CN108431269A - 镀覆性及焊接性优异的奥氏体系热浸镀铝钢板及其制造方法 - Google Patents

镀覆性及焊接性优异的奥氏体系热浸镀铝钢板及其制造方法 Download PDF

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Publication number
CN108431269A
CN108431269A CN201680076174.3A CN201680076174A CN108431269A CN 108431269 A CN108431269 A CN 108431269A CN 201680076174 A CN201680076174 A CN 201680076174A CN 108431269 A CN108431269 A CN 108431269A
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China
Prior art keywords
aludip
austenite
steel plates
base steel
plating
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CN201680076174.3A
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Inventor
金泳河
黄铉锡
陈光根
金兴润
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Posco Holdings Inc
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Posco Co Ltd
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Publication of CN108431269A publication Critical patent/CN108431269A/zh
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B32B15/00—Layered products comprising a layer of metal
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    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
    • B32B15/043—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material of metal
    • B—PERFORMING OPERATIONS; TRANSPORTING
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Abstract

本发明公开了奥氏体系热浸镀铝钢板及其制造方法，所述钢板包括基础钢板和形成在所述基础钢板表面上的热浸镀铝系层，以重量％计，所述基础钢板包含：C：0.3～0.9％、Mn：12～25％、Si：0.5～2.5％、Al：0.3～3.0％、Ti：0.01～0.5％、V：0.05～0.5％、Mo：0.01～0.5％、Sn：0.01～0.2％、Co：0.001～0.1％、W：0.001～0.1％、余量的Fe及不可避免的杂质。

Description

镀覆性及焊接性优异的奥氏体系热浸镀铝钢板及其制造方法
技术领域
本发明涉及镀覆性及焊接性优异的奥氏体系热浸镀铝钢板及其制造方法。
背景技术
近年来，根据用于减缓全球变暖的二氧化碳的管制，强烈需要汽车的轻量化，与此同时，为了提高汽车的冲撞稳定性，持续进行汽车用钢板的超高强度化。
