JP3643559B2 - Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same - Google Patents
Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same Download PDFInfo
- Publication number
- JP3643559B2 JP3643559B2 JP2002015854A JP2002015854A JP3643559B2 JP 3643559 B2 JP3643559 B2 JP 3643559B2 JP 2002015854 A JP2002015854 A JP 2002015854A JP 2002015854 A JP2002015854 A JP 2002015854A JP 3643559 B2 JP3643559 B2 JP 3643559B2
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- film
- chemical conversion
- plated
- workability
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Images
Landscapes
- Chemical Treatment Of Metals (AREA)
- Coating With Molten Metal (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Description
【０００１】
【発明の属する技術分野】
本発明は、めっき皮膜中のＡｌ含有量が２０〜９５mass％の溶融Ａｌ−Ｚｎ系めっき鋼板を下地鋼板とする表面処理鋼板とその製造方法に関する。
【０００２】
【従来の技術】
めっき皮膜中にＡｌを２０〜９５mass％含有する溶融Ａｌ−Ｚｎ系めっき鋼板は、特公昭４６−７１６１号に示されるように溶融亜鉛めっき鋼板に比べて優れた耐食性を示すことから、近年、建材分野を中心に需要が伸びている。
このめっき鋼板は、酸洗脱スケールした熱延鋼板又はこれをさらに冷間圧延して得られた冷延鋼板を下地鋼板とし、連続式溶融めっき設備において以下のようにして製造される。
【０００３】
連続式溶融めっき設備では、下地鋼板は還元性雰囲気に保持された焼鈍炉内で所定温度に加熱され、焼鈍と同時に鋼板表面に付着する圧延油等の除去、酸化膜の還元除去が行われた後、下端がめっき浴に浸漬されたスナウト内を通って所定濃度のＡｌを含有した溶融亜鉛めっき浴中に浸漬される。めっき浴に浸漬された鋼板はシンクロールを経由してめっき浴の上方に引き上げられた後、めっき浴上に配置されたガスワイピングノズルから鋼板の表面に向けて加圧した気体を噴射することによりめっき付着量が調整され、次いで冷却装置により冷却され、所定のめっき皮膜が形成された溶融Ａｌ−Ｚｎ系めっき鋼板が得られる。
【０００４】
連続式溶融めっき設備における焼鈍炉の熱処理条件及び雰囲気条件、めっき浴組成やめっき後の冷却速度等の操業条件は、所望のめっき品質や材質を確保するために所定の管理範囲で精度よく管理される。
上記のようにして製造されためっき鋼板のめっき皮膜は、主としてＺｎを過飽和に含有したＡｌがデンドライト凝固した部分と、残りのデンドライト間隙の部分からなっており、デンドライトはめっき皮膜の膜厚方向に積層している。このような特徴的な皮膜構造により、溶融Ａｌ−Ｚｎ系めっき鋼板は優れた耐食性を示す。
【０００５】
また、めっき浴には通常１．５mass％程度のＳｉが添加されているが、このＳｉの働きにより、溶融Ａｌ−Ｚｎ系めっき鋼板はめっき皮膜／下地鋼板界面の合金相成長が抑えられ、合金相厚さは約１〜２μｍ程度である。この合金相が薄ければ薄いほど優れた耐食性を示す特徴的な皮膜構造の部分が多くなるので、合金相の成長抑制は耐食性の向上に寄与する。また、合金相はめっき皮膜よりも固く加工時にクラックの起点として作用するので、合金相の成長抑制はクラックの発生を減少させ、加工性の向上効果をもたらす。また、クラック部は下地鋼板が露出していて耐食性に劣るので、クラックの発生を減じることは加工部耐食性をも向上させる。
【０００６】
通常、めっき浴には不可避的不純物、鋼板やめっき浴中の機器等から溶出するＦｅ、合金相抑制のためのＳｉが含まれるが、それら以外にも何らかの元素が添加されている場合もあり、合金相やめっき皮膜中にはそれら元素が合金或いは単体の形で存在している。
また、溶融Ａｌ−Ｚｎ系めっき鋼板は実用に供されるに当たって溶融めっきままで使用されることは極く稀であり、通常はめっき鋼板表面に化成処理や塗装を施した表面処理鋼板として使用される。
【０００７】
【発明が解決しようとする課題】
溶融Ａｌ−Ｚｎ系めっき鋼板は、折り曲げ等の加工を施すと加工の程度によって被加工部のめっき皮膜にクラックが生じる。このめっき鋼板では、めっき皮膜／下地鋼板界面に存在する約１〜２μｍ厚の合金相がクラックの起点となり、まためっき皮膜のデンドライト間隙部がクラックの伝播経路になることから、同程度の加工を行った場合でも、同一めっき皮膜厚の溶融亜鉛めっき鋼板に比べてクラックが比較的大きく開口する傾向がある。そのため加工の程度によってはクラックが肉眼で視認され、外観を損ねるという問題がある。さらに、上述のように溶融Ａｌ−Ｚｎ系めっき鋼板は、同一めっき皮膜厚の溶融亜鉛めっき鋼板に比べて優れた耐食性を発揮するが、下地鋼板の露出したクラック部はクラックのない部分と比較して耐食性が顕著に低下するという問題もある。
【０００８】
このような問題に対して、例えば特公昭６１−２８７４８号公報には、溶融Ａｌ−Ｚｎ系めっき鋼板に所定の熱処理を施すことによって、めっき鋼板の延性を改善する方法が示されている。
しかしながら、上述したように溶融Ａｌ−Ｚｎ系めっき鋼板は表面に化成処理を施した化成処理鋼板や塗装を施した塗装鋼板として使用されるのが通常である。そして、単に折り曲げ等の加工による加工部でのクラック発生抑止の観点から、上記従来技術のようにめっき皮膜の延性をある程度改善したとしても、必ずしも実用に供される製品としての性能、すなわち化成処理や塗装を行った表面処理鋼板としての加工性や加工部の耐食性が直ちに改善されるものではない。
【０００９】
したがって本発明の目的は、めっき皮膜中のＡｌ含有量が２０〜９５mass％の溶融Ａｌ−Ｚｎ系めっき鋼板を下地鋼板とし、従来にない優れた加工性及び加工部耐食性が得られる表面処理鋼板及びその製造方法を提供することにある。
【００１０】
【課題を解決するための手段】
上記課題の解決のために本発明者らは、実用製品すなわち溶融Ａｌ−Ｚｎ系めっき鋼板に化成処理を施した表面処理鋼板としての性能に視点を定め、加工性や加工部耐食性を向上させるために最適なめっき皮膜と化成処理皮膜の構成について鋭意検討を行った。その結果、溶融Ａｌ−Ｚｎ系めっき鋼板のめっき皮膜を特定の熱履歴を経たものとし、且つこのめっき皮膜面に特定の化成処理皮膜を形成することにより、従来では達成できなかった極めて優れた加工性と加工部耐食性が得られることを見い出した。
【００１１】
本発明はこのような知見に基づいてなされたもので、その特徴は以下のとおりである。
[1] めっき皮膜中のＡｌ含有量が２０〜９５mass％の溶融Ａｌ−Ｚｎ系めっき鋼板の表面に化成処理皮膜を有する表面処理鋼板であって、
前記めっき皮膜が少なくとも下記(a)の熱履歴を経て得られためっき皮膜であり、前記化成処理皮膜がクロメート処理によるＣｒを金属クロム換算で０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満含むことを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
(a) 溶融めっきされためっき金属が凝固した後、１３０〜３００℃の範囲の温度Ｔ（℃）に昇温加熱され、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴、
又は／及び、溶融めっきされためっき金属が凝固した後の１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴
Ｃ＝（Ｔ−１００）／２ …… (1)
【００１２】
[2] 上記[1]の表面処理鋼板において、(a)の熱履歴の温度Ｔ（℃）が１３０〜２００℃の範囲であることを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
[3] 上記[1]又は[2]の表面処理鋼板において、めっき皮膜がＭｇ、Ｖ、Ｍｎの中から選ばれる１種又は２種以上を合計で０．０１〜１０mass%含有することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
[4] 上記[1]〜[3]のいずれかの表面処理鋼板について、化成処理皮膜が、めっき皮膜面に水性有機樹脂とクロム酸及び／又はクロム酸の一部を還元したクロム酸化合物を含むクロメート処理液を塗布した後、板温８０〜３００℃の温度で乾燥して得られた皮膜であり、且つ該皮膜中に含まれる有機樹脂量（Ａ）と金属クロム換算でのＣｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１以上２００未満であることを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
【００１３】
[5] 上記[1]〜[3]のいずれかの表面処理鋼板において、化成処理皮膜が、めっき皮膜面に形成されるクロメート処理皮膜と、その上層に形成される皮膜であって、水性有機樹脂を含む処理液を塗布して板温８０〜３００℃の温度で乾燥して得られた皮膜とからなることを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
