CN102597322B - 热压部件以及其制造方法 - Google Patents

热压部件以及其制造方法 Download PDF

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Publication number
CN102597322B
CN102597322B CN2010800484743A CN201080048474A CN102597322B CN 102597322 B CN102597322 B CN 102597322B CN 2010800484743 A CN2010800484743 A CN 2010800484743A CN 201080048474 A CN201080048474 A CN 201080048474A CN 102597322 B CN102597322 B CN 102597322B
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steel plate
compound layer
hot press
layer
contain
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CN102597322A (zh
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中丸裕树
中岛清次
三好达也
增冈弘之
大塚真司
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/206—Deep-drawing articles from a strip in several steps, the articles being coherent with the strip during the operation
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • 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
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    • B32B15/015—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 the said other metal being copper or nickel or an alloy thereof
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    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
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    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • C—CHEMISTRY; METALLURGY
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    • C—CHEMISTRY; METALLURGY
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Abstract

本发明提供一种热压部件，在构成部件的钢板表层存在Ni扩散区域，在上述Ni扩散区域上依次具有对应于在Zn-Ni合金平衡状态图中存在的γ相的金属间化合物层以及ZnO层，并且在25℃±5℃的空气饱和的0.5MNaCl水溶液中表示的自然浸渍电位以标准氢电极为基准是-600～-360mV。该热压部件能够不生成氧化皮地进行制造，具有优异的涂装密合性和涂装后耐腐蚀性，并且，能够抑制与腐蚀相伴的向钢中的氢侵入。

Description

热压部件以及其制造方法
技术领域
发明涉及对被加热的钢板进行冲压加工而制造的热压部件，尤其涉及在汽车的行走部、车身构造部等中使用的热压部件及其制造方法。
背景技术
