CN104508163B - 成形性及定形性优异的高强度热浸镀锌钢板及其制造方法 - Google Patents
成形性及定形性优异的高强度热浸镀锌钢板及其制造方法 Download PDFInfo
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- CN104508163B CN104508163B CN201280075009.8A CN201280075009A CN104508163B CN 104508163 B CN104508163 B CN 104508163B CN 201280075009 A CN201280075009 A CN 201280075009A CN 104508163 B CN104508163 B CN 104508163B
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- formability
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- dip galvanized
- steel sheet
- galvanized steel
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- 238000000034 method Methods 0.000 title claims abstract description 31
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 26
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 26
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 50
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 44
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 20
- 230000000717 retained effect Effects 0.000 claims abstract description 20
- 229910001568 polygonal ferrite Inorganic materials 0.000 claims abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 238000001816 cooling Methods 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 13
- 238000007747 plating Methods 0.000 claims description 12
- 238000005097 cold rolling Methods 0.000 claims description 11
- 230000008569 process Effects 0.000 claims description 11
- 238000000137 annealing Methods 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 229910052758 niobium Inorganic materials 0.000 claims description 7
- 229910052720 vanadium Inorganic materials 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 6
- 239000000956 alloy Substances 0.000 claims description 6
- 238000007598 dipping method Methods 0.000 claims description 6
- 238000005246 galvanizing Methods 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 238000005275 alloying Methods 0.000 claims description 4
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- 239000010959 steel Substances 0.000 abstract description 23