[6] 上記[5]の表面処理鋼板において、化成処理皮膜中に含まれる全有機樹脂量（Ａ）と金属クロム換算での全Ｃｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１以上２００未満であることを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
[7] 上記[1]〜[6]のいずれかに記載の表面処理鋼板の表面に単層又は複層の塗膜を形成したことを特徴とする塗装鋼板。
【００１４】
[8] めっき皮膜中のＡｌ含有量が２０〜９５mass％の溶融Ａｌ−Ｚｎ系めっき鋼板の表面に化成処理皮膜を有する表面処理鋼板の製造方法であって、
溶融めっき浴を出た鋼板のめっき皮膜に対して、少なくとも下記(a)の熱履歴を付与する工程と、
(a) 溶融めっきされためっき金属が凝固した後、１３０〜３００℃の範囲の温度Ｔ（℃）に昇温加熱され、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴、
又は／及び、溶融めっきされためっき金属が凝固した後の１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴
Ｃ＝（Ｔ−１００）／２ …… (1)
めっき鋼板の表面にクロメート処理によるＣｒを金属クロム換算で０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満含む化成処理皮膜を形成させる工程とを有することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
【００１５】
[9] 上記[8]の製造方法において、(a)の熱履歴の温度Ｔ（℃）が１３０〜２００℃の範囲であることを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
[10] 上記[8]又は[9]の製造方法において、めっき皮膜がＭｇ、Ｖ、Ｍｎの中から選ばれる１種又は２種以上を合計で０．０１〜１０mass含有することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
[11] 上記[8]〜[10]のいずれかの製造方法において、めっき皮膜に対する(a)の熱履歴の付与を、下記(1)〜(3)のうちの少なくとも１つの段階で行うことを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
(1) 化成処理皮膜の形成前
(2) 化成処理皮膜の形成後
(3) 溶融めっきされためっき金属が凝固した後の冷却過程
【００１６】
[12] 上記[8]〜[11]のいずれかの製造方法において、化成処理皮膜を形成する工程において、めっき皮膜面に水性有機樹脂とクロム酸及び／又はクロム酸の一部を還元したクロム酸化合物を含むクロメート処理液を塗布した後、板温８０〜３００℃の温度で乾燥することにより、皮膜中の有機樹脂量（Ａ）と金属クロム換算でのＣｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１以上２００未満である化成処理皮膜を形成することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
【００１７】
[13] 上記[8]〜[11]のいずれかの製造方法において、めっき皮膜面に、クロメート処理を施し、次いで水性有機樹脂を含む処理液を塗布して板温８０〜３００℃の温度で乾燥することにより化成処理皮膜を形成することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
[14] 上記[13]の製造方法において、めっき皮膜面に、皮膜中に含まれる全有機樹脂量（Ａ）と金属クロム換算での全Ｃｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１以上２００未満である化成処理皮膜を形成することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。
[15] 上記[8]〜[14]のいずれかに記載の製造方法の工程に加えて、さらに、化成処理皮膜面に１コート又は２コート以上の塗装を施す工程を有することを特徴とする塗装鋼板の製造方法。
【００１８】
【発明の実施の形態】
本発明の表面処理鋼板は、めっき皮膜中にＡｌを２０〜９５mass％含有する溶融Ａｌ−Ｚｎ系めっき鋼板を下地鋼板とする。また耐食性等の観点から、めっき皮膜中のＡｌ量より好ましい範囲は４５〜６５mass％である。また、めっき皮膜の特に好ましい成分組成は、Ａｌ：４５〜６５mass％、Ｓｉ：０．７〜２．０mass％、Ｆｅ：１０mass％未満、残部が不可避的不純物を含む実質的なＺｎであり、このような組成の場合に特に優れた耐食性を発揮する。
【００１９】
さらに、めっき皮膜中にＭｇ、Ｖ、Ｍｎの中から選ばれる１種または２種以上を合計で０．０１〜１０mass％含有させることによって、耐食性や加工性をより向上させることができる。これら元素の含有量の合計が０．０１mass％未満では十分な効果が得られず、一方、１０mass％を超えると耐食性向上効果が飽和するとともに、皮膜が硬くなるので加工性が低下する。
【００２０】
但し、この溶融Ａｌ−Ｚｎ系めっき鋼板は、そのめっき組成だけで高い加工部耐食性を得ることは難しく、後述する熱履歴を経ること及び上層の化成処理皮膜と組み合せることによってはじめて優れた加工部耐食性が得られる。
また、この溶融Ａｌ−Ｚｎ系めっき鋼板のめっき付着量に特に制限はないが、一般には片面当たり３０〜２００ｇ／ｍ２程度とすることが適当である。
【００２１】
さらに、この溶融Ａｌ−Ｚｎ系めっき鋼板のめっき皮膜は、少なくとも下記(a)の熱履歴を経て得られためっき皮膜であることが必要である。
(a) 溶融めっきされためっき金属が凝固した後、１３０〜３００℃の範囲の温度Ｔ（℃）に昇温加熱され、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴、
又は／及び、溶融めっきされためっき金属が凝固した後の１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴
Ｃ＝（Ｔ−１００）／２ …… (1)
また、上記(a)の熱履歴において、温度Ｔ（℃）のより好ましい範囲は１３０〜２００℃である。
ここで、上記(1)式は本発明者らがめっき皮膜の昇温加熱及びその後の冷却条件や溶融めっきされためっき金属凝固後の冷却条件がめっき皮膜に与える影響を実験に基づき詳細に検討し、その結果導かれた実験式である。
【００２２】
めっき皮膜を上記(a)の熱履歴を経たものとすることにより、溶融Ａｌ−Ｚｎ系めっき皮膜でありながら、その加工性（耐クラック性など）が大きく向上する。このように加工性が改善されるのは、めっき皮膜が１３０〜３００℃（好ましくは１３０〜２００℃）の温度範囲に昇温加熱された後に特定の条件で徐冷される熱履歴、又は／及びめっき皮膜凝固後の１３０〜３００℃（好ましくは１３０〜２００℃）の温度範囲から特定の条件で徐冷される熱履歴を経ることにより、凝固時点でめっき皮膜に蓄積された歪が開放されるとともに、めっき皮膜中で固体拡散が生じ、めっき皮膜中のＡｌとＺｎの二相分離が効果的に促進される結果、めっき皮膜が軟質化するためであると考えられる。
【００２３】
上記(a)の熱履歴では、めっき皮膜（溶融めっきされためっき金属が凝固した後のめっき皮膜）を１３０〜３００℃、好ましくは１３０〜２００℃の範囲の温度Ｔ（℃）に昇温加熱し、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が上記(1)式に示すＣ（℃／ｈｒ）以下を満足するように冷却するか、或いは溶融めっきされためっき金属が凝固した後のめっき皮膜をその冷却過程である１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が上記(1)式に示すＣ（℃／ｈｒ）以下を満足するように冷却する。
【００２４】
この(a)の熱履歴において、めっき皮膜の昇温加熱温度Ｔが１３０℃未満では上記のような作用が十分に得られず、一方、昇温加熱温度Ｔが３００℃超では下地鋼板とめっき皮膜との界面での合金相の成長を促進させるため、却って加工性に悪影響を及ぼす。またこのような観点から、加工性の改善にとってより好ましい昇温加熱温度Ｔの上限は２００℃である。
また、溶融めっきされためっき金属が凝固した後の冷却過程である１３０〜３００℃の範囲の温度Ｔ（℃）から上記(a)の熱履歴が付与される条件で冷却を行う場合についても、温度Ｔが１３０℃未満では上記のような作用が十分に得られない。
【００２５】
図１(a)は、溶融めっきされためっき金属が凝固した後のめっき鋼板を熱処理した際の、めっき皮膜の昇温加熱温度が表面処理鋼板の加工性に及ぼす影響を調べたもので、この結果が得られた供試材は、いずれも昇温加熱温度から１００℃までのめっき皮膜の平均冷却速度が上記(a)の熱履歴の条件内であるめっき鋼板に、本発明条件を満足する化成処理皮膜を形成した表面処理鋼板である。なお、この試験における加工性の評価は、後述する実施例の加工性の評価に準じて行った。
【００２６】
また図１(b)は、溶融めっきされためっき金属が凝固した後のめっき鋼板を熱処理した際の、めっき皮膜の平均冷却速度（昇温加熱温度から１００℃までの平均冷却速度）が表面処理鋼板の加工性に及ぼす影響を調べたもので、この結果が得られた供試材は、いずれもめっき皮膜の昇温加熱温度が上記(a)の熱履歴の条件内であるめっき鋼板に、本発明条件を満足する化成処理皮膜を形成した表面処理鋼板である。なお、この試験における加工性の評価は、後述する実施例の加工性の評価に準じて行った。
【００２７】
図１(a)，(b)に示されるように、めっき皮膜の昇温加熱温度が１３０〜３００℃の範囲では２Ｔ曲げの加工性の評点が４点以上であり、また好ましい条件である１３０〜２００℃の範囲では加工性の評点は４点〜５点となっている。これに対して昇温加熱温度が１３０〜３００℃の範囲外では加工性の評点は３点しか得られていない。また、昇温加熱温度から１００℃までの平均冷却速度と上記(1)式の“Ｃ”との差が零〜マイナス（本発明範囲内）の場合には２Ｔ曲げの加工性の評点は４〜５点であるのに対し、その差がプラス（本発明範囲外）の場合には加工性の評点は３点しか得られていない。
