CN110088330B - 加工性优异的热浸镀钢材及其制造方法 - Google Patents

加工性优异的热浸镀钢材及其制造方法 Download PDF

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CN110088330B
CN110088330B CN201780077822.1A CN201780077822A CN110088330B CN 110088330 B CN110088330 B CN 110088330B CN 201780077822 A CN201780077822 A CN 201780077822A CN 110088330 B CN110088330 B CN 110088330B
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hot
less
steel product
rolled steel
temperature
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CN110088330A (zh
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金珍有
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • B32B15/013—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 a metal other than iron or aluminium
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • 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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    • 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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    • 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
    • B32B15/18—Layered products comprising a layer of metal comprising iron or steel
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    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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Abstract

本发明公开一种热浸镀钢材及其制造方法，所述热浸镀钢材包含热轧钢材和形成在所述热轧钢材表面的热浸镀层，以重量％计，所述热轧钢材包含：C：0.05～0.15％、Si：0.5％以下(0％除外)、Mn：0.5～1.5％、Nb：0.01～0.05％、V：0.005～0.05％、P：0.03％以下(0％除外)、S：0.015％以下(0％除外)、Al：0.05％以下(0％除外)、N：0.01％以下(0％除外)、余量的Fe和不可避免的杂质，微细组织包含90面积％以上的铁素体，并且包含5000～15000个/μm2的V类析出物。

Description

加工性优异的热浸镀钢材及其制造方法
技术领域
本发明涉及一种加工性优异的热浸镀钢材及其制造方法，更具体地，涉及一种可以被优选用于隧道和斜坡的支撑用岩石锚杆的加工性优异的热浸镀钢材及其制造方法。
