。作为不可避免的杂质,例如Mg、Ca、Sr、Sn、Sb、Bi、Ta及W的1种以上总计为1%以下。
接下来,对本发明的高强度钢板的钢组织进行说明。本发明的高强度钢板具有下述钢组织:以面积百分数计包含铁素体:90%以上,珠光体、马氏体、残余奥氏体及渗碳体的总计:0~10%,铁素体的平均晶体粒径为15.0μm以下,铁素体的平均纵横比为1.2以上。以下,对本发明的高强度钢板的组织构成进行说明。
铁素体:90%以上
铁素体具有良好的延展性。为了满足本发明要实现的高屈强比、优异的拉伸凸缘性及优异的耐二次加工脆性的全部,在本发明中,以面积百分数计,需要含有90%以上的铁素体作为主相。当铁素体的含有量小于90%时,得不到本发明要实现的上述特性。因此,将铁素体设为以面积百分数计为90%以上。优选设为95%以上。
珠光体、马氏体、残余奥氏体、渗碳体的总计:0~10%
通过含有珠光体、马氏体、残余奥氏体及渗碳体的1种以上,拉伸强度和屈服强度进一步增加。另外,以面积百分数的总计含有0~10%的这些,也能得到本发明要实现的特性。然而,若珠光体、马氏体、残余奥氏体及渗碳体的总计以面积百分数计大于10%,则拉伸凸缘性、耐二次加工脆性变差。因此,珠光体、马氏体、残余奥氏体及渗碳体的总计以面积百分数计设为0~10%。优选设为0~5%。需要说明的是,即便铁素体的面积百分数为100%,也能够得到所期望的强度,上述组织的总计面积百分数也可以是0%。
铁素体的平均晶体粒径:15.0μm以下
铁素体的平均晶体粒径对于得到本发明要实现的优异的耐二次加工脆性和0.70以上的高屈强比而言是重要的。然而,若铁素体的平均晶体粒径大于15.0μm,则得不到0.70以上的屈强比,耐二次加工脆性也会变差。因此,铁素体的平均晶体粒径设为15.0μm以下。优选设为10.0μm以下。另外,若铁素体的平均晶体粒径小于5μm,则有时屈强比、拉伸强度过度增加、成型性变差,因此,优选为5μm以上。
铁素体的平均纵横比:1.2以上
铁素体的平均纵横比对于得到优异的拉伸凸缘性和耐二次加工脆性而言是重要的。具体的理由不明,但据认为,在进行成型直至开裂在板厚方向贯通的扩孔试验中,若较之轧制方向的晶粒长度而言,板厚方向的晶粒长度变短,则在平均晶体粒径相同的情况下,晶界(其为开裂传播的障碍)增加,因此拉伸凸缘性提高。当铁素体的平均纵横比小于1.2时,上述效果小。因此,铁素体的平均纵横比设为1.2以上。优选设为1.4以上。另外,如上所述的效果即便是增大铁素体的平均纵横比,也已经饱和,因此10.0以下即可。需要说明的是,本发明中的铁素体为再结晶铁素体。
需要说明的是,对于各组织的面积百分数,在垂直于轧制宽度方向的截面中,用SEM观察从钢板表面起的板厚1/4位置,能够利用ASTM E 562-05中记载的样点法来求出。对于铁素体的平均晶体粒径,用光学显微镜观察从钢板表面起的板厚1/4位置,能够由观察面积和晶粒数来算出当量圆直径。对于铁素体的平均纵横比,在垂直于轧制宽度方向的截面中,用光学显微镜观察从钢板表面起的板厚1/4位置,通过JIS G 0551的表1中记载的、求出每个晶粒的平均线段长度的方法来算出轧制方向及板厚方向的平均晶粒长度,能够利用(轧制方向的平均晶粒长度)/(板厚方向的平均晶粒长度)来求出。
具有上述成分组成、钢组织的高强度钢板为本发明的高强度钢板。另外,本发明的高强度钢板也可以在表面具有热浸镀锌或电镀锌。另外,上述热浸镀锌也可以是合金化热浸镀锌。
接下来,对本发明的高强度钢板的制造方法进行说明。本发明的高强度钢板能够通过实施下述方式的退火来制造:在通过箱式退火炉将冷轧钢板退火的过程中,将炉内气氛中的氢浓度设为5~100%,以120℃/小时以下的速度升温至550℃,在550~750℃的温度区域中均热。需要说明的是,可以利用连续铸造来制作板坯,通过热轧、酸洗及冷轧来制造冷轧钢板。以下,对各制造条件进行说明。