【００２８】
めっき皮膜を上記(a)の熱履歴を経たものとするには、連続式溶融めっき設備内に或いは同設備外にめっき皮膜を熱処理又は保熱するための加熱又は保熱装置を設け、所定の熱処理又は保熱を行う。例えば、連続式溶融めっき設備内に加熱機構（例えば、インダクションヒーター、ガス加熱炉、熱風炉など）を設けてインラインで連続加熱して行ってもよいし、また、コイルに巻取った後にオフラインでバッチ加熱して行ってもよい。また、めっきライン外の連続処理設備において加熱機構（例えば、インダクションヒーター、ガス加熱炉、熱風炉など）により連続加熱して行ってもよい。さらには、めっきライン内や上記連続処理設備で連続加熱されためっき鋼板をコイルに巻き取った後に適当な保熱又は加熱保持を行ってもよい。また、溶融めっきされためっき金属が凝固した後の冷却過程においてめっき皮膜を保熱して徐冷できるような保熱装置を設けてもよい。
但し、加熱又は保熱装置の方式、形状、規模等については特別な制限はなく、要はめっき皮膜に上記(a)の熱履歴を与え得るものであればよい。
【００２９】
以上のような(a)の熱履歴を経ためっき皮膜の表面に特定の化成処理皮膜を形成することにより、この表面処理鋼板は優れた加工性と加工部耐食性を示す。
【００３０】
めっき皮膜面に形成される化成処理皮膜は、クロメート処理によるＣｒを金属クロム換算で０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満含むものとする。上記のようなクラックを生じにくい特定のめっき皮膜の表面に、このような化成処理皮膜を形成することにより加工部耐食性が著しく向上する。なお、この化成処理皮膜は複層皮膜により構成されていてもよく、この場合には皮膜全体として上記Ｃｒを含んでいればよい。したがって、上記Ｃｒは複層皮膜のうちの１層のみに含まれるものであってもよいし、２層以上の皮膜に含まれるものであってもよい。
化成処理皮膜中の金属クロム換算のＣｒ量が０．１ｍｇ／ｍ２未満では加工部耐食性が十分に向上せず、一方、Ｃｒ量が１００ｍｇ／ｍ２以上では加工部耐食性の向上効果が飽和する一方で、Ｃｒ量増加によるＣｒ固定率低下により環境調和性を損う。
【００３１】
また、より好ましい化成処理皮膜としては、水性有機樹脂とクロム酸及び／又はクロム酸の一部を還元したクロム酸化合物を含むクロメート処理液を塗布した後、板温８０〜３００℃の温度で乾燥して得られた皮膜であって、且つ皮膜中に含まれる有機樹脂量（Ａ）と金属クロム換算でのＣｒ量（Ｂ）の重量比（Ａ）／（Ｂ）が１以上２００未満である化成処理皮膜である。
このように化成処理皮膜がＣｒとともに有機樹脂を含むことにより、加工部耐食性がさらに良好になる。
【００３２】
また、このような化成処理皮膜において、有機樹脂量（Ａ）と金属クロム換算でのＣｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１未満では、有機樹脂が加工部耐食性を向上させる効果が十分に発揮されない。一方、質量比（Ａ）／（Ｂ）が２００以上では、Ｃｒによる加工部耐食性の向上効果が十分に得られない。
また、化成処理皮膜を形成する際にクロメート処理液を塗布した後の乾燥温度が板温で８０℃未満では、温度が低いため適正な化成処理皮膜が形成されず、一方３００℃を超えるとめっき皮膜にさらなる熱が加わるために合金化反応が促進され、却って加工性が低下するおそれがある。
【００３３】
さらに、化成処理皮膜は、クロメート処理皮膜とその上層に形成される特定の皮膜からなることが好ましい。この上層皮膜は、水性有機樹脂を含む処理液を塗布して板温８０〜３００℃の温度で乾燥して得られた皮膜であり、化成処理皮膜をクロメート処理皮膜とその上層の上記皮膜から構成することにより、より優れた加工部耐食性が得られる。
上層皮膜を形成する際に処理液を塗布した後の乾燥温度が板温で８０℃未満では、温度が低いため適正な化成処理皮膜が形成されず、一方、３００℃を超えるとめっき皮膜にさらなる熱が加わるために合金化反応が促進され、却って加工性が低下するおそれがある。
【００３４】
この化成処理皮膜（クロメート処理皮膜＋上層皮膜）中に含まれる金属クロム換算での全Ｃｒ量は０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満であり、その限定理由は上述した通りである。上層皮膜中にＣｒを含有させるか否かは任意であるが、Ｃｒを含む場合には耐食性がより向上する。上層皮膜の膜厚は０．１〜５μｍ程度が好ましく、膜厚が０．１μｍ未満では加工部耐食性の改善効果が十分でなく、一方、５μｍを超えると表面処理鋼板のロールフォーミング時にロールにピックアップを生じるおそれがある。
【００３５】
さらに、この化成処理皮膜は、皮膜中に含まれる全有機樹脂量（Ａ）と金属クロム換算での全Ｃｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１以上２００未満であることが好ましい。全有機樹脂量（Ａ）と金属クロム換算での全Ｃｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１未満では、有機樹脂が加工部耐食性を向上させる効果が小さく、一方、質量比（Ａ）／（Ｂ）が２００以上ではＣｒによる加工部耐食性の向上効果が小さい。
【００３６】
次に、本発明による上記表面処理鋼板の製造方法について説明する。
本発明の製造方法は、連続式溶融めっき設備などで製造されるめっき皮膜中のＡｌ含有量が２０〜９５mass％の溶融Ａｌ−Ｚｎ系めっき鋼板を下地鋼板とし、その表面に化成処理皮膜を形成した表面処理鋼板の製造方法であり、溶融めっき浴を出た鋼板のめっき皮膜に対して、少なくとも下記(a)の熱履歴を付与する工程と、めっき鋼板の表面に特定の化成処理皮膜を形成させる工程とを有する。
(a) 溶融めっきされためっき金属が凝固した後、１３０〜３００℃の範囲の温度Ｔ（℃）に昇温加熱され、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴、
又は／及び、溶融めっきされためっき金属が凝固した後の１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴
Ｃ＝（Ｔ−１００）／２ …… (1)
【００３７】
上記(a)の熱履歴の付与は、溶融めっきされためっき金属が凝固した後のめっき鋼板に対して特定の熱処理を施すか、或いは溶融めっきされためっき金属が凝固した後のめっき皮膜の冷却を保熱などによって制御することによりなされる。本発明の製造方法ではめっき鋼板のめっき皮膜面に特定の化成処理皮膜を形成させるが、めっき皮膜に上記(a)の熱履歴を付与するための熱処理は、( ｉ )化成処理皮膜の形成前、 (ii) 化成処理皮膜の形成後（処理液の塗布及びその乾燥工程による皮膜の形成後）、のいずれの段階で行ってもよい。また、これら２つの段階で行ってもよい。
【００３８】
したがって、めっき皮膜に対する(a)の熱履歴の付与は、下記(1)〜(3)のうちの少なくとも１つの段階で行うことができる。
(1) 化成処理皮膜の形成前
(2) 化成処理皮膜の形成後
(3) 溶融めっきされためっき金属が凝固した後の冷却過程
なお、熱処理を行う上記方式うち、(1)の方式は熱処理工程と化成処理工程の各条件をそれぞれ独立に最適化できるという利点があり、また、(2) の方式は連続式溶融めっき設備内で全ての処理を行うのに適している。
【００３９】
上記(a)の熱履歴を付与するための熱処理又は保熱は、連続式溶融めっき設備内に或いは同設備外に設けられた加熱又は保熱装置などにより行う。連続式溶融めっき設備内に加熱機構（例えば、インダクションヒーター、熱風炉など）を設けてインラインで連続加熱して行ってもよいし、また、コイルに巻取った後にオフラインでバッチ加熱して行ってもよい。また、めっきライン外の連続処理設備において加熱機構（例えば、インダクションヒーター、熱風炉など）により連続加熱して行ってもよい。さらには、めっきライン内や上記連続処理設備で連続加熱されためっき鋼板をコイルに巻き取った後に適当な保熱又は加熱保持を行ってもよい。また、溶融めっきされためっき金属が凝固した後の冷却過程においてめっき皮膜を保熱して徐冷できるような保熱装置を設けてもよい。但し、加熱又は保熱装置の方式、形状、規模等については特別な制限はなく、要はめっき皮膜に上記(a)の熱履歴を与え得るものであればよい。
なお、製造される溶融Ａｌ−Ｚｎ系めっき鋼板の好ましいめっき組成、めっき付着量、上記(a)の熱履歴の限定理由及び得られる作用効果などは先に述べた通りである。
【００４０】
本発明の製造方法では、めっき鋼板のめっき皮膜面に、少なくともクロメート処理を含む１又は２以上の処理を行い、Ｃｒを金属クロム換算で０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満含む化成処理皮膜を形成させる。この化成処理皮膜を形成する工程と上記(a)の熱履歴を付与する工程との前後関係は上述した通りである。
上記クロメート処理では、クロメート処理液をめっき鋼板面に塗布し、通常、水洗することなく８０〜３００℃で乾燥処理する。
先に述べたように、この化成処理皮膜は複層皮膜により構成されていてもよく、この場合には複数の処理が順次行われる。また複層皮膜の場合には皮膜全体として上記Ｃｒを含んでいればよく、したがって、このＣｒは複層皮膜のうちの１層のみに含まれるものであってもよいし、２層以上の皮膜に含まれるものであってもよい。
【００４１】
また、化成処理皮膜の好ましい組成及び処理条件は先に述べた通りである。すなわち、特に好ましい化成処理皮膜は、水性有機樹脂とクロム酸及び／又はクロム酸の一部を還元したクロム酸化合物を含むクロメート処理液を塗布した後、板温８０〜３００℃の温度で乾燥して得られた皮膜であって、且つ皮膜中に含まれる有機樹脂量（Ａ）と金属クロム換算でのＣｒ量（Ｂ）の重量比（Ａ）／（Ｂ）が１以上２００未満である化成処理皮膜である。この場合の限定理由及び作用効果は、先に述べた通りである。
