CN116904844A - 一种吉帕级冷基镀锌高强钢及其制备方法 - Google Patents

一种吉帕级冷基镀锌高强钢及其制备方法 Download PDF

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CN116904844A
CN116904844A CN202310704204.2A CN202310704204A CN116904844A CN 116904844 A CN116904844 A CN 116904844A CN 202310704204 A CN202310704204 A CN 202310704204A CN 116904844 A CN116904844 A CN 116904844A
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strength steel
temperature
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rolling
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薛仁杰
王立辉
赵林林
刘自权
曹晓恩
刘鹏
董伊康
张青
佘亚东
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Hebei Dahe Material Technology Co ltd
HBIS Co Ltd
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HBIS Co Ltd
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Abstract

一种吉帕级冷基镀锌高强钢及其制备方法，属于金属材料加工技术领域。其化学成分为C：0.08～0.16%，Mn：1.0～2.0%，Si：0.4～0.8%，Al：0.6～1.0%，Cr：0.4～0.8%，Mo：0.06～0.13%，Nb：0.02～0.04%，Ti：0.02～0.08%，P≤0.015%，S≤0.006%，其余为Fe和不可避免的杂质；其制备方法包括冶炼及连铸、热轧、酸轧、连续镀锌工序。本发明通过析出强化、细晶强化、固溶强化与控轧控冷技术相结合获得了马氏体、铁素体、贝氏体与残余奥氏体相匹配的组织构成，镀锌高强钢性能优异，具有较低液态金属脆化敏感性。

Description

一种吉帕级冷基镀锌高强钢及其制备方法
技术领域
本发明属于金属材料加工技术领域，具体涉及一种吉帕级冷基镀锌高强钢及其制备方法。
背景技术
随着汽车轻量化的发展，传统双相钢难以满足更多高拉延需求。TRIP钢与QP钢虽具有良好的强塑性，但均因焊接性能差、生产成本高而限制了其广泛使用。DH钢在传统双相钢两相的基础上引入残余奥氏体，强塑性得到明显提升，具有更好的应用前景。同时为了提高材料及其耐蚀性，镀锌双相钢具有明显的优势。镀锌吉帕级双相钢一般常用于前后防撞梁、前后纵梁等安全件，在汽车制造过程中需要烤漆与焊接处理，从而提高整车安全性与使用寿命。同时镀锌高强钢焊接过程中极易产生液态金属脆（liquid metal embrittlement，LME）现象，降低高强钢镀锌板材的力学性能。因此开发出具有低液态金属脆化敏感性与高塑性吉帕级高强钢产品具有很大实际应用意义。
中国专利CN107058869B公开了超低屈强比980MPa级冷轧双相钢及其制造方法，该双相钢成分设计上采用低C无Al基础成分体系，但其塑性低在实际应用中极易出现冲压开裂等成形问题。