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- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 240000002853 Nelumbo nucifera Species 0.000 description 1
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- 235000006510 Nelumbo pentapetala Nutrition 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 230000001476 alcoholic effect Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000004040 coloring Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
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- 229910052738 indium Inorganic materials 0.000 description 1
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- 229910017604 nitric acid Inorganic materials 0.000 description 1
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- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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- C21D2211/00—Microstructure comprising significant phases
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
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Abstract
提供一种成形性及定形性优异的高强度热浸镀锌钢板及其制造方法,该钢板的抗拉强度(TS):1180MPa以上、总伸长率(EL):14%以上、扩孔率(λ):30%以上并且屈强比(YR):70%以下。该成形性及定形性优异的高强度热浸镀锌钢板的特征在于,具有以下成分组成:以质量%计,含有C:0.10~0.35%、Si:0.5~3.0%、Mn:1.5~4.0%、P:0.100%以下、S:0.02%以下、Al:0.010~0.5%,剩余部分为Fe以及不可避免的杂质,并且,关于微观组织,以面积率计,含有0~5%的多边形铁素体、5%以上的贝氏体铁素体、5~20%的马氏体、30~60%的回火马氏体以及5~20%的残余奥氏体,并且原奥氏体的平均粒径为15μm以下。
Description
技术领域
本发明涉及适合用作汽车用钢板的、成形性及定形性(shape fixability)优异的高强度热浸镀锌钢板及其制造方法。
背景技术
近年来,从保护地球环境的立场出发,提高汽车的燃料利用率成为重要的课题。因此,通过车身材料的高强度化来谋求薄壁化、通过使车身本身轻质化来谋求燃料利用率提高的研究变得活跃。对于像汽车部件一样的通过冲压加工、弯曲加工而成形为产品的钢板,在保持高强度的同时要求能承受加工的成形性。在专利文献1中通过利用回火马氏体以及残余奥氏体而实现同时兼顾高强度和高加工性。可是,存在如下问题:一般情况下,随着钢板的强度提高,加工后的回弹变大,定形性降低。在专利文献1中并未研究定形性,还有改善的余地。另一方面,在专利文献2中,通过利用由铁素体、贝氏体和C浓度较低的奥氏体组成的组织,能够得到YR较低、定形性优异的钢板。但是并没有对拉伸翻边性能(stretchflangeability)进行评价,不能说具有足够的加工性。在专利文献3中通过利用回火马氏体、贝氏体、残余奥氏体来同时兼顾高强度和高延展性,但并未提及定形性。另外,拉伸翻边性能作为绝对值未必很高,有改善的余地。
现有技术文献
专利文献
专利文献1:日本特开2009-209450号公报
专利文献2:日本特开2010-126808号公报
专利文献3:日本特开2010-90475号公报
发明内容
发明所要解决的课题
