CN116377334B - 超高塑各向同性的980MPa级冷轧高强钢板及其制备方法 - Google Patents
超高塑各向同性的980MPa级冷轧高强钢板及其制备方法 Download PDFInfo
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Abstract
本发明提供了超高塑各向同性的980MPa级冷轧高强钢板及其制备方法,该钢板的成分按重量百分比计如下:C:0.18%~0.24%,Si:0.5%~1.8%,Mn:1.8%~2.4%,Al:0~1.0%,Nb:0~0.03%,Ti:0~0.03%,P≤0.02%,S≤0.01%,余量为Fe和不可避免的杂质。制备方法包括冶炼、铸造、热轧、酸洗、冷轧、连退、光整;应用本发明生产的钢板抗拉强度980MPa以上,屈服强度700~850MPa,强塑积超过34GPa%,横纵向平均强度差异小于10MPa,延伸率差异小于1%。
Description
技术领域
本发明属于金属材料领域,尤其涉及一种超高塑性且各向同性的980MPa级冷轧高强钢及其制备方法。
背景技术
随着全球能源危机和环境恶化的日益加剧,安全、节能和环保已成为汽车制造业的发展潮流。兼具高强度和良好塑性韧性的新型汽车用先进高强钢(AHSS)能够有效实现零件厚度减薄,从而实现汽车减重及节能降耗,受到了钢铁界和汽车界的广泛青睐。然而,随着人们对汽车轻量化和安全性需求的不断提高,商业化冷轧高强钢有限的强塑性能很难满足复杂零部件成形及碰撞的要求,而强塑性能优异的中锰钢等第三代钢种在现有工业产线下面临一系列工艺瓶颈问题,因此开发低成本、高性能的新型先进高强钢成为钢铁和汽车行业的迫切需求。目前,先进高强钢经历了三个阶段的发展,典型钢种有双相钢(Dualphase,DP)、相变诱导塑性钢(Transformation inducedplasticity,TRIP)、淬火配分钢(Quenching and partitioning,Q&P)等。DP钢在980MPa级别的高强钢中应用最广,其延伸率较低约为12%,虽然TRIP钢及Q&P钢的延伸率提高至约20%,但对于一些复杂结构的冷冲压成型零件仍具有难度。此外,由于冷轧带钢在轧制变形过程中组织沿轧制方向呈条带状,能够遗传至产品的最终组织,进而导致产品在不同方向上的性能显现出差异性,给产品制造和应用带来困难。因此亟需开发一种高塑性且各向性能差异小的钢铁材料来应用于较为复杂车身结构件。
公开号为CN104278194A的中国申请专利申请公开了一种高强度高塑性的两步配分Q&P钢板及其制备方法,其化学成分中C含量为0.25~0.35wt%,Si含量0.8~1.2wt%,Al含量0.5~1.0wt%,B含量0.001~0.002wt%。热轧工艺卷取温度为600~650℃,过时效段淬火温度为250~280℃,配分温度为350~400℃。其热处理采用的是两步淬火-配分工艺,未进行实验钢热处理前组织预调控,热处理后所得钢板抗拉强度大于980MPa,延伸率约20%。
在已公开的高强度、高强塑积汽车用钢专利申请中,公开号为CN105018843A的中国申请专利申请公开了一种钒和钛复合添加的Q&P钢及其制造方法,其主要成分的重量百分比为:C:0.17~0.22%、Si:1.3~1.6%、Mn:1.5~2.1%、P≤0.010%、S≤0.008%、V:0.03~0.07%、Ti:0.02~0.04%,余量为Fe和不可避免的杂质。但其热轧工艺卷取温度较低为200℃以下,配分温度较低为170~210℃。抗拉强度1350~1450MPa,延伸率≥15%,强塑积≥22GPa%。
发明内容
本发明的目的在于克服上述问题和不足而提供一种具有力学性能各向同性,强塑积超过34GPa%的超高塑各向同性的980MPa级冷轧高强钢板及其制备方法。
本发明目的是这样实现的:
一种超高塑各向同性的980MPa级冷轧高强钢板,该钢板的成分按重量百分比计如下:C:0.18%~0.24%,Si:0.5%~1.8%,Mn:1.8%~2.4%,Al:0~1.0%,Nb:0~0.03%,Ti:0~0.03%,P≤0.02%,S≤0.01%,余量为Fe和不可避免的杂质。
