CN104603308A - 具有优异的刚度和延性的铁素体轻质高强度钢板及其制造方法 - Google Patents
具有优异的刚度和延性的铁素体轻质高强度钢板及其制造方法 Download PDFInfo
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- CN104603308A CN104603308A CN201280075611.1A CN201280075611A CN104603308A CN 104603308 A CN104603308 A CN 104603308A CN 201280075611 A CN201280075611 A CN 201280075611A CN 104603308 A CN104603308 A CN 104603308A
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Abstract
本发明涉及一种具有优异的刚度和延性的铁素体轻质高强度钢板及其制造方法。本发明的一个实施方式提供一种钢板及其制造方法,该钢板包括0.02wt%至0.1wt%的碳(C),4wt%至15wt%的锰(Mn),4wt%至10wt%的铝(Al),2.0wt%以下(不包括0)的硅(Si),0.01wt%至0.3wt%的钛(Ti),0.005wt%至0.2wt%的锑(Sb),以及作为剩余部分的铁(Fe)和不可避免的杂质,其中,0.25×Ti/C的值在0.17至1.0的范围内,Mn/Al×Log(C×Ti×10000)的值在1.0至10的范围内。
Description
技术领域
本发明涉及一种具有优异的刚度和延性的铁素体轻质高强度钢板及其制造方法,更具体而言,涉及一种可主要用于汽车内部和外部或结构面板的具有优异的刚度和延性的铁素体轻质高强度钢板,以及其制造方法。
背景技术
近来,关于用于汽车的钢板,随着对于汽车燃料消耗中的经济和汽车碰撞过程中的乘客安全的要求的不断提高,用于汽车的钢的强度逐渐提高,同时,由于成形的汽车零部件的复杂性和整体性的趋势,需要具有较高水平的成形性的钢板。此外,根据使用代替石油的新燃料的汽车的出现,由于预期汽车燃油系统(包括电池)的重量相比目前的内燃机燃料系统将大大增加,需要开发一种能够显著降低汽车车身的重量的轻质材料。
由于钢具有显著优于铝和镁的强度和延性,并且其生产成本也相对较低,目前通过减小常规高强度和高延性钢板的厚度实现车身的减重。然而,在未满足采用替代燃料的未来汽车所要求的重量减轻的量的情况下,有色轻质金属(如铝或镁)的使用是不可避免的。
因此,已实施通过添加铝(Al)(轻质元素)至钢中的具有相比常规钢降低的比重的钢的开发。这种轻质钢通常分为多相、奥氏体和铁素体钢,针对铁素体轻质钢的一个一般技术公开于日本专利公告第2005-273004号中。该技术用于通过将2.0%至10.0%的铝添加至超低碳钢中来制造铁素体轻质钢,但是降低比重的作用可能较低,并且抗拉强度×伸长率(TS×El)可能显著地较低。另一技术公开于日本专利申请公告第2006-176843号中。该技术用于通过包括0.8%至1.2%的碳,添加10%至30%的锰(Mn)和8%至12%的铝(Al),以及包括尽可能低的量的(Fe,Mn)3AlC来制造轻质钢,但是拉拔性可能较低。另一技术公开于日本专利申请公告第2006-149204号中。该技术通过控制组织来保证刚度和延性,但抗拉强度只达到400MPa的水平。公开了一些具有620MPa抗拉强度的钢,但其伸长率只有25%,并且由于加工(如拉拔)过程中的拉杯(drawn cup)中的呈山形式的高凸耳,拉杯的高度的3%以上被切去。另一技术公开于日本专利申请公告第2003-355229号中。该技术用于制造包括0.01%至5%的碳(C)、0.01%至5.0%的Mn、3%至10%的Al的钢,并通过添加大量的Al降低了比重。然而,由于热轧和冷轧裂纹的限制,热轧后的热处理(包括冷却)温度和冷压缩率(cold reduction rate)可能受限,并且,虽然TS×El的值为10,000MPa%以上,然而由于TS×El的值达不到16,000MPa%的先进的市售高强度钢的水平,汽车零部件的加工中可能存在局限性。