【００４２】
また、上述したようなクロメート処理後、その上層に特定の上層皮膜を形成してもよく、この場合には化成処理皮膜はクロメート処理と上層皮膜との複合皮膜となる。この化成処理皮膜（クロメート処理皮膜＋上層皮膜）中に含まれる金属クロム換算での全Ｃｒ量は０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満である。上層皮膜中にＣｒを含有させるか否かは任意であるが、Ｃｒを含む場合には耐食性がより向上する。上層皮膜の膜厚は０．１〜５μｍ程度が好ましい。また、この化成処理皮膜は、皮膜中に含まれる全有機樹脂量（Ａ）と金属クロム換算での全Ｃｒ量（Ｂ）の質量比（Ａ）／（Ｂ）が１以上２００未満であることが好ましい。上層皮膜は、例えば水性有機樹脂を含む処理液を塗布して板温８０〜３００℃の温度で乾燥して形成させる。なお、以上の各構成の限定理由及び作用効果は、先に述べた通りである。
【００４３】
以上述べた本発明の表面処理鋼板の表面には単層又は複層の塗膜を形成し、塗装鋼板とすることができる。この塗膜としては、例えば、ポリエステル樹脂系塗膜、エポキシ樹脂系塗膜、アクリル樹脂系塗膜、ウレタン樹脂系塗膜、フッ素樹脂系塗膜等が挙げられる。また、上記樹脂の一部を他の樹脂で変性した、例えばエポキシ樹脂変性ポリエステル樹脂系塗膜等も適用できる。さらに上記樹脂には必要に応じて硬化剤、硬化触媒、顔料、添加剤等を添加することができる。
表面処理鋼板の表面に塗膜を形成するための塗装方法は特に規定しないが、塗装方法としてはロールコーター塗装、カーテンフロー塗装、スプレー塗装等が挙げられる。塗料を塗装後、一般に熱風乾燥、赤外線加熱、誘導過熱等の手段により加熱乾燥して塗膜を形成させる。
【００４４】
【実施例】
［実施例１］
常法で製造した冷延鋼板（板厚０．５ｍｍ）を連続式溶融めっき設備に通板し、５５％Ａｌ−１．５％Ｓｉ−Ｚｎめっき浴（表１のＮｏ．１〜Ｎｏ．１０）、４０％Ａｌ−１．０％Ｓｉ−Ｚｎめっき浴（表１のＮｏ．１１）及び７０％Ａｌ−１．８％Ｓｉ−Ｚｎめっき浴（表１のＮｏ．１２）を用いて溶融めっきを行った。ラインスピードは１６０ｍ／分とし、片面めっき付着量は鋼板間のバラツキが７５〜９０ｇ／ｍ２の範囲に収まるようにした。
【００４５】
このめっき鋼板の製造工程においてめっき皮膜に表１に示す熱履歴を付与するとともに、めっき皮膜面に化成処理を施した。化成処理条件は、アクリルエマルジョン樹脂とクロム酸を樹脂固形分量：Ｃｒ量＝１００：１（質量比）の割合となるように混合した処理液を、金属クロム換算でのＣｒ付着量が２０ｍｇ／ｍ２となるようにめっき鋼板面に塗布し、１２０℃で乾燥した。
このようにして製造した表面処理鋼板について、以下の方法により加工性と加工部耐食性を評価した。その結果を表１に示す。
【００４６】
(1) 加工性
表面処理鋼板を２Ｔ曲げしてこの２Ｔ曲げ先端部のクラックを観察し、以下の基準で評価した。
５：２０倍のルーペで観察してもクラックは認められない。
４：目視で観察するとクラックは認められないが、２０倍のルーペで観察するとクラックが認められる。
３：目視で観察してクラックが認められる。
２：目視で観察して大きく開口したクラックが認められる。
１：剥離を伴うクラックが生じている。
【００４７】
(2) 加工部耐食性
表面処理鋼板を３Ｔ曲げした後、５０℃、９８％ＲＨ以上の湿潤試験機に装入して１０００時間経過後の曲げ部からの錆発生状態を観察し、以下の基準で評価した。
５：異常無し
４：一部に軽度の白錆、黒錆の発生有り
３：全面に軽度の白錆、黒錆の発生有り
２：全面に著しい白錆、黒錆の発生有り
１：赤錆発生あり
【００４８】
【表１】
［実施例２］
常法で製造した冷延鋼板（板厚０．５ｍｍ）を連続式溶融めっき設備に通板し、５５％Ａｌ−１．５％Ｓｉ−Ｚｎめっき浴を用いて溶融めっきを行った。ラインスピードは１６０ｍ／分とし、片面めっき付着量は鋼板間のバラツキが７５〜９０ｇ／ｍ２の範囲に収まるようにした。
【００５０】
このめっき鋼板の製造工程においてめっき皮膜に表２に示す熱履歴を付与するとともに、めっき皮膜面に化成処理を施した。化成処理条件は、金属クロム換算でのＣｒ付着量が２０ｍｇ／ｍ２となるようにめっき鋼板面にクロメート処理を施して８０℃で乾燥し、その上層にウレタンエマルジョン樹脂を含む処理液を塗布し、１２０℃で乾燥した。
このようにして製造した表面処理鋼板について、実施例１と同じ方法により加工性と加工部耐食性を評価した。その結果を表２に示す。
【００５１】
【表２】
［実施例３］
常法で製造した冷延鋼板（板厚０．５ｍｍ）を連続式溶融めっき設備に通板し、５５％Ａｌ−１．５％Ｓｉ−Ｚｎめっき浴に対してＭｇ、Ｖ、Ｍｎのうちの１種又は２種以上を添加しためっき浴を用い、めっき皮膜中のＭｇ、Ｖ、Ｍｎの１種又は２種以上の含有量が合計で０．０１〜１０mass％となるように溶融めっきを行った。ラインスピードは１６０ｍ／分とし、片面めっき付着量は鋼板間のバラツキが７５〜９０ｇ／ｍ２の範囲に収まるようにした。
【００５３】
このめっき鋼板の製造工程においてめっき皮膜に表３に示す熱履歴を付与するとともに、めっき皮膜面に実施例１と同じ条件で化成処理を施した。
このようにして製造した表面処理鋼板について、実施例１と同じ方法により加工性と加工部耐食性を評価した。その結果を表３に示す。
【００５４】
【表３】
【発明の効果】
以上述べたように本発明の表面処理鋼板は、めっき皮膜中のＡｌ含有量が２０〜９５mass％の溶融Ａｌ−Ｚｎ系めっき鋼板を下地鋼板とする表面処理鋼板でありながら極めて優れた加工性と加工部耐食性を有する。また、本発明の製造方法によれば、このような表面処理鋼板を安定して且つ高い生産性で製造することができる。
【図面の簡単な説明】
【図１】図１(a)は、溶融めっきされためっき金属が凝固した後のめっき鋼板を熱処理した場合において、めっき皮膜の昇温加熱温度が表面処理鋼板の加工性に及ぼす影響を示すグラフ、図１(b)は、溶融めっきされためっき金属が凝固した後のめっき鋼板を熱処理した場合において、めっき皮膜の平均冷却速度（昇温加熱温度から１００℃までの平均冷却速度）が表面処理鋼板の加工性に及ぼす影響を示すグラフ[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a surface-treated steel sheet using a molten Al-Zn-based plated steel sheet having an Al content of 20 to 95 mass% as a base steel sheet and a method for producing the same.
[0002]
[Prior art]
In recent years, a molten Al-Zn-based plated steel sheet containing 20 to 95 mass% of Al in the plating film exhibits excellent corrosion resistance as compared with a hot-dip galvanized steel sheet as shown in Japanese Patent Publication No. 46-7161. Demand is growing mainly in the field.
This plated steel sheet is manufactured as follows in a continuous hot dipping apparatus using a hot-rolled steel sheet pickled and descaled or a cold-rolled steel sheet obtained by further cold rolling the base steel sheet.
[0003]
In the continuous hot dip plating facility, the base steel sheet was heated to a predetermined temperature in an annealing furnace maintained in a reducing atmosphere, and simultaneously with the annealing, the rolling oil adhered to the steel sheet surface was removed, and the oxide film was reduced and removed. Thereafter, the lower end passes through a snout immersed in the plating bath and is immersed in a hot dip galvanizing bath containing a predetermined concentration of Al. After the steel plate immersed in the plating bath is pulled up above the plating bath via the sink roll, a pressurized gas is sprayed from the gas wiping nozzle arranged on the plating bath toward the surface of the steel plate. The plating adhesion amount is adjusted and then cooled by a cooling device to obtain a molten Al—Zn-based plated steel sheet on which a predetermined plating film is formed.
