CN111094615B - 涂装后具有优异的鲜映性的钢板及其制造方法 - Google Patents

涂装后具有优异的鲜映性的钢板及其制造方法 Download PDF

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CN111094615B
CN111094615B CN201880059852.4A CN201880059852A CN111094615B CN 111094615 B CN111094615 B CN 111094615B CN 201880059852 A CN201880059852 A CN 201880059852A CN 111094615 B CN111094615 B CN 111094615B
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steel sheet
image
distinctness
rolling
excellent distinctness
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CN111094615A (zh
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白枓填
朴涩琪
金忠元
金正基
金成一
黄铉锡
李济雄
金涏垠
洪初珑
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Posco Holdings Inc
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Posco Co Ltd
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Priority claimed from PCT/KR2018/010750 external-priority patent/WO2019054769A1/ko
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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
    • 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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    • B32B15/013—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
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    • 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
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Abstract

本发明涉及一种用于诸如汽车和家电产品等的外板材料的钢板，涉及一种通过控制钢板的微细组织而在涂装后具有优异的鲜映性的钢板及其制造方法。因此，即使进行常规的涂装或薄膜涂装，也能够获得钢板表面纹理精美并且具有优异的鲜映性的效果。

Description

涂装后具有优异的鲜映性的钢板及其制造方法
技术领域
本发明涉及一种用于诸如汽车和家电产品等的外板材料的钢板，涉及一种涂装后具有优异的鲜映性的钢板及其制造方法。
背景技术
通常，在钢铁工艺中制造的薄冷轧钢板具有优异的加工性，并且由于与其它材料相比价格相对低廉，被广泛用作诸如汽车和家电产品等的外板材料。这种冷轧钢板大部分经过涂装工艺以涂装的状态使用，以提高耐腐蚀性并确保美观。因此，为了在涂装后确保精美的外观，研究集中在涂装溶液和涂装方法等技术。
但是，即使是涂装的钢板，钢板的外观质量也受到钢板自身的表面质量的影响。根据非专利文献1，钢板的表面粗糙度(粗糙度平均值(Roughness average)，Ra)越低，则钢板的中波长粗糙度(波纹度曲线平均值(Waviness curve average)，Wca)越低，并且钢板的Wca越低，涂装后的外观越优异，特别是在EDT和短鼓风(Short blast)等随机(stochastic)轧制加工方法中这种倾向尤为突出。所述非专利文献1中提及了材料的表面粗糙度与鲜映性之间的关系，但是没有提及材料的组织(grain)与鲜映性之间的关系。