通常为了生产这种超高强度冷轧钢板，大部分使用低温相变组织。但是，为了实现超高强度而使用低温相变组织时，在拉伸强度为1000MPa级以上难以确保20％以上的延伸率，从而对于所需要的用途的部件的自由设计上存在局限性。
作为提供成型性及机械性质优异的钢的各种尝试中的代表性例子，国际公开专利公报第2011-122237号中公开了具有700～900MPa的拉伸强度的延展性优良的高张力钢板，以重量％计，所述钢板含有C：0.5～1.5％、Si：0.01～0.1％、Mn：10～25％、P：0.1％以下、S：0.05％以下、Al：0.01～0.1％、Ni：3.0～8.0％、Mo：0.01～0.1％、N：0.01％以下、余量的Fe及不可避免的杂质，并且国际公开专利公报第2002-101109号中公开了以重量％计，包含：C：1.00％以下、Mn：7.00～30.00％、Al：1.00％～10.00％、Si：2.50～8.00％、Al+Si：3.50～12.00％、B：0.00％～0.01％、Fe及不可避免的杂质的钢板。
但是，上述钢板的屈服强度低而冲撞特性差，而且就非镀覆材料而言，难以长时间在腐蚀环境中使用，因此用作汽车用钢材时存在应用上有限制的缺点。
此外，将高锰钢热浸镀锌钢板用作汽车用钢板时，通过冲压加工将部件进行加工后通过点焊或电弧焊接等进行焊接来组装，此时，对高锰钢热浸镀锌钢板进行点焊时，由于焊接热(输入)，焊接热影响部(Heat Affected Zone，HAZ)发生熔解，从而以液相的熔融锌残留，而且由于高锰钢的高电阻值，基材组织的温度高于其他钢种的温度，并且由于高热膨胀系数而产生晶界的扩大。在上述状态下对热影响部施加拉伸力时，在焊接热影响部组织中，液相的熔融锌渗透至基材表面的晶界中并产生裂纹，从而引起作为脆性断裂的焊接液体金属脆化(Liquid Metal Embrittlement，以下称为“LME”)。
已知用于防止超高强度钢镀锌钢板的焊接LME的产生的方案有强化基础钢板的晶界或者消除晶粒内与晶界的硬度差的方案等，但是高锰钢在常温下也具有奥氏体组织，从而显示出高焊接热输入和热膨胀系数，因此在以高锰钢作为镀覆材料的镀锌钢板中，如上所述的方案没有效果，即，在进行点焊时焊接肩部的温度快速上升至最高800℃，另一方面，锌镀层在420℃左右开始熔解成液相，并且焊接肩部的温度越上升，急剧增加熔融而形成的液体的流动性，因此，随着渗透至基础钢板的晶界中而会产生焊接LME裂纹。
由此，正在进行通过使用铝(Al)作为镀层形成物质来改善焊接性的研究。但是，就以高强度钢为基材的热浸镀铝钢板而言，钢中含有的大量的Si、Mn及Al在退火过程中形成单独或复合氧化物而难以确保熔融铝的镀覆性。
发明内容
要解决的技术问题
本发明的多种目的之一为提供镀覆性及焊接性优异的奥氏体系热浸镀铝钢板及其制造方法。
技术方案
本发明的一个方面提供奥氏体系热浸镀铝钢板，所述钢板包括基础钢板和形成在所述基础钢板表面上的热浸镀铝系层，以重量％计，所述基础钢板包含：C：0.3～0.9％、Mn：12～25％、Si：0.5～2.5％、Al：0.3～3.0％、Ti：0.01～0.5％、V：0.05～0.5％、Mo：0.01～0.5％、Sn：0.01～0.2％、Co：0.001～0.1％、W：0.001～0.1％、余量的Fe及不可避免的杂质。
本发明的另一个方面提供制造奥氏体系热浸镀铝钢板的方法，所述方法包括以下步骤：准备基础钢板，以重量％计，所述基础钢板包含：C：0.3～0.9％、Mn：12～25％、Si：0.5～2.5％、Al：0.3～3.0％、Ti：0.01～0.5％、V：0.05～0.5％、Mo：0.01～0.5％、Sn：0.01～0.2％、Co：0.001～0.1％、W：0.001～0.1％、余量的Fe及不可避免的杂质；在露点温度为-30℃以下的还原气氛下，将所述基础钢板加热至700～850℃之后进行保持；冷却经过加热并保持的所述基础钢板；以及将经过冷却的所述基础钢板浸渍于铝系镀浴中进行镀覆。
有益效果
本发明的多种效果之一为本发明的一个实施例的奥氏体系热浸镀铝钢板具有镀覆性及焊接性优异的优点。
但是，本发明的各种有益的优点和效果并不限定于上述的内容，可以在对本发明的具体实施方式进行说明的过程中更加容易理解。