中国专利CN107058895A公开了一种1000MPa级热镀锌双相钢及其制备方法，然而该产品延展性能较差，断后伸长率仅有13%上下，在实际应用过程中难以满足复杂零部件冲压等需求，且容易出现液态金属脆性问题。
中国专利CN114480957A公开了一种成形性好的980MPa级热镀锌双相钢及其制造方法，该双相钢由于含Si元素较高，极易恶化镀层涂覆性，且更易出现液态金属脆性问题，难以保证材料焊接成形过程中不出现开裂问题。
中国专利CN114032457A公开了一种连续热浸镀锌高强钢板及其制造方法，其制备了具有低液态金属脆性的镀锌高强钢，但其碳含量相对较高，不利于后续焊接加工。同时冷轧后需经热处理过程露点过高，表层在获取脱碳层极易发生表层元素富集从而导致由于锌湿润性、锌结合力和漏镀点等相关的质量问题。
发明内容
为解决上述技术问题，本发明提供一种吉帕级冷基镀锌高强钢及其制备方法，其技术方案是：
一种吉帕级冷基镀锌高强钢，所述高强钢化学成分及质量百分含量为C：0.08～0.16%，Mn：1.0～2.0%，Si：0.4～0.8%，Al：0.6～1.0%，Cr：0.4～0.8%，Mo：0.06～0.13%，Nb：0.02～0.04%，Ti：0.02～0.08%，P≤0.015%，S≤0.006%，其余为Fe和不可避免的杂质。
进一步的，所述高强钢的微观组织中按体积百分比计，铁素体25～42%，马氏体40%～65%，贝氏体5～10%，残余奥氏体2～10%。
进一步的，所述高强钢的表层还包括厚度5～12μm的锌镀层，锌镀层的化学成分按重量含量计包括Al：0.3～0.8%，Si：0.5～1.0%，Ce：0.01～0.1%，La：0.01～0.05%，Yr:0.01～0.08%，且0.5≤La/Ce≤1.2，其余为Zn和不可避免的杂质。
进一步的，成品钢抗拉强度≥1000MPa，屈服强度≥550MPa，纵向断后伸长率A80≥17.0%，扩孔率≥60%。
本发明成分设计理由如下：
碳(C)：可以提高材料淬透性，还具有固溶强化作用，提升材料强度。同时还有助于奥氏体的稳定性的提高，提高材料成形性。另一方面C过高会造成材料脆化恶化材料焊接性。从以上角度出发，C的成分范围为0.08～0.16%。
锰(Mn)：作为扩大奥氏体相区元素，可以提高奥氏体的稳定性。同时还可以细化晶粒，提高材料淬透性。Mn含量过低会导致材料强度不足，奥氏体稳定性降低。当Mn含量过高时，组织中的偏析现象显著，材料塑性恶化，增加Mn含量会加重钢表层的内氧化层的形成，提高材料LME的敏感性。
Si：作为铁素体强化元素，可以抑制碳化物析出与渗碳体形成，同时还具有固溶强化作用。Si过高会导致材料塑性的降低与焊接性的降低，同时还会恶化镀层的涂覆性，增加镀锌高强钢的LME 敏感性。从上述角度出发，Si的含量为0.4～0.8%；高的Si含量会增加高强钢的LME敏感性。
铝(Al)：作为Si的互补元素，也具有抑制碳化物析出与渗碳体形成的作用，同时还可以改善材料的可镀性，提高镀层质量。Al元素含量过高，不仅会导致连铸生产困难还会造成焊接困难。因此，本发明中将Al元素含量的范围控制在0.6%～1.0%。
铬(Cr)：作为淬透性元素，可以稳定奥氏体，有助于实现马氏体和奥氏体组织的调节，实现材料的延展性。然而过高的Cr会导致碳化物恶化性能与镀层质量，提高了材料LME敏感性。从上述角度出发Cr的含量设为0.4～0.8%。
Mo：有助于稳定残余奥氏体和提高钢的淬透性，同时还有助于贝氏体组织的形成。但Mo元素成本较高，故本发明Mo元素含量范围控制在0.06～0.13%之间。
Nb与Ti：二者具有显著的细晶强化、固溶强化、析出强化作用，且Nb还可以提高材料奥氏体再结晶温度，有助于各相比例的调控。同时二者还可以形成稳定的碳化物，实现材料中自由碳与固溶碳的有效调控。从上述角度出发Ti的含量设为0.02～0.08%，Nb含量设为0.02～0.04%。