背景技术
岩石锚杆是用于支撑隧道和斜坡的装置(参照专利文献1至3)，需要支撑相当大的负载，因此要求材料的强度优异。因此，在现有技术中，作为这种岩石锚杆用材料主要使用热轧钢材，所述热轧钢材在使钢中的杂质最小化的高纯度钢中添加大量的如C、Si、Mn、Cr等固溶强化元素或者添加大量的如Ti、Nb、V、Mo等析出强化元素来增强强度。
但是，岩石锚杆在实际使用过程中会经过加工成马蹄形状后插入支撑面并通过液压体积膨胀的过程，而添加大量的如C、Si、Mn、Cr等固溶强化元素或如Ti、Nb、V、Mo等析出强化元素的热轧钢材由于加工性差，在加工部位往往出现裂纹。另外，岩石锚杆在制造过程中会经过制管焊接的过程，而添加大量的如C、Si、Mn、Cr等固溶强化元素或如Ti、Nb、V、Mo等析出强化元素的热轧钢材由于碳当量高，存在焊接性差的问题。
专利文献
(专利文献1)韩国授权专利公报第10-0972357号
(专利文献2)韩国授权专利公报第10-1038472号
(专利文献3)韩国授权专利公报第10-1196889号
发明内容
(一)要解决的技术问题
本发明的多种目的中的一种是提供加工性优异的热浸镀钢材及其制造方法。
(二)技术方案
本发明的一个方面提供一种热浸镀钢材，该热浸镀钢材包含热轧钢材和形成在所述热轧钢材表面的热浸镀层，以重量％计，所述热轧钢材包含：C：0.05～0.15％、Si：0.5％以下(0％除外)、Mn：0.5～1.5％、Nb：0.01～0.05％、V：0.005～0.05％、P：0.03％以下(0％除外)、S：0.015％以下(0％除外)、Al：0.05％以下(0％除外)、N：0.01％以下(0％除外)、余量的Fe和不可避免的杂质，微细组织包含90面积％以上的铁素体，并且包含5000～15000个/μm2的V类析出物。
本发明的另一方面提供一种热浸镀钢材的制造方法，包括以下步骤：在1100～1300℃的温度下，对板坯进行再加热，以重量％计，所述板坯包含：C：0.05～0.15％、Si：0.5％以下(0％除外)、Mn：0.5～1.5％、Nb：0.01～0.05％、V：0.005～0.05％、P：0.03％以下(0％除外)、S：0.015％以下(0％除外)、Al：0.05％以下(0％除外)、N：0.01％以下(0％除外)、余量的Fe和不可避免的杂质，对经再加热的所述板坯进行粗轧，然后在奥氏体单相区域温度下进行终轧，以得到热轧钢材；将所述热轧钢材以40～60℃/秒的速度水冷至650～750℃的温度，然后空冷1～5秒；在600～650℃的温度下，对经空冷的所述热轧钢材进行收卷；以及在500～650℃的温度下，对经收卷的所述热轧钢材进行1～5分钟的热处理，然后进行热浸镀。
(三)有益效果
作为本发明的多种效果中的一种，根据本发明的热浸镀钢材具有优异的强度和延展性的平衡。
本发明的多种有益的优点和效果并不限定于上述的内容，可以在说明本发明的具体实施方式的过程中进一步容易理解。
最佳实施方式
下面，对本发明的一个方面的加工性优异的热浸镀钢材进行详细说明。
本发明的热浸镀钢材包含热轧钢材和形成在所述热轧钢材表面的热浸镀层。在本发明中，对热浸镀层的组分不作特别限制，作为一个非限制性实例，所述热浸镀层可以包含Zn、Al和Mg中的一种以上(例如，Zn、Zn-Al、Zn-Al-Mg)。
下面，对作为基材的热轧钢材的合金成分和优选含量范围进行详细说明。除非有特别说明，后面说明的各成分的含量均以重量为基准。
C：0.05～0.15％
C是确保强度的最经济且有效的元素。当碳含量过低时，即使添加如Nb等析出强化元素，也难以确保期望的强度。另一方面，当碳含量过多时，由于强度的过度上升，延展性可能会变差。
Si：0.5％以下(0％除外)
尽管Si通过钢水的脱氧和固溶强化有助于提高强度，但是在本发明中没有有意地添加Si，并且即使不添加硅，在确保物理性质的方面上没有太大的问题。另一方面，当Si含量过多时，在热轧钢材的表面上形成由Si引起的红色氧化皮，由此可能会导致表面质量和焊接性降低。
