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CN113631736A - 热浸镀Zn-Al-Mg系钢板及其制造方法 - Google Patents

热浸镀Zn-Al-Mg系钢板及其制造方法 Download PDF

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Publication number
CN113631736A
CN113631736A CN202080020996.6A CN202080020996A CN113631736A CN 113631736 A CN113631736 A CN 113631736A CN 202080020996 A CN202080020996 A CN 202080020996A CN 113631736 A CN113631736 A CN 113631736A
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China
Prior art keywords
hot
dip
steel sheet
less
phase
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植杉真也
平田健太郎
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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Abstract

本发明实现兼顾了强度和加工性的镀覆钢板。在热浸镀Zn‑Al‑Mg系钢板中，钢基材以质量％计包含C：0.050～0.180％、Si：0.001～0.50％、Mn：1.00～2.80％、Ti：0.01～0.10％、及B：0.0005～0.0100％，热轧工序中的卷取后的渗碳体平均粒径为2μm以下，连续热浸镀锌工序后的金属组织具有铁素体相和面积率为15％以上且低于45％的第二相，第二相由马氏体构成或者由马氏体及贝氏体构成，平均结晶粒径为8μm以下。

Description

热浸镀Zn-Al-Mg系钢板及其制造方法
技术领域
本发明涉及热浸镀Zn-Al-Mg系钢板及其制造方法。
背景技术
近年来，在汽车、建材的领域以轻量化及省资源化为目的的高强度高防锈钢板的需求提高。该高强度高防锈钢板由于实施以压制加工或弯曲加工为代表的各种加工，因此除了高强度及高耐蚀性以外，加工性优异也是重要的。然而，材料的加工性伴随着强度上升而劣化，因此期望确立能够兼顾例如在汽车的结构用构件及增强用构件中所要求的最大抗拉强度780MPa以上那样的高强度和加工性的技术。
例如，在专利文献1中，公开了一种技术，其通过在钢板中添加Si、Nb及Ti，从而减小马氏体及贝氏体组织等硬质相与铁素体相的硬度差，由此兼顾780MPa以上的高抗拉强度和加工性。
此外，从耐蚀性的观点出发，作为防锈效果高的表面处理钢板，已知有热浸镀Zn-Al-Mg系钢板。近年来，从设计性等观点出发，具有黑色外观的钢板的需求提高，因此镀层自身被黑色化的热浸镀Zn-Al-Mg系钢板的需要逐渐增大。在专利文献2中，公开了具有抗拉强度780MPa以上的高强度、弯曲加工性优异的热浸镀Zn-Al-Mg系钢板。
现有技术文献
专利文献
专利文献1：日本公开专利公报“特开2006-283156号公报”
专利文献2：日本公开专利公报“特开2014-189812号公报”
发明内容
发明所要解决的课题
