CN101336303B - 热轧、微合金化的低碳钢带材 - Google Patents

热轧、微合金化的低碳钢带材 Download PDF

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CN101336303B
CN101336303B CN2006800518264A CN200680051826A CN101336303B CN 101336303 B CN101336303 B CN 101336303B CN 2006800518264 A CN2006800518264 A CN 2006800518264A CN 200680051826 A CN200680051826 A CN 200680051826A CN 101336303 B CN101336303 B CN 101336303B
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乔瓦尼·阿尔维迪
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Abstract

通过在决不低于900℃的预带材温度下热轧获得微合金化的低碳钢带材，所述钢带材显示出这样的冶金学和几何学特性，以及涉及平面度和可变形性，使得该带材适宜于获得具有低重量且良好机械抗力的结构，因此能用于替代冷轧带材来生产成品的冲压或切割的工件。具有＞0.7mm厚度的所述钢带材，具有＞70％的屈服载荷/破坏载荷比，在整个组织高于90％的比例中具有优于ASTM E112标准10级的细晶粒组织，及应变下的破坏极限与屈服点之比σFP/Rp0.2＞90％。

Description

热轧、微合金化的低碳钢带材 
技术领域
本发明涉及低碳微合金化钢带材，所述带材显示出如下特性：在生产冲压或切割的成品工件中能够取代冷轧带材，所述冷轧带材至今仍用于获得具有降低的重量和良好机械强度的结构。 
背景技术
例如从JP2003253381、WO03/087414、US6.488.790可知晓用于生产热轧微合金化带材的方法。 
所述微合金化或HSLA“高强度低合金”钢得名的原因是包含少量的铌、钒、钛和硼的添加，它们几乎不超过总量的0.2％。这些元素并不是作为合金添加剂进入铁的晶格，它们的作用是与基体中的碳和氮结合并因此形成细分散的碳化物、氮化物和碳氮化物。这些化合物促进晶粒细化，并利用它们在铁素体晶粒中的析出使得基体硬化。 
还已知，这些钢特别用于如下应用：希望降低将要获得的结构的重量，而不负面地影响其机械强度。它们的特别特征是显示出接近破坏载荷值的屈服点值，这两个值之间的比值高于70％。因此，有可能通过降低应力抵抗截面获得这些结果，同时与此相反，因屈服和破坏载荷的接近，材料可具有高弹性，当承受强的弹性回复时引起成品工件在受压时呈现不期望的外形。因此，用途限于不需要成品工件具有过严公差的情况。 
发明内容
本发明的目的是提供具有≥0.7mm厚度的热轧、微合金化低碳钢的带材，该带材特别在酸洗和表皮光轧时，显示出与生产冲压或剪切的成品工件的冷轧带材基本相同的冶金学和几何特性，以及涉及平面性和可变形性，例如有待用作该冷轧带材的有效的替代品。 
依据本发明的带材优选地(而不专门地)通过薄板坯型的生产线内设备制成，如本申请人的WO2004/026497所公开的，其示意显示在图1中，且如权利要求1所述其特征在于整个组织中百分数＞90％的晶粒具有优于ASTM E 112标准10级的细度，屈服点和破坏载荷之比≥70％。 
附图说明
将由下面参照附图的描述而更加清楚依据本发明的微合金化钢带材的目的、优势和特征，其中： 
图1示意显示了薄板坯铸造和生产线内轧制设备，该设备特别适宜于生产依据本发明的微合金化钢带材； 
图2显示了在一些依据本发明的带材卷中分别在每个带材卷的头部、中间和尾部统计地检测到的特定尺寸铁素体晶粒存在的频率的点线图； 
图3显示了依据本发明钢的应变极限趋势的图解，具有355N/mm2 的保证屈服载荷。 
具体实施方式
如上所述，依据本发明的微合金化钢带材优选地(而不专门地)在如图1示意显示的薄板坯设备中生产，其中特别参考作为国际公开WO2004/026497目的的设备。可观察到下述工作步骤，铸造步骤的下游：a)液芯压下；b)直接邻接连续铸造的粗加工步骤；c)在感应炉中加热；e)精轧；f)坯体受控冷却；g)在轴上卷绕。这样的设备可以在终轧前的步骤中保持预带材(d)的温度高于900℃。高于上述900℃的预带材轧制允许通过充分利用它们的如下作用将大部分微合金化添加剂保持溶于γ铁(奥氏体相)中：在终轧后的冷却步骤期间限制奥氏体晶粒长大和增强铁素体相中的析出硬化。 