(非专利文献1)Assessment of steel surface roughness and waviness inrelation with paint appearance.(Int.J.Mach.Tools Manufact.Vol.38.Nos5-6,PP.647-656.1998)
发明内容
要解决的技术问题
本发明的一个方面的目的在于提供一种通过控制钢板的微细组织而在涂装后能够确保优异的鲜映性的钢板及其制造方法。
本发明的技术问题并不限定于上述内容。本发明的其它技术问题记载于说明书的整体内容中，本发明所属技术领域的技术人员可以基于本发明的说明书中记载的内容很容易地理解本发明的其它技术问题。
技术方案
本发明的一个实施方案涉及一种涂装后具有优异的鲜映性的钢板，以重量％计，所述钢板包含：C：0.001～0.03％、Si：0.001～0.35％、Mn：0.05～2.2％、P：0.003～0.1％、S：0.001～0.025％、Al：0.01～0.1％、N：0.001～0.007％、余量的Fe和不可避免的杂质，钢板的微细组织中主要组织由铁素体相组成，钢板的表层部中的{001}<110>织构(旋转立方织构(R-cube texture))的面积分数为5％以下。
本发明的另一个实施方案涉及一种制造涂装后具有优异的鲜映性的钢板的方法，所述方法包括以下步骤：加热钢坯，以重量％计，所述钢坯包含：C：0.001～0.03％、Si：0.001～0.35％、Mn：0.05～2.2％、P：0.003～0.1％、S：0.001～0.025％、Al：0.01～0.1％、N：0.001～0.007％、余量的Fe和不可避免的杂质；将加热的所述钢坯进行热轧以制造热轧钢板；将所述热轧钢板进行收卷；以及将所述热轧钢板进行冷轧以制造冷轧钢板，其中，所述热轧时以400～1000cc/分钟的速度喷射轧制油。
有益效果
本发明的钢板即使进行常规的涂装或薄膜涂装，也能够获得钢板表面纹理精美并且具有优异的鲜映性的效果。此外，由于钢板的微细组织的微细化和均匀化，能够改善加工性，并且能够减少因加工不良产生的成本。
附图说明
图1的(a)和(b)分别是通过肉眼比较本发明的实施例中的比较例1和发明例1的涂装鲜映性的照片。
图2是示出本发明的实施例中的发明例和比较例的表层部的晶粒尺寸与旋转立方织构分数的关系的图。
图3是示出本发明的实施例中的发明例和比较例的Wa分布的图。
图4的(a)和(b)分别是示出本发明的实施例中的比较例1和发明例1的电子背散射衍射(Electron Back Scatter Diffraction，EBSD)结果的图。
最佳实施方式
以下，对本发明的钢板进行详细的说明。
首先，对本发明的钢板的成分进行详细的说明。优选地，以重量％(以下，记载为“％”)计，本发明的钢板包含：C：0.001～0.03％、Si：0.001～0.35％、Mn：0.05～2.2％、P：0.003～0.1％、S：0.001～0.025％、Al：0.01～0.1％、N：0.001～0.007％。
C：0.001～0.03％
当所述碳(C)的含量小于0.001％时，热轧板的晶粒变得粗大，因此强度降低，而且平面内各向异性增加，另一方面，当所述碳(C)的含量超过0.03％时，钢中固溶C的量增加，因此难以确保耐时效性，而且尽管由于固溶强化提高了强度，但是延展性大幅降低。因此，所述C的含量优选为0.001～0.03％。更优选地，所述C的含量控制在0.002～0.015％。
Si：0.001～0.35％
所述硅(Si)是钢中的固溶强化元素，有利于确保强度，但是Si的含量小于0.001％时，几乎没有提高强度的效果，当Si的含量超过0.35％时，在热轧过程中会引起表面氧化皮缺陷，而且由于铁素体稳定区变宽，在热轧时会发生两相区轧制，从而具有不均匀的微细组织。因此，所述Si的含量优选为0.001～0.35％。更优选地，所述Si的含量为0.01～0.3％。
Mn：0.05～2.2％
与所述Si相同，锰(Mn)也是对钢的固溶强化有效的元素。为了获得这种效果，优选含有0.05％以上的Mn。当Mn的含量小于0.05％时，提高强度的效果小，并且高温延展性降低。另一方面，当Mn的含量超过2.2％时，塑性各向异性增加，并且在退火过程中表层部的氧化物增加，因此镀覆特性降低。因此，所述Mn的含量优选为0.05～2.2％。更优选地，所述Mn的含量为0.1～0.8％。
