CN116043119B - 易焊接超高扩孔性能800MPa级热镀锌复相钢及制备方法 - Google Patents
易焊接超高扩孔性能800MPa级热镀锌复相钢及制备方法 Download PDFInfo
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Abstract
本发明涉及一种易焊接超高扩孔性能800MPa级热镀锌复相钢及制备方法,钢中化学成分为C:0.06%~0.10%,Si:0.10%~0.30%,Mn:1.40%~2.00%,Cr:0.30%~0.60%,Mo:0.30%~0.60%,Nb:0.025%~0.035%,Ti:0.005%~0.015%,Cu:0.30%~0.55%,B:30~50ppm,P≤0.015%,S≤0.005%,C+Mn/6≤0.40%,余量为Fe和杂质。通过调控热轧组织形态配合连续镀锌退火工艺,实现复相钢的高成型性;通过成分设计和组织调控,实现复相钢良好的扩孔性能和焊接性能;通过对生产工艺的整体调控,实现优异的表面质量。
Description
技术领域
本发明涉及汽车用钢制造技术领域,尤其涉及一种新能源汽车用易焊接超高扩孔性能800MPa级热镀锌复相钢及制备方法。
背景技术
汽车的燃油消耗与车身重量密切相关,研究表明,汽车重量每减轻10%,燃油消耗将降低6%~10%,排放量降低4%。针对这一问题,国际钢铁协会组织开展了超轻钢车身项目的研究,在完成该项目后又开展了一项被称为先进概念车超轻钢车身计划,其主要内容为先进高强钢的开发与应用。根据国际钢铁协会发布的第五版先进高强钢应用指南,先进高强钢通常指的是屈服强度超过550MPa的高强钢,抗拉强度超过780MPa的钢有时也被称为超高强度钢。
复相钢作为第一代先进高强钢的一种,其显微组织为铁素体与贝氏体,可能含有马氏体与奥氏体,通过马氏体和贝氏体以及析出强化的复合作用,有些复相钢的强度可达800MPa以上。由于复相钢具有良好的冲压翻边性能及较好的强度与塑性,适应于汽车零部件成型工艺中的辊压成型,目前在汽车产业中得到了较为广泛的应用。但是,针对一些复杂结构的汽车零件,复相钢在疲劳性能、折弯性能等性能指标方面的表现尚不理想,因此,针对800MPa级复相钢疲劳性能和折弯性能进一步升级的研究具有重要的意义和应用价值。
公开号为CN111926247 A的中国专利申请公开了“一种抗拉强度800MPa级热镀锌复相钢及其制备方法”。其退火温度在760~840℃,过时效温度为450~470℃,过时效时间为10~20s。热处理后得到钢板屈服强度≥660MPa,抗拉强度≥800MPa。但其未涉及合金化改进,产品扩孔性能相对不足。
公开号为CN113481436 A的中国专利申请公开了“一种800MPa级热轧复相钢及其生产方法”。其成品钢板的抗拉强度性能≥800MPa,厚度为2.0~5.0mm,但未涉及冷轧板产品。
公开号为CN111041345 A的中国专利申请公开了“一种800MPa级含钒低碳贝氏体复相钢及其生产方法”。其成品钢板的屈服强度≥700MPa,抗拉强度性能≥800MPa,-20℃纵向冲击功≥120J,组织为多边形铁素体和粒状贝氏体。但其产品为热轧产品,并且未提及产品的扩孔性能。
发明内容
本发明提供了一种易焊接超高扩孔性能800MPa级热镀锌复相钢及制备方法,通过调控热轧组织形态配合连续镀锌退火工艺,实现复相钢的高成型性;通过成分设计和组织调控,实现复相钢良好的扩孔性能和焊接性能;通过对生产工艺的整体调控,实现复相钢优异的表面质量。
为了达到上述目的,本发明采用以下技术方案实现:
一种易焊接超高扩孔性能800MPa级热镀锌复相钢,钢中化学成分以质量百分比计为C:0.06%~0.10%,Si:0.10%~0.30%,Mn:1.40%~2.00%,Cr:0.30%~0.60%,Mo:0.30%~0.60%,Nb:0.025%~0.035%,Ti:0.005%~0.015%,Cu:0.30%~0.55%,B:30~50ppm,P≤0.015%,S≤0.005%,C+Mn/6≤0.40%,余量为Fe和不可避免的杂质。