本发明的目的在于,有利地解决上述现有技术所存在的问题,提供一种适合用作汽车部件用材料的、抗拉强度(TS):1180MPa以上、总伸长率(EL):14%以上、扩孔率(λ):30%以上且屈强比(YR):70%以下的成形性及定形性优异的高强度热浸镀锌钢板及其制造方法。此外,屈强比(YR)是屈服强度(YS)与抗拉强度(TS)之比,由YR(%)=(YS/TS)×100表示。
用于解决课题的方法
本发明的发明人员为了达成上述课题并制造成形性及定形性优异的高强度热浸镀锌钢板,从钢板的成分组成以及微观组织的角度出发进行了反复认真研究,其结果得出以下的内容。
适当地调整合金元素,使得组织以面积率计含有0~5%的多边形铁素体、5%以上的贝氏体铁素体、5~20%的马氏体、30~60%的回火马氏体以及5~20%的残余奥氏体,并且使原奥氏体的平均粒径为15μm以下,由此能够同时兼顾高强度、高成形性以及高定形性。
关于通过在回火马氏体主体组织中分散马氏体而定形性提高的理由未必明确,但可认为其原因如下:在电镀后或电镀合金化后的冷却时,与回火马氏体接触的奥氏体产生马氏体转变,在回火马氏体中导入可动位错,从而使YR减少。另外,关于通过使原奥氏体晶粒细化而λ提高的理由尚不明确,但推测是因为,通过原奥氏体晶粒变得微细,退火后的组织的平均粒径变小,拉伸翻边加工时裂纹的传播路径变多从而抑制裂纹的连结。
这样的微观组织通过如下方式而得到,在退火时,在500℃~Ac1点的范围内以5℃/s以上的平均加热速度加热,在加热至(Ac3点-20)~1000℃并保持10~1000秒后,从750℃开始以15℃/s以上的平均冷却速度冷却至(Ms点-80℃)~(Ms点-30℃)的温度范围,然后,加热至350~500℃,保持10~600秒。
本发明基于这样的知识而完成,提供以下的方案。
(1)一种成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,具有如下成分组成:以质量%计,含有C:0.10~0.35%、Si:0.5~3.0%、Mn:1.5~4.0%、P:0.100%以下、S:0.02%以下、Al:0.010~0.5%,剩余部分为Fe以及不可避免的杂质,并且,关于微观组织,以面积率计,含有0~5%的多边形铁素体、5%以上的贝氏体铁素体,5~20%的马氏体,30~60%的回火马氏体、5~20%的残余奥氏体,并且原奥氏体的平均粒径为15μm以下。
(2)根据(1)所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,以质量%计,还含有选自Cr:0.005~2.00%、Mo:0.005~2.00%、V:0.005~2.00%、Ni:0.005~2.00%、Cu:0.005~2.00%中的至少一种元素。
(3)根据(1)或(2)所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,以质量%计,还含有选自Ti:0.01~0.20%、Nb:0.01~0.20%中的至少一种元素。
(4)根据(1)至(3)中任一项所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,以质量%计,还含有B:0.0005~0.0050%。
(5)根据(1)至(4)中任一项所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,以质量%计,还含有选自Ca:0.001~0.005%、REM:0.001~0.005%中的至少一种元素。
(6)根据(1)至(5)中任一项所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,镀锌为合金化镀锌。
(7)一种成形性及定形性优异的高强度热浸镀锌钢板的制造方法,其特征在于,对具有(1)至(5)中任一项所述的成分组成的板坯进行热轧、或者还进行冷轧,其后在实施连续退火时,在500℃~Ac1点的范围内以5℃/s以上的平均加热速度进行加热,在加热至(Ac3点-20℃)~1000℃的温度范围并保持10~1000秒后,从750℃开始以15℃/s以上的平均冷却速度冷却至(Ms点-80℃)~(Ms点-30℃)的温度范围,然后,加热至350℃~500℃并保持10~600秒后,实施热浸镀锌、或者还进行电镀合金化处理。
发明效果
根据本发明,能够得到抗拉强度(TS):1180MPa以上、总伸长率(EL):14%以上、扩孔率(λ):30%以上并且屈强比(YR):70%以下的成形性及定形性优异的高强度热浸镀锌钢板。
具体实施方式
以下,对本发明进行详细的说明。此外,表示成分元素的含量的“%”,除非另有规定,一般是指“质量%”。
1)成分组成
C:0.10~0.35%