附图说明
图1是本发明的奥氏体系热浸镀铝钢板的模式图。
图2是在切断一个发明例的奥氏体系热浸镀铝钢板之后，利用场发射扫描电子显微镜(Field Emission Scanning Electron Microscope，FE-SEM)观察其截面的照片。
图3是观察发明例1的镀覆钢板的试片外观的照片。
图4是观察比较例1的镀覆钢板的试片外观的照片。
最佳实施方式
本发明人认识到如下问题，即在现有的高锰钢中，通过添加大量的锰和碳，可以在常温下确保作为钢的微细组织的奥氏体，但是，由于屈服强度低而存在冲撞性能差的问题，因此为了解决所述问题进行了深入研究。其结果发现，通过适当控制钢的成分体系中起到奥氏体组织的稳定化功能的碳、锰、铝的含量的同时复合添加形成微细析出物的元素，从而能够确保成型性优异且屈服强度优异的钢材。不仅如此，还确认了通过复合添加微量的已知为钢中的晶界强化元素的W和Co来抑制退火热处理时Mn的表面扩散，并抑制点焊时熔融金属渗透至母材中，从而能够使奥氏体系高锰热浸镀铝钢板的镀覆性及焊接性极大化，并完成了本发明。
图1是本发明的奥氏体系热浸镀铝钢板的模式图，图2是在切断一个发明例的奥氏体系热浸镀铝钢板之后，利用场发射扫描电子显微镜(Field Emission ScanningElectron Microscope，FE-SEM)观察其截面的照片。下面，参照图1和图2，对本发明的一个方面的奥氏体系热浸镀铝钢板进行详细说明。
参照图1和图2，本发明的一个方面的奥氏体系热浸镀铝钢板包括基础钢板10和形成在所述基础钢板表面上的热浸镀铝系层30，根据情况，还可以包含形成在基础钢板10与热浸镀铝系层30的界面的Al-Fe-Si-Mn系合金层20。
首先，对基础钢板10的合金成分及优选的含量范围进行详细说明。除非另有特别说明，后述的各成分的含量均以重量为基准。
C：0.3～0.9％
碳是有助于奥氏体组织的稳定化的元素，越增加碳的含量，越有利于确保奥氏体组织。此外，碳增加钢的堆垛层错能而起到同时增加拉伸强度和延伸率的作用。如果碳的含量小于0.3％，则钢板的高温加工时由于脱碳而形成α'马氏体组织，从而存在延迟断裂差的问题，并且存在难以确保所期望的拉伸强度和延伸率的问题。另一方面，当碳的含量超过0.9％时，增加电阻率而会使焊接性变差。因此，本发明中优选将碳的含量限定为0.3～0.9％。
锰(Mn)：12～25％
锰是与碳一起使奥氏体组织稳定化的元素。如果锰的含量小于12％，则变形时形成α'马氏体组织，从而难以确保稳定的奥氏体组织，另一方面，当锰的含量超过25％时，提高强度的效果会饱和，并存在制造成本上升的问题。因此，本发明中优选将锰的含量限定为12～25％。
硅(Si)：0.5～2.5％
硅是通常作为钢的脱氧剂而使用的元素，但是，在本发明中起到通过固溶强化而提高钢的屈服强度和拉伸强度的作用。尤其，在本发明中确认到复合添加适量的硅和作为碳氮化物形成元素的钛和钒时，碳氮化物被微细化，从而与单纯地只添加碳氮化物形成元素时相比，能够得到更加微细的晶粒。本发明中，为了得到所述效果，硅的含量优选为0.5％以上。但是，当硅的含量超过2.5％时，热轧时表面形成大量的硅氧化物，从而降低酸洗性并增加电阻率，从而焊接性会变差。因此，本发明中优选将硅的含量限定为0.5～2.5％。
铝(Al)：0.3～3.0％
铝是通常为了钢的脱氧而添加的元素，但是，本发明中通过提高堆垛层错能而抑制ε马氏体的生成，从而起到提高钢的延展性和耐延迟断裂特性的作用。如果铝的含量小于0.3％，则由于快速的加工硬化现象，钢的延展性降低而存在耐延迟断裂特性变差的问题，另一方面，当铝的含量超过3.0％时，钢的拉伸强度降低，铸造性变差，并且热轧时钢的表面严重氧化，从而存在表面质量变差的问题。因此，本发明中优选将铝的含量限定为0.3～3.0％。
钛(Ti)：0.01～0.5％
钛与钢中的氮反应形成氮化物，从而提高钢的成型性，并与钢中的碳反应形成碳化物，从而提高钢的强度。本发明中为了得到所述效果，钛的含量优选为0.01％以上。但是，当钛的含量超过0.5％时，形成过多的析出物，从而存在钢的疲劳特性变差的问题。因此，本发明中优选将钛的含量限定为0.01～0.5％。