发明内容
技术问题
本发明的一个方面是通过合金组成的优化控制细小析出物来防止晶粒变粗导致的强度的降低和平面各向异性增加导致的延性的降低,从而提供具有优异的刚度和延性的铁素体轻质高强度钢板,以及其制备方法。
解决问题的方案
根据本发明的一个方面,提供了一种铁素体轻质高强度钢板,包括:0.02wt%至0.1wt%的碳(C)、4wt%至15wt%的锰(Mn)、4wt%至10wt%的铝(Al)、2.0wt%以下(不包括0)的硅(Si)、0.01wt%至0.3wt%的钛(Ti)、0.005wt%至0.2wt%的锑(Sb)、作为剩余部分的铁(Fe)和不可避免的杂质,其中0.25×Ti/C的值在0.17至1.0的范围内,Mn/Al×Log(C×Ti×10000)的值在1.0至10的范围内。
根据本发明的另一个方面,提供了一种制备铁素体轻质高强度钢板的方法,所述方法包括:再加热钢坯,所述钢坯包括0.02wt%至0.1wt%的C、4wt%至15wt%的Mn、4wt%至10wt%的Al、2.0wt%以下(不包括0)的Si、0.01wt%至0.3wt%的Ti、0.005wt%至0.2wt%Sb和作为剩余部分的Fe和不可避免的杂质,并具有0.17至1.0范围的0.25×Ti/C的值和1.0至10范围的Mn/Al×Log(C×Ti×10000)的值,然后在850℃以上的温度热轧钢坯以获得热轧钢板;在500℃至700℃的温度范围内卷取热轧钢板。
有益效果
根据本发明,提供的是一种铁素体轻质高强度钢板,由于其比重比常规钢的比重低5%以上,且由于优异的抗拉强度、屈服强度和延性从而抗拉强度×伸长率(TS×El)的值为17,000MPa以上,并且平面各向异性也较低,其能用作较薄的部件,从而在减轻重量方面相对有效,并提供了其制造方法。
附图说明
图1为示出Al含量和比重降低率之间的关系的图表;
图2为示出0.25Ti/C的值和屈服率之间的关系的图表;
图3为示出平面各向异性和制耳率之间的关系的图表;以及
图4为示出强化指数和抗拉强度之间的关系的图表。
最佳实施方式
下文将描述本发明。
首先,将详细描述本发明的组成范围。
碳(C):0.02wt%至0.1wt%
钢中的C通过形成渗碳体[(Fe,Mn)3C]、kappa(κ)碳化物[(Fe,Al)3C]和细小的TiC的弥散强化作用来细化晶粒。此外,通过在退火过程中的再结晶处理中在析出物的周围发生随机成核,C抑制组织的择优取向。C的含量可为0.02wt%以上从而形成适当水平的TiC、(Fe,Mn)3AlC或κ碳化物。由于渗碳体和κ碳化物随C含量的增加而增加,可提高强度,但可降低延性。具体地,在包括铝(Al)的钢中,由于FeAl有序相和κ碳化物在铁素体晶界的析出,可能出现脆性,因此,C的含量可为0.1wt%以下。
锰(Mn):4wt%至15wt%
Mn连同C是控制本发明中的碳化物的特性并通过固溶强化提高强度的元素。Mn与C共存以促进碳化物的高温析出。因此,Mn通过防止碳化物在晶界处的形成来抑制热脆性并最终有助于提高钢板的强度。另外,由于Mn通过增大钢的晶格常数来降低密度,所以锰用于降低钢的比重。此外,在锰含量高的情况下,由于高温下的奥氏体的形成,可能发生碳的聚集,并且,在冷却过程中可能发生共析转变或可形成残余奥氏体,以提高延性。然而,鉴于比重的降低,具有高堆积率的奥氏体结构可减小降低比重的作用。由于对用于在高温下仅形成适量的奥氏体的C和Mn的含量有要求,考虑到上述原因,锰的含量可为4%以上。在锰过量加入的情况下,延性可显著提高,但用于降低比重的铝的含量必须更高。因此,可能发生如脆性的局限性,并且奥氏体可能形成为在铁素体结构中形成条状的奥氏体簇。由于通过形变过程中的塑性诱导转化可大大提高特定方向的奥氏体结构的形变,平面各向异性可显著提高。因此,本发明中的锰的含量可为15%以下。
