CN113122770A - 低碳低成本超高强复相钢板/钢带及其制造方法 - Google Patents
低碳低成本超高强复相钢板/钢带及其制造方法 Download PDFInfo
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Abstract
低成本超高强复相钢板/钢带及其制造方法,其成分重量百分比为:C 0.03~0.07%,Si 0.1~0.5%,Mn 1.3~1.9%,P≤0.02%,S≤0.01%,Al 0.01~0.05%,Cr 0.2~0.5%,Ti 0.07~0.14%、(Ni+Nb+Mo+V)<0.03%,其余为Fe和其他不可避免的杂质;且Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)<3.0;Mn+2Cr+4Ti+4Nb+4V+4Mo‑Si/3+2C≤3.0。本发明所述钢板的抗拉强度≥780MPa,屈服强度≥680MPa,延伸率≥15%,屈强比≥0.9,扩孔率满足:若原始孔为冲压孔:扩孔率≥85%;若原始孔为铰孔:扩孔率≥115%,弯曲性能满足180°弯曲实验弯角直径等于0.5板厚(d=0.5a)时不裂;主要用于汽车底盘、悬挂系统零部件的制备。
Description
技术领域
本发明属于金属材料领域,具体涉及一种低碳低成本超高强复相钢板/钢带及其制造方法,主要应用于制造汽车底盘及悬挂系统的零部件产品。
背景技术
汽车“轻量化”可直接减少排放,降低油耗,是当今汽车制造业发展的目标。汽车“轻量化”的一个重要的措施就是采用高强度和超高强度的钢板来代替低强度钢板。目前,“轻量化”概念进一步沿用至汽车底盘及悬挂系统,日益严苛的环保要求和市场需求也要求汽车底盘材料采用高强钢实现“轻量化”。
然而,除了要求钢板具有更高的强度,汽车底盘及悬挂系统的结构件还要求钢板具有较高的屈服抗拉强度比(即屈服强度与抗拉强度的比值,本文以下简称屈强比),良好的延伸率、良好的扩孔性能和良好的弯曲性能。不同于一些车身零部件需要在碰撞时通过一定的塑性变形来吸收碰撞能量或避免对行人造成刚性碰撞伤害,底盘及悬挂系统往往要求材料不能出现任何塑性变形,因此对材料的屈强比要求极高。此外,根据公知,材料的疲劳极限往往与其屈服强度成正比,因此在同一抗拉强度级别的情况下,材料具有越高的屈服强度就意味着材料具有更高的疲劳极限,因此,对于底盘及悬挂系统零部件来说,具有更高的屈服强度或在同一抗拉强度级别用于更高的屈强比是其所追求的目标之一。
此外,汽车底盘及悬挂系统的零部件,往往具有复杂的结构(如图1),翻边、扩孔、弯曲、拉延等工序往往并存,因而对材料的成形性能具有极高的要求,不仅需要钢材具有较高的延伸率、较大的扩孔率,也需要钢板具有优异的弯曲性能。但是,根据公知,钢板的强度和屈强比、延伸率与扩孔率三个性能指标彼此之间相互制约,因为这既需要钢中有强度和硬度较高的相组分(如马氏体、贝氏体)来保证强度,需要有较软的相组分(如铁素体)来保证塑性和延伸率,还需要组织足够均匀来提高弯曲性能,同时还需要软相和硬相之间的硬度差异尽量小来保证高屈强比和高扩孔性能。
除了上述苛刻的性能要求以外,汽车底盘及悬挂系统的零部件制备还需要材料具有良好的表面质量、可涂装性和正常均匀的色泽,以及较低的碳当量水平以保证零部件的可焊性能,因此常见的成分设计是低碳成分(碳含量小于0.1%)。而在这种成分体系下,为获得兼具高强度高屈强比,高延伸率、高扩孔性和高弯曲性能的钢材,以满足形状复杂、高品质高服役性能的汽车底盘及悬挂系统的零部件的制造,通常会选用以贝氏体为主,铁素体为辅的复相钢,并通过添加大量合金元素,尤其是铌、钼、钒、镍、铝等昂贵的合金元素来实现析出强化,从而提升铁素体强度并保证铁素体塑性,以此来提升屈强比并保证钢材具有较高的延伸率和扩孔率。