Mn：0.5～1.5％
Mn是对钢的固溶强化有效的元素，为了确保适当的强度，需要添加0.5％以上的Mn。但是，当Mn含量过多时，在连铸工艺中存在产生中心偏析部的风险。
Nb：0.01～0.05％
Nb作为析出强化元素，是通过产生NbC类析出物来使延展性的降低最小化的同时，确保强度的有效元素。尤其，当添加适量的Nb时，屈服强度的增加效果显著。为了在本发明中获得这种效果，优选添加0.01％以上的Nb。然而，当Nb的含量过多时，由于制造成本的增加，经济性可能会变差。考虑到这一点，优选地，Nb的上限控制在0.05％。
V：0.005～0.05％
V同样作为析出强化元素，是对确保钢的强度有效的元素。为了在本发明中得到这些效果，优选添加0.005％以上的V。但是，当V含量过多时，可能会降低韧性。考虑到这一点，优选地，V的上限控制在0.05％。
P：0.03％以下(0％除外)
P是钢中不可避免地包含的元素，因此优选将P含量尽可能控制在最低。尤其，当P含量过多时，焊接性变差和钢的脆性发生的风险增加，在本发明中将P含量控制在0.03％以下。
S：0.015％以下(0％除外)
S是钢中不可避免地包含的杂质，因此优选将S含量尽可能控制在最低。尤其，当S含量过多时，可能会与Mn等结合而形成非金属夹杂物，并且发生钢的脆性的风险增加，因此在本发明中将S含量控制在0.015％以下。
Al：0.05％以下(0％除外)
虽然Al有助于钢水的脱氧，但是在本发明中不会有意地添加，并且即使不添加铝，在确保物理性质方面也没有太大的问题。另一方面，当铝含量过多时，在连铸时可能会发生喷嘴堵塞现象等，因此，在本发明中将铝含量控制在0.05％以下。
N：0.01％以下(0％除外)
虽然N有助于提高钢的强度，但是在本发明中不会有意地添加N，并且即使不添加氮，在确保物理性质方面也没有太大的问题。另一方面，当氮含量过多时，发生钢的脆性的风险增加，因此在本发明中将氮含量控制在0.01％以下。
除了所述组分以外的剩余部分是Fe。但是，在一般的制造过程中可能会从原料或周围环境中不可避免地混入不期望的杂质，因此无法排除这些杂质。这些杂质对于本技术领域的普通技术人员来说是公知的，因此，在本说明书中不特别提及其全部内容，其代表性杂质如下。
Cr：0.05％以下
Cr有助于通过对钢进行固溶强化并在冷却时延迟贝氏体的相转变来形成等轴晶粒铁素体，但是在本发明中即使不添加Cr，在确保物理性质方面也没有太大的问题。另一方面，当Cr含量过多时，焊接性变差，因此在本发明中将Cr含量控制在0.05％以下。
Ni：0.05％以下
Ni起到同时提高钢的强度和韧性的作用，但是在本发明中即使不添加Ni，在确保物理性质方面也没有太大的问题。另一方面，当Ni含量过多时，经济性降低，并且焊接性变差，因此在本发明中将Ni含量控制在0.05％以下。
Mo：0.01％以下
Mo通过固溶强化提高屈服强度，并且通过强化晶界来改善冲击韧性，但是在本发明中即使不添加Mo，在确保物理性质方面也没有太大的问题。另一方面，当Mo含量过多时，不仅经济性降低，而且焊接性也会变差，因此在本发明中将Mo含量控制在0.01％以下。
Cu：0.01％以下
Cu起到通过形成微细析出物来提高强度的作用，但是在本发明中即使不添加Cu，在确保物理性质方面也没有太大的问题。另一方面，当Cu含量过多时，热加工性和常温加工性变差，因此在本发明中将Cu含量控制在0.01％以下。
另一方面，优选地，在设计具有如上所述的成分范围的钢材的合金时，由以下式1定义的碳当量(Ceq)控制在0.43以下。这是为了确保适当水平的焊接性。
[式1]Ceq＝[C]+[Mn]/6+([Cu]+[Ni])/15+([Cr]+[Mo]+[V])/5
(其中，[C]、[Mn]、[Cu]、[Ni]、[Cr]、[Mo]和[V]分别表示相应元素的含量(重量％))
下面，对作为基材的热轧钢材的微细组织等进行详细说明。