铝(Al):4wt%至10wt%
Al(以及C、Mn和钛(Ti))是最重要的元素之一,并且Al用于降低钢的比重。要获得这一效果,可以以4%以上的量添加铝。可加入大量的铝以稳定铁素体结构并降低比重,但是在这种情况下,通过大量的金属间化合物(如κ碳化物、FeAl和Fe3Al)的形成可显著降低钢的延性。因此,铝的含量可为10%以下。
硅(Si):2wt%以下(不包括0%)
类似于Al,Si有效降低钢的比重并抑制铁素体中的渗碳体的析出以增加细小的TiC或κ碳化物。因此,硅可提高钢的强度。然而,在C和Al的含量同时较高的情况下,当Si含量大于2%时,由于有序相(如FeAl或Fe3Al)的快速增加,可能发生脆性断裂。因此,Si的含量可为2%以下。
钛(Ti):0.01wt%至0.3wt%
Ti是本发明中的一个非常重要的元素。对于包括大量的铝的钢,铝(甚至在高温下)延伸铁素体区以稳定铁素体,其中,铁素体可被恢复并在高温下以相对高的速率再结晶。因此,即使在热轧温度略降低的情况下,也可形成粗晶粒以降低强度。为了防止这种情况,通过添加0.01%以上的量的Ti可形成细小的高温TiC析出物,因此,晶粒被细化。已知TiN抑制高温处理中例如钢坯再加热中的晶粒生长。然而,在Al含量高的情况下,如在本发明中,由于氮优先形成待结晶的AlN并上浮于钢液中,当Al的含量大于4%时,钢中的氮几乎被除去。因此,钛不可形成TiN,而主要形成TiC。由于最终热轧过程中形成的细小的TiC可以进一步细化晶粒,需要Ti以保证强度。在奥氏体向铁素体转变的过程中,Ti抑制κ碳化物的聚集以分散κ碳化物,因此,可以细化κ碳化物。另外,由于析出物(如TiC)在冷轧过程中向周围物质提供随机成核位点,钛通过防止组织的择优取向的形成可以降低平面各向异性。因此,可添加大量的Ti,但是,在Ti过量加入的情况下,可增加生产成本,并且由于随着沉淀温度升高以防细小的析出,可逐渐形成粗析出物,从而降低抗拉强度和屈服率。因此,钛的含量可为0.3%以下。
锑(Sb):0.005wt%至0.02wt%
Sb用于保证本发明的钢的可涂覆性并抑制AlN和Al2O3于高温下在晶界处的形成。由于Sb超过溶解度极限,并且高温下在晶界处的偏析阻断了氧或氮扩散通过晶界,Sb不仅可抑制AlN和Al2O3在高温下形成,而且也可阻止晶界偏析和具有强的高温氧化趋势的元素(如Al、Si和Mn)的扩散路径。因此,通过抑制表面聚集的氧化物可以提高熔融的锌和基体钢板之间的润湿性,从而Sb对于镀层的附着性是重要的。基于这个目的,可添加0.005%以上量的Sb,但是,在过度添加Sb的情况下,由于晶界处的以熔融状态存在的Sb的量的增加,热延性降低。因此,Sb的含量可为0.2%以下。
除了上述合金元素和组成范围,本发明的钢板的组分体系可以满足以下组分关系。
[关系式1]
0.25×Ti/C:0.17至1.0
关系式1代表当TiC析出物高度细化时,用于有效地获得晶粒细化的条件,并且通过关系式1可有效保证强度和屈服率。另外,通常已知的是TiC析出物不具有降低平面各向异性的作用,反而增加平面各向异性。然而,在本发明的铁素体轻质钢板中,TiC析出物可有效地降低平面各向异性,同时可保证优异的强度和屈服率。在0.25×Ti/C的值小于0.17的情况下,由于可能发生晶粒粗化,以及析出物导致的对位错运动的抑制较弱,不能保证0.8以上的屈服率。在0.25×Ti/C的值大于1的情况下,由于TiC析出物的粗化,屈服率可能反而降低,并且,由于所添加的Ti的量的增加,生产成本可能增加。因此,关系式1中的0.25×Ti/C的值可在0.17至1.0的范围内。
[关系式2]
Mn/Al×Log(C×Ti×10000):1.0至10