C是使马氏体、回火马氏体等低温转变相生成而使TS上升所必需的元素。在C量不足0.10%的情况下,以面积率计,难以确保回火马氏体为30%以上且马氏体为5%以上。另一方面,若C量超过0.35%,则EL、点焊性劣化。因此,使C量为0.10~0.35%,优选为0.15~0.3%。
Si:0.5~3.0%
Si是有助于对钢进行固溶强化而使TS-EL平衡提高、并有助于生成残余奥氏体的元素。为了得到这样的效果,需要使Si量为0.5%以上。另一方面,若Si超过3.0%,则会导致EL的降低以及表面性状、焊接性劣化。因此,使Si量为0.5~3.0%,优选为0.9~2.0%。
Mn:1.5~4.0%
Mn有助于钢的强化,是促进马氏体等低温转变相生成的元素。为了得到这样的效果,需要使Mn量为1.5%以上。另一方面,若Mn量超过4.0%,则EL的劣化将变得明显,加工性下降。因此,使Mn量为1.5~4.0%,优选为2.0~3.5%。
P:0.100%以下
P因晶界偏析使钢劣化,使焊接性劣化,因此希望其量尽可能降低。但是,从制造成本等方面来看,P量选为0.100%以下。
S:0.02%以下
S作为MnS等夹杂物存在,使焊接性劣化,因此希望其量尽可能降低。但是,从制造成本等方面来看,S量选为0.02%以下。
Al:0.010~0.5%
Al作为脱氧剂发挥作用,优选在脱氧工序中添加。为了得到这样的效果,需要使Al量为0.010%以上。另一方面,若Al量超过0.5%,则连续铸造时板坯开裂的危险性增高。因此,Al量选为0.010~0.5%。
剩余部分是Fe以及不可避免的杂质,但能够根据需要适当含有以下元素中的一种以上。
选自Cr:0.005~2.00%、Mo:0.005~2.00%、V:0.005~2.00%、Ni:0.005~2.00%、Cu:0.005~2.00%中的至少一种
Cr、Mo、V、Ni、Cu是有助于生成马氏体等低温转变相的元素。为了得到这样的效果,需要使选自Cr、Mo、V、Ni、Cu中的至少一种元素的含量为0.005%。另一方面,若Cr、Mo、V、Ni、Cu各自的含量超过2.00%,则其效果饱和,导致成本上升。因此,Cr、Mo、V、Ni、Cu的含量分别选为0.005~2.00%。
另外,还能够含有选自Ti:0.01~0.20%、Nb:0.01~0.20%中的至少一种。
Ti以及Nb是形成碳氮化物而有助于通过析出强化使钢高强度化的元素。为了得到这样的效果,需要使Ti以及Nb的含量为0.01%以上。另一方面,若Ti以及Nb的含量超过0.20%,则高强度化的效果饱和,EL降低。因此,Ti以及Nb的含量选为0.01~0.20%。
另外,还能够含有B:0.0005~0.0050%。
B是抑制在奥氏体晶界生成铁素体而有助于生成低温转变相的元素。为了得到这样的效果,需要使B量为0.0005%以上。另一方面,若B量超过0.0050%,则其效果饱和,导致成本上升。因此,B量选为0.0005~0.0050%。
另外,还能够含有选自Ca:0.001~0.005%、REM:0.001~0.005%中的至少一种。
Ca、REM都是通过硫化物的形态控制而有助于改善加工性的元素。为了得到这样的效果,需要使选自Ca、REM中的至少一种元素的含量为0.001%以上。另一方面,若Ca、REM各自的含量超过0.005%,则有可能对钢的清洁度造成不良影响,从而得不到期望的特性。因此,Ca、REM的含量选为0.001~0.005%。
2)微观组织
多边形铁素体的面积率:0~5%
若多边形铁素体的面积率超过5%,则难以同时使TS为1180MPa以上且使扩孔率为30%以上。因此,多边形铁素体的面积率选为0~5%。
贝氏体铁素体的面积率:5%以上
贝氏体转变通过使奥氏体中C浓缩、使奥氏体稳定化而有助于确保对于EL上升有效的残余奥氏体。为了得到该效果,需要使贝氏体铁素体的面积率为5%以上。另一方面,若其面积率超过60%,则难以得到期望的马氏体以及残余奥氏体,所以优选贝氏体铁素体的面积率为5~60%。
马氏体的面积率:5~20%
马氏体有助于TS的提高。另外,有助于使YR降低。
为了得到这样的效果需要使马氏体的面积率为5%以上。另一方面,若超过20%则EL、扩孔率的降低变得明显。因此,马氏体的面积率选为5~20%。
回火马氏体的面积率:30~60%
若回火马氏体的面积率不足30%,则难以同时使TS为1180MPa以上且使扩孔率为30%以上。另一方面,若其面积率超过60%,则YR的上升变得显著,定形性降低。因此,回火马氏体的面积率选为30~60%。此外,本发明中的回火马氏体的维氏硬度为250以上。
残余奥氏体的面积率:5~20%
残余奥氏体有助于EL的提高。为得到这样的效果,需要使残余奥氏体的面积率为5%以上。但是,若其面积率超过20%,则扩孔率的降低变得明显。因此,残余奥氏体的面积率选为5~20%。
