CN116568828A - 经涂覆的钢板和高强度压制硬化钢部件及其制造方法 - Google Patents

经涂覆的钢板和高强度压制硬化钢部件及其制造方法 Download PDF

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CN116568828A
CN116568828A CN202180082401.4A CN202180082401A CN116568828A CN 116568828 A CN116568828 A CN 116568828A CN 202180082401 A CN202180082401 A CN 202180082401A CN 116568828 A CN116568828 A CN 116568828A
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steel sheet
equal
less
steel
layer
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克莱芒·菲利波
桑德拉·勒吉亚尔
大卫·迪索苏瓦
马蒂厄·萨利布
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ArcelorMittal SA
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Abstract

本发明涉及经涂覆的钢板和压制硬化钢部件，其具有包含以下的组成：C：0.26重量％至0.40重量％，Mn：0.5重量％至1.8重量％，Si：0.1重量％至1.25重量％，Al：0.01重量％至0.1重量％，Cr：0.1重量％至1.0重量％，Ti：0.01重量％至0.1重量％，B：0.001重量％至0.004重量％，P≤0.020重量％，S≤0.010重量％，N≤0.010重量％，组成的剩余部分为铁和由熔炼产生的不可避免的杂质。所述压制硬化钢部件包括：主体，所述主体的显微组织包含以表面分数计多于95％的马氏体和少于5％的贝氏体；在钢部件的表面处的涂层；在涂层与主体之间的铁素体相互扩散层，以及相互扩散层中的铁素体晶粒宽度GW相互扩散层与主体中的原始奥氏体晶粒尺寸PAGS主体之间的比率满足以下方程式(GW相互扩散层/PAGS主体)‑1≥30％。

Description

经涂覆的钢板和高强度压制硬化钢部件及其制造方法
本发明涉及经涂覆的钢板，并且涉及具有良好的弯曲特性的高强度压制硬化钢部件。
高强度压制硬化部件可以在汽车中用作用于防入侵或能量吸收功能的结构元件。
在这种类型的应用中，期望生产高机械强度、高抗冲击性和高抗腐蚀性相结合的钢部件。此外，鉴于全球环境保护，汽车行业的主要挑战之一是在不忽视安全要求的情况下减小车辆的重量以提高其燃料效率。
重量减少可以特别地由于使用具有马氏体或贝氏体/马氏体显微组织的钢部件而实现。
出版物WO2016104881涉及用作车辆等的结构部件的热压成型部件，所述热压成型部件需要抗冲击特性，并且更特别地具有1300MPa或更大的拉伸强度；以及通过将钢材加热至可以形成奥氏体单相的温度，淬灭并使用模具使其热成型来制造所述热压成型部件的方法。为了获得这样的特性，基底钢板在表面处包括小于50μm的薄铁素体层，并且应控制碳化物尺寸和密度。基体中的铁素体层允许抑制镀层上形成的细裂纹蔓延到基底，而导致弯曲角小于70°的低弯曲性。
出版物WO2018179839涉及通过对钢板进行热压获得的热压部件，所述钢板具有在厚度方向上变化的显微组织，具有由至少90％铁素体制成的软质层、由铁素体和马氏体制成的过渡层以及主要为马氏体的硬质层，并且具有高强度和有高弯曲性二者。为了获得这样的特性，将冷轧钢板在露点温度为50℃至90℃的气氛下退火，这可能对铝合金涂层有害。