S：0.001～0.025％
所述硫(S)是存在于钢中的杂质，当S的含量超过0.025％时，与Mn等结合形成非金属夹杂物，因此对钢进行切割加工时容易产生微细的裂纹，并且不利于成型性。但是，为了制造S的含量小于0.001％的钢，炼钢时需要过多的时间，从而生产性降低。因此，所述S的含量优选控制在0.001～0.025％。
Al：0.01～0.1％
所述铝(Al)是作为脱氧剂添加的成分，并且Al与钢中的氮结合形成AlN析出物而提高耐时效特性。当Al的含量小于0.01％时，难以充分获得上述的效果。另一方面，当Al的含量超过0.1％时，由于形成AlN析出物，在连续铸造时板坯容易发生缺陷。因此，所述Al的含量优选控制在0.01～0.1％。
N：0.001～0.007％
所述氮(N)是炼钢过程中不可避免地添加的元素，但是固溶强化效果显著，并且与Ti、Al等结合形成粗大的析出物。当N的含量超过0.007％时，由于固溶N的增加，耐时效特性变差，而且为了制造N的含量小于0.001％的钢，炼钢时的生产性降低。因此，本发明中N的含量优选控制在0.001～0.007％。
P：0.003～0.1％
在钢中，磷(P)是为了提高强度而添加的代表性的固溶强化元素，但是由于晶界偏析而引起脆性，因此使耐冲击性变差。为了获得上述的强化效果，需要至少含有0.003％以上的P，但是P的含量超过0.1％时，伸长率急剧降低，并且钢的脆性大幅增加。但是，为了将P的含量控制为小于0.003％，需要过高的制造成本，因此在经济上是不利的。因此，所述P的含量优选控制在0.003～0.1％。
除了上述的成分之外，可以进一步包含选自铌(Nb)：0.005～0.03％和钛(Ti)：0.005～0.10％中的一种以上。
所述Nb通过析出碳起到防止由固溶碳引起的时效的作用。当所述Nb的含量小于0.005％时，固溶碳的量多，因此难以防止时效现象，当Nb的含量超过0.03％时，强度变高，因此铁素体钢板的热加工性变差，并且最终产品的强度增加而不利于成型。因此，所述Nb的含量优选为0.005～0.03％。
添加所述Ti的目的在于确保非时效性并提高成型性，将Ti作为生成氮化物和碳化物的强有力的元素添加到钢中析出TiN和TiC析出物，以析出固溶状态的氮和碳，从而确保非时效性。当Ti的添加量小于0.005％时，TiC析出物的析出量过少，因此难以获得上述效果，当Ti的添加量超过0.10％时，由于形成粗大的TiN，TiC析出物的尺寸也变大，因此成型性变差，并且镀覆特性大幅降低。因此，所述Ti的含量优选为0.005～0.10％，更优选为0.005～0.06％。
除了上述成分之外，余量包含Fe和不可避免的杂质。但是，在不超出本发明的技术思想的范围内不排除添加其它合金元素。
优选地，本发明的钢板的主要组织为铁素体相。即，以面积分数计，本发明的钢板包含95％以上的铁素体相，优选是铁素体单相组织。
本发明的钢板的表层部的平均晶粒尺寸优选为30μm以下。其中，钢板的表层部优选是指从钢板表面到钢板厚度的1/16，更优选是到钢板厚度的1/32。所述钢板的表层部的平均晶粒尺寸因超过30μm而粗大时，加工时组织的不均匀性增加，从而成型性降低，而且长波长粗糙度(Wca或Wa)增加，导致涂装后的鲜映性变差。此外，所述平均晶粒尺寸越小越有利于鲜映性，但是为了使平均晶粒尺寸变小，需要添加过多的合金成分或增加压下量，并且强度和延展性会根据平均晶粒尺寸而发生很大变化，因此所述平均晶粒尺寸优选为1μm以上。
所述钢板的表层部中，晶粒尺寸为10μm以下的晶粒的面积分数与晶粒尺寸为30μm以上的晶粒的面积分数之比(晶粒尺寸为10μm以下的晶粒的面积分数/晶粒尺寸为30μm以上的晶粒的面积分数)优选为0.5以上。钢板的表层部中，晶粒尺寸为10μm以下的晶粒的面积分数与晶粒尺寸为30μm以上的晶粒的面积分数之比小于0.5时，由于组织的不均匀性，成型性变差，并且由于组织的不均匀性，鲜映性会变差。
所述钢板的表层部中，晶粒尺寸的标准偏差优选为8以下。所述标准偏差超过8时，由于组织的不均匀性，成型性和鲜映性会变差。
所述钢板的表层部中，纵横比(Aspect Ratio，短径/长径)为0.3以下的晶粒所占的面积分数优选为15％以下。所述纵横比为0.3以下的晶粒超过15％时，由于表层部的微细组织不均匀，鲜映性会变差。
所述钢板的表层部中的{001}<110>织构(旋转立方织构(Rotated-Cubetexture))的面积分数优选为5.0％以下。作为分析所述织构的面积分数的方法的一个实例，可以利用电子背散射衍射(EBSD)进行分析。