原奥氏体的平均粒径为15μm以下
原奥氏体晶粒的细化有助于λ的提高。为得到这样的效果,需要使原奥氏体的平均粒径为15μm以下。因此,使原奥氏体的平均粒径为15μm以下。下限并无特别规定,但是若过小则可能导致YR上升,因此优选为5μm以上。
此外,还存在作为多边形铁素体、贝氏体铁素体、马氏体、回火马氏体、残余奥氏体以外的相而含有珠光体的情况,但只要满足上述的微观组织的条件,就能达成本发明的目的。
在此,多边形铁素体、贝氏体铁素体、马氏体、回火马氏体的面积率是指,各相的面积在观察面积中所占的比例,由以下所示的方法求得多边形铁素体、马氏体、贝氏体铁素体、回火马氏体的面积率。在对钢板的板厚截面进行研磨后,用3%的硝酸酒精溶液进行腐蚀,用SEM(扫描型电子显微镜)以1500倍的倍率对板厚1/4位置进行三视场拍摄,在此使用Media Cybernetics公司生产的Image-Pro对各视场的对象组织进行区分上色,求得对象组织在该视场中所占的面积率,将各视场的面积率的平均值作为对象组织的面积率。另外,关于残余奥氏体的面积率,在将钢板研磨至板厚1/4位置后,通过化学研磨再研磨0.1mm,对于由此得到的面,用X射线衍射装置使用Mo的Kα线,测定fcc铁的(200)、(220)、(311)面和bcc铁的(200)、(211)、(220)面的积分强度,据此求得残余奥氏体的比例,将该比例作为残余奥氏体的面积率。另外,关于原奥氏体的平均粒径,对钢板的板厚截面进行研磨后,用3%硝酸酒精溶液腐蚀,用SEM(扫描型电子显微镜)以1500倍的倍率观察板厚1/4位置,使视场中的被原奥氏体晶界包围的组织的面积的总和除以其个数来求得平均面积,将该平均面积的开方作为平均粒径。
3)制造条件
本发明的高强度热浸镀锌钢板以如下的方法制造。首先,对具有上述的成分组成的板坯实施热轧、酸洗,或者还实施冷轧。然后,通过连续退火,在500℃~Ac1点的范围内以5℃/s以上的平均加热速度进行加热,在加热至(Ac3点-20℃)~1000℃的温度范围并保持10~1000秒后,从750℃开始以15℃/s以上的平均冷却速度冷却至(Ms点-80℃)~(Ms点-30℃)的温度范围。进而,将钢板加热至350℃~500℃并保持10~600秒后,实施热浸镀锌,或者还进行电镀合金化处理。以下,进行详细地说明。
将具有上述成分组成的钢熔融并制成板坯,对板坯进行热轧后,将其冷却并卷绕。若热轧后的卷绕温度超过650℃,则生成黑色金属污斑,电镀性降低。另一方面,在热轧后的卷绕温度不足400℃的情况下,热轧板的形状恶化。因此,热轧后的卷绕温度优选为400~650℃。
接下来,优选对热轧板进行酸洗,除去热轧板表层的氧化皮。酸洗工序没有特别的限定,可以使用通常方法。根据需要,对酸洗后的热轧板进行冷轧。冷轧工序没有特别的限定,可以使用通常方法。将酸洗后的热轧板或冷轧后的冷轧板在以下的条件下连续退火。
500℃~Ac1点范围内的平均加热速度:5℃/s以上
在500℃~Ac1点范围内的平均加热速度不足5℃/s的情况下,因再结晶而导致奥氏体粗大化,无法得到本发明的微观组织。因此,使500℃~Ac1点范围内的平均加热速度为5℃/s以上。
加热至(Ac3点-20℃)~1000℃的温度范围并均热保持10~1000秒
在均热保持温度不足(Ac3点-20℃)的情况下奥氏体生成得不充分,无法得到本发明的微观组织。另一方面,若均热保持温度超过1000℃,则奥氏体粗大化,退火后的构成相粗大化而导致韧性等降低。因此,使均热保持温度为(Ac3点-20℃)~1000℃。在均热保持时间不足10秒的情况下奥氏体生成得不充分,无法得到本发明的微观组织。另外,若均热保持时间超过1000秒则导致成本上升。因此,使均热保持时间为10~1000秒。
从750℃开始以15℃/s以上的平均冷却速度冷却至(Ms点-80℃)~(Ms点-30℃)的温度范围
在从750℃到(Ms点-80℃)~(Ms点-30℃)的温度范围的平均冷却速度不足15℃/s的情况下,冷却过程中会生成大量铁素体,无法得到本发明的微观组织。因此使平均冷却速度为15℃/s以上。
冷却停止温度:(Ms点-80℃)~(Ms点-30℃)
冷却至冷却到达温度后,奥氏体的一部分转变为马氏体,在其后的再加热时、电镀合金化处理时,马氏体成为回火马氏体,而未转变奥氏体成为残余奥氏体、或者马氏体和/或贝氏体。此时,若冷却到达温度超过(Ms点-30℃)则回火马氏体量不足,若冷却到达温度不足(Ms点-80℃)则未转变奥氏体显著减少、另外回火马氏体增加,从而无法得到本发明的微观组织。因此,使冷却到达温度为(Ms点-80℃)~(Ms点-30℃)。
再加热温度:350~500℃