所述冷轧高强钢板显微组织包括铁素体、贝氏体、残余奥氏体和新鲜马氏体,其中各项显微组织按体积百分比计如下:铁素体10%~40%,贝氏体>30%,残余奥氏体10%~30%,马氏体<20%;优选,所述铁素体是由马氏体基体回火形成的,呈细条状,平均长度小于3μm,平均宽度小于0.5μm;所述且马氏体平均晶粒尺寸小于2μm。
所述冷轧高强钢板抗拉强度980MPa以上,屈服强度700~850MPa,延伸率≥34%,强塑积超过34GPa%,横纵向平均强度差异小于10MPa,延伸率差异小于1%。
本发明成分设计理由如下:
C:C元素是低碳钢传统、经济的强化元素,是稳定奥氏体的主要元素。在一次淬火过程中,C能够提高奥氏体的淬透性,使实验钢得到高位错密度的马氏体。此外,在后续的淬火配分过程,C元素从马氏体向奥氏体中扩散,使得奥氏体更稳定,增加残余奥氏体含量,提高钢的延展性。C元素含量过低会降低制备的钢的强度,同时由于不能稳定足够量的残余奥氏体而导致延伸率下降;但是,C元素含量过高会给冶炼和焊接带来困难。因此,本申请将C元素含量控制在0.2%左右,最优范围为0.18~0.24%。
Si:Si主要起到在配分阶段抑制渗碳体析出的作用,此外Si能够促进铁素体形成,并起到一定的强化铁素体基体的作用。因此,本发明中将Si元素的含量控制为0.5%~1.8%。
Mn:元素为低合金钢的基本组成元素,是奥氏体稳定化元素。Mn元素能显著提高钢的淬透性,在一次淬火过程中,使实验钢得到高位错密度的马氏体。此外,Mn元素有固溶强化和细化铁素体晶粒的作用,能够显著推迟珠光体和贝氏体转变,提高钢的强度。然而,Mn元素含量会提高会增加生成成本,同时使冶炼变得困难。因此,本申请将Mn元素含量控制在1.8~2.4%。
Ti:Ti在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,Ti(C,N)热轧阶段析出起到钉扎原奥氏体晶界,细化原奥氏体晶粒的作用。同时少量Ti析出在连续退火阶段析出,起到强化铁素体、贝氏体的作用,但是过多的Ti析出会占据残余奥氏体保留所需的C原子。因此,本发明中将Ti元素含量控制为0~0.03%。
Nb:Nb对细化晶粒、相变行为、奥氏体中C富集和马氏体形核发挥显著作用。Nb与C和N结合形成细小的碳氮化物,阻止晶粒长大,起到明显强化效果。因此,本申请将Nb元素含量控制在0~0.03%。
Al:Al在传统工艺中是炼钢过程中的脱氧剂,同时,Al还可以有钢中的N结合形成AlN并细化晶粒。但在本发明中加入较多的Al的主要目的为加快冷却过程中奥氏体向铁素体的转变动力学过程,同时同Si一起抑制渗碳体的析出,同时提高奥氏体化温度,便于更好的选取工艺窗口。过少的Al含量对奥氏体化温度影响有限,同时减缓冷却时铁素体的析出速度;而过高的Al含量将造成连铸过程中水口堵塞,影响生产效率。因此,本发明中将Al元素含量的范围控制在0~1.0%。
P:P元素是钢中的有害元素,其含量越低越好。考虑到成本,本发明中将P元素含量控制在P≤0.02%。
S:S元素是钢中的有害元素,其含量越低越好。考虑到成本,本发明中将S元素含量控制在S≤0.01%。
本发明技术方案之二是提供一种超高塑各向同性的980MPa级冷轧高强钢板的制备方法,包括冶炼、铸造、热轧、酸洗、冷轧、连退、光整;
冶炼:
通过转炉进行冶炼,得到上述范围内的合金成分。
热轧:
①加热温度在1200~1270℃之间,保证Ti原子析出行为,对钢板起到良好的固N效果,以及保证Ti(C,N)的析出,起到钉扎原奥氏体晶界,细化原奥氏体晶粒的作用。
②开轧温度在1100~1180℃之间,终轧温度在900℃以上,保证再结晶区的轧制温度,促进原奥氏体晶粒在热轧阶段的动态再结晶行为,细化晶粒。
③卷取温度在650~700℃之间,防止卷取温度过低增大冷轧难度。热轧卷厚度在2.8~4.2mm之间。
酸洗:去除热轧表面所生成的氧化铁皮,保证冷轧钢板表面质量。
冷轧:冷轧压下率为50%~58%,保证冷轧50%以上轧制压下量,促进冷轧组态中的组织纤维化;同时,防止冷轧压下率过高,导致变形抗力过大,难以轧制到目标厚度。
连续退火:
①预淬火:加热温度在(A3+40℃)温度以上,等温时间为80~140s,得到晶粒大于10μm的奥氏体,然后冷却至室温;优选,冷速大于铁素体、珠光体、贝氏体生成临界冷速,得到全马氏体组织;