进一步的,成品钢板的组织包括临界区铁素体、外延铁素体、贝氏体、板条马氏体及孪晶马氏体;其中以体积含量计,临界区铁素体含量为10%~20%,外延铁素体含量为5%~10%,贝氏体含量为45%~65%,板条马氏体含量为15%~25%,孪晶马氏体含量为3%~8%;组织中Cu析出尺寸为5~15nm,Nb析出尺寸为15~25nm,Ti析出尺寸为20~30nm。
进一步的,成品钢板的抗拉强度为800MPa以上,屈服强度为660~750MPa,延伸率≥15%,扩孔率≥80%;点焊电流窗口≥2.5kA。
进一步的,成品钢板镀层中Fe含量为8%~10.5%,镀层硬度为300~400HV。
一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,包括连铸、热轧、酸洗、冷轧、连退镀锌工序,具体过程如下:
1)连铸;连铸拉速为0.6~0.9m/min;
2)热轧;
①加热温度为1180~1220℃,在炉时间为180~240小时;
②开轧温度为1060~1150℃,终轧温度为850~920℃,采用两阶段轧制;
③卷取温度为450~490℃;
3)酸洗;
4)冷轧;冷轧压下率为40%~58%;
5)连退镀锌;
①加热等温温度为740~790℃,等温时间为10~80s;
②缓冷温度为720~750℃,缓冷冷速控制在1~4℃/s;
③钢板以不小于30℃/s的冷速冷却至350~470℃,等温时间为15~40s;
④钢板以大于2℃/s的冷速降至室温;然后进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%。
进一步的,所述连退镀锌过程中的步骤④由以下过程代替:钢板先以大于2℃/s的加热速度升温至480~630℃,等温5~25s,进行合金化退火;再以大于2℃/s的冷速降至室温;最后钢板进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%。
进一步的,所述连铸过程中,铸坯厚度为260~280mm,热轧钢板厚度为3.2~4.0mm。
进一步的,所述连退镀锌过程中,露点温度为-10~0℃,镀锌阶段炉内气氛中H2含量为5%~10%。
与现有技术相比,本发明的有益效果是:
(1)本发明的钢材化学成分主要以C、Mn为主要元素,不添加Ni、V等贵重合金,合金成本较低;同时C含量低于0.1%,保证良好的焊接性能;
(2)钢板组织分布更加均匀且有效减小了组织中各相的硬度差,有效提高了钢板的成型性能;
(3)通过化学成分设计以与工艺相结合,使钢板具有良好的成形性,特别是超高扩孔性能。
附图说明
图1是本发明实施例1所制备钢板的SEM组织照片。
具体实施方式
本发明所述一种易焊接超高扩孔性能800MPa级热镀锌复相钢,钢中化学成分以质量百分比计为C:0.06%~0.10%,Si:0.10%~0.30%,Mn:1.40%~2.00%,Cr:0.30%~0.60%,Mo:0.30%~0.60%,Nb:0.025%~0.035%,Ti:0.005%~0.015%,Cu:0.30%~0.55%,B:30~50ppm,P≤0.015%,S≤0.005%,C+Mn/6≤0.40%,余量为Fe和不可避免的杂质。
进一步的,成品钢板的组织包括临界区铁素体、外延铁素体、贝氏体、板条马氏体及孪晶马氏体;其中以体积含量计,临界区铁素体含量为10%~20%,外延铁素体含量为5%~10%,贝氏体含量为45%~65%,板条马氏体含量为15%~25%,孪晶马氏体含量为3%~8%;组织中Cu析出尺寸为5~15nm,Nb析出尺寸为15~25nm,Ti析出尺寸为20~30nm。
进一步的,成品钢板的抗拉强度为800MPa以上,屈服强度为660~750MPa,延伸率≥15%,扩孔率≥80%;点焊电流窗口≥2.5kA。