铸造方法没有特别限定,只要不发生成分组成的偏析、组织的显著不均匀即可,可以是铸锭法、连续铸造法中的任一者。
对于热轧,既可以将高温的铸造板坯直接轧制,也可以将冷却至室温的板坯再加热然后轧制。另外,在板坯的时点,当存在裂纹等表面缺陷时,可通过磨床等实施板坯修整。当将板坯再加热时,为了将Nb碳氮化物溶解,优选加热至1100℃以上。在热轧中,粗轧为高温的板坯、实施精轧从而形成热轧钢板,卷取为热轧卷板。
粗轧条件及精轧条件无特别限定,按照常规方法进行即可。若精轧温度小于Ar3转变点,则存在下述情况:作为热轧钢板组织而生成在轧制方向伸长的粗大的铁素体,退火后导致延展性的降低。因此,精轧温度优选设为Ar3转变点以上。另外,当使用薄板坯时,也可以省略粗轧。薄板坯是指厚度为200mm以下的板坯。
卷取温度无特别限定,按照常规方法决定即可。从得到本发明要实现的高屈强比的观点考虑,为了适当地控制Nb碳化物的析出量及析出物直径,优选设为500~700℃。另外,在需要进一步提高化学转化处理性的情况下,优选设为650℃以下,最优选的是,关于下限,为550℃以上。关于上限,最优选的卷取温度设为650℃以下。
冷轧按照常规方法进行即可,压下率优选设为30~90%。当压下率为30%以上时,由于在箱式退火时能够使铁素体完全地再结晶,从而可得到优异的拉伸凸缘性,故优选。当压下率为90%以下时,不会导致形状不良,基于该理由故优选。另外,从由拉伸特性的各向异性降低及轧制负荷增大导致的阻碍生产率的观点考虑,更优选将压下率设为75%以下。
在退火中,使用箱式退火炉,将冷轧钢板加热、均热、冷却。与连续退火炉相比较,箱式退火炉的设备设置成本低,因此,有用的是,通过箱式退火炉来得到上述特性(所期望的拉伸强度、屈强比、拉伸凸缘性、二次加工脆性及化学转化处理性)。
箱式退火炉内气氛中的氢浓度:5~100体积%
箱式退火炉内气氛中的氢浓度是对于为了得到本发明要实现的优异的化学转化处理性而言重要的制造条件。在钢板表面生成了Si、Mn等的氧化物的部位,由于未生成化学转化晶体,因此产生未覆盖区域。当氢浓度小于5体积%时,由于在钢板表层形成氧化物,因此化学转化处理性变差。另外,当氢浓度小于5体积%时,形成氧化皮,产生回火色等的外观的劣化。另外,若以在表面具有氧化物的钢板作为基底钢板而实施镀覆,则在生成了氧化物的部位,产生未被镀层被覆的未镀覆部。即便是对于镀覆钢板而言,在这种部位中,也会在化学转化处理时形成未覆盖区域,因此化学转化处理性差。因此,需要将炉内气氛中的氢浓度设为5体积%以上。为了完全地抑制钢板表层的氧化物的形成,优选将炉内气氛中的氢浓度设为10体积%以上。为了完全地抑制钢板表层的氧化物的形成,更优选将炉内气氛中的氢浓度设为50体积%以上。此外,为了完全地抑制钢板表层的氧化物的形成,更优选将炉内气氛中的氢浓度设为90体积%以上。另外,上限为100体积%。余部优选为非活性气体,可使用氮(N2)、氩(Ar)等。需要说明的是,在上述炉内气氛中,也可以含有一氧化碳(CO)、二氧化碳(CO2)等。
直至550℃的升温速度为120℃/小时以下
冷轧钢板的加热中的、从室温至550℃的平均升温速度是对于退火后能得到所期望的微细且在轧制方向上伸长的铁素体晶粒而言重要的制造条件。若直至550℃的升温速度大于120℃/小时,则铁素体晶粒的平均纵横比小于1.2,因此拉伸凸缘性和耐二次加工脆性变差。因此,直至550℃的升温速度设为120℃/小时以下。优选设为100℃/小时以下。另外,基于钢板特性上的理由,升温速度没有下限,但从生产率的观点考虑,优选为10℃/小时以上。需要说明的是,当加热至550℃以上的温度时,550℃以上的区域的平均升温速度无特别限定,既可以为120℃/小时以下,也可以大于120℃/小时。