因此本发明的目的是解决上述的问题并且提供拉伸强度TS大于或等于1500MPa的高机械特性和大于70°的弯曲角相结合的压制硬化钢部件。优选地，根据本发明的压制硬化钢部件具有大于或等于1250MPa的屈服强度YS。
本发明的另一个目的是获得可以通过热成型转变为这样的压制硬化钢部件的经涂覆的钢板。
本发明的目的通过提供根据权利要求1的钢板实现。另一个目的通过提供权利要求2的方法实现。本发明的另一个目的通过提供根据权利要求3的压制硬化钢部件实现。钢部件也可以包括权利要求4至6中任一项的特性。另一个目的通过提供根据权利要求7的方法实现。
现在参照附图，通过不引入限制的实例详细描述并说明本发明：
-图1a示出未根据本发明的试验4的经涂覆的钢板的示意性截面；
-图1b表示未根据本发明的试验4的压制硬化钢部件的示意性截面；
-图2a示出未根据本发明的试验3的经涂覆的钢板的示意性截面；
-图2b表示未根据本发明的试验3的压制硬化钢部件的示意性截面；
-图3a示出根据本发明的试验2的经涂覆的钢板的示意性截面；
-图3b表示根据本发明的试验2的压制硬化钢部件的示意性截面；
-图4a示出根据本发明的试验1的经涂覆的钢板的示意性截面；
-图4b表示根据本发明的试验1的压制硬化钢部件的示意性截面；
-图5a示出未根据本发明的试验5的经涂覆的钢板的示意性截面；
-图5b表示未根据本发明的试验5的压制硬化钢部件的示意性截面。
现在描述根据本发明所述的钢的组成，含量以重量百分比表示。
根据本发明，碳含量为0.26％至0.40％，以确保令人满意的强度。碳大于0.40％时，钢板的可焊性和弯曲性可能降低。如果碳含量低于0.26％，则拉伸强度将达不到目标值。
锰含量为0.5％至1.8％。添加高于1.8％，中心偏析的风险增加，有害于弯曲性。低于0.5％，钢板的淬透性降低。优选地锰含量为0.5％至1.3％。
根据本发明，硅含量为0.1％至1.25％。硅是参与固溶体硬化的元素。添加硅以限制碳化物的形成。高于1.25％，在表面处形成氧化硅，其损害钢的可涂性。此外，钢板的可焊性可能降低。优选地，硅含量为0.2％至1.25％。更优选地，硅含量为0.3％至1.25％。更优选地，硅含量为0.3％至1％。
铝含量为0.01％至0.1％，因为铝是用于在加工期间使呈液相的钢脱氧的非常有效的元素。如果钛含量不足，则铝可以保护硼。铝含量低于0.1％以避免氧化问题和压制硬化期间铁素体形成。优选地铝含量为0.01％至0.05％。
根据本发明，铬含量为0.1％至1.0％。铬是参与固溶体硬化的元素，并且必须高于0.1％。铬含量低于1.0％以限制加工性能问题和成本。
钛含量为0.01％至0.1％以保护硼免于形成BN。钛含量被限制到0.1％以避免TiN形成。
根据本发明，硼含量为0.001％至0.004％。硼改善钢的淬透性。硼含量不高于0.004％以避免连铸期间板坯断裂的风险。
可以任选地添加一些元素。
镍可以作为任选元素被添加高至0.5％，因为镍可以显著地降低延迟断裂的敏感性。
钼含量可以任选地被添加高至0.40％。和硼一样，钼改善钢的淬透性。钼不高于0.40％以限制成本。
根据本发明，铌可以任选地被添加高至0.08％以改善钢的延性。添加高于0.08％，形成NbC或Nb(C,N)碳化物的风险增加，有害于弯曲性。优选地铌含量低于或等于0.05％。
钙也可以作为任选元素被添加高至0.1％。在液体阶段添加钙使得可以产生细的氧化物，这促进了连铸的可铸性。
钢的组成的剩余部分是铁和由熔炼产生的杂质。在这方面，至少P、S和N被认为是残余元素，其是不可避免的杂质。其含量对于S小于0.010％，对于P小于0.020％，对于N小于0.010％。
现在描述根据本发明的经涂覆的钢板的显微组织。