以往，汽车的行走部件、车身构造部件等大多数是通过对具有规定的强度的钢板进行冲压加工而制造的。近年来，从保护地球环境的观点出发，热切希望汽车车身的轻量化，在不断努力使所使用的钢板高强度化而减少其板厚。但是，伴随着钢板的高强度化，其冲压加工性降低，因此，多有难以将钢板加工成所希望的部件形状的情况。
因此，专利文献1中提出了使用由冲模与冲头构成的模具对被加热的钢板进行加工的同时快速冷却，从而能够兼得加工的容易化与高强度化的被称作为热压的加工技术。但是，该热压中存在如下问题：由于在热压前将钢板加热至950℃前后的高温，因此在钢板表面生成氧化皮(Fe氧化物)，该氧化皮在热压时发生剥离，从而损伤模具或者损伤热压后的部件表面。另外，在部件表面残留的氧化皮亦成为外观不良、涂装密合性的降低、涂装后的耐腐蚀性的降低的原因。因此，通常，进行酸洗、喷砂处理等处理来除去部件表面的氧化皮，但这使制造工序变复杂，导致生产率的降低。
据此，期望能够在热压前的加热时抑制氧化皮的生成、且能提高热压后的部件的涂装密合性、涂装后的耐腐蚀性的热压技术，提出了在表面设有镀层等被膜的钢板以及使用其的热压方法。
例如，专利文献2中，公开了被覆有Al或者Al合金的被覆钢板。通过使用该被覆钢板，在热压前的加热时防止脱碳、氧化，从而能够得到具有极高的强度与优异的耐腐蚀性的热压部件。
另外，专利文献3中，公开了如下热压方法，即，在对被覆有Zn或者Zn基合金的钢板进行热压时，在钢板表面生成热压前的加热时防止腐蚀、脱碳且具有润滑功能的Zn-Fe基化合物、Zn-Fe-Al基化合物等合金化合物。公开了在由该方法制造的热压部件中，尤其使用了被覆有Zn-50～55质量％Al的钢板的热压部件中，能够得到优异的防腐蚀效果。
并且，专利文献4中，公开如下耐氢脆性优异的热压方法，即，使用实施了以Al或Zn为主体的镀覆的钢板，在氢浓度6体积％以下、露点10℃以下的气氛中，将其加热至Ac3变态点～1100℃的加热温度后，进行热压。该热压方法中，加热时通过减少气氛中的氢、水蒸汽的量而减少侵入钢中的氢量，从而实现避免伴随超过1000MPa的高强度化而产生的氢脆化。
专利文献1：英国专利第1490535号公报
专利文献2：日本专利第3931251号公报
专利文献3：日本专利第3663145号公报
专利文献4：日本特开2006-51543号公报
然而，专利文献2至4所记载的热压部件中，与热压前的加热时向钢中的氢侵入相比，与使用环境中的腐蚀相伴的向钢中的氢侵入所引起的氢脆化更成为问题。
发明内容
本发明的目的在于，提供一种能够不生成氧化皮地制造的、具有优异的涂装密合性与涂装后耐腐蚀性且能够抑制与腐蚀相伴的向钢中的氢侵入的热压部件及其制造方法。
本发明人们对以上述为目的的热压部件进行深入研究的结果，获得了以下见解。
i)在构成部件的钢板的表层使Ni扩散区域存在，则能抑制与腐蚀相伴的向钢中的氢侵入。
ii)在Ni扩散区域上，设置对应于在Zn-Ni合金平衡状态图中存在的γ相的金属间化合物层，则能获得优异的涂装后耐腐蚀性。
iii)在金属间化合物层上设置ZnO层，则能获得优异的涂装密合性。
本发明是基于这样的见解而进行的，提供一种热压部件，其特征在于，在构成部件的钢板的表层存在Ni扩散区域，在上述Ni扩散区域上，依次具有对应于在Zn-Ni合金平衡状态图中存在的γ相的金属间化合物层以及ZnO层，并且在25℃±5℃的空气饱和的0.5MNaCl水溶液中表示的自然浸渍电位(spontaneous immersion potential)以标准氢电极为基准是-600～-360mV。
本发明的热压部件中，优选为，Ni扩散区域在钢板的深度方向上遍及1μm以上地存在，金属间化合物层以岛状存在，在ZnO层的紧下方具有选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层。
本发明的热压部件能够通过如下方法制造，即：将在钢板表面具有含13质量％以上的Ni的Zn-Ni合金镀层的镀Ni系钢板，加热至Ac3变态点～1200℃的温度范围后，进行热压；或者将在钢板表面具有含10质量％以上不足13质量％的Ni、且钢板单面中的附着量超过50g/m2的Zn-Ni合金镀层的镀Ni系钢板，以12℃/秒以上的平均升温速度加热至Ac3变态点～1200℃的温度范围后，进行热压。此时，优选在加热至Ac3变态点～1200℃的温度范围之际，以85℃/秒以上的平均升温速度进行加热。