②二次退火:加热等温温度在780~850℃,700℃以下平均加热速率大于5℃/s,此阶段加热速率过低会破坏马氏体基体结构,700℃以上平均加热速率在2~20℃/s,此阶段加热速率过低奥氏体晶粒容易粗大,过快可能导致奥氏体含量不足,等温时间<2s,缓冷温度700~750℃,缓冷冷速控制在0.5~5℃/s;
③过时效:缓冷后以大于30℃/s的冷速冷却至360~410℃,等温300~600s,随后以大于2℃/s的冷速降至室温;
其通过控制一次退火过程,调控预淬火后马氏体基体的尺寸形貌,获得晶粒尺寸大于10μm的等轴状全马氏体组织,保证后续二次退火新奥氏体形核点弥散均匀,通过采用短时退火,保证退火过程中奥氏体一直保持均匀分布特征,减弱或消除各向异性;此外,马氏体基体上奥氏体长大迅速,马氏体基体上短时退火工艺下原奥氏体含量不会减少且晶粒细小,能够保证钢板足够高的强度和塑性,并且本发明组织中包含高温退火阶段所得的回火马氏体,代替临界区铁素体组织,有利于提高钢板屈服强度。因此,马氏体基体上短时退火钢板具有奥氏体化充分、晶粒细小且均匀的特点,有利于保留组织中的残余奥氏体,在保证钢板各向同性的前提下大幅度提高材料的屈服强度和塑性,具有很好的应用前景。
光整:钢板进入光整机进行板形调整,光整延伸率控制在0.1%~0.4%。
通过上述方法可以得到钢板抗拉强度980MPa以上,屈服强度700~850MPa,且力学性能各向同性,强塑积超过34GPa%。
本发明的有益效果在于:
(1)本发明的钢材化学成分主要以C、Si、Mn、Al为主要元素,无明显贵重合金,同时C含量低于0.24%,有利于生产及应用过程中的激光焊接及电阻点焊;
(2)本发明采用双退火的热处理思路,有效的细化了原奥氏体晶粒尺寸,并且组织中各相分布均匀,促进了钢中残余奥氏体保留,有效提高了钢的屈服强度和塑性;
(3)本发明通过低成本的合金设计以及巧妙工艺设计,实现兼顾各向同性及高塑性的力能指标。
附图说明
图1为本发明实施例1显微组织SEM图。
具体实施方式
下面通过实施例对本发明作进一步的说明。
本发明实施例根据技术方案的组分配比,进行冶炼、铸造、热轧、酸洗、冷轧、连退、光整;
热轧:加热温度1200~1270℃;开轧温度1100~1180℃,终轧温度900℃以上;卷取温度650~700℃;
冷轧:冷轧压下率为50%~58%;
连续退火:
①预淬火:加热温度在(A3+40℃)温度以上,等温时间为80~140s,然后冷却至室温;
②二次退火:等温温度在780~850℃,700℃以下平均加热速率大于5℃/s,700℃以上平均加热速率在2~20℃/s,等温时间<2s,缓冷温度700~750℃,缓冷冷速控制在0.5~5℃/s;
③过时效:缓冷后以大于30℃/s的冷速冷却至360~410℃,等温300~600s,随后以大于2℃/s的冷速降至室温;
光整:之后钢板进入光整机进行板形调整,光整延伸率控制在0.1%~0.4%。
进一步;预淬火后钢板显微组织为全马氏体组织结构。
发明实施例钢的成分(wt%)及A3温度见表1。本发明实施例钢加热、轧制的主要工艺参数见表2。本发明实施例钢的退火主要工艺参数见表3。本发明实施例钢的组织见表4。本发明实施例钢的性能见表5。
表1本发明实施例钢的成分(wt%)及A3温度
实施例 | C | Mn | Si | Al | Ti | Nb | P | S | A3/℃ |
1 | 0.19 | 2.22 | 1.65 | -- | 0.02 | 0.02 | 0.010 | 0.004 | 864 |
2 | 0.20 | 2.21 | 1.80 | -- | 0.02 | -- | 0.008 | 0.003 | 861 |
3 | 0.22 | 2.0 | 1.63 | -- | -- | 0.02 | 0.010 | 0.005 | 872 |
4 | 0.21 | 2.14 | 1.04 | 0.55 | 0.03 | -- | 0.006 | 0.004 | 893 |
5 | 0.19 | 2.17 | 1.25 | 0.42 | 0.02 | 0.02 | 0.010 | 0.004 | 887 |
6 | 0.22 | 2.05 | 0.64 | 0.81 | 0.01 | 0.02 | 0.009 | 0.003 | 921 |