钒(V)：0.05～0.5％
钒是与碳及/或氮反应形成析出物的元素，尤其，在本发明中在低温下形成微细析出物，从而起到增加钢的屈服强度的重要作用。本发明中为了得到所述效果，钒的含量优选为0.05％以上。但是，当钒的含量超过0.5％时，在高温下形成粗大的碳氮化物，从而存在热加工性变差且钢的屈服强度降低的问题。因此，本发明中优选将钒的含量限定为0.05～0.5％。
钼(Mo)：0.01～0.5％
钼是起到提高高温强度的作用的元素，尤其，在本发明中起到增加钢的屈服强度的作用，为了得到所述效果，钢中的钼的含量优选为0.01％以上。但是，当钼的含量超过0.5％时，不仅热加工性会变差，而且存在不利于产品的成本竞争力方面的问题。因此，本发明中优选将钼的含量限定为0.01～0.5％。
锡(Sn)：0.01～0.2％
如同本发明通常在钢中含有大量的硅和锰时，退火时氧亲和力高的硅和锰在钢板的表层形成单独或复合氧化物，从而镀覆性变差。锡通过有效抑制钢中锰的表面浓缩来抑制锰系氧化物的形成，从而对改善镀覆性起到主要的作用。本发明中为了得到所述效果，锡的含量优选为0.01％以上。但是，当锡的含量超过0.2％时，不仅会使所述效果饱和，而且难以在成本竞争力方面确保经济性。因此，本发明中优选将锡的含量限定为0.01～0.2％。
钨(W)：0.001～0.1％
钨是晶界强化元素，为了改善钢的强度而添加微量的钨。并且，钨通过形成晶界碳化物来抑制退火热处理时锰通过晶界向表面扩散，从而改善镀覆性，并且在点焊时熔融金属渗透至母材时防止向晶界扩散，从而抑制LME裂纹的产生。本发明中为了得到所述效果，钨的含量优选为0.001％以上。但是，当钨的含量超过0.1％时，不仅会使所述效果饱和，而且在成本竞争力方面难以确保经济性。因此，本发明中优选将钨的含量限定为0.001～0.1％。
钴(Co)：0.001～0.1％
钴在与钨一起复合添加时形成化合物，从而有助于改善高温强度。并且，与钨一起在退火热处理时抑制锰通过晶界向表面扩散，从而改善镀覆性，并且在点焊时熔融金属渗透至母材时防止向晶界扩散，从而抑制LME裂纹的产生。本发明中为了得到所述效果，钴的含量优选为0.001％以上。但是，当钴的含量超过0.1％时，不仅会使所述效果饱和，而且在成本竞争力方面难以确保经济性。因此，本发明中优选将钴的含量限定为0.001～0.1％。
除所述组成以外的余量为Fe。但是，在通常的制造过程中从原料或周围环境不可避免地会混入并不需要的杂质，因此，无法排除所述杂质。所述杂质对于本技术领域中具有通常知识者而言是众所周知的，因此，本说明书中对其所有的内容不进行特别的提及。
另外，并不排除所述组成以外的有效成分的添加，例如，以重量％计，基础钢板还可以包含选自Cr：0.5％以下(0％除外)、Nb：0.05％以下(0％除外)及Sb：0.1％以下(0％除外)中的一种以上。
铬(Cr)：0.5％以下(0％除外)
铬通过在表层形成致密的氧化物薄膜来抑制氧流入到内部而抑制脱碳，从而起到使奥氏体组织稳定化的作用，但是，当添加0.5％以上的铬时，在晶界中形成碳化物而起到裂纹成核作用，从而存在使耐延迟断裂性变差的问题，因此，优选添加0.5％以下的铬。
铌(Nb)：0.05％以下(0％除外)
当复合添加铌和钒时，形成碳氮化物，从而起到使晶粒微细化并提高强度的作用，但是，当添加0.05％以上的铌时，减少高温延展性(hot ductility)，从而使板坯的质量变差，因此，优选添加0.05％以下的铌。
锑(Sb)：0.1％以下(0％除外)
锑是退火热处理时浓缩在钢板表层正下方的元素，锑抑制Si、Mn及Al合金元素沿晶界扩散到表面，从而可以确保热浸镀铝性。但是，在冷轧酸洗时，使氧化皮残留在表层部，从而导致酸洗性变差，因此，锑的含量优选控制为0.1％以下。
另外，设计具有如上所述的成分范围的钢材时，优选包含W和Co的含量之和0.01％以上。如果W和Co的含量之和小于0.01％，则难以通过W和Co充分实现晶界强化且难以充分抑制Si、Mn及Al的表面浓缩，由此会产生未镀覆，或者点焊LME特性会变差。