[0004]
Operating conditions such as annealing furnace heat treatment and atmosphere conditions, plating bath composition and cooling rate after plating in continuous hot dip plating equipment are accurately controlled within a prescribed control range to ensure the desired plating quality and material. The
The plating film of the plated steel sheet produced as described above is mainly composed of a part where Al containing Zn is supersaturated and dendrite solidified and a part of the remaining dendrite gap, and the dendrite is in the film thickness direction of the plating film. Laminated. Due to such a characteristic film structure, the molten Al—Zn-based plated steel sheet exhibits excellent corrosion resistance.
[0005]
In addition, Si of about 1.5 mass% is usually added to the plating bath, but due to the action of this Si, the molten Al-Zn-based plated steel sheet suppresses the alloy phase growth at the plating film / underlying steel sheet interface, and the alloy The phase thickness is about 1-2 μm. The thinner the alloy phase is, the more portions of the characteristic film structure exhibiting excellent corrosion resistance. Therefore, the suppression of the growth of the alloy phase contributes to the improvement of the corrosion resistance. In addition, since the alloy phase is harder than the plating film and acts as a starting point of cracks during processing, suppressing the growth of the alloy phase reduces the occurrence of cracks and brings about an effect of improving workability. Moreover, since the base steel plate is exposed in the crack portion and the corrosion resistance is poor, reducing the occurrence of cracks also improves the corrosion resistance of the processed portion.
[0006]
Usually, the plating bath contains unavoidable impurities, Fe eluted from the steel plate and equipment in the plating bath, Si for alloy phase suppression, but some elements may be added in addition to them, In the alloy phase and the plating film, these elements exist in the form of an alloy or a simple substance.
In addition, hot-dip Al-Zn-based plated steel sheets are rarely used as hot-plated as they are put to practical use, and are usually used as surface-treated steel sheets that have been subjected to chemical conversion treatment or coating on the surface of the plated steel sheet. The
[0007]
[Problems to be solved by the invention]
When the molten Al—Zn-based plated steel sheet is subjected to processing such as bending, cracks occur in the plating film of the processed part depending on the degree of processing. In this plated steel sheet, the alloy phase of about 1 to 2 μm thickness present at the plating film / underlying steel plate interface is the starting point of cracks, and the dendrite gap of the plating film is the propagation path of cracks, so the same level of processing is possible. Even when it is performed, cracks tend to open relatively large compared to hot dip galvanized steel sheets having the same plating film thickness. Therefore, depending on the degree of processing, there is a problem that the crack is visually recognized with the naked eye and the appearance is impaired. Furthermore, as described above, the hot-dip Al-Zn-based plated steel sheet exhibits excellent corrosion resistance as compared with the hot-dip galvanized steel sheet having the same plating film thickness, but the exposed cracked part of the base steel sheet is compared with the part without cracks. Therefore, there is a problem that the corrosion resistance is remarkably lowered.
[0008]
For example, Japanese Patent Publication No. 61-28748 discloses a method for improving the ductility of a plated steel sheet by applying a predetermined heat treatment to the molten Al-Zn-based plated steel sheet.
However, as described above, the molten Al—Zn-based plated steel sheet is usually used as a chemical conversion-treated steel sheet having a surface subjected to chemical conversion treatment or a coated steel sheet having been coated. And, from the viewpoint of suppressing crack occurrence at the processed part by processing such as bending, even if the ductility of the plating film is improved to some extent as in the above prior art, performance as a product that is practically used, that is, chemical conversion treatment In addition, the workability as a surface-treated steel sheet with coating or the corrosion resistance of the processed part is not immediately improved.
[0009]
Accordingly, an object of the present invention is to use a surface-treated steel sheet that is obtained by using a molten Al-Zn-based plated steel sheet having an Al content in a plating film of 20 to 95 mass% as a base steel sheet, and excellent workability and processed part corrosion resistance that are not conventionally obtained It is in providing the manufacturing method.
[0010]
[Means for Solving the Problems]
In order to solve the above-mentioned problems, the present inventors set a viewpoint on the performance as a surface-treated steel sheet obtained by subjecting a practical product, that is, a molten Al—Zn-based plated steel sheet, to chemical conversion treatment, and to improve workability and corrosion resistance of a processed part. The structure of the optimal plating film and chemical conversion film was investigated. As a result, the coating film of the molten Al—Zn-based plated steel sheet has undergone a specific thermal history, and by forming a specific chemical conversion treatment film on the surface of the plating film, extremely excellent processing that could not be achieved conventionally. And the corrosion resistance of the processed part was found.
[0011]
The present invention has been made based on such findings, and the features thereof are as follows.
[1] A surface-treated steel sheet having a chemical conversion film on the surface of a molten Al-Zn-based plated steel sheet having an Al content of 20 to 95 mass% in the plated film,
The plating film is a plating film obtained through the heat history of at least the following (a), the chemical conversion coating may contain less than 0.1 mg / m 2 or more 100 mg / m 2 reckoned as metal chromium to Cr by chromate treatment A surface-treated steel sheet with excellent workability and corrosion resistance on the machined part.
(a) After the hot-plated plated metal is solidified, it is heated to a temperature T (° C.) in the range of 130 to 300 ° C., and then the average cooling rate from the temperature T (° C.) to 100 ° C. is as follows ( 1) Thermal history satisfying C (° C./hr) or less shown in the formula,
Or / and the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C. after the hot-plated plated metal solidifies is below C (° C./hr) shown in the following formula (1) History C that satisfies the following conditions: C = (T-100) / 2 (1)
[0012]
[2] In the surface-treated steel sheet of [1], the surface treatment with excellent workability and processed portion corrosion resistance, wherein the thermal history temperature T (° C.) of (a) is in the range of 130 to 200 ° C. steel sheet.
[3] In the surface-treated steel sheet according to [1] or [2], the plating film contains 0.01 to 10 mass% in total of one or more selected from Mg, V, and Mn. A surface-treated steel sheet with excellent workability and corrosion resistance of the processed part.
[4] The surface-treated steel sheet according to any one of [1] to [3] above, wherein the chemical conversion treatment film comprises a chromic acid compound obtained by reducing an aqueous organic resin and chromic acid and / or a part of chromic acid on the plating film surface. It is the film | membrane obtained by apply | coating the chromate process liquid containing, and drying at the temperature of 80-300 degreeC of plate | board temperature, and the amount of organic resin (A) contained in this film | membrane, and the Cr amount in conversion of metal chromium ( A surface-treated steel sheet excellent in workability and processed part corrosion resistance, wherein the mass ratio (A) / (B) of B) is from 1 to less than 200.
[0013]
[5] In the surface-treated steel sheet according to any one of the above [1] to [3], the chemical conversion treatment film is a chromate treatment film formed on the plating film surface and a film formed on the upper surface thereof, which is an aqueous organic A surface-treated steel sheet excellent in workability and processed part corrosion resistance, comprising a coating obtained by applying a treatment liquid containing a resin and drying at a plate temperature of 80 to 300 ° C.
[6] In the surface-treated steel sheet of [5], the mass ratio (A) / (B) of the total organic resin amount (A) contained in the chemical conversion coating and the total Cr amount (B) in terms of chromium metal is A surface-treated steel sheet excellent in workability and processed portion corrosion resistance, characterized by being 1 or more and less than 200.
[7] A coated steel sheet, wherein a single-layer or multi-layer coating film is formed on the surface of the surface-treated steel sheet according to any one of [1] to [6].
[0014]
[8] A method for producing a surface-treated steel sheet having a chemical conversion film on the surface of a molten Al-Zn-based plated steel sheet having an Al content of 20 to 95 mass% in the plated film,
A step of imparting at least a thermal history of (a) below to the plating film of the steel sheet exiting the hot dipping bath,
(a) After the hot-plated plated metal is solidified, it is heated to a temperature T (° C.) in the range of 130 to 300 ° C., and then the average cooling rate from the temperature T (° C.) to 100 ° C. is as follows ( 1) Thermal history satisfying C (° C./hr) or less shown in the formula,
Or / and the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C. after the hot-plated plated metal solidifies is below C (° C./hr) shown in the following formula (1) History C that satisfies the following conditions: C = (T-100) / 2 (1)
Excellent Cr by chromate treatment on the surface of the plated steel sheet in workability and the processing unit corrosion, characterized in that a step of forming a chemical conversion film containing less than 0.1 mg / m 2 or more 100 mg / m 2 reckoned as metal chromium A method for producing a surface-treated steel sheet.
[0015]
[9] A surface-treated steel sheet excellent in workability and processed portion corrosion resistance, characterized in that in the production method of [8], the temperature T (° C.) of the thermal history in (a) is in the range of 130 to 200 ° C. Manufacturing method.
[10] In the production method of [8] or [9], the plating film contains 0.01 to 10 mass in total of one or more selected from Mg, V, and Mn. A method for producing a surface-treated steel sheet excellent in workability and corrosion resistance of the processed part.
[11] In the manufacturing method according to any one of [8] to [10] above, the thermal history of (a) is applied to the plating film in at least one of the following (1) to (3) : A method for producing a surface-treated steel sheet having excellent workability and corrosion resistance of a processed part.