作为本发明的热浸镀钢材的基材的热轧钢材的一个技术特征在于，包含5000～15000个/μm2的V类析出物。当V类析出物的单位面积的数量小于5000个/μm2时，可能会无法确保充分的强度，另一方面，当V类析出物的单位面积的数量超过15000个/μm2时，可能会难以确保充分的延展性。在本发明中，对V类析出物的具体种类不作特别限制，例如，可以是VC、VN、V(C，N)。
根据一个实例，所述V类析出物的平均直径可以是5～10nm，并且其最大直径可以是20nm以下。当V类析出物的平均直径小于5nm时，由于析出物在相对低的温度下产生，因此，可能会难以充分确保单位面积的数量，另一方面，当V类析出物的平均直径超过10nm，或者最大直径超过20nm时，由于粗大的析出物，析出强化效果可能不充分，因此，可能会难以确保充分的强度。其中，平均直径表示通过观察热轧钢材的厚度方向上的截面来检测的V类析出物的平均圆等效直径(equivalent circular diameter)，并且最大直径表示通过观察热轧钢材的厚度方向上的截面来检测的V类析出物的最大圆等效直径(equivalentcircular diameter)。
在本发明中，对作为基材的热轧钢材的微细组织不作特别限制，例如，作为基材的热轧钢材的微细组织可以包含铁素体、珠光体和贝氏体，在此情况下，铁素体的面积分数可以是90％以上。当铁素体的面积分数小于90％时，由于加工性变差，在制管后扩管时产生裂纹的可能性变大。
根据一个实例，铁素体的纵横比(aspect ratio)可以是0.8至1.4。当铁素体的纵横比控制在如上所述的水平时，材质各向异性降低，从而在岩石锚杆的制管和扩管时有可能利于加工性。当铁素体的纵横比小于0.8或超过1.4时，由于加工性变差，在制管和扩管时可能会产生裂纹。另一方面，铁素体的纵横比可以通过电子背散射衍射(ElectronBackscatter Diffraction，EBSD)来计算得出。更具体地，在随机位置以500倍的倍率测量EBSD10次，并且针对由此获得的数据，利用基本由TSL OIM Analysis 6.0软件提供的颗粒形状纵横比(Grain Shape Aspect Ratio)程序来计算平均值并获得铁素体的纵横比。
根据本发明的热浸镀钢材具有强度和延展性优异的优点，根据一个非限制性实例，本发明的热浸镀钢材的拉伸强度可以是450～650MPa、屈服强度可以是400～600MPa、延伸率可以是25～35％。
本发明的热浸镀钢材具有加工性优异的优点，根据一个非限制性实例，屈服强度和延伸率的乘积可以是12000～15000MPa·％。
以上说明的本发明的热浸镀钢材可以通过多种方法制造，并且对其制造方法不作特别限制。作为一个优选实例，可以通过如下方法制造。
下面，对本发明的另一方面的加工性优异的热浸镀钢材的制造方法进行详细说明。
首先，在1100～1300℃的温度下，对具有上述的组分体系的板坯进行再加热。当再加热温度小于1100℃时，在后续工艺的热轧工艺中，轧制负荷可能会过度增加，另一方面，当再加热温度超过1300℃时，由于部分奥氏体晶粒的异常生长引起的部分粗大化，最终微细组织的晶粒尺寸可能会不均匀。另一方面，在本发明中，对板坯再加热时间不作特别限制，只要常规条件即可。作为一个非限制性实例，板坯再加热时间可以是100～400分钟。
接着，对经再加热的板坯进行粗轧，然后在奥氏体单相区域温度下进行终轧，以得到热轧钢材。
其中，粗轧表示在终轧之前执行的一系列中间轧制过程，在本发明中，对粗轧的具体条件不作特别限制，只要是常规条件即可。作为一个非限制性实例，经粗轧的板坯的厚度可以是经再加热的板坯的厚度的10～25％，并且粗轧温度可以设置为可确保终轧温度的充分高的温度。
终轧在奥氏体单相区域温度下实施，其目的在于增加组织的均匀性。
根据一个实例，在热轧时，终轧温度可以是800～900℃。在所述温度范围内进行热终轧时，经终轧的热轧钢材的奥氏体组织将具有10～40μm的平均晶粒尺寸。另一方面，当终轧温度小于800℃时，热轧负荷增加，由此可能会降低生产性，另一方面，当终轧温度超过900℃时，板坯的奥氏体晶粒粗大化，因此可能会难以确保期望的加工性。