此外，设计具有如上所述的成分范围的钢材时，优选包含Mo和V的含量之和0.6％以上。如果Mo和V的含量之和小于0.6％，则在退火热处理过程中无法顺利形成微细碳氮化物，从而无法充分实现晶粒微细化，由此，强度的提高效果以及基于应力分散来改善点焊LME特性的效果会不足。
作为一个例子，基础钢板10可以包含碳氮化物，所述碳氮化物包含Ti及/或V，所述碳氮化物的平均圆当量直径(equivalent circular diameter)可以为100nm以下(0nm除外)。如果碳氮化物的平均圆当量直径超过100nm，则对晶粒微细化的效果不足，从而会使钢的屈服强度变差。
作为一个例子，基础钢板10的屈服比(屈服强度/拉伸强度)可以为0.68以上。如果屈服比小于0.68，则结构部件在冲撞时冲撞吸收能力会不充分。
热浸镀铝系层30形成在基础钢板的表面，从而有助于提高钢板的耐蚀性。本发明中对热浸镀铝系层30的组成不作特别限定，可以是纯铝镀层或可以是包含Si、Mg等的铝系合金镀层。下面，对热浸镀铝系层30中可包含的元素的种类及其优选的含量范围进行详细说明。
Si：7～12％
需要优异的加工性或耐氧化性时，可以添加适量的Si。但是，添加过多的Si时，会使镀浴温度过度上升，并析出粗大的Si初晶，因此反而会存在耐蚀性和加工性变差的可能性。考虑到这点，Si的含量可以为7～12％，优选可以为8～10％。
Mg：3～5％
需要优异的耐蚀性时，可以添加适量的Mg。此外，添加Mg会使镀层的表层硬度上升而降低摩擦系数，从而提高加工性。但是，当Mg的含量过多时，由于氧亲和力强而形成Mg氧化物，从而会导致镀浴浮渣的产生。考虑到这点，Mg的含量可以为3～5％。
根据情况，本发明的奥氏体系热浸镀铝钢板还可以包括形成在基础钢板10与热浸镀铝系层30的界面上的Al-Fe-Si-Mn系合金层20，这时Al-Fe-Si-Mn系合金层可以包含合计为23重量％以上的Fe和Mn。合金层中含有的Fe和Mn可以是来源于热浸镀时的镀浴成分的，或者也可以是从基础钢板扩散的。Fe和Mn的含量之和小于23重量％的情况是由以下原因引起，即，由于在退火热处理的过程中在基础钢板的表面浓缩而形成的层(layer)状的Si、Mn或Al氧化物，在浸渍于镀浴中进行镀覆的过程中，基础钢板中的Fe和Mn向Al-Fe-Si-Mn系合金层的扩散被阻止，在这种情况下，镀覆性和粘附性会变差。
作为一个例子，Al-Fe-Si-Mn系合金层20的厚度表示为x，热浸镀铝系层30的厚度表示为y时，y/x可以为1以上且6以下。如果y/x小于1，则由于Si、Mn或Al氧化物而在浸渍于镀浴的过程中，熔融铝的湿润性差，从而镀层的厚度变薄，并且存在退火氧化物的局部部位的镀层厚度薄，从而会在整个试片中引起镀层厚度的不均匀所导致的流痕形状的镀覆缺陷。另一方面，当y/x超过6时，钢板的Fe的扩散不顺利，从而形成薄的Al-Fe-Si-Mn系合金层，并且镀层/基材界面的弱合金化所带来的锚定(anchoring)效果微小，从而镀覆粘附性会变差。
作为一个例子，Al-Fe-Si-Mn系合金层20与热浸镀铝系层30的界面中，在与基础钢板水平的方向上以2μm以下(0μm除外)的间隔，可以断续地形成有厚度为1μm以下(0μm除外)的Al-Si-Mg合金相。当Al-Si-Mg合金相的厚度超过1μm，或者所述间隔超过2μm时，在脆(brittle)的Al-Si-Mg合金相中会产生裂纹，或者由于在水平方向上连续形成的合金相而导致镀层内会发生剥离现象。
如前所述，以上说明的本发明的奥氏体系热浸镀铝钢板可以通过各种方法来制造，对其制造方法不作特别限制。但是，作为一个具体实施方案可以通过如下所述的方法制造。
首先，在还原气氛下将满足前述合金组成的基础钢板进行加热后进行保持。
此时，露点温度优选控制为-30℃。这是为了最大限度地抑制Si、Mn及Al氧化物浓缩在钢板表面，如果露点温度超过-30℃，则钢中的Mn与氧反应而在钢板表层形成带状的厚Mn氧化物，从而熔融铝的湿润性变差。