然而，若在钢板中大量地添加Ti则会导致再结晶温度的上升，因此需要提高镀覆工序中的还原加热温度。由于还原加热温度的高温化会成为镀覆不良的原因，因此在专利文献1中记载的技术无法说适于镀覆钢板。此外，根据专利文献2中记载的制造方法，由于根据热轧条件有可能镀覆后的马氏体量减少，因此有时不能稳定地得到780MPa以上的强度。
本发明的一方案的目的是实现稳定地兼顾780MPa以上的抗拉强度和高加工性的热浸镀Zn-Al-Mg系钢板。
用于解决课题的手段
为了解决上述的课题，本发明的一方案的热浸镀Zn-Al-Mg系钢板(也可称为熔融Zn-Al-Mg系镀覆钢板)，其在钢基材的表面具有热浸镀Zn-Al-Mg系层(也可称为熔融Zn-Al-Mg系镀层)，其中，上述钢基材以质量％计包含C：0.050～0.180％、Si：0.001～0.50％、Mn：1.00～2.80％、Ti：0.01～0.10％、及B：0.0005～0.0100％，剩余部分包含Fe及不可避免的杂质，热轧工序中的卷取后的渗碳体的平均粒径为2μm以下，连续热浸镀锌工序后的金属组织具有铁素体相和面积率为15％以上且低于45％的第二相，上述第二相由马氏体构成或者由马氏体及贝氏体构成，平均结晶粒径为8μm以下。
为了解决上述的课题，本发明的一方案的热浸镀Zn-Al-Mg系钢板的制造方法，其是在钢基材的表面具有热浸镀Zn-Al-Mg系层的热浸镀Zn-Al-Mg系钢板的制造方法，该制造方法依次包含热轧工序、冷轧工序、和依次进行退火及热浸镀Zn-Al-Mg系的连续热浸镀锌工序，其中，在上述热轧工序中，热轧后的平均冷却速度为20℃/秒以上且低于80℃/秒，卷取温度为400℃以上且低于600℃。
发明效果
根据本发明的一方案，能够实现稳定地兼顾了780MPa以上的抗拉强度和高加工性的热浸镀Zn-Al-Mg系钢板。
附图说明
图1是表示本发明的一实施例中的各钢的成分的图。
图2是表示本发明的一实施例中的各钢的制造条件及特性的图。
具体实施方式
以下，对本发明的一实施方式进行详细说明。需要说明的是，以下的记载用于更好地理解发明的主旨，只要没有特别指定，并不限定本发明。此外，本说明书中只要没有特殊记载，则表示数值范围的“A～B”是指“A以上且B以下”。
〔基材钢板的化学组成〕
对相当于镀覆原板的基材钢板的成分元素进行说明。本说明书中，关于基材钢板的化学组成的“％”只要没有特别说明，则是指“质量％”。
(C)
C(碳)是钢的高强度化而需要的元素。为了得到抗拉强度为780MPa以上的强度水平，需要0.050％以上的C含量。但是，若C含量变得过量则组织的不均匀性变得显著，加工性降低。因此，C含量被限制为0.180％以下，也可以管理为0.160％以下。
(Si)
Si(硅)除了对高强度化有效以外，还具有抑制渗碳体的析出的作用，在抑制珠光体等的生成的方面是有效的。为了充分发挥这些作用，确保0.001％以上的Si含量。但是，若大量地含有Si，则在钢板表面产生Si浓集层，成为导致镀覆性的降低的要因。因此，Si含量被限制为0.50％以下，更优选设定为0.25％以下。
(Mn)
Mn(锰)对高强度化是有效的。为了稳定地得到抗拉强度为780MPa以上的强度水平，确保1.00％以上的Mn含量。但是，若Mn含量变得过大则变得容易产生偏析，加工性降低。因此，Mn含量设定为2.80％以下。
(Ti)
钢板包含0.01质量％以上且0.1质量％以下的Ti(钛)。Ti通过与C反应，从而包含Ti的碳化物作为微细的粒子析出，其是对钢板的高强度化有效的元素。此外，Ti由于与钢中的S(硫)及N(氮)的亲和性也高，因此不仅与C反应而生成析出物，而且与S及N也反应而生成析出物。由于抑制奥氏体-铁素体相变而需要的B容易与N结合，因此Ti的添加对确保固溶的B的含量是有效的。通过Ti的含量为0.01质量％以上，可确保抑制奥氏体-铁素体相变而需要的固溶的B的含量，显著地表现出使析出物微细析出的效果。此外，通过Ti的含量为0.1质量％以下，基材钢板中的Ti的含量不会变得过量，能够抑制基材钢板的制造成本。