另外，优选使用在Zn-Ni合金镀层上进一步具有选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层的镀Ni系钢板，作为镀Ni系钢板。
作为镀Ni系钢板的衬底钢板，优选使用具有如下成分组成的钢板，即，以质量％计，含有C：0.15～0.5％、Si：0.05～2.0％、Mn：0.5～3％、P：0.1％以下、S：0.05％以下、Al：0.1％以下、N：0.01％以下，剩余部分为Fe以及不可避免的杂质；或者使用以质量％计进一步将选自Cr：0.01～1％、Ti：0.2％以下、B：0.0005～0.08％中的至少一种、以及Sb：0.003～0.03％，独立地或同时含有的钢板。
根据本发明能够制造如下热压部件，即，能够不生成氧化皮地制造的、具有优异的涂装密合性和涂装后耐腐蚀性且能够抑制与腐蚀相伴的向钢中的氢侵入的热压部件。本发明的热压部件适合用于具有980MPa以上的强度的汽车的行走部件、车体构造部件中。
附图说明
图1是模式性表示构成热压部件的钢板的板厚剖面方向组织的图。
图2是模式性表示本实施例所使用的冲压方法的图。
图3是模式性表示本实施例所使用的电化学电池的图。
具体实施方式
1)热压部件
1-1)构成部件的钢板的Ni扩散区域
如上所述，在构成部件的钢板的表层使Ni扩散区域存在，则抑制与腐蚀相伴的向钢中的氢侵入。虽然还未完全明确其理由，但考虑为如下。即，由腐蚀引起的向钢板内部的氢侵入与湿润环境下的Fe锈的氧化还原反应有关，因此为了抑制氢侵入，Fe锈需要为难以变化的稳定的锈。对于Fe锈的稳定化，Ni扩散区域是有效的，因此Ni扩散区域的存在将抑制与腐蚀相伴的向钢中的氢侵入。
但是，为了有效地抑制这样的氢的侵入，需要在构成部件的钢板的深度方向上遍及1μm以上地使Ni扩散区域存在，优选为遍及2μm以上地存在，更加优选为遍及3μm以上地存在。对深度的上限没有特别限定，但在50μm左右时，其效果饱和。Ni扩散区域的深度可通过基于EPMA(Electron Probe Micro Analyzer：电子探针显微分析仪)的厚度方向剖面的分析、或基于GDS(Glow Discharge Spectroscopy：辉光放电光谱)的深度方向的分析来求得。
此外，本发明的所谓的Ni扩散区域是指，在热压前的加热时从Ni系镀层向钢中扩散的Ni以固溶状态存在的区域。另外，本发明的热压部件是对具有Zn-Ni合金层的镀Ni系钢板进行热压而制造的，因此在Ni扩散区域有时作为杂质含有Zn，但这对本发明的效果没有损害。
1-2)Ni扩散区域上的对应于Zn-Ni合金的平衡状态图中存在的γ相的金属间化合物层
设于Ni扩散区域上的该金属间化合物层，因其腐蚀电位对钢具有替化防腐蚀效果，所以在涂装后耐腐蚀性的提高方面有效。此外，所谓对应于在Zn-Ni合金平衡状态图中存在的γ相的金属间化合物层，指的是由Ni2Zn11、NiZn3，Ni5Zn21中的任一个的金属间化合物形成的层。这样的金属间化合物可通过如下方法检测，即，在部件表面进行直接X射线衍射而检测，或者将通过FIB(Focused Ion Beam：聚焦离子束)加工而制成的薄片，利用TEM(Transmission Electron Microscopy：透射电子显微镜)一边从厚度方向剖面观察、一边进行电子线衍射而检测。
为了获得该金属间化合物层的上述效果，需要将其存在量控制为如下。
金属间化合物层的存在量可利用电化学的方法测定，即用在25℃±5℃的空气饱和的0.5MNaCl水溶液中表示的以标准氢电极为基准的自然浸渍电位来进行测定。若金属间化合物层少，自然浸渍电位比-360mm高，则失去对钢的替化防腐蚀效果，涂装后耐腐蚀性劣化。另一方面，若金属间化合物层多，自然浸渍电位比-600mm低，则随着腐蚀，氢产生量增大，从而即使存在Ni扩散区域，有时也引起氢侵入。因此，需要设置如下存在量的金属间化合物层，即，能使在25℃±5℃的空气饱和的0.5MNaCl水溶液中表示的自然浸渍电位以标准氢电极为基准是-600～-360mV。为设成如上所述的存在量，优选使金属间化合物层以岛状存在。这里，本发明中，对岛状的金属间化合物层，进行剖面SEM(Scanning Electron Microscopy：扫描电子显微镜)观察而如下地进行定义。
(1)由部件切出10mm×10mm×板厚的检测体，埋入树脂模具进行研蘑。