除了关系式1,关系式2是另一个重要参数(以下称为“强化指数”)。C和Mn作为奥氏体形成元素提高钢的强度和延性。然而,在C和Mn含量高的情况下,由奥氏体分解出的第二相可能增加,具体地,在包括Al的钢中,可以促进奥氏体中的第二相的浓度,以增加具有高脆性的第二相(如FeAl、Fe3Al和(Fe,Mn)3AlC,以及Al)的占比。因此,可形成热轧和冷轧裂缝。因此,可发生热轧和冷轧处理中的限制。在本发明中,由于使用各种公式分析Mn、Al、C和Ti的作用,可以确定强度与Mn/Al×Log(C×Ti×10000)的值(称为强化指数)是成正比的。在强化指数为1以上的情况下,易于制造具有540MPa以上的抗拉强度的低比重轻质钢板,其中,由于TiC析出物引起的晶粒细化,不会形成裂缝并可显著降低平面各向异性。然而,在Mn、Ti和C的含量相对较高或Al的含量较低的情况下,由于具有高浓度的Mn的(Fe,Mn)3C的形成或κ碳化物团簇条结构的形成,冷轧过程中容易形成裂纹。因此,强化指数可为10以下。
本发明的钢板是一种包括具有铁素体为主要结构的微观结构的铁素体轻质钢板。本发明的钢板可具有100%的铁素体微观结构以保证机械性能,如优异的抗拉强度、屈服强度和延性,但是由于制造过程,可能不可避免地形成如马氏体的微观结构。
另外,在本发明中,可包括一种以上选自TiC、(Fe,Mn)3AlC、(Fe,Al)3C和(Fe,Mn)3C的析出物,并且通过上述析出物可以改进物理性能,如晶粒细化、强度和屈服率。
通过析出物的形成,本发明的钢板可具有10μm以下的平均晶粒直径。通过使晶粒如上述被细化,可保证强度和屈服率在一个优异的水平。由于晶粒直径较细时可示出理想的效果,所以在本发明中不具体限制晶粒直径的下限。然而,由于制造方法,晶粒直径不可被控制为小于1μm,所以平均晶粒直径可在1μm至10μm的范围内。
本发明的钢板相比常规钢具有5%以上的比重降低率,如相比590DP钢或超低碳钢,其通常具有7.84g/cc的比重,并且本发明的钢板具有540MPa以上的抗拉强度,0.8以上的屈服率,17,000MPa%以上的抗拉强度×伸长率(TS×El)的值,以及0.3以下的平面各向异性。在钢板由于相对于抗拉强度较高的屈服强度而具有低比重,优异的比强度,以及特别地优异的刚度,从而被用做面板材料的情况下,不仅形状冻结性能(shapefreezing properties)是优异的,而且延性也高,因此,一般部件可以用较薄的部件取代。因此,产品中的减重效果相对较大。
同时,平面各向异性是表示在每个方向上的材料的塑性变形的程度差异的一个指标。当平面各向异性高时,由于每个方向的塑性变形的差异大,拉杯中的凸耳的量增加,因此,被去除的部分大大增加。最终,材料的产率变低,且成形的产品中的残余应力增加,从而导致畸变或成形缺陷。因此,平面各向异性的值可以较低。可以如下定义平面各向异性。
平面各向异性(△r)=(r0+r90-2r45)/2
此处,r0、r45和r90分别为在相对于轧制方向的0°、45°和90°的Lankford(r)值,并且通过测定15%的变形前的宽度和15%的变形后的宽度之间的差值可以获得r的值。
同时,本发明的钢板可为热轧钢板、冷轧钢板和电镀钢板中的任意一种,电镀钢板可包括选自锌(Zn)基、Zn-Fe基、Zn-Al基、Zn-镁(Mg)基、Zn-Al-Mg基、Al-Si基和Al-Mg-Si基的镀层以提高耐腐蚀性。另外,镀层可具有10μm至200μm范围内的平均厚度。在镀层的平均厚度小于10μm的情况下,基体钢板的耐腐蚀性的提高可能是不显著的,而在镀层的平均厚度大于200μm的情况下,耐腐蚀性的提高效果可能受限制,因此,制造成本会增加。
下文将描述本发明的制造方法。
首先,将满足上述合金组分和组成范围的钢坯再加热,然后将再加热的钢坯在850℃以上的温度热轧以获得热轧钢板。所述再加热可在本领域公知的一般条件下进行,例如可在900℃至1350℃的温度范围内进行。在尽可能低的温度下的最终热轧可以有效获得细晶粒,并且用于晶粒的细化的热轧温度可为850℃或850℃以上、Ar3温度或Ar3温度以上。在热轧温度低于850℃的情况下,热轧过程中可形成铁素体以形成奥氏体条结构,并且由于κ碳化物的析出增加平面各向异性,可形成瘦长的结构。同时,不具体限制热轧温度的上限,但热轧可以在1200℃以下的温度进行,因为在热轧温度过高的情况下,制造成本可增加并可发生晶粒粗化。