(B)
B(硼)会抑制钢的奥氏体-铁素体相变，有助于相变组织强化。通过抑制奥氏体-铁素体相变而降低Ti系碳化物等的析出开始温度，具有使这些碳化物微细化的效果。为了充分得到上述效果，确保0.0005％以上的B含量。设定为0.0010％以上更有效。但是，含有大量的B会成为因硼化物的生成而导致加工性降低的要因。在添加B的情况下，需要在0.0100％以下的范围内进行，也可以管理为0.0050％以下。
(P)
P(磷)由于对固溶强化是有效的，因此优选确保0.005％以上的P含量。也可以管理为0.010％以上。但是，若P含量变得过大则变得容易产生偏析，加工性降低。P含量被限制为0.050％以下。
(S)
S(硫)成为使加工性降低的要因。S的含量被容许至0.020％为止。但是，过量的低S化会导致炼钢负荷的增大，因此通常S含量为0.001％以上较佳。
(Al)
Al(铝)具有脱氧作用。为了充分发挥该作用，优选按照钢中的Al含量成为0.005％以上的方式添加Al。但是，过量的Al含有会导致加工性的降低。因此，Al含量被限制为0.100％以下，也可以管理为0.050％以下。
(Nb、V)
Nb(铌)及V(钒)与Ti同样地通过组织的微细化而提高组织的均匀性，并且通过碳化物的粒子分散强化，不会使弯曲性等加工性劣化而有助于强度提高。因此，根据需要也可以含有Nb、V中的1种或2种。为了充分得到上述效果，更有效的是：关于Nb，确保0.01％以上的含量，关于V，确保0.03％以上的含量。但是，若大量地含有这些元素则会导致加工性的降低。因此，在添加它们中的1种或2种的情况下，Nb含量设定为0.10％以下，V含量也设定为0.10％以下的范围。
(Mo、Cr)
Mo(钼)及Cr(铬)都具有通过固溶强化而提高强度的作用，因此也可以根据需要含有Mo、Cr中的1种或2种。为了充分发挥上述作用，更有效的是：关于Mo，确保0.01％以上，关于Cr，也确保0.01％以上的含量。但是，若大量地含有这些元素则会导致延展性的降低。因此，在添加它们中的1种或2种的情况下，Mo含量设定为1.00％以下，Cr含量也设定为1.00％以下的范围。
本实施方式的钢板包含C、Si、Mn、Ti及B，并可进一步包含上述的各成分作为其他的成分。作为优选的方案，进一步包含P、S及Al中的1种以上。作为更优选的方案，含有P、S及Al中的全部。作为又一方案，除了包含C、Si、Mn、Ti及B以外，还包含P、S及Al中的1种以上，优选的是，包含P、S及Al全部，在该方案中，可列举出进一步包含Nb、V、Cr及Mo中的1种以上。需要说明的是，剩余部分包含Fe及不可避免的杂质。
〔钢基材的金属组织〕
本发明中，以具有在主相铁素体中分散有马氏体、或分散有马氏体和贝氏体作为第二相的复合组织的DP(双相)钢板作为钢基材的适用对象。在热浸镀锌后的金属组织中，分散于主相铁素体中的由马氏体、或由马氏体和贝氏体构成的第二相以面积率计合计设定为15％以上且低于45％。若第二相的面积率不足15％，则变得难以稳定地得到780MPa以上的抗拉强度。相反若变成45％以上则变得过硬而加工性降低。
第二相最优选仅为马氏体，但也可以部分地分散有贝氏体。例如，贝氏体在马氏体与贝氏体的合计体积中所占的体积比例更优选为0～5％的范围。后述的实施例中的本发明例都满足该条件。
本发明中，通过将组织微细化而提高加工性。获知若考虑使用板厚为0.8～2.0mm左右的镀覆钢板来制造汽车的结构用构件及增强用构件的情况，则在第二相的平均结晶粒径被微细化至8μm以下时，可确保充分的加工性，对于设计自由度的扩大变得有用。作为主相的铁素体也优选被微细化，但关于加工性，第二相的平均结晶粒径特别重要。