(2)使用(1)的埋入且研磨的检测体，利用SEM，以加速电压5～25kV、倍率500倍拍摄背散射电子像。
(3)以任意的10个视角来拍摄照片。
(4)拍摄的照片中，如图1模式性表示那样，若金属间化合物层在钢板的表面不连续地存在则为评点1，若金属间化合物层连续地存在、或者金属间化合物层在视角中不存在则为评点0。
(5)10张照片的评点的合计点为7点以上的情况下，判断为岛状。
1-3)对应于在Zn-Ni合金平衡状态图中存在的γ相的金属间化合物层上的ZnO层
设于最表层的ZnO层，不仅与上述金属间化合物层的密合性优异，与在涂装衬底处理时形成的化学成膜处理皮膜的密合性也优异，从而大幅提高涂装密合性。其厚度为0.1μm以上，则与化学成膜处理皮膜的密合性充分，另外，若为5μm以下，则ZnO层自身凝集破坏，不会损坏涂料密合性，从而优选为0.1～5μm。
此外，与上述的金属间化合物层的情况相同，ZnO层能够基于X射线衍射、或者利用TEM观察的电子线衍射来确认，并且，也能够测定其厚度。
ZnO层与其下面的金属间化合物层的密合性优异，但若在ZnO层的紧下方设置选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层，则其密合性将进一步提高，其结果，能获得更加优异的涂装密合性。
2)制造方法
本发明的热压部件能够通过如下方法制造，即，将在钢板表面具有含有13质量％以上的Ni的Zn-Ni合金镀层的镀Ni系钢板加热至Ac3变态点～1200℃的温度范围后，进行热压。
通过将上述的镀Ni系钢板加热至Ac3变态点～1200℃的温度范围，使镀层的Ni向钢板内扩散，形成Ni扩散区域。另外，通过表面的含有13质量％以上的Ni的Zn-Ni合金镀层，形成如上述的金属间化合物层，并且，Zn的一部分扩散至表面，从而在最表层形成ZnO层。
即使Zn-Ni合金镀层的Ni含有率低于13质量％，也能够通过将Ni含有率设为10质量％以上、将钢板单面中的Zn-Ni合金镀层的附着量设为超过50g/m2，以12℃/秒以上的平均升温速度来加热至Ac3变态点～1200℃的温度范围的后，进行热压而制造本发明的热压部件。
若Zn-Ni合金镀层的Ni含有率低于10质量％，平均升温速度低于12℃/秒，则不仅Ni扩散区域的形成不充分，Zn的蒸发也变得过于活跃，从而无法形成上述的金属间化合物层。另外，当钢板单面中的Zn-Ni合金镀层的附着量为50g/m2以下时，Ni扩散区域的形成变不充分。这里，所谓加热至Ac3变态点～1200℃的温度范围之际的平均升温速度定义为，从室温至最高达到板温为止的温度除以从室温至最高达到板温为止的时间的值。
与Ni含量无关地钢板表面被Zn-Ni合金镀层所被覆，因此热压前的加热时，不会生成氧化皮。
在加热至Ac3变态点～1200℃的温度范围之际，优选以85℃/秒以上的平均升温速度来加热。越加快升温速度，越缩短钢板维持高温的时间，因此能够使加热时的钢板的奥氏体晶粒细粒化，从而能够提高热压后的部件的韧性，并且能够显著抑制Zn的蒸发，进而能够形成如上述的金属间化合物层而使涂装后耐腐蚀性变良好，而且，能够防止过度形成ZnO层，能够稳定地确保涂装密合性。此外，这样的升温速度可通过通电加热或高频加热来实现。
镀Ni系钢板的Ni系镀层可以是Zn-Ni合金镀覆单层，也可以为在Ni层上或者不含Zn的Ni基合金层上设上述Zn-Ni镀覆合金层的多层。作为Ni基合金，可以举出向Ni使总计20质量％以下的选自Fe、Co、Cr、Mn、Cu、Mo等中的至少1种的元素含有的Ni基合金。
Ni扩散区域的深度、ZnO层的厚度可根据加热条件(温度、时间)来调整，金属间化合物层的存在量可根据镀Ni系的附着量来调整。此外，ZnO层不仅可通过通常进行的大气中的加热自然形成，也可以通过在氧浓度为0.1体积％以上的气氛中的加热而自然形成。
这样的Ni系镀层可通过电镀法等来形成。
在钢板表面的Zn-Ni合金镀层上，进一步设置选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层，加热至Ac3变态点～1200℃的温度范围，则Zn的一部分贯穿这些化合物层扩散至表面，在最表层形成ZnO层，因此可以在ZnO层的紧下方设置选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层。此时，对于设于Zn-Ni合金层上的这样的化合物层的厚度而言，若为0.1μm以上则能够充分提高涂装密合性，若为3.0μm以下则不会使含Si化合物层变脆，不会降低涂装密合性，因此，优选为0.1～3.0μm，更加优选为0.4～2.0μm。