所述{001}<110>织构(旋转立方织构)是主要在冷轧过程中形成的最稳定的织构，其特征在于，在织构中具有最低的塑性各向异性指数(r)值，并且能量稳定，因此在退火时不会发生再结晶。
作为钢板的织构形成<111>织构(γ-纤维织构(γ-fiber texture)，轧制方向的垂直方向与<111>面平行的晶粒)时塑性各向异性指数值增加，从而具有优异的拉延性，但是对于鲜映性而言，重要的是钢板的表层部中存在旋转立方织构。因此，在本发明中，当表层部中的旋转立方织构的面积分数超过5.0％时，由于轧制、通过(passing)和张力等，钢板的表面上出现旋转立方簇(cluster)，并且用肉眼可以识别表面纹理(texture)的弯曲，因此鲜映性变差。
本发明的表层部中的{001}<110>织构的平均晶粒尺寸优选小于钢板整体的平均晶粒尺寸，更优选为20μm以下。{001}<110>织构的平均晶粒尺寸大于钢板整体的平均晶粒尺寸时，表面发生弯曲，因此鲜映性会变差。
本发明的钢板的长波长粗糙度(Wa)优选为0.5μm以下，更优选为0.45μm以下。
此外，本发明的钢板可以是包含镀层的镀覆钢板。对所述镀覆钢板的种类不作限定，可以是Al系镀覆钢板、Zn系镀覆(GI、GA)钢板和Zn-Al-Mg系合金镀覆钢板，在方法方面，可以应用EG镀覆、热浸镀等。
以下，对制造本发明的钢板的方法的一个实例进行详细的说明。为了制造本发明的钢板，可以加热满足上述钢的合金组成的钢坯，并将加热的钢坯进行热轧来制造。进一步地，可以将经热轧的所述钢板进行冷轧。对上述的各个工艺进行详细的说明。
准备满足上述钢的合金组成的钢坯并进行加热。所述钢坯的加热可以通过本发明所属技术领域中的常规方法进行。作为优选的一个实例，为了钢坯组织的均匀化，所述加热优选在1100～1300℃的气氛中进行100～300分钟。当所述加热温度低于1100℃时，组织的均匀化不充分，并且粗大的碳化物和氮化物等无法再固溶，因此不利于钢的成型性，当所述加热温度超过1300℃时，由于晶粒的生长，形成不均匀的微细组织。当所述加热时间小于100分钟时，无法以均匀的温度加热至板坯的深层部，当所述加热时间超过300分钟时，晶粒过度生长，并且在经济上不优选。
将加热的所述钢坯进行热轧。
所述热轧优选在850～1150℃的温度范围进行。在高于1150℃的温度下开始进行热轧时，热轧钢板的温度变高，从而晶粒尺寸变得粗大，并且热轧钢板的表面质量变差。另一方面，在低于850℃的温度下完成热轧时，由于过度延迟的再结晶，形成伸长的晶粒，从而各向异性严重且成型性也变差，而且表层部发生两相区(铁素体+奥氏体)轧制，从而不均匀的微细组织发达。
优选地，所述热轧时向钢的表面以400～1000cc/分钟喷射轧制油进行油轧。通过所述油轧在轧辊的表面形成油膜，从而通过降低轧制负荷并减少摩擦系数而提高钢板的表面质量，并且表层部的剪切变形量减少，因此有利于从表层部到深层部形成均匀的微细组织。当以小于400cc/分钟的所述轧制油的喷射量进行油轧时，难以期待上述效果，当所述轧制油的喷射量超过1000cc/分钟时，在轧制过程中由于打滑现象而在表面上发生缺陷，并且可通过性变差，在经济上是不利的。
通常，随着热轧温度降低，晶粒变得微细，并且具有均匀的微细组织。但是，当温度进一步降低时，轧辊和热轧板材之间的摩擦增加，导致表层部的剪切变形增加，从而在厚度方向无法具有均匀的组织。此外，当轧制温度降低至相变温度以下时，发生两相区轧制，从而表层部的微细组织更加不均匀。因此，在进行适当的油轧时，即使轧制温度降低，也能减轻表层部的剪切变形，并降低表层部的相变温度。结果，当如上所述进行油轧时，发生剪切变形的温度范围变窄，因此在适当的轧制温度下形成微细且均匀状态的组织。
接着，将经轧制的所述钢板进行冷却。优选地，所述冷却中将经热轧的钢板以10～100℃/秒的平均冷却速度冷却至500～750℃的温度。冷却至所述500～750℃后进行收卷。优选地，冷却至600～700℃的温度并收卷。所述冷却时，当冷却至低于500℃的温度并收卷时，钢中形成不必要的低温铁素体相，使得热轧钢板的强度上升，从而在冷轧时轧制负荷增加，并且可通过性变差。另一方面，当冷却至超过750℃的温度并收卷时，形成铁素体晶粒，从而具有不均匀的微细组织，因此不优选。所述冷却时的平均速度小于10℃/秒时，基体组织的晶粒变得粗大，并且微细组织变得不均匀，当平均冷却速度超过100℃/秒时，容易形成低温铁素体相，并且轧制板的形状变差。