只要采用第二相的平均结晶粒径成为8μm以下的后述的制造条件，则铁素体相也被充分微细化。例如，铁素体相的平均结晶粒径成为10μm以下。在后述的实施例中第二相的平均结晶粒径为8μm以下的镀覆钢板中，铁素体相的平均结晶粒径都为10μm以下。
〔制造方法〕
上述的热浸镀Zn-Al-Mg系钢板可以利用对钢板坯依次实施热轧、酸洗、冷轧、退火、热浸镀锌的各工序的一般的热浸镀锌系钢板的制造生产线来制造。为了兼顾钢材的强度及加工性，除了控制钢基材的化学组成以外，还需要按照结晶粒径充分微细化的方式对制造条件下功夫。具体而言，在热轧工序中，将平均冷却速度设定为20℃/秒以上且低于80℃/秒，将卷取温度设定为400℃以上且低于600℃。
需要说明的是，更优选的是：在热轧工序中通过830～940℃的精轧温度实施热轧，在冷轧工序中将冷轧率设定为40～70％，在退火工序中通过740～880℃实施退火后，在至浸渍于镀浴为止的冷却过程中至少将至450℃为止的平均冷却速度设定为5℃/秒以上。
(热轧工序)
在上述的热轧工序中，优选将热轧中的精轧温度设定为830～940℃。通过精轧温度为830℃以上，钢板的变形阻力不会变高，能够防止由热轧引起的钢板的制造性的降低。此外，通过精轧温度为940℃以下，能够防止卷材表面中的氧化皮缺陷的产生，抑制表面品质的降低。
精轧后的钢板(热轧钢板)以20℃/秒以上且低于80℃/秒的平均冷却速度被冷却至400℃以上且低于600℃的卷取温度。在平均冷却速度为20℃/秒以下的情况、或卷取温度为600℃以上的情况下，热轧钢板组织的渗碳体发生粗大化，在热浸镀锌工序中的还原加热中粗大的渗碳体的一部分作为未熔化碳化物残存。其结果是，热浸镀锌后的马氏体量减少，得不到780MPa以上的抗拉强度。此外，在平均冷却速度为80℃/秒以上的情况、或卷取温度低于400℃的情况下，因位错密度变高而热轧钢板的硬度增大，不仅冷轧工序中的负荷增大，而且导致热浸镀锌工序后的加工性的降低。
只要为20℃/秒以上且低于80℃/秒的平均冷却速度及400℃以上且低于600℃的卷取温度，则热轧中的卷取后的渗碳体粒径成为2μm以下。由此，在热浸镀锌工序中的还原加热中，能够抑制未熔化碳化物的残存，因此热浸镀锌后的马氏体量增加。因此，能够稳定地制造以高水平兼顾了780MPa以上的强度及加工性的镀覆钢板。
(冷轧工序)
在上述的冷轧工序中，优选将冷轧率设定为40～70％。低于40％的冷轧率时退火后的组织变得粗大而弯曲性降低。另一方面，超过70％的冷轧率时，由冷轧带来的组织微细化效果饱和。此外，赋予过高的冷轧率会增大冷轧工序的负荷，不优选。按照该冷轧工序中的冷轧率成为上述的范围的方式，根据最终的目标板厚来调整热轧后的板厚。根据情况，也可以在热轧后且该冷轧工序之前，插入中间冷轧+中间退火的工序。
(连续热浸镀锌工序)
在连续热浸镀锌工序中，依次进行退火及热浸镀Zn-Al-Mg系。
在即将浸渍于热浸镀锌浴中之前进行的退火中，也可以在还原性气氛下，按照材料温度(最高到达温度)成为740～880℃的方式进行加热。若材料温度达不到740℃则再结晶化变得不充分而容易残存未再结晶组织，因此难以稳定地得到良好的加工性。若超过880℃则奥氏体母相的晶粒粗大化，为了赋予良好的加工性而需要的第二相的微细化变得不充分。材料温度保持在740～880℃的范围的时间例如在60秒以下的范围内设定即可。
在退火后的冷却过程中，优选至少450℃为止的平均冷却速度成为5℃/秒以上。若该温度域中的冷却速度比这慢，则变得容易部分地生成珠光体，变得难以稳定地得到780MPa以上的高强度。此外，从铁素体粒径及第二相粒径的微细化的方面出发，冷却速度设定为5℃/秒以上也是有效的。本发明中作为对象的钢由于如上所述含有规定的Ti及根据需要含有的Nb，因此通过像这样选定加热后的冷却速度，能够得到铁素体的平均结晶粒径为10μm以下、并且第二相的平均结晶粒径为8μm以下的微细的组织。