作为含Si化合物，例如可以使用硅树脂、硅酸锂、硅酸钠、胶体二氧化硅、硅烷偶联剂等。作为含Ti化合物，例如可以使用钛酸锂、钛酸钙等钛酸盐、以钛醇盐或螯合型钛化合物为主剂的钛偶联剂等。作为含Al化合物，例如，可以使用铝酸钠或铝酸钙等铝酸盐、以铝醇盐或螯合型铝化合物为主剂的铝偶联剂等。作为含Zr化合物，例如可以使用锆酸锂或锆酸钙等锆酸盐、以锆醇盐或螯合型锆化合物为主剂的锆偶联剂等。
为了在Zn-Ni合金镀层上形成这样的化合物层，将选自上述的含Si化合物、含Ti化合物、含Al化合物、含Zr化合物中的至少一种的化合物附着处理于Zn-Ni合金镀层上之后，不水洗而加热干燥即可。这些化合物的附着处理可以为涂覆法、浸渍法、喷涂法中的任一种，可以使用辊涂机、挤压式涂机、模涂机等。此时，在利用挤压式涂机等的涂覆处理、浸渍处理、喷涂处理后，可利用气刀法或辊拉深法来进行涂覆量的调整、外观的均匀化、厚度的均匀化。另外，加热干燥优选为以钢板最高达到温度成为40～200℃的方式进行。更加优选为以50～160℃来进行。
另外，为了在Zn-Ni合金镀层上形成这样的化合物层，也可以利用如下方法，即，进行将具有Zn-Ni合金镀层的镀Ni系钢板浸渍于含有如下成分的酸性的水溶液的反应型处理之后，水洗或者不水洗地进行加热干燥；其中，酸性的水溶液含有选自Si、Ti、Al、Zr中的至少一种的阳离子、且含有选自磷酸离子、氟酸离子、氟化物离子中的至少一种的阴离子。
为了获得具有980MPa以上的强度的热压部件，作为镀Ni系钢板的衬底钢板，优选使用例如具有如下成分组成的钢板，即，以质量％计，含有C：0.15～0.5％、Si：0.05～2.0％、Mn：0.5～3％、P：0.1％以下、S：0.05％以下、Al：0.1％以下、N：0.01％以下，剩余部分为Fe以及不可避免的杂质；或使用进一步以质量％计将选自Cr：0.01～1％、Ti：0.2％以下、B：0.0005～0.08％中的至少1种、以及Sb：0.003～0.03％，独立地或同时含有的钢板。
下面说明各成分元素的限定理由。这里，只要没有特别说明，表示成分的含有率的“％”是“质量％”的意思。
C：0.15～0.5％
C是提高钢的强度的元素，为了使热压部件的TS为980MPa以上，C量需要为0.15％以上。另一方面，若C量超过0.5％，则素材钢板的冲切加工性显著降低。因此，C量为0.15～0.5％。
Si：0.05～2.0％
与C相同，Si也是提高钢的强度的元素，为了使热压部件的TS为980MPa以上，Si量需要为0.05％以上。另一方面，若Si量超过2.0％，则热轧时，被称作红氧化皮的表面缺陷的产生显著增多，并且，轧制载荷增大，从而导致热轧钢板的延展性的劣化。并且，若Si量超过2.0％，则当实施在钢板表面形成以Zn、Al为主体的镀膜的镀覆处理时，有对镀覆处理性产生负面影响的情况。因此，Si量为0.05～2.0％。
Mn：0.5～3％
Mn是在抑制铁素体变态，提高淬透性方面有效的元素，另外，由于会降低Ac3变态点，所以也是在降低热压前的加热温度方面有效的元素。为了显出这样的效果，Mn量需要为0.5％以上。另一方面，若Mn量超过3％，则发生偏析而降低素材钢板以及热压部件的特性的均匀性。因此，Mn量为0.5～3％。
P：0.1％以下
若P量超过0.1％，则产生偏析而降低素材钢板以及热压部件的特性的均匀性，并且，韧性也显著降低。因此，P量为0.1％以下。
S：0.05％以下
若S量超过0.05％，则热压部件的韧性降低。因此，S量为0.05％以下。
Al：0.1％以下
若Al量超过0.1％，则降低素材钢板的冲切加工性、淬透性。因此，Al量为0.1％以下。
N：0.01％以下
若N量超过0.01％，则在热轧时或热压前的加热时，形成AlN氮化物，降低素材钢板的冲切加工性、淬透性。因此，N量为0.01％以下。
剩余部分是Fe以及不可避免的杂质，但根据以下理由，优选将选自Cr：0.01～1％、Ti：0.2％以下、B：0.0005～0.08％中的至少1种、以及Sb：0.003～0.03％，独立地或同时含有。
Cr：0.01～1％