P和S：作为杂质元素，其中P元素固溶存在于铁素体，易发生二次冷加工脆性，因此P元素含量越低越好；而S元素则会与Mn元素发生相互作用形成MnS，对材料的扩孔性能和热加工性均有负面影响，故S元素的含量也是越低越好，在本发明中将P含量上限设定为0.015%，S含量上限设定为0.006%。
上述吉帕级冷基镀锌高强钢的制备方法包括冶炼及连铸、热轧、酸轧、连续镀锌工序；
冶炼及连铸工序：根据化学成分要求冶炼，然后进行连铸制备板坯；
热轧工序：精轧开始温度1050～1095℃，边部温度补偿30～60℃，终轧温度870～910℃；
酸轧工序：冷轧压下率50～75%，轧机F4机架轧辊粗糙度Ra为1.0～1.5μm，换辊公里≤300km；F5机架毛化辊粗糙度Ra为3.0～3.6μm，辊面Pc值≥75个/cm，辊面镀铬层10～20μm，压下率1～7%，F5换辊公里≤100km；
连续镀锌工序：预氧化段露点温度-20～-5℃，时间10～30s，其氧含量为6～15*103ppm；均热温度800～850℃，均热时间100～200s，均热段露点温度-45～-20℃；缓冷温度为650～700℃；快冷温度440～470℃，快冷冷却速率20～40℃/s，入锌锅板带温度=锌锅温度+0～5℃。
进一步的，所述热轧工序，在1190～1255℃温度条件下保温200～300min，之后进行3+1道次粗轧，并进行7道次精轧。轧制结束后层冷段采用后段水冷至500～600℃进行卷取，之后挡风墙放置≥72h。
进一步的，所述酸轧工序，酸洗温度80℃～90℃，酸液浓度150～200g/L。
进一步的，所述连续镀锌工序，锌锅温度440～470℃，炉鼻子露点温度-30～-10℃；镀后冷却塔温度150～200℃，板带再以10～15℃/s冷却速率冷却至室温。
进一步的，所述连续镀锌工序，光整延伸率0.3～0.8%。
本发明工艺设计的理由：
1、通过成分的控制，特别是钢体与镀层成分的合理调配，提高了镀层高温结合力，Ce、La、Yr加入降低了镀层高温脆性，从而有利于降低材料的液态金属脆性。
2、通过毛化辊粗糙度与峰值密度的控制，有利于基体表层在预氧化段形成理想的脱碳层，从而抑制表层奥氏体的形成，同时还有助于增强镀层的结合力，有利于后期材料成形性的提高。入锌锅板带温度不低于锌液温度，有利于Fe2Al5抑制层的形成，提高镀层结合力与改善板带表面质量。
3、通过温度及冷速的合理控制，实现了各相比例及尺寸分布；通过细晶强化、固溶强化和析出强化实现了材料强塑性提升。
4、在铁素体、马氏体基础上引入一定量的残余奥氏体与贝氏体的组织构成，从而通过提高材料的综合性能。
采用上述技术方案所产生的有益效果在于：（1）本发明通过合理设计钢基及镀层成分与工艺，通过细晶强化、固溶强化、析出强化提高了材料强塑性，本发明高强钢的微观组织主要为铁素体、马氏体、贝氏体、残余奥氏体，按体积百分比计，其中铁素体25～42%，马氏体40%～65%，贝氏体5～10%，残余奥氏体2%～10%。通过引入残余奥氏体提高了材料成形性，引入贝氏体提高了材料各相协同变形能力与翻边性，从而解决超高强度级别汽车用钢的成形性能差和延展性能不足等问题；（2）轧制工艺结合镀液成分及镀锌工艺的设计，实现表层组织的细化，避免了表层奥氏体组织的形成，改善了镀层质量，从而提高了材料液态金属脆性。
本发明通过析出强化、细晶强化、固溶强化与控轧控冷技术相结合获得了马氏体、铁素体、贝氏体与残余奥氏体相匹配的组织构成，强塑性得到明显提升，生产的吉帕级冷基镀锌高强钢性能优异，抗拉强度≥1000MPa，屈服强度≥550MPa，纵向断后伸长率A80≥17.0%，扩孔率≥60%，具有较低液态金属脆化敏感性。