对于该退火，优选通过能够以1次的生产线通板进行退火及热浸镀Zn-Al-Mg系的连续镀覆生产线来进行。在退火后的上述冷却中，冷却至浸渍于热浸镀锌浴中时的适宜材料温度后，将钢板直接浸渍于热浸镀锌浴中。退火气氛设定为还原性气氛，按照在浸渍于镀浴中之前钢板不与大气接触的方式管理。
热浸镀Zn-Al-Mg系只要采用一直以来实施的方法即可。镀浴组成例如优选为以质量％计Al：3.0～22.0％、Mg：0.05～10.0％、Ti：0～0.10％、B：0～0.05％、Si：0～2.0％、Fe：0～2.0％、剩余部分为Zn及不可避免的杂质的组成。所得到的镀覆钢板的镀层组成基本反映了镀浴组成。
所得到的镀覆钢板在密闭容器中与水蒸汽接触，将镀层黑色化。通过该工序，能够使镀层表面的亮度(L*值)降低至60以下(优选为40以下、进一步优选为35以下)。由此，可得到在热浸镀Zn-Al-Mg系层的表层存在Zn的黑色氧化物、表面的亮度L*为60以下的钢板。如果镀覆钢板的表层为这样的亮度，则可得到黑色的、设计性优异的镀覆钢板。需要说明的是，可根据所需的亮度L*，适当设定与水蒸汽的接触时间等。镀层表面的亮度(L*值)使用分光型色差计来测定。
本发明并不限定于上述的各实施方式，可以在权利要求中所示的范围内进行各种变更，关于将不同的实施方式中分别公开的技术方案适当组合而得到的实施方式，也包含于本发明的技术范围内。
实施例
对本发明的一个实施例进行以下说明。
〔试验方法〕
将具有图1中所示的化学组成的板坯以加热温度1250℃、精轧温度880℃、从精轧至卷取为止的平均冷却速度15～70℃/秒、卷取温度420～630℃进行热轧，得到板厚为1.8～2.8mm的热轧钢板。将热轧钢板酸洗后，以45～65％的轧制率进行冷轧而制成板厚为1.0mm的镀覆原板(钢基材)，将其在连续热浸镀生产线中通板，在氢-氮混合气体气氛中以750～850℃的各种温度进行退火，通过8～12℃/秒的冷却速度冷却至约420℃。
之后，在钢板表面不与大气接触的状态下在下述的浴组成的熔融Zn-Al-Mg系镀浴中浸渍后捞起，通过气体摩擦接触法将镀覆附着量调整为每一面约90g/m2，从而制造热浸镀Zn-Al-Mg系钢板，将其作为供试材。镀浴温为约410℃。
镀浴组成如下所述；
以质量％计Al：6％、Mg：3％、Ti：0.002％、B：0.0005％、Si：0.01％、Fe：0.1％、剩余部分：Zn。
将各钢(本发明例：钢A～G、比较例：钢a)的制造条件示于图2中。其中，“CT”表示卷取温度，“冷却速度”表示热轧中的从精轧至卷取为止的平均冷却速度，“退火温度”表示连续热浸镀锌生产线中的还原加热温度。
〔试验项目〕
对于所得到的供试材的镀覆钢板，进行以下的试验。
(拉伸特性)
使用按照试验片的长度方向相对于镀覆原板(钢基材)的轧制方向成为直角的方式采集的JIS5号试验片，按照JIS Z2241求出抗拉强度TS、总伸长率T.El。
(弯曲试验)
使用按照试验片的长度方向相对于镀覆原板(钢基材)的轧制方向成为直角的方式采集的弯曲试验片，按照JIS Z2248实施弯曲角度45度的V型块弯曲试验。试验后，从弯曲的外侧通过目视观察弯曲部，算出未见到开裂的最小的弯曲前端内侧半径作为极限弯曲半径R，求出极限弯曲半径R除以板厚t而得到的值作为弯曲性的指标R/t。
(金属组织)
关于热轧材及镀覆材的金属组织，对与轧制方向平行的截面(L截面)利用扫描型电子显微镜进行观察。对于热轧材，利用苦味醇试剂腐蚀后，进行10个视场的图像解析而求出渗碳体的平均粒径。
