CN107829038B - 一种高强塑积、高可镀性细晶热镀锌双相钢及其生产方法 - Google Patents
一种高强塑积、高可镀性细晶热镀锌双相钢及其生产方法 Download PDFInfo
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims description 13
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 43
- 239000010959 steel Substances 0.000 claims abstract description 43
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 16
- 238000000137 annealing Methods 0.000 claims abstract description 16
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Abstract
本发明公开了一种高强塑积、高可镀性细晶双相钢及其生产方法,属于冶金材料领域。本发明的高强塑积、高可镀性细晶双相钢化学成分为:C为0.08~0.12wt.%,Mn为1.8~2.5wt.%,Si为<0.005wt.%,Al为0.3~0.5wt.%,P为0.04~0.08wt.%,Nb为0.03~0.06wt.%,Ni为0.02~0.05wt.%,S为≤0.005wt.%,余量为Fe。其生产方法包括,真空熔炼、锻坯、第一阶段奥氏体再结晶区轧制、第二阶段两相区热轧、多道次冷轧和快速退火。本发明能大幅度的合金元素在退火过程中的选择氧化,提高其可镀性,并优化了带钢的组织和性能。
Description
技术领域
本发明属于冶金材料领域,具体涉及一种高强塑积、高可镀性细晶热镀锌双相钢及其制备方法。
背景技术
节能减排是当前国际社会的主题,其中汽车轻量化是节能减排的主要措施,降低车身重量并提高安全性是汽车行业最重要的发展方向。为了实现节能减排和提高安全性这一目标,先进高强度钢的概念应运而生。双相(DP)钢作为先进高强钢因具有较高的抗拉强度、较低的屈服强度、较高的初始加工硬化率以及成本低和制备工艺简单等原因,在现代汽车工业中得到了普遍应用。汽车在服役过程中所处的环境复杂多样且较为严苛,会造成车体的腐蚀。为了防止汽车板在使用过程中出现腐蚀现象,需要对汽车板进行防腐处理。热浸镀锌钢板由于具有优异的防腐蚀性能,能够大幅度提高车身耐锈蚀穿孔的能力,因而成为汽车车身用材中使用最为广泛的材料。但是由于DP钢中存在较多的合金元素,尤其是Si和Mn在连续热镀锌退火过程中发生选择性氧化,恶化钢板的表面质量,影响钢板的可镀性。但是降低Si和Mn元素的含量会使DP钢的力学性能达不到要求。而利用Cr和Mo元素去代替Si和Mn元素虽然双相钢的性能得到保证,但是一方面Cr和Mo等合金元素较昂贵,增加了双相钢的制造成本;另一方面Cr和Mo元素同样发生选择性氧化;因此,降低钢中易氧化元素的含量是从根本上解决选择氧化问题的唯一方法;Mn元素可以在镀锌过程中与锌液中的Al发生铝热还原反应,对钢板的可镀性影响较小。降低钢中Si元素的含量,会使双相钢在热镀锌过程中在铁素体-马氏体界面上形成大渗碳体,从而恶化双相钢的延展性。目前,有学者提出了在成份设计上采取以Al代Si的成分设计思路,但仍加入了一些Cr和Mo等易氧化的元素来保证带钢的强度要求,仍然无法很好的解决选择氧化的问题。