本发明的经涂覆的钢板的截面示意地表示在图3a和图4a中。经涂覆的钢板包括主体(2)；在所述主体(2)的顶部的脱碳层(3)，所述脱碳层(3)在上部包括厚度为1μm至100μm的铁素体层(4)；以及涂层(1)。优选地，铁素体层的厚度为20μm至100μm。更优选地，铁素体层的厚度为25μm至100μm。更优选地，铁素体层的厚度为30μm至80μm。
经涂覆的钢板的主体(2)的显微组织包含以表面分数计60％至90％的铁素体，剩余部分为马氏体-奥氏体岛、珠光体或贝氏体。
铁素体在冷轧钢板的临界区退火期间形成。在均热结束时显微组织的剩余部分为奥氏体，其在钢板冷却期间转变成马氏体-奥氏体岛、珠光体或贝氏体。
由于控制炉内气氛以设定露点温度严格高于-10℃且低于或等于20℃，在冷轧钢板退火期间获得存在于主体顶部上的脱碳层。
根据本发明的经涂覆的钢板可以通过任何合适的制造方法来生产并且本领域技术人员可以确定合适的制造方法。然而，优选使用根据本发明的方法，所述方法包括以下步骤：
提供能够被进一步热轧的具有上述钢组成的半成品。在1150℃至1300℃的温度下将半成品再加热。
然后在800℃至950℃的热轧终止温度下对钢板进行热轧。
然后使热轧钢冷却并且在低于670℃的温度T卷取下进行卷取，并且任选地进行酸洗以除去氧化物。
然后任选地对经卷取的钢板进行冷轧以获得冷轧钢板。冷轧压下率优选为20％至80％。低于20％，在后续热处理期间的再结晶不利，这可能损害钢板的延性。高于80％，在冷轧期间存在边缘开裂的风险。
然后使钢板在具有0％至15％的H2的HNx气氛下退火，到700℃至850℃的退火温度TA并在所述退火温度TA下保持10秒至1200秒的保持时间tA，以获得退火钢板。低于700℃，脱碳层的形成的动力学太缓慢以致无法在其上部获得铁素体层。保持时间tA大于或等于10秒以允许铁素体层形成，并且小于或等于1200秒以限制该铁素体层的厚度。
在该退火期间，控制炉内的气氛以具有严格高于-10℃且低于或等于+20℃的露点温度TDP1以形成根据本发明的脱碳层。如果TDP1低于或等于-10℃，脱碳层的形成变慢并且在脱碳层的上部中无法形成铁素体层。钢部件的弯曲性将太低。如果TDP1高于20℃，钢板的表面可能被完全氧化，损害钢板的可涂性和机械特性。
在本发明的一个实施方案中，将退火钢板加热至700℃至850℃的退火温度T2并在所述温度T2下保持10秒至1200秒的保持时间t2，气氛具有严格高于-10℃且低于或等于+20℃的露点温度TDP2。然后用铝合金涂层涂覆钢板。
现在描述根据本发明的压制硬化钢部件的显微组织。图3b和图4b示意地表示压制硬化钢部件的截面。
钢部件从钢部件的主体至表面连续地包括：
-主体(7)，所述主体(7)的显微组织包含以表面分数计多于95％的马氏体和少于5％的贝氏体，
-铁素体相互扩散层(6)，
-基于铝的涂层(5)。
在对从根据本发明的钢板切割的钢坯进行加热期间，主体的所有显微组织要素转变为奥氏体，并且脱碳层的铁素体转变为具有比主体的奥氏体更宽晶粒尺寸的奥氏体。在热成型之后，然后对钢部件进行模压淬火。相互扩散层从先前的宽晶粒尺寸奥氏体层生长，因此具有比主体中的原始奥氏体晶粒尺寸更大的晶粒宽度。为了在不使机械特性劣化的情况下改善钢板的弯曲性，相互扩散层中的铁素体晶粒宽度GW相互扩散层与主体中的原始奥氏体晶粒尺寸PAGS主体之间的比率满足以下方程式：
(GW相互扩散层/PAGS主体)-1≥30％
铁素体晶粒宽度为相互扩散层的两个平行晶粒边界之间的平均距离，晶粒边界沿钢板的厚度方向定向。根据本发明的退火温度TA、退火时间tA和露点温度TDP1的结合促进形成相互扩散层中的大晶粒宽度GW相互扩散层。此外，钢坯在压制成型之前的热处理控制奥氏体晶粒生长，从而控制了主体中的PAGS。