如中国专利公开号CN109055657A公开了一种超低碳高强度的复相钢板,通过大量添加铌、钼、镍等贵金属元素,实现获得屈服强度≥690MPa,屈强比0.89~0.92,但未考虑钢板的扩孔性能。同样,中国专利公开号CN101906567A公开了一种高强度热轧钢板,通过大量添加铌、钼、镍等昂贵的合金元素,获得了抗拉强度大于780MPa,扩孔率(原始孔为冲孔)为40%以上的性能。
但是,随着钢铁行业和汽车行业内部竞争日益激烈,这种添加大量合金元素、尤其是钼、钒、铌等昂贵合金的钢材,极大地增加了整个汽车行业产业链的成本压力,因此,市场上急需一种不添加或几乎不添加昂贵的合金元素(即低成本),又兼具高强度及高屈强比、高延伸率、高扩孔与高弯曲性能的具有优异服役和综合成形性能的钢板。
但是一旦不添加钼、钒、铌等昂贵合金,低成本复相钢很难达到高强度(如抗拉强度800MPa)级别,如中国专利公开号CN103667948A公开了一种不含铌、钒、镍、钼等贵金属微合金元素的复相钢及其制造方法,该专利设计的复相钢虽然具有较低的合金成本,且复相钢的扩孔性能较好,但是强度较低,实施例中的屈服强度只有不高于520MPa的屈服强度和不高于725MPa的抗拉强度,因此只能设计用来制造汽车车轮,而无法满足汽车底盘零部件对复相钢产品零部件强度的要求。
为解决低成本复相钢强度不足的问题,主要的方法之一是不添加钼、钒、铌等昂贵合金,而选择大量加入锰、铬、钛等相对价格较低的合金元素,通过相变强化、固溶强化和第二相强化的方式提升复相钢强度。如中国专利公开号CN102732790A公开了一种超低碳贝氏体钢板及其制造方法,该钢板抗拉强度大于770MPa,虽然不包含铌、钼、钒等贵金属微合金元素,但是。却含有3.0%~4.5%的锰,导致其成本依旧较高,而该专利并未考虑复相钢的扩孔性能与弯曲性能。再比如中国专利公开号CN101285156A公开了一种利用薄板坯连铸连轧技术生产制造的贝氏体钢,虽然该专利通过薄板坯连铸连轧技术设计、制造出一种不含铌、钼、钒等贵金属微合金元素的高强贝氏体钢,可以兼具高强度、高屈强比、高延伸率和一定的弯曲性能,但是由于其大量添加铬、锰、钛等元素,其产品的生产制造成本仍然较高,且该产品弯曲性能一般,且依旧未考虑其扩孔性能。实际上,锰、铬元素极易在钢板中形成偏聚,造成局部成分和相组分差异,从而导致钢板的扩孔率和弯曲性能恶化,而锰元素在连铸时容易造成板坯内柱状晶粗大,粗大的柱状晶会对后续钢板热轧和冷轧组织产生遗传影响,进而影响钢板组织均匀性、对扩孔性能和弯曲性能产生不利影响。
另一种低成本高强度复相钢的制备方法,是通过大量添加硅元素,通过固溶强化提升复相钢强度。如中国专利公开号CN1756853A公开了一种含有铁素体、贝氏体\马氏体和第二相组成的高强度热轧复相钢及其制造方法。该专利通过添加大量的硅元素(最高1.5%)来保证复相钢具备超高强度,从而降低其他合金元素的使用量。但是,硅元素含量过高会导致热轧钢板/钢带表面出现严重的红色氧化铁皮,进而直接造成钢板/钢带成品的表面出现严重色差,直接影响其作为汽车用结构件的表面质量和美观。根据公知:于洋,王畅,王林等,基于高温氧化特性的含Si钢红铁皮缺陷研究[J],轧钢,2016,33(2):10-15;于洋,王畅,王林等,基于高温氧化特性的含Si钢红铁皮缺陷研究[J],轧钢,2016,33(2):10-15;王畅,于洋,王林等,硅元素对炉生铁皮界面微观结构的影响研究[J],轧钢,2016,33(5):6-10;当钢中硅含量较高时,可形成红鳞等缺陷而导致钢材表面质量降低,其中含0.5%的硅含量的汽车用钢中发现带钢表面存在等间距的条带状铁皮,红铁皮缺陷占带钢表面比例约30%。因此,采用高硅元素的方案来设计并制造超高强复相钢并不适合应用于汽车工业。