接着，冷却热轧钢材。此时，当通过传统的连续冷却来冷却热轧钢材时，可能会难以充分确保等轴铁素体，并且由于过度形成针状铁素体，延展性可能会变差。因此，在本发明中，将热轧钢材以40～60℃/秒的速度水冷至650～750℃的温度，然后通过空冷1～5秒的二段式冷却来冷却热轧钢材。
其中，650～750℃的温度是铁素体转变最快的温度，是使等轴铁素体最有效生长的温度，下面将其称为中间温度。更优选地，中间温度范围为680～720℃。
当中间温度超过750℃或者空冷时间超过5秒时，虽然形成等轴铁素体，但是由于过度形成铁素体，屈服强度可能会变差，另一方面，当中间温度小于650℃或者空冷时间小于1秒时，难以形成等轴铁素体，因此延展性可能会变差。另外，当空冷时间超过5秒时，由于NbC析出物粗大化，在收卷时生成的微细NbC析出物效果降低，因此可能会难以确保所期望的加工性。
当水冷时的冷却速度小于40℃/秒时，在输出辊道(ROT)冷却区间中可能会无法确保充分的空冷时间，另一方面，当水冷时的冷却速度超过60℃/秒时，由于过快的冷却速度，可能会难以确保期望的中间温度。
另一方面，当空冷后热轧钢材的温度超过期望的收卷温度时，在对经空冷的所述热轧钢材进行收卷之前，以40～60℃/秒的速度将经空冷的所述热轧钢材水冷至期望的收卷温度，其中，限制冷却速度的目的在于在中间温度之后确保适当的收卷温度。
接着，在550～650℃的温度下，对经冷却的热轧钢材进行收卷。收卷温度范围更优选为600～650℃。所述温度范围是生成NbC析出物最快的温度范围，当在所述温度范围内进行收卷时，析出微细的NbC，从而可以补偿由于形成等轴铁素体而降低的屈服强度。当收卷温度超过650℃时，由于形成粗大的珠光体，屈服强度可能会降低，另外，由于NbC析出物粗大化，可能会难以确保期望的加工性。另一方面，当收卷温度小于550℃时，晶粒变微细化，因此屈服强度增加，但是延展性可能会变差，并且微细NbC析出物的含量减少，由此可能会难以确保期望的加工性。
接着，在500～650℃的温度下，对经收卷的热轧钢材进行1～5分钟的热处理。此时，热处理温度范围更优选为550～600℃，热处理温度范围进一步更优选为550～590℃，更优选地，热处理时间范围为2～4分钟。
在这种热处理过程中，析出残留的NbC析出物，并且析出微细的V(C，N)析出物，从而通过析出强化效果提高钢的强度。当热处理温度小于500℃或者热处理时间小于1分钟时，镀覆粘附性变差，并且V类析出物可能无法充分析出，另一方面，当热处理温度超过650℃或者热处理时间超过5分钟时，生产性可能会变差。
接着，对经热处理的热轧钢材进行热浸镀，以制造热浸镀钢材。
具体实施方式
下面，通过实施例对本发明进行更详细说明。但是，这些实施例仅是用于例示本发明的实施方式，本发明并不限定于这些实施例。这是因为本发明的权利范围由权利要求书中记载的内容和由此合理推导的内容而确定。
在1150℃的温度下，对具有以下表1和2的组分的板坯进行200分钟的再加热，然后以以下表3的条件进行粗轧和终轧，以得到热轧钢材。此时，在所有的实例中，使经粗轧的板坯的厚度恒定为经再加热的板坯的厚度的20％。然后，将热轧钢材以50℃/秒的速度水冷至以下表3的中间温度并空冷5秒，然后在以下表3的收卷温度下进行收卷。在表3的中间温度中记载连续冷却的实例的情况是实施连续冷却至收卷温度而没有空冷的实例。另一方面，在经空冷的热轧钢材的温度没有达到以下表3的收卷温度的实例的情况下，进一步以50℃/秒的速度水冷至收卷温度。然后，在以下表3的热处理温度下，对经收卷的热轧钢材进行2分钟的热处理，然后执行热浸镀锌。
然后，分析制造的热轧镀覆钢材的微细组织，评价机械物理性质，并将其结果表示在以下表4中。另外，在所有的实例中，除了铁素体以外的剩余组织是珠光体和/或贝氏体。
[表1]
Figure GDA0002095231870000101
[表2]