此时，加热温度优选为700～850℃。如果加热温度低于700℃，则加热温度低于Al相变点(约726℃)，从而难以确保奥氏体单相组织。另一方面，加热温度过高时，由于二次再结晶而导致钢的拉伸强度或延伸率会降低，并且钢板表面上形成厚的Si、Mn及Al氧化物，从而会引起未镀覆的产生以及镀覆剥离现象。为了防止上述问题，加热温度优选控制为850℃，更优选控制为820℃以下。
作为一个例子，所述还原气氛可以是3～20体积％的氢气(H2)和余量的氮气(N2)气氛。如果氢的含量小于3体积％，则不可避免地形成在钢板表面的铁氧化薄膜的还原不充分，从而存在会引起残余氧化层所导致的镀层剥离的可能性。但是，氢的含量过高时，随着增加氢的含量，不仅会增加成本，而且会增加爆炸的风险，因此，氢的含量优选限定为20体积％以下。
之后，将在还原气氛下进行加热及保持的基础钢板进行冷却。
作为一个例子，经过冷却的基础钢板的温度，即浸渍于铝系镀浴之前那一刻或之后那一刻的基础钢板的温度可以为560～660℃。如果基础钢板的温度低于560℃，则急剧增加熔融铝在钢板表面进行凝固的速度，从而随着在钢板表面上的流动性的减少，会加速各部位的镀覆附着量的偏差，并存在产生未镀覆缺陷的可能性，另一方面，当基础钢板的温度超过660℃时，促进钢板的熔解而加速Fe-Al化合物形态的浮渣的产生，从而存在产生未镀覆的可能性。
之后，将经过冷却的基础钢板浸渍于铝系镀浴中进行镀覆。铝系镀浴可以是纯铝镀浴或包含Si、Mg等的铝系合金镀浴。
作为一个例子，将基础钢板的进入温度表示为Td(℃)，并将所述铝系镀浴的温度表示为Tp(℃)时，所述Td可以满足(Tp-80)℃以上且(Tp-10)℃以下。如果Td低于(Tp-80)℃，则镀浴的粘度过度上升，从而减少卷绕钢板的辊(roll)的移动性，由此导致钢板与辊之间的滑移(slip)，从而存在引起钢板表面缺陷的可能性。另一方面，当Td超过(Tp-10)℃时，促进钢板的熔解而加速Fe-Al化合物形态的浮渣的产生，因此会引起未镀覆。
接着，根据需要，可以在720～840℃的温度下，对镀铝系钢板进行合金化热处理。将合金化热处理温度控制为720℃以上，从而能够确保铝系镀层中的充分的Fe含量，并且将合金化热处理温度控制为840℃以下，从而能够防止由于镀层中的Fe的含量过多而在加工时镀层脱落的粉化现象。
具体实施方式
下面，通过实施例对本发明进行更具体的说明。但是，需要注意的是，以下的实施例仅用于例示本发明以进行具体化，并不是为了限定本发明的权利范围。这是因为本发明的权利范围是由权利要求书中记载的内容和由此合理推导的内容所决定。
在1180℃的加热炉中，对具有如下述表1中示出的合金组成的钢锭进行均质化处理1小时，然后以900℃的精轧温度进行轧制，从而制造热轧钢板。之后，以400℃的收卷温度收卷所述热轧钢板之后进行酸洗，然后以55％的冷轧压下率进行冷轧，从而制造冷轧钢板。之后，在包含5体积％的氢气的氮气气氛下，以下述表2中示出的温度进行加热并进行均热60秒。之后，将所述钢板浸渍于镀浴中5秒，从而制造镀覆钢板。此时，发明例1至发明例5中使用了由9重量％的Si和余量的Al组成的镀浴，比较例1至比较例5中使用了由0.2重量％的Al和余量的Zn组成的镀浴。之后，通过气体擦拭(Air wipping)使镀覆在表面的镀覆附着量保持为70g/m2的水平。
为了评价经过镀覆工序的所述钢板的机械性质，以垂直于轧制方向并以40mm×200mm切断钢板，并进行侧面研磨抛光，然后以JIS 5号标准制作拉伸试片，并利用拉伸试验仪测量屈服强度(YS)和拉伸强度(TS)，并一起示于表2中。
为了评价完成镀覆工序的所述钢板的镀覆性，测量了相对于经过镀覆的表面的整体面积的铝系镀层的覆盖面积率，并一起示于下述表2中。为了观察截面，将试片切断为15mm×15mm，并研磨截面之后，利用扫描电子显微镜(Scanning Electron Microscope，SEM)观察镀层。此外，为了测量钢板的镀覆粘附性，将30mm×80mm尺寸的试片进行180°弯曲加工之后进行了弯曲试验(bending test)。根据钢板的材质特性，在基材不会断裂的范围进行了0T弯曲(bending)。在弯曲(Bending)部粘贴透明胶带并揭开时，如果镀层粘在所述胶带上一起脱落，则表示为“剥离”，如果镀层完全没有粘在所述胶带上，则表示为“未剥离”，将其示于下述表2中。