此后,如此得到的热轧钢板可在500℃至700℃范围内的温度下被卷取。在700℃以下的温度下卷取的原因是抑制κ碳化物的粗化和过度析出,并防止粗晶粒的二次再结晶现象导致的异常粗大的晶粒的形成。在卷取温度低于500℃的情况下,TiC的析出可能是不足的,且可能不形成κ碳化物,而是可以形成大量的马氏体。因此,退火后不仅强度是不足的,且屈服强度也可能降低,因此,不能保证刚度。
同时,本发明的制造方法还可包括在热轧钢板的卷取后的冷轧以获得冷轧钢板。在卷取后可进一步实施酸洗处理以除去在高温下形成的氧化物。可在压缩率为40%至90%的范围内进行冷轧轧制。在冷压缩率为40%以上的情况下,可以保证由于冷轧而存储的能量,并可以获得新的再结晶结构。特别地,当冷压缩率较高时,具有{001}<110>至{110}<110>之间的取向和提高平面各向异性的粗晶粒可能会破碎,并在随后的退火处理中可再结晶成具有最低的平面各向异性的{111}<110>至{111}〈112〉组织。然而,在冷压缩率大于90%的情况下,由于在卷板的角上可形成裂纹,以及冷轧钢板的表面积增加的现象导致已知由表面剪切变形形成的{110}<110>组织强烈地发展,冷压缩率可为90%以下。例如,冷压缩率可在60%至80%的范围内。
此后,可将由此获得的冷轧钢板以1℃/s至20℃/s范围内的速率加热至再结晶温度(Tnr)至900℃范围内的温度。在加热速率小于1℃/s的情况下,产率会降低,且由于长时间暴露于高温下,可能发生晶粒粗化和强度降低,从而降低材料等级。在加热速率大于20℃/s的情况下,由于不充分的再结晶,延性会降低。在加热终止温度低于再结晶温度的情况下,由于会残留加工硬化结构而不能保证延性,在加热终止温度高于900℃的情况下,由于粗晶粒的形成而提高延性,但由于碳化物的重新溶解从而强度可能降低。
随后,所述冷轧钢板可在加热终止温度下退火10秒至180秒。所述退火处理用于充分发展可有效降低平面各向异性的{111}组织,基于此目的,退火时间可为10秒以上。然而,在退火时间大于180秒的情况下,产率可显著降低,并且由于用于热浸镀或合金化处理的时间的增加,耐腐蚀性和表面性能可能恶化。
同时,退火后的冷轧钢板可以按需进行冷却和过时效处理,并且所述冷却和过时效处理可以采用本领域公知的方法进行。例如,以1℃/s至100℃/s范围内的速率冷却退火后的冷轧钢板至200℃至500℃范围内的温度,然后进行等温热处理。
同时,在本发明中,对于如此获得的冷轧钢板可进一步进行电镀处理,经过此处理可提高钢板的耐腐蚀性。
下文将根据以下实施例详细描述本发明。然而,以下实施例仅仅用于举例说明本发明,且本发明的范围不局限于此。
具体实施方式
通过真空感应熔炼法(vacuum induction melting)制备了具有如下表1所描述的合金组成的钢坯,然后将所述钢坯在1200℃的温度下加热并从炉中取出。如下表2所示,在860℃至930℃范围内的温度下完成热轧以获得3mm至3.5mm厚的热轧钢板。将所制造的热轧钢板在350℃至720℃范围内的温度下卷取,保持1小时,然后将其随炉冷却至室温。然后,通过酸洗除鳞并进行冷轧以得到0.7mm至1mm厚的冷轧钢板。此后,通过以5℃/s的速率加热冷轧钢板,在下表2所示的条件下进行退火,并以20℃/s的速率将所述冷轧钢板快速冷却至400℃,以及通过在等温热处理100秒后空冷所述冷轧钢板至室温而制得最终的冷轧钢板。测定了所制造的冷轧钢板的力学性能,其结果在下表3中示出。此时,以这样的方式测定了比重,其中,制备尺寸为100mm×100mm的钢板,在室温下测定其重量,所述钢板被0.05mm粗的丝悬挂,将所述钢板浸泡在盛有室温下的水的烧杯中,然后测定其重量。此时,水的比重为1g/cc,作为比重降低率的参照的钢的比重为7.84g/cc。以这样的方式测定了制耳率,其中,制造了具有95mm的直径的圆形形状的钢板,通过使用具有50mm的直径的冲头实施拉拔以具有1.9的拉拔率,测定了由此制备的杯的最大高度(杯的凸出高度)和最小高度(杯的谷深),然后利用方程计算了制耳率,(最大高度-最小高度)/最大高度。钢板伸长了15%的量,通过测定的伸长前后的宽度的变化的数值获得了平面各向异性。在对比实施例5的情况下,描述了在10%的伸长率后得到的结果。