在一个实施方案中，压制硬化钢部件还可以包括在主体与相互扩散层之间的具有碳梯度的马氏体层，如图4b的(8)所表示的。在加热钢坯期间，碳从主体扩散到表面。然后脱碳层的铁素体上部转变为具有碳梯度的奥氏体层。在模压淬火期间，该具有碳梯度的奥氏体层转变为具有碳梯度的马氏体层。
根据本发明的压制硬化钢部件具有大于或等于1500MPa的拉伸强度TS和高于70°的弯曲角。弯曲角根据方法VDA238-100弯曲标准(归一化为1.5mm的厚度)在压制硬化部件上确定。
在本发明的一个优选实施方案中，屈服强度YS高于或等于1250MPa。根据ISO标准ISO 6892-1测量TS和YS。
根据本发明的压制硬化钢部件可以通过任何合适的制造方法来生产并且本领域技术人员可以确定合适的制造方法。然而，优选使用根据本发明的方法，所述方法包括以下步骤：
将根据本发明的经涂覆的钢板切割成预定的形状以获得钢坯。然后在10秒至900秒期间将钢坯加热至880℃至950℃的温度以获得经加热的钢坯。然后将经加热的钢坯转移至压型机，之后进行热成型和模压淬火。
现在通过以下实施例说明本发明，实施例绝不是限制性的。
实施例
将组成汇总在表1中的6个类别铸造成半成品，并加工成钢板，然后根据表2中汇总的工艺参数加工成钢部件。
表1-组成所测试的组成汇总在下表中，其中以重量百分比表示元素含量。
钢 C Mn Si Al Cr Ti B P S N Ni Mo Nb
A 0.34 0.6 0.56 0.043 0.32 0.017 0.002 0.009 0.0018 0.0027 0.43 0.19 0.052
B 0.32 0.7 0-35 0.03 0.5 0.026 0.002 0.014 0.0022 0.0059 0.028 0.21 -
C 0.36 0.6 0.53 0.035 0.34 0.014 0.003 0.011 0.001 0.0034 0.4 0.20 0.049
D 0.33 0.6 0.53 0.028 0.33 0.013 0.003 0.013 0.001 0.0041 0.4 0.17 0.046
E 0.36 1.3 0.28 0.003 0.25 0.02 0.003 0.01 0.002 0.006 - - -
E 0.21 1.2 0.27 0.018 0.15 0.037 0.002 0.01 0.002 0.006 0.012 - -
钢A至D是根据本发明的。
加下划线的值：不对应于本发明
表2-工艺参数
在1200℃下将作为铸件的钢半成品再加热，以800℃至950℃的热轧终止温度进行热轧，在550℃下进行卷取并以60％的压下率进行冷轧。然后将钢板加热至温度TA并在所述温度下在具有受控露点的含有5％H2的HNx气氛下持续保持时间tA。然后使钢板冷却至560℃至700℃的温度，然后用包含10％的硅的铝-硅涂层进行热浸镀。
在涂覆之前样品1、2、5和6在温度T2下经历第二退火，将钢板在所述T2温度下在具有5％H2和受控露点的HNx气氛中持续保持时间t2。应用以下具体的条件：
加下划线的值：不对应于本发明
对经涂覆的钢板进行分析，并将脱碳层的相应特性汇总在表3中。
表3-经涂覆的钢板的脱碳层的特性
加下划线的值：不对应于本发明
然后，将经涂覆的钢板切割以获得钢坯，在900℃下加热6分钟并进行热成型。对钢部件进行分析，并将相应的显微组织、相互扩散层中的铁素体晶粒宽度GW相互扩散层和主体中的原始奥氏体晶粒尺寸PAGS主体汇总在表4中。将机械特性汇总在表5中。
表4-压制硬化钢部件的显微组织
加下划线的值：不对应于本发明
n.d.：未确定
通过以下方法确定表面分数、相互扩散层中的铁素体晶粒宽度和PAGS：从压制硬化钢部件中切割试样，抛光并用本身已知的试剂蚀刻以露出显微组织。之后通过光学显微镜或扫描电子显微镜，例如用与BSE(背散射电子)装置连接的具有场发射枪的扫描电子显微镜(“FEG-SEM”)在大于5000倍的放大倍数下检查截面。