应注意，这些方面在传统工艺中通常被忽视，其中来自连续铸造的板坯被冷却并随后为终轧而加热。因此，微合金化添加剂的作用显 著降低，因为在冷却时，这些析出物粗大且不受控，因此降低了微细且扩散的析出物的期望作用。这种条件即使在随后的板坯加热的过程中也不会恢复，除非达到高的增溶温度(高于1200℃)，然而这也会导致其它负面结果，如晶粒生长和带材的表面脱碳并因此使它们的性质恶化。结果，HSLA的生产，尤其是＜2mm的厚度的HSLA的生产，利用传统的系统只能通过更复杂和麻烦的工艺循环来进行，因为在热轧后，必须冷轧带材，以及在具有受控冷却的退火线中处理。 
依据本发明的微合金化钢带材显示出等于或高于70％的屈服和破坏载荷之比，以及在冷条件下良好的成型和切割能力。这些特性是因为有利的显微组织状态使得该产品能够允许成为同等厚度冷轧微合金化钢带材的有效替代，较少添加微合金化和合金化元素，如铌、钒、钛、锰和铬(如表1所示)，获得了其它优势。 
实验测试显示，本发明的带材的特征在于，在整个组织中高于90％的百分比下具有优于ASTM E 112标准10级的细晶粒组织，如可从图2中的曲线得到，清楚地显示了大部分晶粒(特别是在带材的头部)，具有与ASTM E 112标准10级相应或更低(因此具有更好的细度)的尺寸。晶粒细度和均匀性的这些特性使这种热轧带材特别抵抗疲劳测试。如从图3可见，显示了在依据本发明的带材中进行的实验测试，应变抗力高于用传统工艺所得产品的应变抗力，并且与同级冷轧带材的应变抗力相当。应注意，这既发生于“最终应变”范围，即对于载荷极限值，在该值下当工件经受低于107的N次循环时发生破坏，又发生于“不确定应变”范围内，即由实验测试确定的极限载荷，在该极限载荷下，即使工件承受的应变循环次数高于传统用于钢的次数(即N＝107)工件也不会破坏。特别地，发现对于S355MC钢在N＝107循环(对应于357N/mm2)检测到的应变抗力更优，具有5-10％的余量(margin)，与50％的无破坏几率一致。另外，在平面弯曲产生的应变下破坏点(σFP)和屈服点之间的比值σFP/Rp0.2接近1，且等于0.96，因此经常高于与对比热轧材料基准相关的比值(在0.88和0.90之间)，实际对应于对同级冷轧带材检测到的相同比值的值。 
这些带材的特别细的显微组织使得这些带材适宜于最终切割和通过冲孔在其中形成孔，以及冷成型复杂形状，特别是对于具有最低保证屈服载荷(在275和700N/mm2之间)的高强度钢，以等于厚度的弯曲半径折叠180°。具有复杂形状工件的冷成型因带材的恒定剖面和其偏差低于0.05mm的平行度而更加容易。 
不同的钢等级具有包含在下表1中所列极限内的化学分析结果： 
  元素   含量(％)
  C   0.04-0.08
  Mn   0.15-2.0
  Si   0.06-0.60
  P   最大0.010
  S   最大0.010
  Cr   最大0.35
  Ni   最大0.20
  Mo   最大0.25
  Cu   最大0.20
  Nb   0.012-0.070
  V   0.02-0.03
  Ti   ≤0.11
  Al   0.025-0.050
  N   最大0.0115
从上表可以推出，微合金化元素(V、Ti和Nb)的总量不超过0.2％。 

Claims (5)

1.热轧、微合金化的低碳钢带材，具有不小于0.7mm的厚度和细晶粒显微组织，在精轧的上游，将所述钢带材的预带材保持在不小于900℃的温度，适宜于通过冷压和切割获得成品工件，其具有275-700N/mm2的屈服载荷，其特征在于，至少90％的晶粒具有优于ASTM E 112标准10级的细度，应变下的破坏极限和屈服载荷的比值σFP/Rp0.2不小于90％，以及屈服载荷和破坏载荷之间的比值不小于70％，只有在进行酸洗和表皮光轧时，这些冶金学和几何学特性基本与冷轧带材的特性相同。
2.依据权利要求1的热轧、微合金化的低碳钢带材，其特征在于厚度的公差不大于0.05mm。
3.依据权利要求1的热轧、微合金化的低碳钢带材，其特征在于不包含硼添加剂作为微合金化元素。
4.依据权利要求3的热轧、微合金化的低碳钢带材，其特征在于微合金化元素的总含量不超过0.2％。
5.依据权利要求3的热轧、微合金化的低碳钢带材，其特征在于微合金化元素V、Ti和Nb的总含量不超过0.2％。
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