因此,对于这类应用于汽车底盘和悬挂系统零部件制造用的抗拉强度达到800MPa级别的低碳复相钢(以下简称低碳高强复相钢),现有的技术无法解决其低成本设计与高综合服役性能之间的矛盾,即便采用现在已公开的低成本设计,材料的强度、屈强比、扩孔性能和弯曲性能也无法兼得。因此,如何获得兼具低成本与高强度高扩孔特性的复相钢板/钢带,以满足汽车零部件的生产制造需要,一直是钢铁工业界的难题。
发明内容
本发明的目的在于提供一种低成本超高强复相钢板/钢带及其制造方法,该钢板的抗拉强度≥780MPa、屈服强度≥680MPa,延伸率≥15%,屈强比≥0.9,扩孔率满足:若原始孔为冲压孔:扩孔率≥85%;若原始孔为铰孔:扩孔率≥115%,弯曲性能满足180°弯曲实验弯角直径等于0.5板厚(d=0.5a)时不裂;主要用于汽车底盘、悬挂系统零部件的制备。
为达到上述目的,本发明的技术方案是:
低成本超高强复相钢板/钢带,其成分重量百分比为:C:0.03~0.07%,Si:0.1~0.5%,Mn:1.3~1.9%,P≤0.02%,S≤0.01%,Al:0.01~0.05%,Cr:0.2~0.5%,还含有Ti:0.07~0.14%、(Ni+Nb+Mo+V)<0.03%,其余为Fe和不可避免的杂质;且同时需满足:
[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]<3.0;
(Mn+2Cr+4Ti+4Nb+4V+4Mo-Si/3+2C)≤3.0。
优选的,所述的钢板/钢带的化学成分中C:0.04~0.06%,以重量百分比计。
优选的,所述的钢板/钢带的化学成分中Si:0.1~0.27%,以重量百分比计。
优选的,所述的钢板/钢带的化学成分中Mn:1.45~1.75%,以重量百分比计。
优选的,所述的钢板/钢带的化学成分中Cr:0.35~0.50%,以重量百分比计。
本发明所述钢板/钢带的微观组织含有铁素体、下贝氏体,还含有碳化物析出相、夹杂物相或微量马氏体相,其中铁素体含量≤70%,铁素体+下贝氏体含量≥90%。
优选的,所述的钢板/钢带的板坯铸态组织中,柱状晶的比例≤10%,或柱状晶区的厚度<40mm。
优选的,所述的钢板/钢带成品态的微观组织中,铁素体晶粒平均直径<6μm,或晶粒度ASTM评级>11.8。
优选的,所述的钢板/钢带的成品态的微观组织中含有TiN颗粒,且单个颗粒的最长边长<10μm或面积<50μm2。
通过上述方案所述钢板/钢带的抗拉强度≥780MPa、屈服强度≥680MPa,扩孔率性能指标:若原始孔为冲压孔:扩孔率≥85%;若原始孔为铰孔:扩孔率≥115%;180°弯曲d=0.5a合格。
在本发明钢的成分设计中:
碳(C):碳直接影响钢板/钢带的强度、焊接性、成形性和薄板坯连铸的可制造性。碳含量越高,越有利于提高钢板的强度,若碳含量低于0.03%,钢板/钢带的强度达不到目标要求;碳含量高于0.07%,容易造成钢板/钢带强度过高,从而导致扩孔率不满足要求。因此,本发明控制碳含量的范围为0.03~0.07%。