表5-压制硬化钢部件的机械特性
确定了测试样品的机械特性并汇总在下表中：
加下划线的值：与目标值不匹配
实施例显示由于其特定的组成和显微组织，根据本发明的钢部件(即实施例1至2)是唯一显示出所有目标特性的钢部件。
图3a表示试验2的经涂覆的钢板的示意性截面。本发明的工艺参数、退火温度TA、退火时间tA和露点温度TDP1的结合允许获得脱碳层(3)，在所述脱碳层(3)中在上部形成有铁素体层(4)。
然后使经涂覆的钢板热成型。图3b表示试验2的压制硬化钢部件的示意性截面。
在相互扩散层(5)中形成的铁素体的晶粒宽度是由纯铁素体层产生的，在所述纯铁素体层中在加热期间发生较大晶粒尺寸的奥氏体形成。相互扩散层在这个大的奥氏体晶粒尺寸上生长。然后相互扩散层(6)中的铁素体的晶粒宽度大于主体(7)中的原始奥氏体晶粒尺寸，产生弯曲角高于70°的良好弯曲性。
图4a表示试验1的经涂覆的钢板的示意性截面。本发明的工艺参数、退火温度TA、退火时间tA和露点温度TDP1的结合允许获得脱碳层(3)，在所述脱碳层(3)中，因更高的C含量而在上部中形成比试验1中更厚的铁素体层(4)。
然后使经涂覆的钢板热成型。图4b表示试验1的压制硬化钢部件的示意性截面。
在相互扩散层(6)中形成的铁素体晶粒宽度是由纯的铁素体层产生的，在所述纯的铁素体层中在加热期间发生较大晶粒尺寸的奥氏体形成。相互扩散层在这个大的奥氏体晶粒尺寸上生长。然后相互扩散层(6)中的铁素体晶粒宽度大于主体(7)中的原始奥氏体晶粒尺寸，产生弯曲角高于70°的良好弯曲性。此外，由于经涂覆的钢板中的厚铁素体层(4)，在压制硬化钢部件的主体与相互扩散层之间形成具有碳梯度的马氏体层，产生高于1500MPa的拉伸强度。
在试验3中，经涂覆的钢板具有脱碳层，在脱碳层的上部没有铁素体层，如图2a示意性地表示。没有铁素体层是由于-10℃的低露点温度，其使脱碳的动力学变慢。
然后使经涂覆的钢板热成型。图2b表示试验3的压制硬化钢部件的示意性截面。由于没有铁素体层，因此相互扩散层(6)中的铁素体晶粒宽度等于主体(7)中的原始奥氏体晶粒尺寸，导致低于70°的低弯曲角。
在试验4中，-40℃的低露点温度意味着在经涂覆的钢板中没有脱碳层和铁素体层。
图1a表示该试验的具有涂层(1)和主体(2)的经涂覆的钢板的示意性截面。
然后使经涂覆的钢板热成型。图1b表示试验4的压制硬化钢部件的示意性截面。由于没有铁素体层，因此相互扩散层(6)中的铁素体晶粒宽度等于主体(7)中的原始奥氏体晶粒尺寸，导致低于70°的低弯曲角。
在试验5中，将钢板在均热温度下保持10800秒，这在经涂覆的钢板中在脱碳层中形成比先前试验更厚的铁素体层。图5a表示试验5的经涂覆的钢板的示意性截面，所述经涂覆的钢板具有涂层(1)、脱碳层(3)、具有更粗晶粒尺寸的更厚的铁素体层(4)和主体(2)。
然后使经涂覆的钢板热成型，并且图5b表示试验5的压制硬化钢部件的示意性截面。在加热钢部件期间，主体的显微组织是奥氏体，并且厚的铁素体层转变为具有碳梯度的奥氏体层。但是由于铁素体层的厚度大于100μm，在相互扩散层与具有碳梯度的奥氏体层之间仍然存在铁素体层。
在钢部件的模压淬火期间，铁素体层仍然存在并且具有碳梯度的奥氏体层转变为具有碳梯度的马氏体层，导致多相层。这引起屈服强度降低。
在试验6中，钢板具有0.21％的低的碳水平。这样低的碳含量与工艺参数结合在经涂覆的钢板中产生具有铁素体层的脱碳层。尽管如此，由于碳的水平低，没有实现压制硬化钢部件的屈服强度和拉伸强度。

Claims (7)

1.一种经涂覆的钢板，所述经涂覆的钢板由具有包含以下的组成的钢制成：
C：0.26重量％至0.40重量％
Mn：0.5重量％至1.8重量％
Si：0.1重量％至1.25重量％
Al：0.01重量％至0.1重量％