进一步的,成品钢板镀层中Fe含量为8%~10.5%,镀层硬度为300~400HV。
本发明所述一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,包括连铸、热轧、酸洗、冷轧、连退镀锌工序,具体过程如下:
1)连铸;连铸拉速为0.6~0.9m/min;
2)热轧;
①加热温度为1180~1220℃,在炉时间为180~240小时;
②开轧温度为1060~1150℃,终轧温度为850~920℃,采用两阶段轧制;
③卷取温度为450~490℃;
3)酸洗;
4)冷轧;冷轧压下率为40%~58%;
5)连退镀锌;
①加热等温温度为740~790℃,等温时间为10~80s;
②缓冷温度为720~750℃,缓冷冷速控制在1~4℃/s;
③钢板以不小于30℃/s的冷速冷却至350~470℃,等温时间为15~40s;
④钢板以大于2℃/s的冷速降至室温;然后进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%。
进一步的,所述连退镀锌过程中的步骤④由以下过程代替:钢板先以大于2℃/s的加热速度升温至480~630℃,等温5~25s,进行合金化退火;再以大于2℃/s的冷速降至室温;最后钢板进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%。
进一步的,所述连铸过程中,铸坯厚度为260~280mm,热轧钢板厚度为3.2~4.0mm。
进一步的,所述连退镀锌过程中,露点温度为-10~0℃,镀锌阶段炉内气氛中H2含量为5%~10%。
本发明所述一种易焊接超高扩孔性能800MPa级热镀锌复相钢的化学成分设计的理由如下:
C::C是高强钢中必须的强化元素,其作用是决定临界区等温奥氏体化状态,同时保证钢板强度。在本发明中,C直接关系钢板组织中贝氏体、板条马氏体及孪晶马氏体的含量及C含量,进而影响钢板的扩孔性能;更重要的是,C与Mn的复合添加直接影响钢板的焊接性能,因此本发明严格限制C含量范围。
Mn:Mn是高强钢中强化元素,其作用是保证临界区奥氏体稳定化,保证临界冷速,防止珠光体转变,保证钢板淬透性,进而保证马氏体含量及强度。在本发明中,C与Mn的复合添加直接影响钢板的焊接性能,因此本发明严格限制Mn含量范围。
C+Mn/6:在本发明中,C与Mn的复合添加直接影响钢板的焊接性能,而本发明的主要技术效果之一就是钢的易焊接性能,因此本发明严格限定了C+Mn/6的范围。
Cr:Cr是高强钢中强化元素,与Mn的作用相似,其作用是促进临界区奥氏体稳定化,保证临界冷速,防止珠光体转变;保证钢板淬透性进而促进马氏体形成,对强度贡献明显。在本发明中,添加Cr的额外技术效果在于替代一部分Mn,进而有效解决C或Mn对钢板焊接性能的影响。
Mo:Mo是高强钢中强化元素,与Mn、Cr作用相似,其作用是促进临界区奥氏体稳定化,保证临界冷速,防止珠光体转变,保证钢板淬透性进而促进马氏体形成,对强度贡献明显。在本发明中,添加Mo的额外技术效果在于替代一部分Mn,进而有效解决C或Mn对钢板焊接性能的影响。
Si:Si元素是铁素体强化元素,其作用是提高钢板强度,抑制碳化物的析出。在本发明中,严格控制Si含量,防止因Si引起的漏镀现象。
B:B是保证临界区转变的关键元素,在本发明中,B主要控制马氏体含量及马氏体类型、C含量,过低的B会导致马氏体含量减少,过高的B则会导致板条马氏体和孪晶马氏体的比例及C含量改变。
Cu:Cu元素在钢中以单质的形式析出,起到强化基体作用,在本发明中,添加Cu配合卷取及镀锌温度的设计,充分发挥了Cu析出的良好效果。
Nb:Nb元素可以与C、N等元素形成Nb析出,促进拖拽作用及热轧阶段应变诱导析出,钉扎晶界细化原奥氏体晶粒,进而细化最终组织晶粒;在本发明中的额外作用是加速贝氏体相变,有利于提高钢板的成形性能,因此Nb元素的含量需控制在合适的范围。