(1) Before formation of chemical conversion coating
(2) After formation of chemical conversion coating
(3) Cooling process after solidification of hot-plated plated metal
[12] In the production method according to any one of [8] to [11] above, in the step of forming the chemical conversion film, chromium is obtained by reducing the aqueous organic resin and chromic acid and / or a part of chromic acid on the plating film surface. After applying a chromate treatment solution containing an acid compound, the coating is dried at a temperature of 80 to 300 ° C., whereby the mass ratio of the amount of organic resin (A) in the film to the amount of Cr (B) in terms of chromium metal ( A method for producing a surface-treated steel sheet excellent in workability and processed part corrosion resistance, characterized in that a chemical conversion film having A) / (B) of 1 or more and less than 200 is formed.
[0017]
[13] In the production method according to any one of [8] to [11] above, the plating film surface is subjected to chromate treatment, and then a treatment liquid containing an aqueous organic resin is applied to a plate temperature of 80 to 300 ° C. A method for producing a surface-treated steel sheet excellent in workability and processed portion corrosion resistance, characterized in that a chemical conversion treatment film is formed by drying.
[14] In the production method of [13] above, the mass ratio (A) / (B of the total organic resin amount (A) contained in the coating film and the total Cr content (B) in terms of metallic chromium on the plating film surface ) Is formed from 1 to less than 200, and is a method for producing a surface-treated steel sheet having excellent workability and corrosion resistance of the processed part.
[15] In addition to the process of the production method according to any one of [8] to [14] above, the process further includes a step of applying one coat or two coats or more on the chemical conversion film surface. Manufacturing method of painted steel sheet.
[0018]
DETAILED DESCRIPTION OF THE INVENTION
The surface-treated steel sheet of the present invention uses a molten Al-Zn-based plated steel sheet containing 20 to 95 mass% Al in the plating film as a base steel sheet. Moreover, from a viewpoint of corrosion resistance and the like, a preferable range from the amount of Al in the plating film is 45 to 65 mass%. Moreover, the particularly preferable component composition of the plating film is Al: 45 to 65 mass%, Si: 0.7 to 2.0 mass%, Fe: less than 10 mass%, and the balance is substantially Zn containing inevitable impurities. In the case of such a composition, particularly excellent corrosion resistance is exhibited.
[0019]
Furthermore, the corrosion resistance and workability can be further improved by adding 0.01 to 10 mass% of one or more selected from Mg, V, and Mn in the plating film. If the total content of these elements is less than 0.01 mass%, a sufficient effect cannot be obtained. On the other hand, if it exceeds 10 mass%, the corrosion resistance improving effect is saturated and the film becomes hard, so that workability is lowered.
[0020]
However, this molten Al-Zn-based plated steel sheet is difficult to obtain high processed part corrosion resistance only by its plating composition, and it is only an excellent processed part that has undergone a thermal history described later and combined with an upper chemical conversion film. Corrosion resistance is obtained.
Moreover, although there is no restriction | limiting in particular in the plating adhesion amount of this fusion | melting Al-Zn type plated steel plate, Generally it is appropriate to set it as about 30-200 g / m < 2 > per single side | surface.
[0021]
Furthermore, the plating film of the molten Al—Zn-based plated steel sheet needs to be a plating film obtained through at least the following thermal history (a).
(a) After the hot-plated plated metal is solidified, it is heated to a temperature T (° C.) in the range of 130 to 300 ° C., and then the average cooling rate from the temperature T (° C.) to 100 ° C. is as follows ( 1) Thermal history satisfying C (° C./hr) or less shown in the formula,
Or / and the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C. after the hot-plated plated metal solidifies is below C (° C./hr) shown in the following formula (1) History C that satisfies the following conditions: C = (T-100) / 2 (1)
In the thermal history (a), a more preferable range of the temperature T (° C.) is 130 to 200 ° C.
Here, the above formula (1) is a detailed study by the present inventors based on experiments on the influence of the heating condition of the plating film and the subsequent cooling conditions and the cooling condition after solidification of the hot-plated plated metal on the plating film. The empirical formula derived as a result.
[0022]
By making the plating film undergo the thermal history of (a), the workability (such as crack resistance) is greatly improved while it is a molten Al—Zn plating film. Thus, the workability is improved because the plating film is heated to a temperature range of 130 to 300 ° C. (preferably 130 to 200 ° C.) and then slowly cooled under specific conditions, or / The strain accumulated in the plating film at the time of solidification is released by passing through a thermal history that is gradually cooled under specific conditions from a temperature range of 130 to 300 ° C. (preferably 130 to 200 ° C.) after the plating film is solidified. In addition, solid diffusion occurs in the plating film, and the two-phase separation of Al and Zn in the plating film is effectively promoted, so that the plating film is softened.
[0023]
In the thermal history of (a) above, the plating film (plating film after the hot-plated plated metal is solidified) is heated to 130-300 ° C, preferably 130-200 ° C in temperature T (° C). Thereafter, cooling is performed so that the average cooling rate from the temperature T (° C.) to 100 ° C. satisfies C (° C./hr) or less shown in the above equation (1), or the hot-plated plated metal is solidified. So that the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C., which is the cooling process, of the plated film after satisfying C (° C./hr) shown in the above formula (1) Cool down.
[0024]
In the thermal history of (a), when the heating temperature T of the plating film is less than 130 ° C., the above-mentioned effects cannot be obtained sufficiently, while when the heating temperature T exceeds 300 ° C., the base steel plate and the plating are plated. In order to promote the growth of the alloy phase at the interface with the film, the workability is adversely affected. From such a viewpoint, the upper limit of the heating temperature T that is more preferable for improving the workability is 200 ° C.
Moreover, also about the case where it cools on the conditions where the thermal history of said (a) is provided from the temperature T (degreeC) of the range of 130-300 degreeC which is the cooling process after the hot-plated plated metal solidifies, If the temperature T is less than 130 ° C., the above-described effects cannot be obtained sufficiently.
[0025]
Fig. 1 (a) shows the effect of the heating and heating temperature of the plating film on the workability of the surface-treated steel sheet when heat-treating the plated steel sheet after the hot-plated plated metal solidifies. All of the test materials from which the results were obtained satisfy the conditions of the present invention in the plated steel sheet in which the average cooling rate of the plating film from the heating temperature to 100 ° C. is within the thermal history condition of (a) above. It is the surface treatment steel plate which formed the chemical conversion treatment film. The evaluation of workability in this test was performed in accordance with the evaluation of workability in Examples described later.
[0026]
Fig. 1 (b) shows the surface treatment of the average cooling rate of the plating film (average cooling rate from the heating temperature to 100 ° C) when the plated steel sheet after the hot-plated plated metal solidifies is heat-treated. Investigating the effect on the workability of the steel sheet, the specimens from which this result was obtained are all plated steel sheets in which the heating temperature of the plating film is within the thermal history conditions of (a) above, It is the surface treatment steel plate which formed the chemical conversion treatment film which satisfies the conditions of the present invention. The evaluation of workability in this test was performed in accordance with the evaluation of workability in Examples described later.
[0027]
As shown in FIGS. 1 (a) and 1 (b), when the heating temperature of the plating film is in the range of 130 to 300 ° C., the 2T bending workability score is 4 or more, which is a preferable condition. In the range of ˜200 ° C., the workability score is 4 to 5 points. On the other hand, when the heating / heating temperature is outside the range of 130 to 300 ° C., only 3 scores of workability are obtained. In addition, when the difference between the average cooling rate from the heating temperature to 100 ° C. and “C” in the above equation (1) is zero to minus (within the range of the present invention), the 2T bending workability rating is 4 On the other hand, when the difference is plus (outside the scope of the present invention), only 3 points of workability are obtained.
[0028]
In order for the plating film to have undergone the thermal history of (a) above, a heating or heat retention device for heat-treating or heat-retaining the plating film is provided inside or outside the continuous hot-dip plating equipment, Heat treatment or heat retention is performed. For example, a heating mechanism (for example, an induction heater, a gas heating furnace, a hot blast furnace, etc.) may be provided in a continuous hot dip plating facility and continuously heated inline, or after being wound on a coil and offline. You may carry out by batch heating. Moreover, you may carry out by heating continuously with a heating mechanism (for example, an induction heater, a gas heating furnace, a hot stove etc.) in the continuous processing equipment outside a plating line. Furthermore, you may perform appropriate heat retention or heat retention after winding the plated steel plate continuously heated by the plating line or the said continuous processing equipment to a coil. Moreover, you may provide the heat retention apparatus which heat-retains a plating film in the cooling process after the hot-plated plating metal solidifies, and can cool gradually.
However, there are no particular restrictions on the method, shape, scale, etc. of the heating or heat retaining device, and the main point is that it can give the thermal history of (a) to the plating film.
[0029]
By forming a specific chemical conversion treatment film on the surface of the plating film having undergone the thermal history of (a) as described above, this surface-treated steel sheet exhibits excellent workability and corrosion resistance of the processed part.
[0030]
Chemical conversion coating formed on the plated film surface, the Cr by chromate treatment is intended to include less than 0.1 mg / m 2 or more 100 mg / m 2 reckoned as metal chromium. By forming such a chemical conversion treatment film on the surface of a specific plating film that hardly causes cracks as described above, the corrosion resistance of the processed part is remarkably improved. In addition, this chemical conversion treatment film may be comprised by the multilayer film, and the said film should just contain the said Cr in this case. Therefore, the Cr may be included in only one layer of the multilayer coating, or may be included in two or more coatings.