附图说明
图1为本发明实施例1镀锌高强钢的显微组织图；
图2为本发明实施例1镀锌高强钢的截面结构示意图；
图3为对比例1镀锌高强钢的截面结构示意图。
实施方式
下面结合实施例对本发明做进一步详细说明。
本发明吉帕级冷基镀锌高强钢的化学成分及质量百分含量为C：0.08～0.16%，Mn：1.0～2.0%，Si：0.4～0.8%，Al：0.6～1.0%，Cr：0.4～0.8%，Mo：0.06～0.13%，Nb：0.02～0.04%，Ti：0.02～0.08%，P≤0.015%，S≤0.006%，其余为Fe和不可避免的杂质。其微观组织按体积百分比计，铁素体25～42%，马氏体40%～65%，贝氏体5～10%，残余奥氏体2～10%。
上述镀锌高强钢锌镀层的厚度5～12μm，锌镀层的化学成分按重量含量计包括Al：0.3～0.8%，Si：0.5～1.0%，Ce：0.01～0.1%，La：0.01～0.05%，Yr:0.01～0.08%，且0.5≤La/Ce≤1.2，其余为Zn和不可避免的杂质。锌镀层成分中Al有助于在基体与镀层间形成Fe2Al5抑制层提高镀层结合力，Si的加入有助于降低材料摩擦系数，提高带钢与锌液的浸润性。Ce与La、Yr加入有利于降低镀层抑制晶间腐蚀，增强合金镀层抗晶间腐蚀能力。Yr还有助于提高镀层延展性，从而降低液态金属脆性改善材料成形性。
上述吉帕级冷基镀锌高强钢的制备方法，包括冶炼、连铸、热轧、酸轧、连续镀锌工序，具备步骤为：
（1）根据化学成分要求冶炼，然后进行连铸制备板坯；
（2）热轧工序：将板坯加热保温、粗轧、精轧、卷取、冷却，获得热轧板带。
（3）酸轧工序：热轧板带经酸洗、冷轧获得具有一定粗糙度的冷硬板带。
（4）连续镀锌工序：冷硬板经预氧化、均热、缓冷及快冷退火、镀后冷却、光整后，获得吉帕级镀锌高强钢。
采用上述成分设计和工艺生产的吉帕级冷基镀锌高强钢性能优异，抗拉强度≥1000MPa，屈服强度≥550MPa，纵向断后伸长率A80≥17.0%，扩孔率≥60%，具有较低液态金属脆化敏感性。
实施例及对比例吉帕级镀锌高强钢的化学成分及重量百分比见表1，热轧、酸轧、连续镀锌工序工艺参数控制见表2-5，镀层成分及厚度见表6。
表1、实施例及对比例吉帕级镀锌高强钢的化学成分组成（wt%）
表2、实施例及对比例热轧工艺参数控制
表3、实施例及对比例酸轧工艺参数控制
表4、实施例及对比例连续镀锌工艺参数控制-1
表5、实施例及对比例连续镀锌工艺参数控制-2
表6、实施例及对比例镀层成分及厚度
实施例和对比例镀锌高强钢基体表层化学成分采用辉光放电光谱方法进行测量，[C]/C、[Mn]/Mn、[Si]/Si和[Cr]/Cr表示镀锌高强钢基体表层的化学成分与所述钢板的化学成分的质量分数比例，如表7所示。实施例的各元素比例明显比对比例元素的比例低，其实施例表层奥氏体化温度将明显高于基体与对比例。
表7、镀锌高强钢基体表层与钢板的化学成分的质量分数比例
将实施例及对比例的吉帕级冷基镀锌高强钢以50℃/s速度加热到1000℃，保温30s，拉伸速率为0.13/s，拉伸变形至15%，然后快速冷却到室温。观察测量镀锌高强钢表层出现的裂纹，测量裂纹的密度，测量裂纹最大深度。实施例和对比例的显微组织、力学性能及裂纹统计如表8所示。
表8、镀锌高强钢的显微组织、力学性能及裂纹统计