对于收卷的所述钢板，通过本发明所属技术领域中的常规方法冷却至常温。例如，通过空冷或水冷以0.001～100℃/秒的冷却速度进行冷却。当冷却速度小于0.001℃/秒时，由于冷却速度慢，发生晶粒的生长，并且降低制造时的生产性。另一方面，当冷却速度超过100℃/秒时，难以均匀地冷却整个卷材，因此卷材的不同位置处会形成不均匀的微细组织。
可以将经热轧的所述钢板进行冷轧。优选地，将热轧钢板进行酸洗处理以去除附着在表面的氧化皮之后，以60～90％的压下率进行所述冷轧。当所述压下率小于60％时，在退火过程中形成再结晶而无法获得充分的变形能，因此具有不均匀的微细组织，并且成型性也会变差。对冷轧压下率的上限无需进行限制，但是冷轧压下率超过90％时，冷轧时轧制板的形状质量变差，因此冷轧压下率优选为90％以下。
所述冷轧后，可以在700～900℃的温度下进行退火热处理。
此外，所述冷轧后可以进行镀覆以制造镀覆钢板。对所述镀覆的种类不作特别限定，可以应用本发明所属技术领域中可使用的镀覆。可以应用Al系镀覆或者热浸镀锌(GI)、合金化热浸镀锌(GA)等Zn系镀覆和Zn-Al-Mg系合金镀覆，在方法方面，可以应用电镀、热浸镀和真空沉积等。作为优选的实例，可以应用利用热浸镀的镀锌钢板。这是将经退火的钢板浸渍在Zn镀浴中并使其通过后以5～50℃/秒进行冷却。之后，可以通过平整轧制改善粗糙度、形状校正和屈服点延伸。
具体实施方式
以下，对本发明的实施例进行详细的说明。下述实施例仅用于描述本发明，而并不用于限定本发明的权利范围。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出的内容所决定。
(实施例)
制造具有下表1的成分的钢坯，并以下表2的工艺条件制造冷轧钢板。对如上所述制造的冷轧钢板进行分析的结果示于表3中。表1中的成分的单位为重量％，余量包含Fe和不可避免的杂质。通过下表2的工艺制造的热轧钢板的尺寸是厚度为3.2mm，长度和宽度为1200mm，并且以700～800mpm的轧制速度的条件一致地制造钢板。
[表1]
类别 C Si Mn P S Al N Nb Ti
钢种1 0.002 0.010 0.08 0.009 0.003 0.03 0.003 0.009 0.029
钢种2 0.003 0.002 0.07 0.009 0.004 0.03 0.003 0.001 0.046
钢种3 0.002 0.028 0.14 0.018 0.01 0.03 0.003 0.003 0.001
在上表1中，钢种2的Nb和钢种3的Nb及Ti表示不可避免地包含的微量，而不是特别控制的。
[表2]
Figure GDA0002411414710000091
Figure GDA0002411414710000101
对于如上表2中所示制造的发明例和比较例，对各试片的表层部的织构中的旋转立方织构，通过电子背散射衍射(EBSD)计算{001}<110>织构(旋转立方织构)的面积分数。
此外，计算表层部的平均晶粒尺寸和晶粒尺寸为10μm以下的晶粒的面积分数与晶粒尺寸为30μm以上的晶粒的面积分数之比(晶粒尺寸为10μm以下的晶粒的面积分数/晶粒尺寸为30μm以上的晶粒的面积分数)，并且计算钢板的表层部中纵横比(短径/长径)为0.30以下的晶粒所占的面积分数。
此外，测量各个试片的加工(约5％左右的双轴拉伸加工)后的表面Wa值并得出结果。
上述得出的结果示于表3中。
[表3]
Figure GDA0002411414710000102
Figure GDA0002411414710000111
此外，图1的(a)和(b)分别示出对所述比较例1和发明例1的冷轧钢板在涂装之前进行约5％左右的双轴拉伸加工后进行涂装后，为了通过肉眼比较表面，利用格栅和光源比较鲜映度的结果。根据图1的结果，可知发明例1的鲜映度高于比较例1。图2是示出本发明的实施例中的发明例和比较例的表层部的晶粒尺寸与旋转立方织构分数的关系的图，可知发明例的表层部中均确保了均质的晶体，因此旋转立方织构也满足本发明的范围。
图3示出所述发明例和比较例的冷轧钢板的Wa平均值和其偏差。所述Wa如下测量：以双轴拉伸状态加工约5％，然后利用表面的中波长粗糙度测量仪测量Wa。如图3所示，可知发明例的Wa值低于比较例，因此具有优异的鲜映性。
此外，图4的(a)和(b)分别是通过比较例1和发明例1的EBSD分析计算表层部的旋转立方织构的面积分数的图。可以确认比较例1包含6.1％，而发明例1包含4.5％。