Ti:Ti可以捕捉钢中游离的N原子,起到固N的作用。同时TiN可在凝固过程中析出,起到钉扎晶界的作用,钉扎原奥氏体晶界能够细化原奥氏体晶粒。同时少量Ti在连续退火阶段析出,能够起到强化铁素体、贝氏体的作用,但添加过多的Ti效果有限且会增加成本,因此Ti含量需控制在合适的范围内。
P:P元素是钢中的有害元素,其含量越低越好。综合考虑成本,本发明将P元素含量控制在0.015%以下。
S:S元素是钢中的有害元素,其含量越低越好。综合考虑成本,本发明将S元素含量控制在0.005%以下。
本发明所述一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,包括连铸、热轧、酸洗、冷轧、连退镀锌等一系列工序,具体步骤如下:
1、连铸:连铸拉速为0.6~0.9m/min,铸坯厚度为260~280mm。
2、热轧:
①加热温度控制在1180~1220℃,在炉时间为180~240小时;该阶段促进Ti原子析出行为,对钢板起到良好的固N效果,同时保证Ti析出,起到钉扎原奥氏体晶界、细化原奥氏体晶粒的作用,保证Ti析出尺寸在20~30nm。温度过高将导致Ti析出粗化。
②开轧温度控制在1060~1150℃,终轧温度控制在850~920℃,采用两阶段轧制。
开轧温度配合Nb析出进行设计,在该阶段动态再结晶的基础上以应变诱导析出的方式促进Nb析出,保证原始奥氏体晶粒尺寸为8.5~10μm;终轧温度设计原则是:防止温度过高导致冷却阶段过冷度大使贝氏体等硬相组织产生,防止温度过低先共析铁素体形成。
③卷取温度为450~490℃,目的是得到足够量的贝氏体,保证贝氏体和马氏体含量大于40%,有利于后续连续退火过程中细化晶粒;热轧钢板厚度控制在3.2~4.0mm。
3、酸洗:目的是去除热轧钢板表面所生成的氧化铁皮,保证冷轧钢板的表面质量。
4、冷轧:冷轧压下率为40%~58%,压下率控制在40%以上的目的是促进冷轧态组织纤维化;而冷轧压下率大于58%会导致变形抗力过大,难以轧制到目标厚度。
5、连退镀锌:露点温度为-10~0℃,镀锌阶段炉内气氛中H2含量为5%~10%。
①钢板加热等温温度控制在740~790℃,等温时间控制在10~80s。采取较低的加热温度,目的在于保证钢板的奥氏体化程度,额外的技术效果是促进该阶段Cu以单质形式析出,起到强化基体的作用,并直接影响强度。等温时间过低,会导致奥氏体形核不充分,组织中存在条带状分布;等温时间过高,会导致奥氏体粗化。该阶段通过温度、时间配合,保证奥氏体行为的基础上最大程度促进Cu析出行为。此外,控制临界区铁素体含量为10%~20%。
②钢板缓冷温度为720~750℃,缓冷冷速控制在1~4℃/s;控制外延铁素体含量为5%~10%。
③缓冷后的钢板以不小于30℃/s的冷速冷却至350~470℃,等温时间为15~40s。冷却速度的确定原则是:要防止低温阶段额外的外延铁素体形成,保证该阶段过冷奥氏体状态及C分布。温度过低则过冷奥氏体会发生马氏体相变,温度过高则C浓度梯度改变,不能保证组织中贝氏体含量为45%~65%,板条马氏体含量为15%~25%,孪晶马氏体含量为3%~8%。
④钢板以大于2℃/s的冷速降至室温;保证该阶段马氏体转变行为,板条马氏体含量为15%~25%,孪晶马氏体含量为3%~8%。然后,钢板进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%,以满足屈服强度的要求。
连退镀锌过程中的步骤④可以由以下过程代替:钢板先以大于2℃/s的加热速度升温至480~630℃,等温5~25s,该阶段进行合金化退火,通过温度与时间配合,保证镀层中Fe含量在8%~10.5%,满足镀层硬度为300~400HV的要求。然后钢板再以大于2℃/s的冷速降至室温;保证该阶段马氏体转变行为,板条马氏体含量为15%~25%,孪晶马氏体含量为3%~8%。最后钢板进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%,以满足屈服强度的要求。