[表1]
[表2]
[表3]
如表1至表3所示,对于满足本发明所提出的合金组分、组成范围和制造条件的发明实施例1至5,可以理解的是TS×El的值为17,000MPa以上,因为抗拉强度和延性都是优异的。另外,由于比重比常规钢的比重低5%以上,可以理解的是,有效达到了产品的减重。特别地,可以理解的是,当屈服率为0.8以上时,刚度也是非常优异的,并且,当制耳率在2%以内时,可以提高产品的实际产量。
相比较,在检测满足本发明所提出的组分体系、但不满足制造条件的对比实施例1至3时,TiC和碳化物析出对于对比实施例1来说是不充足的,因为没有满足卷取温度条件。所以,由于未防止晶粒生长,屈服率低且强度也低是可以理解的。对于对比实施例2,尽管通过在合适的温度范围内的卷取使细小析出物充分地分散,但由于高的退火温度而发生了晶粒生长,因此,屈服率相对较低且抗拉强度显著降低是可以理解的。对于对比实施例3,由于不充足的退火时间导致未完成再结晶,从而轧制结构保持不变,因此,伸长率为相当低的水平是可以理解的。由于这样低的伸长率导致不可拉拔,因此无法测定制耳率,并且由于钢板在用于测定平面各向异性的伸长过程中断裂,因此也无法测定平面各向异性。
同时,对比实施例4至10采用不满足本发明所提出的组分体系的钢,其中可以理解的是,强度或伸长率低,或制耳率高。同样,对于对比实施例5,由于低伸长率导致不可拉拔,所以无法测定制耳率。对于对比实施例8至10和12,可以理解的是,裂缝在冷轧过程中形成于钢板的角上。特别地,对于对比实施例8,由于钢板在轧制初始阶段就断裂了,因此甚至不能制造冷轧样品。
基于上述结果,图1中示出了Al含量和比重降低率之间的关系的图表。如图1所示,可以理解的是,必须包括4%以上的量的Al以获得5%以上的优异的比重降低率。
图2是示出0.25×Ti/C的值和屈服率之间关系的图表。如图2所示,可以理解的是,当0.25×Ti/C的值为0.17或以上时,细小的TiC析出物被充分分散,因此,可以得到0.8以上的屈服率。然而,在0.25×Ti/C的值大于1的情况下,可以理解的是,由于粗TiC析出物,沉淀强化效应反而消失了。
图3是示出平面各向异性和制耳率之间关系的图表。如图3所示,在平面各向异性为0.3以下的情况下,可以理解的是,制耳率被最小化,其中制耳率为2%以下。然而,在制耳率大于0.3的情况下,可以理解的是制耳率增加,因此,产品的产量会降低。
图4是示出强化指数和抗拉强度之间的关系的图表。如图4所示,可以理解的是以Mn/Al×Log(C×Ti×10000)表示的强化指数与抗拉强度是成正比的。在强化指数为1或以上的情况下,可以理解的是可以制造具有540MPa以上的抗拉强度的轻质钢板,其中,由于由TiC析出物引起的晶粒细化,不会形成裂缝并可以最小化平面各向异性。
Claims (12)
1.铁素体轻质高强度钢板,其包含:
0.02wt%至0.1wt%的碳(C);
4wt%至15wt%的锰(Mn);
4wt%至10wt%的铝(Al);
2.0wt%以下(不包含0)的硅(Si);
0.01wt%至0.3wt%的钛(Ti);
0.005wt%至0.2wt%的锑(Sb);以及
作为剩余部分的铁(Fe)和不避免的杂质,
其中,0.25×Ti/C的值在0.17至1.0的范围内,Mn/Al×Log(C×Ti×10000)的值在1.0至10的范围内。
2.根据权利要求1所述的铁素体轻质高强度钢板,其中,所述钢板包含选自TiC、(Fe,Mn)3AlC、(Fe,Al)3C和(Fe,Mn)3C的一种或多种析出物。