Cr：0.1重量％至1.0重量％
Ti：0.01重量％至0.1重量％
B：0.001重量％至0.004重量％
P≤0.020重量％
S≤0.010重量％
N≤0.010重量％
以及任选地包含以下元素中的一种或更多种：
Ni≤0.5重量％
Mo≤0.40重量％
Nb≤0.08重量％
Ca≤0.1重量％
所述组成的剩余部分是铁和由熔炼产生的不可避免的杂质，
所述经涂覆的钢板从所述经涂覆的钢板的主体至表面包括：
-主体，所述主体的显微组织包含以表面分数计60％至90％的铁素体，剩余部分为马氏体-奥氏体岛、珠光体或贝氏体，
-这样的主体的顶部为脱碳层，所述脱碳层在上部中包括厚度为1μm至100μm的铁素体层，
-由铝或铝合金制成的涂层。
2.一种用于生产经涂覆的钢板的方法，所述方法包括以下连续的步骤：
-铸造钢以获得板坯，所述钢具有根据权利要求1的组成，
-在1100℃至1300℃的温度T再热下将所述板坯再加热，
-在800℃至950℃的热轧终止温度下对经再加热的板坯进行热轧，
-在低于670℃的卷取温度T卷取下对经热轧的钢板进行卷取，以获得经卷取的钢板，
-任选地对所述经卷取的钢板进行酸洗，
-任选地对所述经卷取的钢板进行冷轧，以获得冷轧钢板，
-将经热轧的钢板或所述冷轧钢板加热至700℃至850℃的退火温度TA，并将所述钢板在所述温度TA下保持10秒至1200秒的保持时间tA，以获得退火钢板，气氛包含0％至15％的H2并且具有严格高于-10℃且低于或等于+20℃的露点TDP1，
-将所述退火钢板冷却至560℃至700℃的温度范围，
-用铝或用铝合金涂层涂覆所述退火钢板，
-将所述经涂覆的钢板冷却至室温。
3.一种压制硬化钢部件，所述钢部件具有包含以下的组成：
C：0.26重量％至0.40重量％
Mn：0.5重量％至1.8重量％
Si：0.1重量％至1.25重量％
Al：0.01重量％至0.1重量％
Cr：0.1重量％至1.0重量％
Ti：0.01重量％至0.1重量％
B：0.001重量％至0.004重量％
P≤0.020重量％
S≤0.010重量％
N≤0.010重量％
以及任选地包含以下元素中的一种或更多种：
Ni≤0.5重量％
Mo≤0.40重量％
Nb≤0.08重量％
Ca≤0.1重量％
所述组成的剩余部分是铁和由熔炼产生的不可避免的杂质，
所述钢部件从所述钢部件的主体至表面连续地包括：
-主体，所述主体的显微组织包含以表面分数计多于95％的马氏体和少于5％的贝氏体，
-铁素体相互扩散层，
-基于铝的涂层，
其中所述相互扩散层中的铁素体晶粒宽度GW相互扩散层与所述主体中的原始奥氏体晶粒尺寸PAGS主体之间的比率满足以下方程式：
(GW相互扩散层/PAGS主体)-1≥30％。
4.根据权利要求3所述的压制硬化钢部件，其中所述压制硬化钢部件包括在所述主体与所述铁素体相互扩散层之间的具有碳梯度的马氏体层。
5.根据权利要求3和4中任一项所述的压制硬化钢部件，其中所述压制硬化钢部件具有大于或等于1500MPa的拉伸强度TS以及高于70°的弯曲角。
6.根据权利要求5所述的压制硬化钢部件，其中所述压制硬化钢部件具有大于或等于1250MPa的屈服强度YS。
7.一种用于制造根据权利要求3至6中任一项所述的压制硬化钢部件的方法，包括以下连续步骤：
-提供钢板，所述钢具有根据权利要求1的组成，或者通过根据权利要求2所述的方法生产，
-将所述钢板切割成预定的形状，以获得钢坯，
-在10秒至900秒期间将所述钢坯加热至880℃至950℃的温度，以获得经加热的钢坯，
-将所述经加热的板坯转移至压型机，
-在所述压型机中使所述经加热的板坯热成型，以获得成型的部件，
-对所述成型的部件进行模压淬火。
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