硅(Si):硅具有一定的固溶强化作用,Si含量越高越有利于提升钢板/钢带的屈服强度。同时,硅还有抑制碳化物析出的效果,可以通过添加硅元素来形成无碳化物析出的贝氏体组织;但当硅含量高于0.5%时,热轧钢板/钢带表面易生成严重的红色氧化铁皮,不仅恶化钢板/钢带的表面质量,同时损害钢板/钢带的可镀性,不利于生产热镀锌钢板/钢带。因此,本发明将硅含量限定在0.1~0.5%的范围内。
锰(Mn):锰可以有效地提升钢板/钢带的强度,而且成本相对其他合金元素较低,因此本发明将锰作为主要添加元素。但是当锰含量高于1.90%时,不仅板坯铸态组织中柱状晶的比例或厚度会大幅增加,从而对后续成品组织均匀性的控制产生严重不良影响以外,Mn含量增加还会导致最终成品组织中马氏体含量的增加,损害扩孔性能;当锰含量低于1.40%时,钢板/钢带的强度不足。因此本发明将锰含量限定在1.30~1.90%。
铝(Al):铝是作为炼钢过程的主要脱氧剂而加入,但铝含量小于0.01%时,脱氧效果不足:铝含量超过0.05%时,影响钢水粘度,可能会造成水口结瘤,并损害钢板/钢带的焊接性能。因此,本发明将铝含量限定在0.01~0.05%。
铬(Cr):铬有利于扩大贝氏体相区,保证钢板/钢带在轧后冷却中可以得到贝氏体组织,有利于提高强度和扩孔率。但添加量超过0.5%时,强度提升不再显著,反而会不利于钢板/钢带的可焊性,导致板坯铸态组织中柱状晶的比例或厚度大幅增加,且还会导致钢板表面出现铬元素富集而形成,从而影响最终产品的组织均匀性。但当含量小于0.2%时,对贝氏体相区的扩大并不显著。因此,本发明将铬含量限定在0.2~0.5%。
钛(Ti):钛是本发明复相钢中的主要合金元素,通过固溶强化,和形成细小的碳化物之后的第二相强化来提升复相钢的强度。当微合金含量低与0.07%时,钢板/钢带的强度不足,而当微合金含量高于0.14%时,一方面会增加成本,另一方面容易形成碳化物中心偏析,不利于扩孔性能。
铌、钒、钼和镍(Nb、V、Mo、Ni):加入铌、钒、钼和镍也可以产生固溶强化和第二相强化,从而提升复相钢强度。此外,这些贵金属微合金元素的计入还可以实现细化晶粒的效果,从而有利于复相钢的扩孔率。但,相比钛元素,铌、钒、钼和镍的合金成本极高。虽可作为可选元素加入钢中,但从低成本角度考虑,本发明中不建议添加铌、钒、钼和镍,即Nb+V+Mo+Ni<0.03%。
钢中的杂质元素的上限控制在P:≤0.02%,S:≤0.01%,钢质越纯净效果更佳。
本发明所述钢板/钢带的微观组织为为铁素体+下贝氏体的微观组织,铁素体含量≤70%。铁素体+下贝氏体含量≥90%。若铁素体组织高于70%,钢板/钢带将无法达到所要求的强度;若铁素体+下贝氏体含量低于90%,则钢板/钢带的扩孔性能达不到要求。
本发明所述的钢板/钢带的微观组织中,铁素体晶粒平均直径<6μm,或晶粒度ASTM评级>12.3。若晶粒平均直径不低于5μm或晶粒度评级不大于12.3,则钢板/钢带将无法达到所要求的强度。
本发明所述的钢板/钢带的微观组织中含有TiN颗粒,且单个颗粒的最长边长<10μm。若单个颗粒的最长边长不小于10μm,将导致钢板/钢带无法达到所要求的扩孔性能。
此外,上述合金元素与碳元素的计量关系还应满足如下公式:
①[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]<3.0,以保证钢板/钢带具有低合金成本;
②(Mn+2Cr+4Ti+4Nb+4V+4Mo-0.5Si+5C)≤3.0,以保证钢板/钢带微观组织中能够析出一定量碳化物颗粒,而不发生碳化物析出过多、过粗大或过于聚集而造成的扩孔率降低。从而可以保证钢板/钢带兼具较高的强度和扩孔性能。