此外，关于镀覆材，都呈现出以铁素体作为主相、存在马氏体、或马氏体和贝氏体作为第二相的金属组织。进行10个视场的图像解析，求出第二相的面积率及平均结晶粒径(当量圆直径)。
〔试验结果〕
将关于以上的试验项目的试验结果归纳示于图2中。需要说明的是，图2中的带下划线的项目表示为本发明规定范围外或特性不充分。
在本发明例中的任一者中，热轧材的渗碳体粒径均为2μm以下，镀覆材的由马氏体或马氏体及贝氏体构成的第二相的面积率均为15％以上且低于45％，该第二相的平均结晶粒径为8μm以下，抗拉强度TS为780MPa以上，抗拉强度TS×总伸长率T.El为14000MPa·％以上，并且弯曲性的指标R/t为1.5以下。即，本发明例中，稳定地得到以高水平兼顾了强度和加工性的镀覆钢板。
另一方面，通过钢板的化学组成、卷取温度(CT)、或从精轧至卷取为止的平均冷却速度中的任一个以上的条件中本发明规定范围外的条件制造的供试材(比较例)的任一者中，上述第二相的面积率均低于15％，抗拉强度TS均成为780MPa以下。即，未得到满足本发明所追求的强度的镀覆钢板。
〔总结〕
本发明的一方案的热浸镀Zn-Al-Mg系钢板，其在钢基材的表面具有热浸镀Zn-Al-Mg系层，其中，上述钢基材以质量％计包含C：0.050～0.180％、Si：0.001～0.50％、Mn：1.00～2.80％、Ti：0.01～0.10％、及B：0.0005～0.0100％，剩余部分包含Fe及不可避免的杂质，热轧工序中的卷取后的渗碳体的平均粒径为2μm以下，连续热浸镀锌工序后的金属组织具有铁素体相和面积率为15％以上且低于45％的第二相，上述第二相由马氏体构成或者由马氏体及贝氏体构成，平均结晶粒径为8μm以下。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板，也可以以质量％计进一步包含P：0.005～0.050％、S：0.001～0.020％、及Al：0.005～0.100％中的1种以上。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板，也可以以质量％计进一步包含Nb：0～0.10％、V：0～0.10％、Cr：0～1.00％、及Mo：0～1.00％中的1种以上。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板，上述热浸镀Zn-Al-Mg系层的表层也可以存在Zn的黑色氧化物，表面的亮度L*为60以下。
本发明的一方案的热浸镀Zn-Al-Mg系钢板的制造方法，其是在钢基材的表面具有热浸镀Zn-Al-Mg系层的热浸镀Zn-Al-Mg系钢板的制造方法，该制造方法依次包含热轧工序、冷轧工序、和依次进行退火及热浸镀Zn-Al-Mg系的连续热浸镀锌工序，在上述热轧工序中，热轧后的平均冷却速度为20℃/秒以上且低于80℃/秒，卷取温度为400℃以上且低于600℃。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板的制造方法，上述钢基材也可以以质量％计包含C：0.050～0.180％、Si：0.001～0.50％、Mn：1.00～2.80％、Ti：0.01～0.10％、及B：0.0005～0.0100％，剩余部分包含Fe及不可避免的杂质，上述热轧工序中的卷取后的渗碳体的平均粒径为2μm以下，上述连续热浸镀锌工序后的金属组织具有铁素体相和面积率为15％以上且低于45％的第二相，上述第二相由马氏体构成或者由马氏体及贝氏体构成，平均结晶粒径为8μm以下。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板的制造方法，上述钢基材也可以以质量％计进一步包含P：0.005～0.050％、S：0.001～0.020％、及Al：0.005～0.100％中的1种以上。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板的制造方法，上述钢基材也可以以质量％计进一步包含Nb：0～0.10％、V：0～0.10％、Cr：0～1.00％、及Mo：0～1.00％中的1种以上。