均热温度:550~750℃
均热温度是对于控制铁素体粒径而言重要的条件。当均热温度小于550℃时,铁素体的再结晶变得不充分,拉伸凸缘性变差。若均热温度大于750℃,则铁素体晶粒、Nb碳化物变得粗大,因此得不到本发明要实现的拉伸强度、高屈强比及优异的拉伸凸缘性和耐二次加工脆性。因此,均热温度设为550~750℃。关于下限,优选的均热温度为600℃以上。关于上限,优选的均热温度为700℃以下。均热时间无特别限定,但为了使铁素体完全地再结晶,优选设为1小时以上,为了抑制铁素体晶粒的过度的粗大化,优选设为60小时以下。需要说明的是,均热时间为均热温度处于上述温度范围(550~750℃,优选为600~700℃)的状态的时间,也可以不是恒温保持。需要说明的是,从化学转化处理性的观点考虑,为了抑制钢板表层的氧化物生成,均热温度越低越优选。
上述均热后,将冷轧钢板冷却。冷却条件无特别限定,利用通常的方法适当确定即可。
上述退火后,也可以对高强度钢板的表面实施镀覆。镀覆为例如电镀锌、热浸镀锌。热浸镀锌优选为合金化热浸镀锌。
另外,根据需要,也可以对高强度钢板、具有镀层的高强度钢板实施伸长率为0.1~5.0%的平整轧制(temper roll)。
经以上工序,可得到本发明要实现的高强度钢板,进一步实施有机系皮膜处理(organic coating treatment)等表面处理,也不会损害本发明要实现的特性。
实施例
以下,利用实施例详细说明本发明。
于1250℃将具有表1所示的成分组成的钢A~P的板坯均热1小时后,在最终板厚3.2mm、精轧温度900℃(Ar3转变点以上)的条件下制作热轧钢板,冷却后,于卷取温度580℃卷取。将制得的热轧钢板酸洗后,实施最终板厚1.4mm(冷轧率56%)的冷轧从而形成冷轧钢板,通过箱式退火炉(其中,No.24中设为连续退火炉)实施表2所示条件的退火,制造No.1~24的高强度钢板。退火时的炉内气氛中的氢浓度设为100体积%(其中,No.17设为4%,No.24设为10%)。对一部分高强度钢板实施电镀锌、热浸镀锌或合金化热浸镀锌。实施了电镀锌的钢板的附着量设为3g/m2。对于实施了热浸镀锌的钢板而言,在于650℃进行30秒钟均热后,在热浸镀锌浴中浸渍从而实施附着量为45g/m2的热浸镀锌,然后冷却。对于合金化热浸镀锌的钢板而言,在热浸镀锌浴中浸渍后,进一步进行于510℃保持10秒的合金化处理。需要说明的是,在表2中,将热浸镀锌钢板记为GI,将合金化热浸镀锌钢板记为GA,将电镀锌钢板记为EG。
对得到的高强度钢板,进行钢组织的观察、拉伸试验、扩孔率(λ)、脆化转变温度、化学转化处理性的测定。
用SEM将垂直于轧制宽度方向的截面中的从钢板表面起的板厚1/4位置放大1000倍,利用ASTM E 562-05中记载的样点法求出各组织的面积百分数。对于铁素体的平均晶体粒径而言,用光学显微镜将板厚1/4位置放大400倍,由观察面积和晶粒数求出当量圆直径。对于各组织的面积百分数和铁素体的平均粒径而言,设为10个视野的算数平均。对于铁素体的平均纵横比而言,用光学显微镜将垂直于轧制宽度方向的截面中的从钢板表面起的板厚1/4位置放大400倍并观察,按照JIS G 0551的表1中记载的、求出每个晶粒的平均线段长度的方法,将总线段长度分别设为20mm,算出轧制方向及板厚方向的平均晶粒长度,利用(轧制方向的平均晶粒长度)/(板厚方向的平均晶粒长度)来求出。结果示于表2。需要说明的是,表2中的α是指铁素体,P是指珠光体,M是指马氏体,γ是指残余奥氏体,θ是指渗碳体。
对于拉伸强度(TS)及屈强比(YR)而言,使用以拉伸方向垂直于轧制方向的方式采集到的JIS5号拉伸试验片,利用按照JIS Z2241的拉伸试验来求出。结果示于表2。将拉伸强度为300~500MPa评价为良好,将屈强比为0.70以上评价为良好。