7 | 0.18 | 2.26 | 0.91 | 0.77 | 0.02 | 0.02 | 0.010 | 0.005 | 912 |
8 | 0.21 | 2.13 | 0.68 | 0.90 | -- | 0.03 | 0.010 | 0.005 | 934 |
9 | 0.20 | 2.32 | 1.32 | 0.44 | 0.02 | -- | 0.010 | 0.005 | 882 |
10 | 0.23 | 2.08 | 1.15 | 0.86 | 0.02 | -- | 0.010 | 0.004 | 918 |
表2本发明实施例钢加热、轧制的主要工艺参数
实施例 | 加热温度/℃ | 开轧温度/℃ | 终轧温度/℃ | 卷取温度/℃ |
1 | 1233 | 1104 | 903 | 664 |
2 | 1256 | 1141 | 918 | 653 |
3 | 1207 | 1135 | 914 | 686 |
4 | 1271 | 1148 | 928 | 608 |
5 | 1264 | 1126 | 919 | 691 |
6 | 1244 | 1117 | 932 | 667 |
7 | 1257 | 1124 | 922 | 682 |
8 | 1270 | 1159 | 936 | 654 |
9 | 1268 | 1133 | 927 | 657 |
10 | 1242 | 1166 | 929 | 653 |
表3本发明实施例钢的退火主要工艺参数
表4本发明实施例钢的组织
表5本发明实施例钢的性能
由上可知,通过上述方法可以得到钢板抗拉强度980MPa以上,屈服强度700~850MPa,且力学性能各向同性,强塑积超过34GPa%。
为了表述本发明,在上述中通过实施例对本发明恰当且充分地进行了说明,以上实施方式仅用于说明本发明,而并非对本发明的限制,有关技术领域的普通技术人员,在不脱离本发明的精神和范围的情况下,还可以做出各种变化和变型,所作的任何修改、等同替换、改进等,均应包含在本发明的保护范围之内,本发明的专利保护范围应由权利要求限定。
Claims (4)
1.一种超高塑各向同性的980MPa级冷轧高强钢板,其特征在于,该钢板的成分按重量百分比计如下:C:0.18%~0.24%,Si:0.5%~1.8%,Mn:2.21%~2.4%,Al:0~1.0%,Nb:0~0.03%,Ti:0~0.03%,P≤0.02%,S≤0.01%,余量为Fe和不可避免的杂质;所述冷轧高强钢板显微组织包括铁素体、贝氏体、残余奥氏体和马氏体,其中各项显微组织按体积百分比计如下:铁素体10%~40%,贝氏体>37.4%,残余奥氏体21.3%~30%,马氏体<9.8%。
2.根据权利要求1所述的一种超高塑各向同性的980MPa级冷轧高强钢板,其特征在于,所述铁素体呈细条状,平均长度小于3μm,平均宽度小于0.5μm;所述马氏体平均晶粒尺寸小于2μm。
3.根据权利要求1所述的一种超高塑各向同性的980MPa级冷轧高强钢板,其特征在于,所述冷轧高强钢板抗拉强度980MPa以上,屈服强度700~850MPa,延伸率≥34%,强塑积超过34GPa%,横纵向平均强度差异小于10MPa,延伸率差异小于1%。
4.一种权利要求1-3任一项所述的超高塑各向同性的980MPa级冷轧高强钢板的制备方法,包括冶炼、铸造、热轧、酸洗、冷轧、连续退火、光整;其特征在于:
热轧:加热温度1200~1270℃; 开轧温度1100~1180℃,终轧温度900℃以上;卷取温度650~700℃;
冷轧:冷轧压下率为50%~58%;
连续退火:
①预淬火:加热温度在(A3+40℃)以上,等温时间为80~140s,然后冷却至室温;预淬火后钢板显微组织为全马氏体组织结构;
②二次退火:等温温度在780~850℃,700℃以下平均加热速率大于5℃/s,700℃以上平均加热速率在2~20℃/s,等温时间<2s,缓冷温度700~750℃,缓冷冷速控制在0.5~5℃/s;
③过时效:缓冷后以大于30℃/s的冷速冷却至过时效温度360~410℃,等温300~600s,随后以大于2℃/s的冷速降至室温;
光整:之后钢板进入光整机进行板形调整,光整延伸率控制在0.1%~0.4%。
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