对于本发明的一方案的热浸镀Zn-Al-Mg系钢板的制造方法，对于上述热浸镀Zn-Al-Mg系层的表层，也可以存在Zn的黑色氧化物，且表面的亮度L*为60以下。

Claims (9)

1.一种热浸镀Zn-Al-Mg系钢板，其在钢基材的表面具有热浸镀Zn-Al-Mg系层，其中，
所述钢基材以质量％计包含C：0.050～0.180％、Si：0.001～0.50％、Mn：1.00～2.80％、Ti：0.01～0.10％、及B：0.0005～0.0100％，剩余部分包含Fe及不可避免的杂质，
热轧工序中的卷取后的渗碳体的平均粒径为2μm以下，
连续热浸镀锌工序后的金属组织具有铁素体相和面积率为15％以上且低于45％的第二相，
所述第二相由马氏体构成或者由马氏体及贝氏体构成，平均结晶粒径为8μm以下。
2.根据权利要求1所述的热浸镀Zn-Al-Mg系钢板，其中，以质量％计进一步包含P：0.005～0.050％、S：0.001～0.020％、及Al：0.005～0.100％中的1种以上。
3.根据权利要求1或2所述的热浸镀Zn-Al-Mg系钢板，其中，以质量％计进一步包含Nb：0～0.10％、V：0～0.10％、Cr：0～1.00％、及Mo：0～1.00％中的1种以上。
4.根据权利要求1～3中任一项所述的热浸镀Zn-Al-Mg系钢板，其中，对于所述热浸镀Zn-Al-Mg系层的表层，其存在Zn的黑色氧化物，且表面的亮度L*为60以下。
5.一种热浸镀Zn-Al-Mg系钢板的制造方法，其是在钢基材的表面具有热浸镀Zn-Al-Mg系层的热浸镀Zn-Al-Mg系钢板的制造方法，该制造方法依次包含热轧工序、冷轧工序、和依次进行退火及热浸镀Zn-Al-Mg系的连续热浸镀锌工序，
在所述热轧工序中，
热轧后的平均冷却速度为20℃/秒以上且低于80℃/秒，
卷取温度为400℃以上且低于600℃。
6.根据权利要求5所述的热浸镀Zn-Al-Mg系钢板的制造方法，其中，所述钢基材以质量％计包含C：0.050～0.180％、Si：0.001～0.50％、Mn：1.00～2.80％、Ti：0.01～0.10％、及B：0.0005～0.0100％，剩余部分包含Fe及不可避免的杂质，
所述热轧工序中的卷取后的渗碳体的平均粒径为2μm以下，
所述连续热浸镀锌工序后的金属组织具有铁素体相和面积率为15％以上且低于45％的第二相，
所述第二相由马氏体构成或者由马氏体及贝氏体构成，平均结晶粒径为8μm以下。
7.根据权利要求6所述的热浸镀Zn-Al-Mg系钢板的制造方法，其中，所述钢基材以质量％计进一步包含P：0.005～0.050％、S：0.001～0.020％、及Al：0.005～0.100％中的1种以上。
8.根据权利要求6或7所述的热浸镀Zn-Al-Mg系钢板的制造方法，其中，所述钢基材以质量％计进一步包含Nb：0～0.10％、V：0～0.10％、Cr：0～1.00％、及Mo：0～1.00％中的1种以上。
9.根据权利要求5～8中任一项所述的热浸镀Zn-Al-Mg系钢板的制造方法，其中，对于所述热浸镀Zn-Al-Mg系层的表层，其存在Zn的黑色氧化物，且表面的亮度L*为60以下。
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