在加工工艺方面,普通的冷轧DP钢连续退火工艺为:将冷轧板加热到铁素体(α)和奥氏体(γ)两相区,保温一段时间后快速冷却到马氏体转变温度(Ms)以下进行时效处理,之后以一定的冷速冷却到室温,得到铁素体+(20%~40%)马氏体的双相组织。但是在连续热镀锌生产线上,带钢在临界区退火后要快速冷却到入锌锅温度进行镀锌,镀锌之后再快速冷却到室温。通常锌锅温度在450℃以上(高于Ms温度),而在这个温度下镀锌时,奥氏体很容易转变为贝氏体组织从而降低DP钢的强度。
DP钢的性能取决于组织中马氏体的体积分数,马氏体的分布及铁素体和马氏体的晶粒尺寸。马氏体的体积分数增加,DP钢的强度增加,但其延伸率降低。研究表明,细化DP钢的晶粒尺寸即可提高DP钢的强度又不损坏DP钢的韧性,是保证DP钢强韧性平衡的主要措施。
发明内容
针对以上存在的问题,本发明提供了一种高强塑积、高可镀性细晶热镀锌DP钢及其生产方法,其目的是解决DP钢在热镀锌生产过程中合金元素的选择性氧化及性能较差的问题。
本发明提供的热浸镀用DP钢的化学成分及其含量是:C为0.08~0.12wt.%,Mn为1.8~2.5wt.%,Si为<0.005wt.%,Al为0.3~0.5wt.%,P为0.04~0.08wt.%,Nb为0.03~0.06wt.%,Ni为0.02~0.05wt.%,S为≤0.005wt.%,余量为Fe;
本发明的高强塑积、高可镀性细晶热镀锌DP钢按以下步骤进行:
1)按照C为0.08~0.14wt.%,Mn为1.8~2.5wt.%,Si为<0.005wt.%,Al为0.3~0.5wt.%,P为0.06~0.08wt.%,Ni为0.02~0.05wt.%,Nb为0.03~0.07wt.%,S为≤0.005wt.%,余量为Fe的设定成分冶炼钢水,钢水浇铸成铸坯后,重新加热到1200~1300℃,等温2~3h后,锻造成方坯用于热轧。热轧分为两个阶段,第一阶段在奥氏体再结晶区轧制,压下量为50%~65%,控制开轧温度1050~1100℃,终轧温度950~1000℃;第二阶段为两相区热轧,压下量为80%~90%,控制开轧温度850~880℃,终轧温度770~800℃,然后快速冷却到250~350℃进行卷取,得到热轧板。
2)热轧板酸洗后进行多道次冷轧,压下量为70%~85%,得到冷轧板。
3)热镀锌退火工艺为:炉内保护气氛的体积分数为10%H2+90%N2,露点为-30℃,锌锅中Al含量为0.2%。将冷轧板以50~80℃/s的加热速率升温到750~800℃等温1~2min后快速冷却到460~470℃,快冷速率为50~80℃/s,最后进入锌锅进行热浸镀锌5~10s,最后以10~15℃/s的冷速冷却到室温。进一步地,在上述技术方案中,锌锅温度为450-470℃。
进一步地,在上述技术方案中,冷轧5-12道次。
本发明提供上述方法得到的高强塑积、高可镀性细晶热镀锌DP钢,镀锌板表面平整,无漏镀或镀锌不均匀处,镀锌板的强塑积超过20GPa,铁素体平均晶粒尺寸<4μm。
与现有技术相比,本发明的特点和有益效果是:
1)普通的DP钢存在大量的Si、Cr、Mo等合金元素造成热镀锌退火后表面质量差,本发明利用Al元素替代Si元素,取消了Cr和Mo元素,从而能大幅度减少连续退火镀锌过程中的选择性氧化,提高其可镀性。并降低了钢的成本。
2)本发明提高了Mn元素的含量,添加了Ni元素,并在退火后利用较大的冷速冷却到入锌锅温度,此时奥氏体的稳定性增加,过冷奥氏体的孕育期延长,避免了过冷奥氏体在镀锌过程中形成贝氏体组织。
3)本发明热镀锌退火阶段利用快速加热和快速冷却的退火工艺,缩短了生产时间提高了生产效率。.