为了评价点焊性，使用前端直径为6mm的Cu-Cr电极，流通焊接电流，并在2.6kN的电极压力(welding force)在16个循环(Cycle)的通电时间和15个循环(Cycle)的保持(Holding)时间的条件下进行焊接。将钢板厚度表示为t时，将点焊熔核直径(nuggetdiameter)小于4vt的时刻的焊接电流设为下限，将发生飞溅现象的时刻的焊接电流设为上限(喷溅电流(Expulsion current))，并将从下限至没有产生LME裂纹的电流为止的差值命名为未产生LME裂纹的电流范围，并示于表2中。
另外，图3是观察发明例1的镀覆钢板的试片外观的照片，图4是观察比较例1的镀覆钢板的试片外观的照片。
[表1]
[表2]
[表3]
参照表3可以确认，发明例1至发明例5的基础钢板的组成、制造条件、y/x及合金层中的Fe及Mn含量总和均满足本发明所提出的范围，由此铝系镀层的覆盖面积率均显示为95％以上，从而镀覆性非常优异，而且没有剥离的部分，从而镀覆粘附性也优异。
但是，比较例1和比较例3的钢中的Si含量没有达到本发明所提出的范围而未能有效地使碳氮化物的尺寸微细化，从而具有相对粗大的晶粒，因此屈服强度远低于800MPa。
此外，比较例2的裂纹区间的露点温度脱离了本发明所提出的范围，从而钢板表面上形成带状的厚Mn氧化物，因此镀覆性变差并同时产生镀层脱落的镀覆剥离现象。并且，由于所形成的Mn氧化物，即使进行镀覆，镀层的厚度也薄，由此减少了镀层与合金层的厚度比，并且浸渍于镀浴中进行镀覆的过程中，基材中的Fe、Mn向合金层中的扩散受阻，从而降低了合金层中的Fe、Mn含量的总和。
此外，比较例4的钢中的W和Co的含量没有达到本发明所提出的范围，从而未能有效地抑制钢中Mn的表面浓缩，因此Mn系氧化物形成在钢板表面，并且由于钢板的进入温度比镀浴温度高约20℃，从而随着热冲击所带来的控制氧化物的效果微弱，铝镀层的覆盖面积率止于73％而镀覆性差，由此导致在镀层与基础钢板的界面中镀层剥离的结果。由于形成在钢板表面的层(layer)状的Mn氧化物，即使进行镀覆，镀层的厚度也薄，由此减少了镀层与合金层的厚度比，并且在浸渍于镀浴中进行镀覆的过程中，基材中的Fe、Mn向合金层中的扩散受阻，从而降低了合金层中的Fe、Mn含量的总和。
此外，比较例5的裂纹区间的退火温度超出本发明所提出的范围，从而由于二次再结晶而导致钢的材质即拉伸强度未能达到所期望的水平，并且不仅达到退火温度所需要的时间相对较长，而且随着退火温度的上升，增加了钢中的Si、Mn或Al向钢板表面的扩散，从而在镀层与基础钢板的界面上形成带状的Si、Mn或Al氧化物，并且由于钢板的进入温度比镀浴温度高约160℃，从而虽然具有热冲击所带来的控制氧化物的效果，但是钢板的进入温度低，从而急剧增加熔融铝在钢板表面进行凝固的速度，因此，随着在钢板表面上的流动性的减少，会加速各部位的镀覆附着量的偏差，并引起未镀覆缺陷而导致铝镀层的覆盖面积率止于78％，并且即使在还原气氛下进行热处理，也由于进行镀铝之后残留在镀层与钢板的界面上的Si、Mn或Al氧化物而引起镀层脱落的现象。此外，在退火热处理的过程中由于浓缩在钢板表面而形成的层(layer)状的Si、Mn或Al氧化物，即使进行镀覆，镀层的厚度也薄，由此减少了镀层与合金层的厚度比，并且浸渍于镀浴中进行镀覆的过程中，基材中的Fe、Mn向合金层中的扩散受阻，从而降低了合金层中的Fe、Mn含量的总和。
另外，可以确认发明例1至发明例5的镀层的主要成分由铝组成，从而抗LME裂纹性变高，不发生LME裂纹的电流范围超过1.0kA的水平，因此焊接性优异。
但是，比较例1至比较例5的镀层的主要成分由锌组成，从而在点焊时，无法抑制低熔点的锌渗透到母材中，导致LME裂纹从相对低的焊接电流值开始产生，因此不产生LME的电流范围没有达到1.0kA。

Claims (16)