本发明的超低碳低成本超高强复相钢板/钢带的制造方法,包括如下步骤:
1)冶炼、连铸
按上述化学成分冶炼并通过连铸铸造成铸坯,连铸时板坯冷却速率≥5K/s;
2)热轧轧制、轧后冷却
板坯在不低于700℃的温度下进加热炉,对铸坯加热,加热温度为1100~1250℃;热轧第一、第二道次每道次压下率≥55%,精轧终轧温度为850~950℃;
3)轧后冷却、卷取
轧后采用水冷,卷取温度为550~630℃;
4)酸洗。
进一步地,步骤3)酸洗后,还包括热镀锌退火工艺,获得热轧热镀锌钢板成品。
上述步骤1)中,连铸时的板坯冷却速率将影响钢板/钢带最终组织中的晶粒尺寸、液相中形成的夹杂物尺寸和板坯组织中柱状晶的比例。若冷却速度低于5K/s时,一方面板坯柱状晶的厚度或比例会高于设计要求,从而容易在后续成品组织中形成带状组织,影响钢板/钢带的弯曲性能;另一方面,连铸时板坯冷速的下降会导致最终组织中的晶粒尺寸将无法设计要求,而且会导致钢中液相生成的夹杂物(典型如TiN)的尺寸粗大,对扩孔和弯曲性能产生不利影响。
上述步骤2)中,板坯进加入炉之前的最低温度将影响产品最终的性能。当板坯进加入炉之前的最低温度小于700℃时,碳化钛会在板坯中大量析出,而在后续的再加热过程中,板坯中已析出的碳化钛无法再完全重溶进板坯中,造成热轧后基体中的固溶钛和碳化钛均较少,导致产品强度不足。而当精轧终轧温度小于850℃时,在精轧前就会有铁素体析出,造成最终组织中贝氏体含量偏低,使钢板/钢带无法达到设定强度。但考虑到板坯加热温度,精轧终轧温度不超过950℃。此外,上述步骤2)中,为保证钢板/钢带具有细小和高度均匀的组织,热轧第一、第二道次每道次压下率≥55%;压下率不足时,无法获得细小的组织均匀的组织,导致钢板/钢带强度不够,弯曲性能不能达到设计要求。不仅如此,上述步骤2)中的高压下率必须与步骤1)中连铸时板坯的高冷速相配合,若连铸冷速无法达到5K/s以上,会导致板坯中液相生成的夹杂物(以TiN为主)尺寸过大,此时若在步骤2)中采用≥55%的大压下率,会导致粗大的TiN开裂,如附图1所示,从而成为钢板/钢带内部的裂纹源,造成钢板/钢带扩孔和弯曲性能的恶化;而若连铸冷速可以达到5K/s以上时,板坯中液相生成的夹杂物(以TiN为主)尺寸细小,如附图2所示,不会在步骤2)中的大热轧压下时破裂,从而不会对钢板/钢带的扩孔和弯曲性能产生不利影响。
上述步骤3)中,卷取温度是获得高强度、高扩孔率的最为关键的工艺参数之一。当卷取温度大于640℃时,由于合金碳化物的强烈析出和粗化,对钢板扩孔率有负面作用,另一方面,当卷取温度小于550℃时会严重抑制碳化物的析出,造成钢板强度无法达到设定要求,因此。本发明将卷取温度限定为550~630℃。
经检测,本发明提供的超高强热轧钢板/钢带性能满足如下指标:
1、常温力学性能:
抗拉强度≥780MPa;屈服强度≥680MPa;屈强比≥0.9。
2、断裂延伸率:
A50≥15%或A5≥19%。
3、扩孔率性能:
若原始孔为冲压孔:则扩孔率大于85%,最高可达到100%以上;
若原始孔为铰孔:则扩孔率大于115%,最高可达到130%以上。
4、弯曲性能:
180°冷弯,d=0.5a合格。
本发明的有益效果:
1.本发明采用低成本的成分设计,减少合金元素,尤其是贵金属合金元素的添加量,并要求[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]≤3.0,和(Nb+V+Mo+Ni)<0.03,以确保复相钢具备极低的合金成本。在复相钢的常见合金元素中,铌和钒合金成本最高,在考虑品位的情况下,单价可以达到锰元素成本单价的20倍;其次是钼和镍,在考虑品位的情况下,单价可以达到锰元素成本单价的10倍,因此,这类元素在本发明中基本不予采用。而其他的合金元素,如钛、铝、锰、铬等,则选取最优化的成分设计,尽量减小添加量,实现综合成本最低。
2.出于低成本的市场需求,本发明基本不添加昂贵的合金元素,从而容易造成材料强度不足,如中国专利CN103667948A。为提升材料强度,本发明主要采用细晶强化结合Ti元素强化,通过优化析出强化和固溶强化的配比,并实现微观组织的高度均匀与夹杂物的足够细小,来实现高强度、高延伸率、高扩孔率与优良弯曲性能的兼得。在本发明中,仍然添加了一定量的锰、铬、钛,尤其是铬和钛,一方面通过固溶于基体中实现强化,即固溶强化;另一方面通过形成碳化物析出实现强化,即第二相强化。这两种强化机制,固溶强化对强度的提升弱于第二相强化,但是碳化物的析出会损害复相钢的扩孔性能。因此需要在两种强化机制中寻找平衡,即要求合金元素添加量与碳元素含量之间满足如下关系:(Mn+2Cr+4Ti+4Nb+4V+4Mo-Si/3+2C)≤3.0。本发明公式表示材料中各合金元素对第二相析出效应的贡献,其中,Mn、Cr、Ti(或Nb、Mo、V)三类元素形成碳化物析出相的能力逐渐提升,故采用了梯度的系数设计,而Si元素有抑制碳化物析出的作用,故在公式中设计为负系数,因此,上式值越大,代表材料中添加的合金元素整体对析出强化的贡献会更高。本发明发现,当上式值高于3.0时,材料的扩孔性能会大幅下降。
3.通过成分和工艺的设计,实现细小的高均匀的组织及尺寸细小的夹杂物,从而获得优良的弯曲性能。在设计中首先采用较低的Mn和Cr的设计,以避免连铸后钢板板坯中出现大尺寸的柱状晶组织,以尽量降低柱状晶对后续生产获得高均匀度组织的不利影响;其次,在连铸中采用高冷速设计,一方面继续降低板坯中柱状晶比例提升细小等轴晶的比例,另一方面降低液相中生成的夹杂物的尺寸(以TiN为代表);最后在热轧的第一、二道次,采用大压下的轧制工艺设计,在进一步破坏柱状晶的同时,获得细小的组织,实现高强度、高弯曲、和高延伸率的兼得。
本发明制造的超高强热轧钢板产品和钢带产品及热镀锌钢板成品可用于制备汽车底盘、悬挂系统零部件的制造,并同时兼备低成本、高强度、高扩孔性与良好的弯曲性能,从而弥补了汽车产业链中市场亟需的低成本高质量的底盘用钢产品的空白。
附图说明
图1为连铸冷速不足5K/s时TiN颗粒的尺寸及其在热轧大压下之后的形貌(热轧态组织照片)。
图2为连铸冷速达到5K/s以上时TiN颗粒的尺寸及其在热轧大压下之后的形貌(热轧态组织照片)。
具体实施方式
下面结合实施例对本发明做进一步说明。
将表1中所示的不同成分的钢经冶炼后按表2所示加热+热轧工艺后得到厚度小于4mm的钢板。取沿纵向50mm标距和5mm标距的拉伸试样测定屈服、抗拉强度及延伸率,取钢板中部区域测定扩孔率和180°弯曲性能;试验数据如表2所示。其中,扩孔率采用扩孔试验测定,用凸模把中心带孔的试件压入凹模,使试件中心孔扩大,直到板孔边缘出现颈缩或贯穿裂纹为止。由于试件中心原始孔的制备方式对扩孔率测试结果存在较大影响,因此,分别采用冲孔和铰孔制备试件中心原始孔,后续试验及测试方法按ISO/DIS 16630标准中规定的扩孔率测试方法执行。180°弯曲实验采用GB/T232-2010标准中弯曲性能的测定方法执行。