拉伸凸缘性利用按照JIS Z 2256的扩孔试验来评价。结果示于表2。将扩孔率(λ)为100%以上评价为良好。
耐二次加工脆性由脆化转变温度评价。如图1所示,使用以拉深比为1.8进行深拉深成型而得到的直径50mm、高度35mm的圆筒深拉深成型材料,测定不发生纵向裂纹失效的最低温度(转变温度),在-60℃以下的情况下,判定为特性良好。使冷却剂温度T以10℃的范围变化。
对于化学转化处理性而言,利用前述的方法实施化学转化处理,利用前述的方法使用SEM测定未覆盖区域的面积百分数并进行评价。将未覆盖区域的面积百分数为5%以下的情况评价为具有本发明要实现的优异的化学转化处理性,表2中记载了未覆盖区域面积百分数。
表2中示出钢组织的观察结果和拉伸试验结果及化学转化处理性等结果。由于No.1~3、6、8~10、13、14、18、20、21满足本发明的全部要件,因此,得到了本发明要实现的高屈强比、且拉伸凸缘性、耐二次加工脆性及化学转化处理性优异的高强度钢板。另一方面,No.4、5、7、11、12、15~17、19、22、23、24的钢成分或制造条件在本发明的范围外,未得到所期望的钢组织或表面状态,因此未得到本发明要实现的高屈强比、且拉伸凸缘性、耐二次加工脆性及化学转化处理性优异的高强度钢板。
产业上的可利用性
适用于以汽车内板部件等为中心,需要高屈强比、且优异的拉伸凸缘性、耐二次加工脆性及化学转化处理性的领域。
Claims (9)
1.化学转化处理性优异的高强度钢板,其特征在于,所述高强度钢板具有下述成分组成和钢组织,
所述成分组成以质量%计,含有C:0.02%以上且小于0.06%、Si:小于0.3%、Mn:小于1.0%、P:0.04%以下、S:0.020%以下、Al:0.01~0.10%、N:0.010%以下、Nb:0.003%以上且小于0.070%,余部由Fe及不可避免的杂质构成,
所述钢组织为:(i)以面积百分数计,包含铁素体:90%以上,珠光体、马氏体、残余奥氏体及渗碳体的总计:0~10%;(ii)所述铁素体的平均晶体粒径为15.0μm以下;(iii)所述铁素体的平均纵横比为1.2以上,
所述高强度钢板的拉伸强度为500MPa以下。
2.根据权利要求1所述的化学转化处理性优异的高强度钢板,其特征在于,以质量%计,进一步含有Cr:小于0.5%、Mo:0.3%以下、B:0.005%以下、Cu:0.3%以下、Ni:0.3%以下中的任意1种或2种以上。
3.根据权利要求1或2所述的化学转化处理性优异的高强度钢板,其特征在于,在表面具有热浸镀锌层。
4.根据权利要求3所述的化学转化处理性优异的高强度钢板,其特征在于,所述热浸镀锌层为合金化热浸镀锌层。
5.根据权利要求1或2所述的化学转化处理性优异的高强度钢板,其特征在于,在表面具有电镀锌层。
6.化学转化处理性优异的高强度钢板的制造方法,其特征在于,所述高强度钢板的制造方法为权利要求1或2所述的高强度钢板的制造方法,在通过箱式退火炉将冷轧钢板退火的过程中,
将炉内气氛中的氢浓度设为5~100体积%,
以120℃/小时以下的速度升温至550℃,
在550~750℃的温度区域中均热1~60小时。
7.根据权利要求6所述的化学转化处理性优异的高强度钢板的制造方法,其特征在于,在所述退火后,实施热浸镀锌。
8.根据权利要求7所述的化学转化处理性优异的高强度钢板的制造方法,其特征在于,在实施所述热浸镀锌后,对热浸镀锌实施合金化处理。
9.根据权利要求6所述的化学转化处理性优异的高强度钢板的制造方法,其特征在于,在所述退火后,实施电镀锌。
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