4)本发明得到的热镀锌双相钢,组织细小均匀,强塑积较高。
附图说明
图1是本发明实施例1高强塑积,高可镀性细晶热镀锌DP钢的生产流程图;
图2是本发明实施例1制备的DP钢的SEM图;
图3是本发明实施例2制备的DP钢的SEM图;
图4是本发明实施例3制备的DP钢的SEM图。
具体实施方式
实施例1
本实施例的高强塑积,高可镀性细晶热镀锌DP钢,其化学成分为:C为0.11wt.%,Mn为2.1wt.%,Si为<0.005wt.%,Al为0.35wt.%,P为0.06wt.%,Ni为0.02wt.%,Nb为0.04wt.%,S为≤0.005wt.%,余量为Fe
本实施例的高强塑积、高可镀性细晶热镀锌DP钢的生产方法按照以下步骤进行:
(1)按照质量百分比:C 0.11%,Mn 2.1%,Si<0.005%,Al 0.35%,P 0.06%,Ni0.02%,Nb 0.04%,S<0.005%,余量为Fe的设定成分来冶炼钢水,在真空感应炉中浇铸成65Kg铸坯,将铸坯切头去尾加热至1230℃等温2h,在此温度下锻造成截面为80mm×80mm的矩形坯料,然后用锯床加工成80mm×80mm×100mm的矩形坯用于热轧。第一阶段在奥氏体再结晶区进行热轧,开轧温度为1100℃,终轧温度为970℃,压下分配为80~50~40mm。第二阶段为两相区轧制,开轧温度为870℃,终轧温度为800℃,压下分配为40~22~13~9~6~5.3mm,然后层流快速冷却到330℃进行卷曲,得到热轧板。
(2)热轧板酸洗后进行12个道次的冷轧,控制压下量在70%,得到冷轧板。
(3)将冷轧板以60℃/s的加热速率加热到770℃,等温1min后快速冷却到463℃,立即进入锌锅进行热浸镀锌并保持10s,锌锅温度为460℃,其中退火炉内保护气氛的体积分数为10%H2+90%N2,露点为-30℃,锌锅中Al含量为0.2%。之后以10℃/s的冷速冷却到室温。得到的热浸镀锌板表面平整,无漏镀和镀锌不均匀处,基板由铁素体和马氏组成,铁素体平均晶粒尺寸3.7μm(图2),按照GBT228-2002拉伸试样国家标准,标距为50mm时,强塑积为20.4GPa。
实施例2
本实施例的高强塑积,高可镀性细晶热镀锌DP钢,其化学成分为:C为0.09wt.%,Mn为2.0wt.%,Si为<0.005wt.%,Al为0.33wt.%,P为0.07wt.%,Ni为0.03wt.%,Nb为0.05wt.%,S为≤0.005wt.%,余量为Fe
本实施例的高强塑积、高可镀性细晶热镀锌DP钢的生产方法按照以下步骤进行:
(1)按照质量百分比:C 0.09%,Mn 2.0%,Si<0.005%,Al 0.33%,P 0.07%,Ni0.03%,Nb 0.05%,S<0.005%,余量为Fe的设定成分来冶炼钢水,在真空感应炉中浇铸成65Kg铸坯,将铸坯切头去尾加热至1250℃等温2.5h,在此温度下锻造成截面为66mm×66mm的矩形坯料,然后用锯床加工成66mm×66mm×80mm的矩形坯用于热轧。第一阶段在奥氏体再结晶区进行热轧,开轧温度为1080℃,终轧温度为1000℃,压下分配为66~40~30mm。第二阶段为两相区轧制,开轧温度为850℃,终轧温度为780℃,压下分配为30~16~10~7~5~4.5mm,然后层流快速冷却到350℃进行卷曲,得到热轧板。
(2)热轧板酸洗后进行10个道次的冷轧,控制压下量在73%,得到冷轧板。
(3)将冷轧板以70℃/s的加热速率加热到780℃,等温1.5min后快速冷却到465℃,立即进入锌锅进行热浸镀锌并保持8s,锌锅温度为462℃,其中退火炉内保护气氛的体积分数为10%H2+90%N2,露点为-30℃,锌锅中Al含量为0.2%。之后以12℃/s的冷速冷却到室温。得到的热浸镀锌板表面平整,无漏镀和镀锌不均匀处,基板由铁素体和马氏组成,铁素体平均晶粒尺寸3.5μm(图3),强塑积为20.9GPa。
实施例3