表1中,实施例A~I为本发明的钢,对比例J~N中碳或锰或其他合金元素含量超出本发明成分的范围,表中M指成分中[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]项的计算值,R指成分中(Mn+2Cr+4Ti+4V+4Nb+4Mo-Si/3+2C)项的计算值。此外,比较例O和比较例P分别是中国专利CN101906567A和中国专利CN101285156A中的公开的实施例,从对比中可以看出,比较例O和比较例P的M和R值都超过本发明设计范围,表示这两个比较例的合金成本都高于本发明案例,且未采用本发明设计的公式优化合金配比。
表2为表1中各钢种的不同制造工艺,同样分为实施例和比较例两大类,其中比较例O和比较例P的工艺为对应专利中公开的制造工艺。表3则为上述实施例和比较例的力学性能检测值。其中,比较例O和比较例P的性能为对应专利中公开的性能,从表中可以看出,比较例O和比较例P的性能均逊于本发明中的实施例。
可见,当C、Mn、Ti等合金成分偏离本发明范围时,如Mn、Ti含量较低时,如对比例K和M,会导致钢板的强度均小于设计要求;而当C、Ti含量或R值高出本发明的成分范围时,如对比例J、L和N,其中C、Mn含量超标会导致组织中生产大量的马氏体,恶化材料的扩孔性能和弯曲性能,而Ti含量和R值过高也会导致组织中碳化物粗化,恶化材料的扩孔性能,均不符合本发明的目的。
当板坯进炉温度过低时,如对比钢A-2,会导致强度不满足本发明设计标准;若卷取温度过低,如对比例D-2,会导致钢中碳化物析出受到抑制,导致钢板强度过低。当热轧前两道次压下率不够时,无法彻底消除钢板的带状组织,且不能充分细化晶粒,实现组织均匀性,会导致钢板延伸率的弯曲性能变差,如对比例B-2;而当连铸冷却速度不够,但热轧却追求大压下率时,会导致钢中粗大的TiN颗粒破碎,形成潜在裂纹源,大幅恶化材料的延伸率、扩孔性能和弯曲性能,如对比例C-2。
综上所述,本发明在碳锰钢的基础上,控制合理的成分范围,限制合金元素的含量,优化各元素配比,大幅降低合金成本,在常规的汽车用钢生产线基础上,进一步连铸冷却速度,热轧压下率,卷取温度,生产出兼具高强度、高扩孔性能与优良弯曲性能的低成本超高强热轧钢板/钢带,其屈服强度不小于680MPa,抗拉强度不小于780MPa,扩孔率不小于85%(原始孔为冲孔)或不小于115%(原始孔为铰孔),180°弯曲d=0.5a,以弥补汽车行业市场对兼具低成本和高强度高成性能的底盘、悬挂件用材的迫切需求。
Claims (14)
1.低碳低成本超高强复相钢板/钢带,其成分质量百分比为:C:0.03~0.07%,Si:0.1~0.5%,Mn:1.3~1.9%,P≤0.02%,S≤0.01%,Al:0.01~0.05%,Cr:0.2~0.5%,Ti:0.07~0.14%、(Ni+Nb+Mo+V)<0.03%,其余为Fe和其他不可避免的杂质;且同时需满足:
【Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)】≤3.0;
(Mn+2Cr+4Ti+4Nb+4V+4Mo-Si/3+2C)≤3.0。
2.如权利要求1所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述C含量为:0.04~0.06%,以重量百分比计。
3.如权利要求1所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述Si含量为:0.1~0.27%,以重量百分比计。