3.根据权利要求1所述的铁素体轻质高强度钢板,其中,钢板中的晶粒的平均直径为10μm以下。
4.根据权利要求1所述的铁素体轻质高强度钢板,其中,钢板具有7.2g/cc以下的比重,540MPa以上的抗拉强度,0.8以上的屈服率,17,000MPa%以上的抗拉强度×伸长率(TS×El),以及0.3以下的平面各向异性。
5.根据权利要求1所述的铁素体轻质高强度钢板,其中,所述钢板为热轧钢板、冷轧钢板和电镀钢板中的任意一种。
6.根据权利要求5所述的铁素体轻质高强度钢板,其中,所述电镀钢板包含选自锌(Zn)基、Zn-Fe基、Zn-Al基、Zn-镁(Mg)基、Zn-Al-Mg基、Al-Si基和Al-Mg-Si基的镀层。
7.根据权利要求5所述的铁素体轻质高强度钢板,其中,所述电镀钢板包含具有10μm至200μm范围内的平均厚度的镀层。
8.一种制造铁素体轻质高强度钢板的方法,所述方法包括:
再加热钢坯,所述钢坯包含0.02wt%至0.1wt%的C,4wt%至15wt%的Mn,4wt%至10wt%的Al,2.0wt%以下(不包括0)的Si,0.01wt%至0.3wt%的Ti,0.005wt%至0.2wt%的Sb,以及作为剩余部分的Fe和不可避免的杂质,并具有0.17至1.0范围的0.25×Ti/C的值和1.0至10范围内的Mn/Al×Log(C×Ti×10000)的值,然后在850℃以上的温度热轧所述钢坯以获得热轧钢板;以及
在500℃至700℃的温度范围内卷取所述热轧钢板。
9.根据权利要求8所述的方法,还包括:
在所述热轧钢板的卷取后冷轧所述热轧钢板以获得冷轧钢板;
以1℃/s至20℃/s范围内的速率将所述冷轧钢板加热至Tnr至900℃范围内的温度,其中Tnr为再结晶温度;以及
将所述加热的冷轧钢板退火10秒至180秒。
10.根据权利要求9所述的方法,其中,以40%至90%范围内的压缩率实施冷轧。
11.根据权利要求9所述的方法,还包括:退火后,在以1℃/s至100℃/s的速率将所述冷轧钢板冷却至200℃至500℃范围内的温度后进行等温热处理。
12.根据权利要求9所述的方法,还包括在退火后电镀所述冷轧钢板。
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CN102301027A (zh) * | 2009-02-02 | 2011-12-28 | 杰富意钢铁株式会社 | 高强度热镀锌钢板及其制造方法 |
CN102341517A (zh) * | 2009-04-14 | 2012-02-01 | 新日本制铁株式会社 | 切削性优异的低比重锻造用钢 |
CN102471852A (zh) * | 2009-07-28 | 2012-05-23 | 杰富意钢铁株式会社 | 高强度冷轧钢板及其制造方法 |
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CN104603308B (zh) | 2017-07-28 |
WO2014038759A1 (en) | 2014-03-13 |
EP2893050B1 (en) | 2019-03-13 |
EP2893050A4 (en) | 2016-06-01 |
KR101449119B1 (ko) | 2014-10-08 |
US9856542B2 (en) | 2018-01-02 |
JP2015532682A (ja) | 2015-11-12 |
KR20140030969A (ko) | 2014-03-12 |
JP6159802B2 (ja) | 2017-07-05 |
EP2893050A1 (en) | 2015-07-15 |
US20150218668A1 (en) | 2015-08-06 |
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