When the amount of Cr in terms of metallic chromium in the chemical conversion coating is less than 0.1 mg / m 2 , the corrosion resistance of the processed part is not sufficiently improved. On the other hand, when the Cr amount is 100 mg / m 2 or more, the effect of improving the processed part corrosion resistance is saturated. On the other hand, environmental harmony is impaired by a decrease in Cr fixation rate due to an increase in Cr content.
[0031]
Moreover, as a more preferable chemical conversion treatment film, after applying a chromate treatment liquid containing an aqueous organic resin and chromic acid and / or a chromic acid compound obtained by reducing a part of chromic acid, drying is performed at a plate temperature of 80 to 300 ° C. The weight ratio (A) / (B) of the amount of organic resin (A) contained in the coating and the amount of Cr (B) in terms of metallic chromium is less than 1 and less than 200. It is a chemical conversion treatment film.
Thus, when a chemical conversion treatment film contains organic resin with Cr, a process part corrosion resistance becomes still better.
[0032]
Moreover, in such a chemical conversion treatment film, when the mass ratio (A) / (B) of the amount of organic resin (A) and the amount of Cr (B) in terms of metallic chromium is less than 1, the organic resin improves the corrosion resistance of the processed part. The effect to make it not fully demonstrated. On the other hand, when the mass ratio (A) / (B) is 200 or more, the effect of improving the processed portion corrosion resistance by Cr cannot be sufficiently obtained.
Moreover, when the drying temperature after applying the chromate treatment liquid at the time of forming the chemical conversion treatment film is less than 80 ° C. at the plate temperature, an appropriate chemical conversion treatment film is not formed because the temperature is low. Since further heat is applied to the film, the alloying reaction is accelerated, and the workability may be reduced.
[0033]
Furthermore, it is preferable that a chemical conversion treatment film consists of a chromate treatment film and the specific film formed in the upper layer. This upper layer film is a film obtained by applying a treatment liquid containing an aqueous organic resin and drying at a plate temperature of 80 to 300 ° C., and the chemical conversion film is composed of the chromate-treated film and the above-mentioned film on the upper layer. By doing so, more excellent processed portion corrosion resistance can be obtained.
If the drying temperature after applying the treatment liquid when forming the upper layer film is less than 80 ° C. in plate temperature, an appropriate chemical conversion film is not formed because the temperature is low. Since heat is applied, the alloying reaction is accelerated, and the workability may be reduced.
[0034]
The total Cr amount in terms of metallic chromium contained in this chemical conversion coating (chromate treatment coating + upper layer coating) is 0.1 mg / m 2 or more and less than 100 mg / m 2 , and the reason for the limitation is as described above. Whether or not Cr is contained in the upper film is optional, but when Cr is contained, the corrosion resistance is further improved. The film thickness of the upper layer film is preferably about 0.1 to 5 μm, and if the film thickness is less than 0.1 μm, the effect of improving the corrosion resistance of the processed part is not sufficient, while if it exceeds 5 μm, it is picked up by the roll during roll forming of the surface-treated steel sheet May occur.
[0035]
Further, in this chemical conversion coating, the mass ratio (A) / (B) of the total amount of organic resin (A) contained in the coating and the total amount of Cr (B) in terms of chromium metal is 1 or more and less than 200. Is preferred. If the mass ratio (A) / (B) of the total organic resin amount (A) and the total Cr amount (B) in terms of metallic chromium is less than 1, the organic resin has a small effect of improving the corrosion resistance of the processed part, while the mass When the ratio (A) / (B) is 200 or more, the effect of improving the processed portion corrosion resistance by Cr is small.
[0036]
Next, the manufacturing method of the said surface treatment steel plate by this invention is demonstrated.
The production method of the present invention uses a molten Al-Zn-based plated steel sheet having an Al content of 20 to 95 mass% in a plated film produced by a continuous hot-dip plating facility as a base steel sheet, and forms a chemical conversion film on the surface. A method for producing a surface-treated steel sheet, a step of imparting at least the thermal history of (a) below to the plated film on the steel sheet that has exited the hot dipping bath, and a specific chemical conversion film is formed on the surface of the plated steel sheet And a step of causing
(a) After the hot-plated plated metal is solidified, it is heated to a temperature T (° C.) in the range of 130 to 300 ° C., and then the average cooling rate from the temperature T (° C.) to 100 ° C. is as follows ( 1) Thermal history satisfying C (° C./hr) or less shown in the formula,
Or / and the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C. after the hot-plated plated metal solidifies is below C (° C./hr) shown in the following formula (1) History C that satisfies the following conditions: C = (T-100) / 2 (1)
[0037]
The thermal history given in (a) above is applied to the plated steel sheet after solidification of the hot-plated plated metal or cooling of the plating film after the hot-plated plated metal is solidified. Is controlled by heat retention or the like. In the production method of the present invention, a specific chemical conversion treatment film is formed on the plated film surface of the plated steel sheet. The heat treatment for imparting the thermal history of (a) to the plating film is performed by ( i ) before forming the chemical conversion treatment film. may be carried out in (ii) conversion after the formation of the conversion coating (after the formation of the process liquid coating and coating by the drying step), any stage of the. Moreover, you may carry out in these two steps.
[0038]
Therefore, the application of the thermal history of (a) to the plating film can be performed in at least one of the following (1) to (3) .
(1) Before formation of chemical conversion coating
(2) After formation of chemical conversion coating
(3) Cooling process after solidification of hot-plated plated metal In addition, among the above methods of performing heat treatment, the method of (1) has the advantage that each condition of the heat treatment step and the chemical conversion treatment step can be optimized independently. In addition, the method (2) is suitable for performing all treatments in a continuous hot dip plating facility .
[0039]
The heat treatment or heat retention for imparting the thermal history (a) is performed by a heating or heat retention device or the like provided in the continuous hot dip plating facility or outside the facility. A heating mechanism (for example, an induction heater, a hot blast furnace, etc.) may be provided in the continuous hot dip plating equipment, and may be continuously heated in-line, or may be batch-heated offline after being wound on a coil. Also good. Moreover, you may carry out by heating continuously with a heating mechanism (for example, an induction heater, a hot stove, etc.) in the continuous processing equipment outside a plating line. Furthermore, you may perform appropriate heat retention or heat retention after winding the plated steel plate continuously heated by the plating line or the said continuous processing equipment to a coil. Moreover, you may provide the heat retention apparatus which heat-retains a plating film in the cooling process after the hot-plated plating metal solidifies, and can cool gradually. However, there are no particular restrictions on the method, shape, scale, etc. of the heating or heat retaining device, and the main point is that it can give the thermal history of (a) to the plating film.
In addition, the preferable plating composition of the hot-dip Al—Zn-based plated steel sheet to be produced, the coating adhesion amount, the reason for limiting the thermal history in the above (a), the obtained effects and the like are as described above.
[0040]
In the production method of the present invention, the plating film surface of the plated steel sheet, at least chromate treatment carried out one or more processes including, Cr chemical conversion treatment containing less than 0.1 mg / m 2 or more 100 mg / m 2 reckoned as metal chromium A film is formed. The anteroposterior relationship between the step of forming the chemical conversion film and the step of imparting the thermal history (a) is as described above.
In the chromate treatment, a chromate treatment solution is applied to the surface of the plated steel sheet and is usually dried at 80 to 300 ° C. without being washed with water.
As described above, the chemical conversion film may be composed of a multilayer film. In this case, a plurality of processes are sequentially performed. In the case of a multilayer coating, it is sufficient that the entire coating contains Cr. Therefore, this Cr may be included in only one layer of the multilayer coating, or a coating having two or more layers. May be included.
[0041]
Moreover, the preferable composition and process conditions of a chemical conversion treatment film are as having described previously. That is, a particularly preferable chemical conversion coating is applied at a plate temperature of 80 to 300 ° C. after applying a chromate treatment liquid containing an aqueous organic resin and chromic acid and / or a chromic acid compound obtained by reducing a part of chromic acid. And a weight ratio (A) / (B) of the amount of organic resin (A) contained in the film and the amount of Cr (B) in terms of metallic chromium is 1 or more and less than 200. It is a treatment film. The reason for limitation and the operational effect in this case are as described above.
[0042]
Further, after the chromate treatment as described above, a specific upper layer film may be formed on the upper layer. In this case, the chemical conversion treatment film is a composite film of the chromate treatment and the upper layer film. The total Cr amount in terms of metal chromium contained in this chemical conversion coating (chromate coating + upper layer coating) is 0.1 mg / m 2 or more and less than 100 mg / m 2 . Whether or not Cr is contained in the upper film is optional, but when Cr is contained, the corrosion resistance is further improved. The thickness of the upper film is preferably about 0.1 to 5 μm. Moreover, this chemical conversion treatment film has a mass ratio (A) / (B) of the total organic resin amount (A) contained in the film to the total Cr amount (B) in terms of metallic chromium being 1 or more and less than 200. Is preferred. The upper layer film is formed, for example, by applying a treatment liquid containing an aqueous organic resin and drying at a plate temperature of 80 to 300 ° C. In addition, the reason for limitation of each above structure and an effect are as having stated previously.
[0043]
A single-layer or multi-layer coating film can be formed on the surface of the surface-treated steel sheet of the present invention described above to form a coated steel sheet. Examples of the coating film include a polyester resin coating film, an epoxy resin coating film, an acrylic resin coating film, a urethane resin coating film, and a fluororesin coating film. Moreover, for example, an epoxy resin-modified polyester resin-based coating film in which a part of the resin is modified with another resin can be applied. Further, a curing agent, a curing catalyst, a pigment, an additive and the like can be added to the resin as necessary.