4.如权利要求1所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述Mn含量为:1.45~1.75%,以重量百分比计。
5.如权利要求1所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述Cr含量为:0.35~0.50%,以重量百分比计。
6.如权利要求1所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述化学成分中Nb+Mo+V<0.03%,以重量百分比计。
7.如权利要求1-6任一项所述的低碳低成本超高强复相钢板/钢带,其特征在于,钢中组织含有铁素体、下贝氏体,还含有碳化物析出相、夹杂物相或微量马氏体相,其中铁素体含量≤70%,铁素体+下贝氏体含量≥90%。
8.如权利要求7所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述钢板/钢带的微观组织中还含有TiN颗粒,且单个颗粒的最长边长<8μm或面积<50μm2。
9.如权利要求7所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述铁素体晶粒平均直径<6μm,或铁素体晶粒度ASTM评级>11.8。
10.如权利要求1-9任一项所述的低碳低成本超高强复相钢板/钢带,其特征在于,所述钢板/钢带的抗拉强度≥780MPa、屈服强度≥680MPa,扩孔率满足:若原始孔为冲压孔:扩孔率≥85%;若原始孔为铰孔:扩孔率≥115%,弯曲性能满足180°弯曲d=0.5a合格。
11.如权利要求1-10任一项所述的低碳低成本超高强复相钢板/钢带的制造方法,包括如下步骤:
1)冶炼、连铸
按权利要求1-6任一项所述的化学成分冶炼并通过连铸铸造成板坯,连铸时冷速≥5K/s;
2)板坯热送、轧制、轧后冷却、卷取
板坯在不低于700℃的温度下进加热炉,对板坯加热,加热温度为1100~1250℃;板坯热轧时前两道次压下率均≥55%;精轧终轧温度为850~950℃,卷取温度为550~630℃;
3)酸洗。
12.如权利要求11所述的低碳低成本超高强复相钢板/钢带的制造方法,其特征在于,步骤3)酸洗后,还包括热镀锌退火工艺,获得热轧热镀锌钢板成品。
13.如权利要求11所述的低碳低成本超高强复相钢板/钢带的制造方法,其特征在于,步骤1)中,所述板坯铸态组织中柱状晶的比例≤10%,或柱状晶区的厚度<40mm。
14.如权利要求11所述的低碳低成本超高强复相钢板/钢带的制造方法,其特征在于,所述钢板/钢带的厚度为0.7~4.0mm。
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WO2021136352A1 (zh) | 2021-07-08 |
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KR20220115575A (ko) | 2022-08-17 |
JP2023507528A (ja) | 2023-02-22 |
AU2020416427A1 (en) | 2022-07-21 |
EP4086363A4 (en) | 2023-06-14 |
BR112022010497A2 (pt) | 2022-09-06 |
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