Cr是使钢强化且提高淬透性方面有效的元素。为了达到这样的效果，优选Cr量为0.01％以上。另一方面，若Cr量超过1％，则导致成本显著提高，因此其上限优选为1％。
Ti：0.2％以下
Ti是使钢强化且通过细粒化来提高韧性方面有效的元素。另外，比下述B优先地形成氮化物，因此也是在发挥因固溶B引起的提高淬透性的效果方面有效的元素。但是，若Ti量超过0.2％，则热轧时的轧制载荷极端增大，并且，热压部件的韧性降低，因此，其上限优选为0.2％以下。
B：0.0005～0.08％
B是在提高热压时的淬透性、热压后的韧性方面有效的元素。为了显出这样的效果，优选B量为0.0005％以上。另一方面，若B量超过0.08％，则热轧时的轧制载荷极端增大，并且，热轧后产生马氏体相、贝氏体相而钢板产生破裂等，因此，优选其上限为0.08％。
Sb：0.003～0.03％
Sb具有抑制从热压前加热钢板开始，到通过热压的一系列的处理使钢板冷却的期间，在钢板表层部产生脱碳层的效果。为了现出这样的效果，其量需要为0.003％以上。另一方面，若Sb量超过0.03％，则导致轧制载荷的增大，降低生产率。因此，Sb量为0.003～0.03％。
作为热压前的加热方法，可以举出利用电炉、煤气炉等的加热、火焰加热、通电加热、高频加热、感应加热等，但并不限定于此。
实施例
对具有以质量％计，含有C：0.23％、Si：0.12％、Mn：1.5％、P：0.01％、S：0.01％、Al：0.03％、N：0.005％、Cr：0.4％、B：0.0022％，剩余部分为Fe以及不可避免的杂质的成分组成的、Ac3变态点为818℃、板厚1.6mm的冷轧钢板的两面，在由50g/L(升)的硫酸钠、100g/L的硫酸镍六水合物、50g/L的硫酸锌七水合物形成的pH2、温度50℃的电镀液中，将电流密度以10～50A/dm2的方式变化，实施电镀处理，从而形成了表1、2所示的不同的Ni含有率以及附着量的Zn-Ni合金镀层。之后，除了一部分的钢板，涂覆表1、2所示的含Si化合物、含Ti化合物、含Al化合物、含Zr化合物后，以达到温度成为140℃的条件进行干燥，从而形成厚度0.5μm的、含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的一种的化合物层。将从这样获得的素材钢板采取的200mm×220mm的坯件，以平均升温速度8℃/秒加热的情况下在大气气氛的电炉内，以表1、2所示的加热温度下加热10分钟后，从炉内取出，立即利用在图2模式性表示的那样的冲压方法来进行拉深加工，从而制成热压部件No.1、4、7～21、28～30、34、37、40、41。另外，对于一部分的钢板而言，通过直接通电加热而以平均升温速度12℃/秒或者以90℃/秒进行加热，达到表1、2所示的加热温度后，从炉内取出，立即利用与上述相同的冲压方法来进行拉深加工，从而制成热压部件No.2、3、5、6、22～27、31～33、35、36、38、39。另外，进行拉深加工时的冲头宽度为70mm、加工高度为30mm。而且，从部件头部的平坦部采取试样，利用上述的方法，测定了成为Ni扩散区域的深度、ZnO层的厚度、金属间化合物层的存在量的指标的自然浸渍电位，并且，利用上述的剖面SEM观察来确认了金属间化合物层的状态。另外，利用以下方法，调查耐氧化皮性、涂装密合性、涂装后耐腐蚀性、耐氢侵入性。
耐氧化皮性：目视观察热压后的非冲头接触面，根据以下的基准评价。
○：无氧化皮的附着
×：有氧化皮的附着
涂装密合性：从部件头部的平坦部采取试样，使用日本Parkerizing株式会社制PB-SX35，在非冲头接触面以标准条件实施了化学成膜处理之后，在170℃×20分钟的烘烤条件下，将关西Paint株式会社制的电沉积涂料GT-10HT Gray成膜为膜厚20μm，制成涂装试验片。进而，利用切割刀，对制成的试验片的实施了化学成膜处理以及电沉积涂装的面切入到达钢质地的棋盘格(10×10个、1mm间隔)，进行了利用粘接带贴着·剥离的棋盘格胶带剥离试验。根据以下的基准评价，若为○、△则评为满足本发明的目的。
○：无剥离
△：在1～10个棋盘格上发生剥离
×：在11个以上的棋盘格上发生剥离
涂装后耐腐蚀性：在利用与上述涂装密合性的情况相同的方法制成的涂装试验片的实施了化学成膜处理以及电沉积涂装的面上，利用切割刀向涂膜切入十字纹(cross cut)之后，以依据SAE-J2334的腐蚀试验周期条件来进行腐蚀试验，对25周期后的最大单侧涂膜膨胀宽度进行测定，根据以下的基准评价，若为○、△则评为满足本发明的目的。