冷却至冷却到达温度后,若再加热至350~500℃的温度范围,则冷却时生成的马氏体回火,成为回火马氏体,另外,在未转变奥氏体中进行C浓缩,作为残余奥氏体而稳定化。另外,进行贝氏体转变,C从贝氏体铁素体扩散从而使未转变奥氏体更稳定化。在再加热温度不足350℃的情况下,由于所进行的贝氏体转变成为含有碳化物的贝氏体,因此在未转变奥氏体中C未充分地浓缩,作为残余奥氏体的稳定性不足。另一方面,若再加热温度超过500℃,则未转变奥氏体容易生成碳化物或者发生珠光体转变,无法得到本发明的微观组织。因此,再加热温度选为350~500℃。优选为380~480℃。
再加热温度下的保持时间:10~600秒
在保持时间不足10秒的情况下,贝氏体的生成不充分,另外,若保持时间超过600秒,则未转变奥氏体容易生成碳化物或者发生珠光体转变,无法得到本发明的微观组织。因此保持时间选为10~600秒。
热浸镀锌处理优选以如下方式进行,将如上所述得到的钢板浸渍于440℃以上500℃以下的镀锌浴中,其后,通过气刀吹扫(gaswiping)等方法调整电镀附着量。另外,在使镀锌合金化时,优选在460℃以上550℃以下的温度范围内保持1秒以上40秒以下来进行合金化。镀锌优选使用Al量为0.08~0.18%的镀锌浴。
对于实施了热浸镀锌合金化处理之后的钢板,能够以形状矫正、表面粗糙度的调整为目的进行平整轧制。另外,还能够实施树脂、油脂表面涂层等各种涂装处理。
其他的制造方法的条件没有特别的限定,但优选在以下的条件下进行。
为防止宏观偏析,板坯优选以连续铸造法制造,但也能够由铸锭法、薄板坯铸造法制造。为了对板坯进行热轧,既可以将板坯暂时冷却至室温,其后再加热而进行热轧,也能够不将板坯冷却至室温地装入加热炉进行热轧。或者还能够适用在稍微进行保热后立刻进行热轧的节能工艺。在对板坯进行加热的情况下,为了使碳化物溶解或防止轧制载荷的增大,优选加热至1100℃以上。另外,为防止氧化皮损耗增大,板坯的加热温度优选为1300℃以下。
在对板坯进行热轧时,即使降低板坯的加热温度,从能够防止轧制时的问题的观点出发,也能够对粗轧后的薄板坯(sheet bar)进行加热。另外,能够适用连续轧制工艺,即将薄板坯彼此连接,连续地进行精轧。精轧由于存在使各向异性增大从而使冷轧、退火后的加工性降低的情况,因此优选在Ar3转变点以上的精轧温度下进行。另外,为了实现轧制载荷的降低和形状、材质的均匀化,优选在精轧的所有轧道或者一部分轧道上进行摩擦系数为0.10~0.25的润滑轧制。
卷绕后的钢板通过酸洗等除去氧化皮,之后,将热轧板在上述的条件下退火、或者将热轧板进行冷轧后在上述条件下退火,然后实施热浸镀锌。在实施冷轧的情况下,冷轧压下率优选为40%以上。另外,为了降低冷轧时的轧制载荷,还能够对卷绕后的钢板实施热轧板退火。
实施例
将表1所示的成分组成的钢通过转炉熔炼,通过连续铸造而制成钢板坯(表1中,N为不可避免的杂质)。将这些钢板坯加热至1200℃后进行粗轧、精轧,在卷绕温度400~650℃的范围内进行卷绕,制成板厚2.3mm的热轧板。接下来,通过分批处理将一部分在到达温度600℃、热处理时间5小时的条件下实施软化,在酸洗后,冷轧至板厚1.4mm,制造冷轧钢板以供退火。将另一部分热轧至板厚2.3mm的钢板进行酸洗,然后直接供于退火。退火通过连续热浸镀锌生产线,以表2、3所示的条件进行,浸渍于460℃的镀浴中,形成附着量为35~45g/m2的镀层,并以冷却速度10℃/s进行冷却从而制成热浸镀锌钢板1~29。另一部分在电镀后还以525℃进行电镀合金化处理,并以冷却速度10℃/s进行冷却,从而制成合金化热浸镀锌钢板。然后,对得到的电镀钢板,以上述的方法测定多边形铁素体、贝氏体铁素体、马氏体、回火马氏体的面积率、残余奥氏体的面积率以及原奥氏体的平均粒径。另外,在与轧制方向垂直的方向上选取JIS5号拉伸试验片,以应变速度10-3进行拉伸试验。再有,选取150mm×150mm的试验片,按照JFST1001(日本钢铁联盟标准,2008年)进行三次扩孔试验并求得平均的扩孔率(%),对拉伸翻边性能进行评价。其结果由表4、5表示。
在本发明中能够确认到YR为70%以下,具有高定形性。另外,能够确认到TS为1180MPa以上、EL为14%以上、λ为30%以上,具有高的强度和成形性。因此,根据本发明例,发挥如下优异效果:能够得到定形性优异的热浸镀锌钢板,有助于汽车的轻质化,极其有助于汽车车身的高性能化。
工业实用性
根据本发明,能够得到抗拉强度(TS):1180MPa以上、总伸长率(EL):14%以上、扩孔率(λ):30%以上且屈强比(YR):70%以下的、成形性及定形性优异的高强度热浸镀锌钢板。若将本发明的高强度热浸镀锌钢板用于汽车用部件,则能够有助于汽车的轻质化,极其有助于汽车车身的高性能化。
Claims (5)
1.一种成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,