根据上表3的结果和附图确认的结果，当满足本发明的条件时，能够确保优异的鲜映性。

Claims (16)

1.一种涂装后具有优异的鲜映性的钢板，以重量％计，所述钢板包含：C：0.001～0.03％、Si：0.001～0.35％、Mn：0.05～2.2％、P：0.003～0.1％、S：0.001～0.025％、Al：0.01～0.1％、N：0.001～0.007％、余量的Fe和不可避免的杂质，
所述钢板的微细组织中主要组织由铁素体相组成，
所述钢板的表层部中的{001}<110>织构的面积分数为5％以下，
其中，所述{001}<110>织构是主要在冷轧过程中形成的最稳定的织构，并且所述{001}<110>织构是在织构中具有最低的塑性各向异性指数r值且能量稳定而在退火时不会发生再结晶的织构。
2.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，所述钢板包含选自Nb：0.005～0.03％和Ti：0.005～0.10％中的一种以上。
3.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，所述钢板的表层部的平均晶粒尺寸为30μm以下。
4.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，所述钢板的表层部的晶粒尺寸的标准偏差为8以下。
5.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，所述钢板的表层部中，晶粒尺寸为10μm以下的晶粒的面积分数与晶粒尺寸为30μm以上的晶粒的面积分数之比为0.5以上。
6.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，所述钢板的表层部中，纵横比为0.3以下的晶粒所占的面积分数为15％以下。
7.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，以面积分数计，所述钢板包含95％以上的铁素体相。
8.根据权利要求1所述的涂装后具有优异的鲜映性的钢板，其中，所述钢板还包含表面上的镀层，所述镀层为Al系镀层、Zn系镀层和Zn-Al-Mg系合金镀层中的任一种。
9.一种制造涂装后具有优异的鲜映性的钢板的方法，包括以下步骤：
加热钢坯，以重量％计，所述钢坯包含：C：0.001～0.03％、Si：0.001～0.35％、Mn：0.05～2.2％、P：0.003～0.1％、S：0.001～0.025％、Al：0.01～0.1％、N：0.001～0.007％、余量的Fe和不可避免的杂质；
将加热的所述钢坯进行热轧以制造热轧钢板；
将所述热轧钢板进行收卷；以及
将所述热轧钢板进行冷轧以制造冷轧钢板，
其中，所述热轧时以400～1000cc/分钟的速度喷射轧制油。
10.根据权利要求9所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，所述钢坯包含选自Nb：0.005～0.03％和Ti：0.005～0.10％中的一种以上。
11.根据权利要求9所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，所述加热在1100～1300℃的温度范围进行100～300分钟。
12.根据权利要求9所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，所述热轧后以10～100℃/秒的冷却速度进行冷却。
13.根据权利要求9所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，所述热轧后在500～750℃的范围进行收卷。
14.根据权利要求9所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，所述冷轧以60～90％的压下率进行。
15.根据权利要求9所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，还包括在所述冷轧后形成镀层的步骤，所述镀层为Al系镀层、Zn系镀层和Zn-Al-Mg系合金镀层中的任一种。
16.根据权利要求15所述的制造涂装后具有优异的鲜映性的钢板的方法，其中，形成所述镀层的步骤通过电镀、热浸镀和真空沉积中的任一种方法进行。
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