表8中，实施例通过合理设计钢基成分与工艺控制，通过细晶强化、固溶强化、析出强化提高了材料强塑性，通过引入残余奥氏体提高了材料成形性，引入贝氏体提高了材料各相协同变形能力与翻边性，从而解决超高强度级别汽车用钢的成形性能差和延展性能不足等问题。从表8中可看出本发明实施例镀锌高强钢的裂纹密度与深度均远小于对比例，对钢基体性能影响不大。实施例1镀锌高强钢的显微组织如图1所示，其和对比例的截面结构示意图如图2和图3所示，由图2、3可以看出，本发明通过控制镀锌高强钢表层的化学成分，与板带入锌液温度，使得表层奥氏体化温度显著升高，有利于抑制层的形成与镀层结合力的提高，从而改善了镀锌高强钢的液态金属脆性，避免了裂纹出现，解决了镀锌高强钢在焊接时钢板表面易出现深裂纹的技术问题。

Claims (10)

1.一种吉帕级冷基镀锌高强钢，其特征在于，所述高强钢化学成分及质量百分含量为C：0.08～0.16%，Mn：1.0～2.0%，Si：0.4～0.8%，Al：0.6～1.0%，Cr：0.4～0.8%，Mo：0.06～0.13%，Nb：0.02～0.04%，Ti：0.02～0.08%，P≤0.015%，S≤0.006%，其余为Fe和不可避免的杂质。
2.根据权利要求1所述的吉帕级冷基镀锌高强钢，其特征在于，所述高强钢的微观组织中按体积百分比计，铁素体25～42%，马氏体40～65%，贝氏体5～10%，残余奥氏体2～10%。
3.根据权利要求1或2所述的吉帕级冷基镀锌高强钢，其特征在于，所述高强钢的表层还包括厚度5～12μm的锌镀层，锌镀层的化学成分按重量含量计包括Al：0.3～0.8%，Si：0.5～1.0%，Ce：0.01～0.1%，La：0.01～0.05%，Yr:0.01～0.08%，且0.5≤La/Ce≤1.2，其余为Zn和不可避免的杂质。
4.根据权利要求1-3任一项所述的吉帕级冷基镀锌高强钢，其特征在于，成品钢抗拉强度≥1000MPa，屈服强度≥550MPa，纵向断后伸长率A80≥17.0%，扩孔率≥60%。
5.基于权利要求1-4任一项所述的吉帕级冷基镀锌高强钢的制备方法，其特征在于，其包括冶炼及连铸、热轧、酸轧、连续镀锌工序；
冶炼及连铸工序：根据化学成分要求冶炼，然后进行连铸制备板坯；
热轧工序：精轧开始温度1050～1095℃，边部温度补偿30～60℃，终轧温度870～910℃；
酸轧工序：冷轧压下率50～75%，轧机F4机架轧辊粗糙度Ra为1.0～1.5μm，换辊公里≤300km；F5机架毛化辊粗糙度Ra为3.0～3.6μm，辊面Pc值≥75个/cm，辊面镀铬层10～20μm，压下率1～7%，F5换辊公里≤100km；
连续镀锌工序：预氧化段露点温度-20～-5℃，时间10～30s，其氧含量为6～15*103ppm；均热温度800～850℃，均热时间100～200s，均热段露点温度-45～-20℃；缓冷温度为650～700℃；快冷温度440～470℃，快冷冷却速率20～40℃/s，入锌液板带温度=锌锅温度+0～5℃。
6.根据权利要求5所述的吉帕级冷基镀锌高强钢的制备方法，其特征在于，所述热轧工序，在1190～1255℃温度条件下保温200～300min，之后进行3+1道次粗轧，并进行7道次精轧。
7.根据权利要求6所述的吉帕级冷基镀锌高强钢的制备方法，其特征在于，所述热轧工序，轧制结束后层冷段采用后段水冷至500～600℃进行卷取，之后挡风墙放置≥72h。
8.根据权利要求7所述的吉帕级冷基镀锌高强钢的制备方法，其特征在于，所述酸轧工序，酸洗温度80～90℃，酸液浓度150～200g/L。
9.根据权利要求8所述的吉帕级冷基镀锌高强钢的制备方法，其特征在于，所述连续镀锌工序，锌锅温度440～470℃，炉鼻子露点温度-30～-10℃；镀后冷却塔温度150～200℃，板带再以10～15℃/s冷却速率冷却至室温。
10.根据权利要求1-9任一项所述的吉帕级冷基镀锌高强钢的制备方法，其特征在于，所述连续镀锌工序，光整延伸率0.3～0.8%。
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