本实施例的高强塑积,高可镀性细晶热镀锌DP钢,其化学成分为:C为0.12wt.%,Mn为2.3wt.%,Si为<0.005wt.%,Al为0.37wt.%,P为0.06wt.%,Ni为0.02wt.%,Nb为0.04wt.%,S为≤0.005wt.%,余量为Fe
本实施例的高强塑积、高可镀性细晶热镀锌DP钢的生产方法按照以下步骤进行:
(1)按照质量百分比:C 0.12%,Mn 2.3%,Si<0.005%,Al 0.37%,P 0.06%,Ni0.02%,Nb 0.04%,S<0.005%,余量为Fe的设定成分来冶炼钢水,在真空感应炉中浇铸成65Kg铸坯,将铸坯切头去尾加热至1270℃等温2.3h,在此温度下锻造成截面为60mm×60mm的矩形坯料,然后用锯床加工成60mm×60mm×80mm的矩形坯用于热轧。第一阶段在奥氏体再结晶区进行热轧,开轧温度为1070℃,终轧温度为980℃,压下分配为60→36→22mm。第二阶段为两相区轧制,开轧温度为860℃,终轧温度为790℃,压下分配为22→15→10→7→5→4.3,然后层流快速冷却到300℃进行卷曲,得到热轧板。
(2)热轧板酸洗后进行8个道次的冷轧,控制压下量在76%,得到冷轧板。
(3)将冷轧板以65℃/s的加热速率加热到780℃,等温2min后快速冷却到468℃,立即进入锌锅进行热浸镀锌并保持12s,锌锅温度为465℃,其中退火炉内保护气氛的体积分数为10%H2+90%N2,露点为-30℃,锌锅中Al含量为0.2%。之后以15℃/s的冷速冷却到室温。得到的热浸镀锌板表面平整,无漏镀和镀锌不均匀处,基板由铁素体和马氏组成,铁素体平均晶粒尺寸4μm(图4),强塑积为20.6GPa。
Claims (6)
1.一种高强塑积、高可镀性细晶热镀锌双相钢的生产方法,其特征在于按照以下步骤进行:
(1)按照化学成分及百分含量为:C为0.08~0.12wt.%,Mn为1.8~2.5wt.%,Si为<0.005wt.%,Al为0.3~0.5wt.%,P为0.04~0.08wt.%,Nb为0.03~0.06wt.%,Ni为0.02~0.05wt.%,S为≤0.005wt.%,余量为Fe的设定成分冶炼钢水,浇铸成铸坯后,加热至1200~1300℃,等温2~3h,然后锻成方坯用于热轧;轧制完成后快速冷却到250~350℃温度以下进行卷曲,得到热轧板;
(2)热轧板酸洗后进行多道次冷轧,控制压下量为70%~85%,得到冷轧板;
(3)热镀锌退火工艺为:将冷轧板以50~80℃/s的加热速率升温到750~800℃等温1~2min后快速冷却到460~470℃,快冷速率为50~80℃/s,最后进入锌锅进行热浸镀锌5~10s,最后以10~15℃/s的冷速冷却到室温。
2.根据权利要求1所述的高强塑积、高可镀性细晶热镀锌双相钢的生产方法,其特征在于:热轧分为两个阶段:第一阶段在奥氏体再结晶区轧制;开轧温度为1050~1100℃,终轧温度为950~1000℃,压下量为50%~65%;第二阶段为两相区热轧,开轧温度为850~880℃,终轧温度为770~800℃,压下量为80%~90%。
3.根据权利要求1所述的高强塑积、高可镀性细晶热镀锌双相钢的生产方法,其特征在于:退火炉内保护气氛的体积分数为10%H2+90%N2,露点为-30℃,锌锅中Al含量为0.2%。
4.根据权利要求1所述的高强塑积、高可镀性细晶热镀锌双相钢的生产方法,其特征在于:锌锅温度为450-470℃。
5.根据权利要求1所述的高强塑积、高可镀性细晶热镀锌双相钢的生产方法,其特征在于:冷轧5-12道次。
6.根据权利要求2~5任意一项所述生产方法得到的高强塑积、高可镀性细晶热镀锌双相钢,其特征在于:得到的镀锌板表面平整,无漏镀或镀锌不均匀处,基板由铁素体和马氏体 组成,镀锌板的强塑积超过20GPa,铁素体平均晶粒尺寸<4μm。
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