为使本发明实施例的目的、技术方案和技术效果更加清楚,现对本发明实施例中的技术方案进行清楚、完整地描述。但以下所描述的实施例仅是本发明一部分实施例,而不是全部的实施例。结合本发明中的实施例,本领域普通技术人员在没有做出创造性劳动前提下所获得的所有其它实施例,都属于本发明保护的范围。
【实施例】
各实施例钢的化学成分及焊接电流窗口见表1,各实施例连铸和热轧工艺参数见表2,各实施例连退镀锌工艺参数见表3,各实施例成品钢板力学性能见表4。实施例1所制备钢板的SEM组织照片如图1所示。
表1钢的化学成分(wt%)及焊接电流窗口
表2连铸和热轧工艺参数
表3连退镀锌工艺参数
表4钢板力学性能
实施例 | 临界F | 外延F | B | 板条M | 孪晶M | Cu析出尺寸/nm | Ti析出尺寸/nm | Nb析出尺寸/nm | Rp0.2/MPa | Rm/MPa | A80/% | λ/% |
1 | 18.6 | 5.8 | 48.9 | 18.6 | 5.5 | 8.6 | 20.6 | 15.8 | 689 | 820 | 16.7 | 86.5 |
2 | 17.5 | 5.9 | 46.5 | 19.4 | 3.8 | 9.4 | 29.6 | 19.5 | 742 | 835 | 18.5 | 84.4 |
3 | 12.8 | 6.8 | 53.6 | 24.6 | 7.5 | 5.6 | 22.8 | 22.8 | 694 | 802 | 16.8 | 83.6 |
4 | 19.6 | 9.4 | 59.6 | 22.8 | 7.4 | 12.6 | 28.4 | 23.4 | 724 | 835 | 19.7 | 92.5 |
5 | 11.2 | 8.6 | 62.4 | 24.1 | 8 | 11.8 | 29.6 | 19.8 | 748 | 826 | 21.2 | 88.5 |
6 | 16.5 | 8.5 | 53.4 | 19.6 | 7.8 | 13.9 | 22.8 | 16.8 | 672 | 808 | 17.6 | 87.2 |
7 | 12.8 | 7.7 | 55.8 | 15.4 | 5.6 | 12.4 | 28.4 | 17.5 | 668 | 819 | 16.5 | 80.5 |
8 | 11.4 | 7.5 | 51.4 | 18.5 | 3.4 | 8.9 | 29.6 | 22.5 | 705 | 812 | 16.1 | 86.4 |
9 | 10.5 | 5.4 | 49.6 | 22.5 | 5.8 | 9.8 | 25.8 | 24.2 | 738 | 831 | 20.8 | 83.2 |
10 | 10.9 | 5.9 | 46.2 | 21.3 | 6.2 | 13.1 | 27.8 | 23.1 | 722 | 824 | 21.6 | 81.5 |
11 | 11.6 | 6.8 | 48.7 | 24.8 | 7.6 | 14.2 | 22.5 | 18.5 | 741 | 813 | 18.6 | 90.2 |
12 | 18.5 | 6.4 | 49.9 | 20.3 | 7.5 | 5.9 | 24.9 | 19.6 | 666 | 825 | 19.2 | 81.9 |
表4中Rp0.2为屈服强度,Rm为抗拉强度,A80为延伸率,λ为扩孔率。
由上述实施例可以得出结论,通过本发明低成本合金设计及配套的工艺设计,所制备的镀锌钢板抗拉强度在800MPa以上,屈服强度为660~750MPa,延伸率在15%以上,扩孔率在80%以上,符合易焊接高扩孔的性能指标。
以上所述,仅为本发明较佳的具体实施方式,但本发明的保护范围并不局限于此,任何熟悉本技术领域的技术人员在本发明揭露的技术范围内,根据本发明的技术方案及其发明构思加以等同替换或改变,都应涵盖在本发明的保护范围之内。
Claims (5)