具有如下成分组成:以质量%计,含有C:0.10~0.35%、Si:0.5~3.0%、Mn:1.5~4.0%、P:0.100%以下、S:0.02%以下、Al:0.010~0.5%,剩余部分为Fe以及不可避免的杂质,并且,关于微观组织,以面积率计,含有0~5%的多边形铁素体、5%以上的贝氏体铁素体、5~20%的马氏体、30~60%的回火马氏体以及5~20%的残余奥氏体,并且原奥氏体的平均粒径为15μm以下。
2.根据权利要求1所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,
还含有以下的A~D中的至少一项:
A:以质量%计,选自Cr:0.005~2.00%、Mo:0.005~2.00%、V:0.005~2.00%、Ni:0.005~2.00%、Cu:0.005~2.00%中的至少一种元素,
B:以质量%计,选自Ti:0.01~0.20%、Nb:0.01~0.20%中的至少一种元素,
C:以质量%计,B:0.0005~0.0050%,
D:以质量%计,选自Ca:0.001~0.005%、REM:0.001~0.005%中的至少一种元素。
3.根据权利要求1或2所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,
镀锌为合金化镀锌。
4.根据权利要求1所述的成形性及定形性优异的高强度热浸镀锌钢板,其特征在于,
所述原奥氏体的平均粒径为5μm以上。
5.一种成形性及定形性优异的高强度热浸镀锌钢板的制造方法,其特征在于,
对具有权利要求1或2所述的成分组成的板坯进行热轧、或者还进行冷轧,其后在实施连续退火时,在500℃~Ac1点的范围内以5℃/s以上的平均加热速度进行加热,在加热至(Ac3点-20℃)~1000℃的温度范围并保持10~1000秒后,从750℃开始以15℃/s以上的平均冷却速度冷却至(Ms点-80℃)~(Ms点-30℃)的温度范围,然后,加热至350℃~500℃并保持10~600秒后,实施热浸镀锌、或者还进行电镀合金化处理。
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JP5287770B2 (ja) * | 2010-03-09 | 2013-09-11 | Jfeスチール株式会社 | 高強度鋼板およびその製造方法 |
JP5327106B2 (ja) * | 2010-03-09 | 2013-10-30 | Jfeスチール株式会社 | プレス部材およびその製造方法 |
JP5333298B2 (ja) * | 2010-03-09 | 2013-11-06 | Jfeスチール株式会社 | 高強度鋼板の製造方法 |
JP5136609B2 (ja) * | 2010-07-29 | 2013-02-06 | Jfeスチール株式会社 | 成形性および耐衝撃性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
JP5798740B2 (ja) * | 2010-12-08 | 2015-10-21 | 新日鐵住金株式会社 | 成形性に優れた高強度冷延鋼板及びその製造方法 |
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- 2012-07-31 CN CN201280075009.8A patent/CN104508163B/zh active Active
- 2012-07-31 EP EP12882412.5A patent/EP2881481B1/en active Active
- 2012-07-31 IN IN11262DEN2014 patent/IN2014DN11262A/en unknown
- 2012-07-31 WO PCT/JP2012/004863 patent/WO2014020640A1/ja active Application Filing
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EP2881481A4 (en) | 2016-02-24 |
US20150203947A1 (en) | 2015-07-23 |
CN104508163A (zh) | 2015-04-08 |
EP2881481B1 (en) | 2019-04-03 |
IN2014DN11262A (zh) | 2015-10-09 |
WO2014020640A1 (ja) | 2014-02-06 |
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