1.奥氏体系热浸镀铝钢板，所述钢板包括基础钢板和形成在所述基础钢板表面上的热浸镀铝系层，以重量％计，所述基础钢板包含：C：0.3～0.9％、Mn：12～25％、Si：0.5～2.5％、Al：0.3～3.0％、Ti：0.01～0.5％、V：0.05～0.5％、Mo：0.01～0.5％、Sn：0.01～0.2％、Co：0.001～0.1％、W：0.001～0.1％、余量的Fe及不可避免的杂质。
2.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，以重量％计，所述基础钢板还包含选自Cr：0.5％以下(0％除外)、Nb：0.05％以下(0％除外)及Sb：0.1％以下(0％除外)中的一种以上。
3.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，所述基础钢板包含合计0.01％以上的W和Co。
4.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，所述基础钢板包含合计0.6％以上的Mo和V。
5.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，所述基础钢板包含平均圆当量直径为100nm以下的碳氮化物。
6.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，所述基础钢板的屈服比(屈服强度/拉伸强度)为0.68以上。
7.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，所述热浸镀铝系层包含7～12重量％的Si。
8.根据权利要求7所述的奥氏体系热浸镀铝钢板，其中，所述热浸镀铝系层还包含3～5重量％的Mg。
9.根据权利要求1所述的奥氏体系热浸镀铝钢板，其中，所述热浸镀铝钢板还包括形成在所述基础钢板与热浸镀铝系层的界面的Al-Fe-Si-Mn系合金层，所述Al-Fe-Si-Mn系合金层包含合计23重量％以上的Fe和Mn。
10.根据权利要求9所述的奥氏体系热浸镀铝钢板，其中，所述Al-Fe-Si-Mn系合金层的厚度表示为x，所述热浸镀铝系层的厚度表示为y时，y/x为1以上且6以下。
11.根据权利要求9所述的奥氏体系热浸镀铝钢板，其中，所述Al-Fe-Si-Mn系合金层与热浸镀铝系层的界面中，在与基础钢板水平的方向上以2μm以下(0μm除外)的间隔，断续地形成有厚度为1μm以下(0μm除外)的Al-Si-Mg合金相。
12.制造奥氏体系热浸镀铝钢板的方法，所述方法包括以下步骤：
准备基础钢板，以重量％计，所述基础钢板包含：C：0.3～0.9％、Mn：12～25％、Si：0.5～2.5％、Al：0.3～3.0％、Ti：0.01～0.5％、V：0.05～0.5％、Mo：0.01～0.5％、Sn：0.01～0.2％、Co：0.001～0.1％、W：0.001～0.1％、余量的Fe及不可避免的杂质；
在露点温度为-30℃以下的还原气氛下，将所述基础钢板加热至700～850℃之后进行保持；
冷却经过加热并保持的所述基础钢板；以及
将经过冷却的所述基础钢板浸渍于铝系镀浴中进行镀覆。
13.根据权利要求12所述的制造奥氏体系热浸镀铝钢板的方法，其中，将经过冷却的所述基础钢板的进入温度表示为Td(℃)，所述铝系镀浴温度表示为Tp(℃)时，所述Td满足(Tp-80)℃以上且(Tp-10)℃以下。
14.根据权利要求12所述的制造奥氏体系热浸镀铝钢板的方法，其中，所述还原气氛为3～20体积％的氢气(H2)及余量的氮气(N2)气氛。
15.根据权利要求12所述的制造奥氏体系热浸镀铝钢板的方法，其中，经过冷却的所述基础钢板的进入温度(Td)为560～660℃。
16.根据权利要求12所述的制造奥氏体系热浸镀铝钢板的方法，其中，所述方法还包括进行所述镀覆后，在720～840℃的温度下进行合金化热处理的步骤。
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