○：0mm≤膨胀宽度＜1.5mm
△：1.5mm≤膨胀宽度＜3.0mm
×：3.0mm≤膨胀宽度
耐氢侵入性：从部件头部的平坦部采取试样，将一侧的面(冲头接触面)镜面磨削而使板厚为1mm。接着，以试样作为工作极，以白金作为对极，对磨削面进行Ni镀覆而作为氢检测面，安装于图3中模式性表示的电化学电池，一边使非磨削面在大气中、在室温下腐蚀，一边利用电化学的氢透过法测定侵入钢中的氢量。即，向氢检测面侧填充0.1MNaOH水溶液，通过盐桥设置参比电极(Ag/AgCl)，向非磨削面(评价面：非冲头接触面)侧滴下0.5MNaCl溶液，在大气中、室温下腐蚀，使氢检测面侧的电位成为0VvsAg/AgCl，一边以1次/日的频率向腐蚀部滴下纯水，一边连续5日测定氢透过电流值，从其最大电流值，根据以下的基准评价与腐蚀相伴的耐氢侵入性。若为◎、○则评为满足本发明的目的。此外，对于热压时的氧化皮的生成显著的部件，利用喷砂处理除去表面的氧化皮之后进行试验。
◎：最大电流值为冷轧钢板的情况的1/10以下
○：最大电流值为大于冷轧钢板的情况的1/10至其1/2以下
×：最大电流值为大于冷轧钢板的情况的1/2至与冷轧钢板相同
结果示于表3、4。可知作为本发明的热压部件No.1～27、30不仅耐氧化皮性、涂装密合性、涂装后耐腐蚀性优异、在耐氢侵入性方面也优异。
Figure BDA0000157613560000141
Figure BDA0000157613560000151
表3
Figure BDA0000157613560000161
表4
Figure BDA0000157613560000171

Claims (10)

1.一种热压部件，其特征在于，在构成部件的钢板的表层存在Ni扩散区域，在所述Ni扩散区域上依次具有对应于在Zn-Ni合金平衡状态图中存在的γ相的金属间化合物层和ZnO层，并且，在25℃±5℃的空气饱和的0.5MNaCl水溶液中表示的自然浸渍电位以标准氢电极为基准是-600～-360mV，
并且，Ni扩散区域在钢板的深度方向上遍及1μm以上地存在。
2.根据权利要求1所述的热压部件，其特征在于，金属间化合物层以岛状存在。
3.根据权利要求1或2所述的热压部件，其特征在于，在ZnO层的紧下方具有选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层。
4.一种权利要求1所述的热压部件的制造方法，其特征在于，将在钢板表面具有含13质量%以上的Ni的Zn-Ni合金镀层的镀Ni系钢板，加热至Ac3变态点～1200℃的温度范围后，进行热压。
5.一种权利要求1所述的热压部件的制造方法，其特征在于，将在钢板表面具有含10质量%以上、低于13质量%的Ni、且钢板单面中的附着量超过50g/m2的Zn-Ni合金镀层的镀Ni系钢板，以12℃/秒以上的平均升温速度加热至Ac3变态点～1200℃的温度范围后，进行热压。
6.根据权利要求4或5所述的热压部件的制造方法，其特征在于，在加热至Ac3变态点～1200℃的温度范围之际，以85℃/秒以上的平均升温速度进行加热。
7.根据权利要求4～6中任一项所述的热压部件的制造方法，其特征在于，使用在Zn-Ni合金镀层上进一步具有选自含Si化合物层、含Ti化合物层、含Al化合物层、含Zr化合物层中的至少一种的化合物层的镀Ni系钢板，作为镀Ni系钢板。
8.根据权利要求4～7中任一项所述的热压部件的制造方法，其特征在于，镀Ni系钢板的衬底钢板具有如下成分组成，即，以质量%计，含有C：0.15～0.5%、Si：0.05～2.0%、Mn：0.5～3%、P：0.1%以下、S：0.05%以下、Al：0.1%以下、N：0.01%以下，剩余部分为Fe以及不可避免的杂质。
9.根据权利要求8所述的热压部件的制造方法，其特征在于，镀Ni系钢板的衬底钢板以质量%计进一步含有选自Cr：0.01～1%、Ti：0.2%以下、B：0.0005～0.08%中的至少一种。
10.根据权利要求8或9所述的热压部件的制造方法，其特征在于，镀Ni系钢板的衬底钢板以质量%计进一步含有Sb：0.003～0.03%。
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