1.一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,其特征在于,钢中化学成分以质量百分比计为C:0.06%~0.10%,Si:0.10%~0.30%,Mn:1.40%~2.00%,Cr:0.30%~0.60%,Mo:0.30%~0.60%,Nb:0.025%~0.035%,Ti:0.005%~0.015%,Cu:0.30%~0.55%,B:30~50ppm,P≤0.015%,S≤0.005%,C+Mn/6≤0.40%,余量为Fe和不可避免的杂质;成品钢板的组织包括临界区铁素体、外延铁素体、贝氏体、板条马氏体及孪晶马氏体;其中以体积含量计,临界区铁素体含量为10%~20%,外延铁素体含量为5%~10%,贝氏体含量为45%~65%,板条马氏体含量为15%~25%,孪晶马氏体含量为3%~8%;组织中Cu析出尺寸为5~15nm,Nb析出尺寸为15~25nm,Ti析出尺寸为20~30nm;成品钢板的抗拉强度为800MPa以上,屈服强度为660~750MPa,延伸率≥15%,扩孔率≥80%;
所述易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,包括连铸、热轧、酸洗、冷轧、连退镀锌工序,具体过程如下:
1)连铸;连铸拉速为0.6~0.9m/min;
2)热轧;
① 加热温度为1180~1220℃,在炉时间为180~240小时;
② 开轧温度为1060~1150℃,终轧温度为850~920℃,采用两阶段轧制;
③ 卷取温度为450~490℃;
3)酸洗;
4)冷轧;冷轧压下率为40%~58%;
5)连退镀锌;
① 加热等温温度为740~790℃,等温时间为10~80s;
② 缓冷温度为720~750℃,缓冷冷速控制在1~4℃/s;
③ 钢板以不小于30℃/s的冷速冷却至350~470℃,等温时间为15~40s;
④ 钢板以大于2℃/s的冷速降至室温;然后进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%。
2.根据权利要求1所述的一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,其特征在于,成品钢板镀层中Fe含量为8%~10.5%,镀层硬度为300~400HV。
3.根据权利要求1所述的一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,其特征在于,所述连退镀锌过程中的步骤④由以下过程代替:钢板先以大于2℃/s的加热速度升温至480~630℃,等温5~25s,进行合金化退火;再以大于2℃/s的冷速降至室温;最后钢板进入光整机进行板形调整,光整延伸率控制在0.2%~0.4%。
4.根据权利要求1所述的一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,其特征在于,所述连铸过程中,铸坯厚度为260~280mm,热轧钢板厚度为3.2~4.0mm。
5.根据权利要求1或3所述的一种易焊接超高扩孔性能800MPa级热镀锌复相钢的制备方法,其特征在于,所述连退镀锌过程中,露点温度为-10~0℃,镀锌阶段炉内气氛中H2含量为5%~10%。
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CN113416889A (zh) * | 2021-05-21 | 2021-09-21 | 鞍钢股份有限公司 | 焊接性能良好超高强热镀锌dh1470钢及制备方法 |
CN113416888A (zh) * | 2021-05-21 | 2021-09-21 | 鞍钢股份有限公司 | 高扩孔高塑性980MPa级双相镀锌钢板及其制备方法 |
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