Figure GDA0002095231870000102
[表3]
Figure GDA0002095231870000111
[表4]
Figure GDA0002095231870000112
如表4可知，满足本发明中提出的所有合金组分和制造条件的发明例1和2的强度和延伸率的乘积为12000MPa％以上，并且表现出强度和延展性的平衡非常优异。
另一方面，比较例1至11的合金组成和制造条件中的一种以上超出本发明中提出的条件，因此表现出强度和延伸率的平衡较差。

Claims (11)

1.一种热浸镀钢材，该热浸镀钢材包含热轧钢材和形成在所述热轧钢材表面的热浸镀层，以重量％计，所述热轧钢材包含：C：0.05～0.15％、Si：0.5％以下且0％除外、Mn：0.5～1.5％、Nb：0.01～0.05％、V：0.005～0.05％、P：0.03％以下且0％除外、S：0.015％以下且0％除外、Al：0.05％以下且0％除外、N：0.01％以下且0％除外、余量的Fe和不可避免的杂质，微细组织包含90面积％以上的铁素体，除了所述铁素体以外，余量为珠光体和贝氏体中的一种以上，并且包含5000～15000个/μm2的V类析出物，
所述铁素体的纵横比为0.8至1.4，
其中，所述热浸镀钢材的屈服强度和延伸率的乘积为12000～15000MPa·％。
2.根据权利要求1所述的热浸镀钢材，其中，
所述V类析出物的平均直径为5～10nm。
3.根据权利要求1所述的热浸镀钢材，其中，
所述V类析出物的最大直径为20nm以下。
4.根据权利要求1所述的热浸镀钢材，其中，
所述不可避免的杂质包含Cr、Ni、Mo和Cu，并且以重量％计，将其抑制为Cr：0.05％以下、Ni：0.05％以下、Mo：0.01％以下、Cu：0.01％以下。
5.根据权利要求4所述的热浸镀钢材，其中，
所述热轧钢材中由以下式1定义的碳当量Ceq为0.43以下，
[式1]Ceq＝[C]+[Mn]/6+([Cu]+[Ni])/15+([Cr]+[Mo]+[V])/5
其中，[C]、[Mn]、[Cu]、[Ni]、[Cr]、[Mo]和[V]分别表示相应元素的重量百分比含量。
6.根据权利要求1所述的热浸镀钢材，其中，
所述热浸镀层包含Zn、Al和Mg中的一种以上。
7.一种热浸镀钢材的制造方法，包括以下步骤：
在1100～1300℃的温度下，对板坯进行再加热，以重量％计，所述板坯包含：C：0.05～0.15％、Si：0.5％以下且0％除外、Mn：0.5～1.5％、Nb：0.01～0.05％、V：0.005～0.05％、P：0.03％以下且0％除外、S：0.015％以下且0％除外、Al：0.05％以下且0％除外、N：0.01％以下且0％除外、余量的Fe和不可避免的杂质，
对经再加热的所述板坯进行粗轧，然后在奥氏体单相区域温度下进行终轧，以得到热轧钢材；
将所述热轧钢材以40～60℃/秒的速度水冷至650～750℃的温度，然后空冷1～5秒；
在550～650℃的温度下，对经空冷的所述热轧钢材进行收卷；以及
在500～600℃的温度下，对经收卷的所述热轧钢材进行1～5分钟的热处理，然后进行热浸镀，
其中，所述热浸镀钢材的屈服强度和延伸率的乘积为12000～15000MPa·％。
8.根据权利要求7所述的热浸镀钢材的制造方法，其中，
所述板坯再加热时间为100～400分钟。
9.根据权利要求7所述的热浸镀钢材的制造方法，其中，
经粗轧的板坯的厚度为经再加热的所述板坯的厚度的10～25％。
10.根据权利要求7所述的热浸镀钢材的制造方法，其中，
终轧温度为800～900℃。
11.根据权利要求7所述的热浸镀钢材的制造方法，进一步包括以下步骤：
当经空冷的所述热轧钢材的温度超过650℃时，经空冷的所述热轧钢材在进行收卷之前，将经空冷的所述热轧钢材以40～60℃/秒的速度水冷至550～650℃的温度。
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