A coating method for forming a coating film on the surface of the surface-treated steel sheet is not particularly defined, but examples of the coating method include roll coater coating, curtain flow coating, and spray coating. After the paint is applied, it is generally heated and dried by hot air drying, infrared heating, induction heating, or the like to form a coating film.
[0044]
【Example】
[Example 1]
A cold-rolled steel sheet (thickness 0.5 mm) manufactured by a conventional method was passed through a continuous hot-dip plating facility, and a 55% Al-1.5% Si-Zn plating bath ( No. 1 to No. 10 in Table 1). ), 40% Al-1.0% Si-Zn plating bath ( No. 11 in Table 1) and 70% Al-1.8% Si-Zn plating bath ( No. 12 in Table 1). Went. The line speed was 160 m / min, and the amount of single-sided plating was such that the variation between the steel sheets was within the range of 75 to 90 g / m 2 .
[0045]
In the manufacturing process of this plated steel sheet, the thermal history shown in Table 1 was given to the plating film, and the plating film surface was subjected to chemical conversion treatment. The chemical conversion treatment conditions were as follows. A treatment liquid in which an acrylic emulsion resin and chromic acid were mixed at a ratio of resin solid content: Cr content = 100: 1 (mass ratio) had a Cr deposition amount of 20 mg / m in terms of metal chromium. 2 was applied to the surface of the plated steel sheet and dried at 120 ° C.
The surface-treated steel sheet thus manufactured was evaluated for workability and processed part corrosion resistance by the following methods. The results are shown in Table 1.
[0046]
(1) Workability The surface-treated steel sheet was bent 2T, and cracks at the tip of the 2T bending were observed and evaluated according to the following criteria.
5: No cracks are observed even when observed with a 20X magnifier.
4: Cracks are not observed when visually observed, but cracks are observed when observed with a 20-fold magnifier.
3: Cracks are observed by visual observation.
2: The crack which opened large visually and observed visually is recognized.
1: A crack accompanied by peeling occurs.
[0047]
(2) Processed part corrosion-resistant surface-treated steel sheet was bent 3T, then placed in a wet testing machine at 50 ° C and 98% RH and observed for rust generation from the bent part after 1000 hours. It was evaluated with.
5: No abnormality 4: Mild white rust and black rust occurred in some areas 3: Mild white rust and black rust occurred in the entire area 2: Significant white rust and black rust occurred in the entire area 1: Red rust occurred Yes [0048]
[Table 1]
[Example 2]
A cold-rolled steel plate (thickness 0.5 mm) produced by a conventional method was passed through a continuous hot-dip plating facility and hot-dip plated using a 55% Al-1.5% Si-Zn plating bath. The line speed was 160 m / min, and the amount of single-sided plating was such that the variation between the steel sheets was within the range of 75 to 90 g / m 2 .
[0050]
In the manufacturing process of this plated steel sheet, the thermal history shown in Table 2 was given to the plating film, and the plating film surface was subjected to chemical conversion treatment. The chemical conversion treatment was performed by subjecting the plated steel sheet to chromate treatment so that the amount of Cr deposited in terms of chromium metal was 20 mg / m 2 , drying at 80 ° C., and applying a treatment liquid containing urethane emulsion resin on the upper layer. And dried at 120 ° C.
With respect to the surface-treated steel sheet thus manufactured, the workability and the processed portion corrosion resistance were evaluated by the same method as in Example 1. The results are shown in Table 2.
[0051]
[Table 2]
[Example 3]
A cold-rolled steel plate (thickness 0.5 mm) manufactured by a conventional method is passed through a continuous hot-dip plating facility, and Mg, V, or Mn is added to a 55% Al-1.5% Si-Zn plating bath. Using a plating bath to which one or more types are added, hot-dip plating is performed so that the content of one or more of Mg, V, and Mn in the plating film is 0.01 to 10 mass% in total. It was. The line speed was 160 m / min, and the amount of single-sided plating was such that the variation between the steel sheets was within the range of 75 to 90 g / m 2 .
[0053]
In the production process of this plated steel sheet, the thermal history shown in Table 3 was given to the plating film, and the surface of the plating film was subjected to chemical conversion treatment under the same conditions as in Example 1.
With respect to the surface-treated steel sheet thus manufactured, the workability and the processed portion corrosion resistance were evaluated by the same method as in Example 1. The results are shown in Table 3.
[0054]
[Table 3]
【The invention's effect】
As described above, the surface-treated steel sheet of the present invention has extremely excellent workability even though it is a surface-treated steel sheet in which a molten Al-Zn-based plated steel sheet having an Al content in the plating film of 20 to 95 mass% is a base steel sheet. Corrosion resistance of processed parts. Moreover, according to the manufacturing method of this invention, such a surface treatment steel plate can be manufactured stably and with high productivity.
[Brief description of the drawings]
FIG. 1 (a) is a graph showing the influence of the temperature rise and heating temperature of a plating film on the workability of a surface-treated steel sheet when the plated steel sheet after the hot-plated plated metal solidifies is heat-treated. Fig. 1 (b) shows that when the plated steel sheet after the hot-plated plated metal solidifies, the average cooling rate of the plating film (average cooling rate from the heating temperature to 100 ° C) is the surface treatment. Graph showing the effect on workability of steel sheet
Claims (15)
前記めっき皮膜が少なくとも下記(a)の熱履歴を経て得られためっき皮膜であり、前記化成処理皮膜がクロメート処理によるＣｒを金属クロム換算で０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満含むことを特徴とする加工性と加工部耐食性に優れた表面処理鋼板。
(a) 溶融めっきされためっき金属が凝固した後、１３０〜３００℃の範囲の温度Ｔ（℃）に昇温加熱され、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴、
又は／及び、溶融めっきされためっき金属が凝固した後の１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴
Ｃ＝（Ｔ−１００）／２ …… (1)A surface-treated steel sheet having a chemical conversion film on the surface of a molten Al-Zn-based plated steel sheet having an Al content of 20 to 95 mass% in the plated film,
The plating film is a plating film obtained through the heat history of at least the following (a), the chemical conversion coating may contain less than 0.1 mg / m 2 or more 100 mg / m 2 reckoned as metal chromium to Cr by chromate treatment A surface-treated steel sheet with excellent workability and corrosion resistance on the machined part.
(a) After the hot-plated plated metal is solidified, it is heated to a temperature T (° C.) in the range of 130 to 300 ° C., and then the average cooling rate from the temperature T (° C.) to 100 ° C. is as follows ( 1) Thermal history satisfying C (° C./hr) or less shown in the formula,
Or / and the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C. after the hot-plated plated metal solidifies is below C (° C./hr) shown in the following formula (1) History C that satisfies the following conditions: C = (T-100) / 2 (1)
溶融めっき浴を出た鋼板のめっき皮膜に対して、少なくとも下記(a)の熱履歴を付与する工程と、
(a) 溶融めっきされためっき金属が凝固した後、１３０〜３００℃の範囲の温度Ｔ（℃）に昇温加熱され、その後、温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴、
又は／及び、溶融めっきされためっき金属が凝固した後の１３０〜３００℃の範囲の温度Ｔ（℃）から１００℃までの平均冷却速度が下記(1)式に示すＣ（℃／ｈｒ）以下を満足する熱履歴
Ｃ＝（Ｔ−１００）／２ …… (1)
めっき鋼板の表面にクロメート処理によるＣｒを金属クロム換算で０．１ｍｇ／ｍ２以上１００ｍｇ／ｍ２未満含む化成処理皮膜を形成させる工程とを有することを特徴とする加工性と加工部耐食性に優れた表面処理鋼板の製造方法。A method for producing a surface-treated steel sheet having a chemical conversion film on the surface of a molten Al-Zn-based plated steel sheet having an Al content of 20 to 95 mass% in the plating film,
A step of imparting at least a thermal history of (a) below to the plating film of the steel sheet exiting the hot dipping bath,
(a) After the hot-plated plated metal is solidified, it is heated to a temperature T (° C.) in the range of 130 to 300 ° C., and then the average cooling rate from the temperature T (° C.) to 100 ° C. is as follows ( 1) Thermal history satisfying C (° C./hr) or less shown in the formula,
Or / and the average cooling rate from the temperature T (° C.) in the range of 130 to 300 ° C. to 100 ° C. after the hot-plated plated metal solidifies is below C (° C./hr) shown in the following formula (1) History C that satisfies the following conditions: C = (T-100) / 2 (1)
Excellent Cr by chromate treatment on the surface of the plated steel sheet in workability and the processing unit corrosion, characterized in that a step of forming a chemical conversion film containing less than 0.1 mg / m 2 or more 100 mg / m 2 reckoned as metal chromium A method for producing a surface-treated steel sheet.
(1) 化成処理皮膜の形成前
(2) 化成処理皮膜の形成後
(3) 溶融めっきされためっき金属が凝固した後の冷却過程The workability and processed part according to claim 8, 9 or 10, wherein the thermal history of (a) is given to the plating film in at least one of the following (1) to (3). A method for producing a surface-treated steel sheet having excellent corrosion resistance.
(1) Before formation of chemical conversion coating
(2) After formation of chemical conversion coating
(3) Cooling process after the hot-plated plated metal solidifies
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002015854A JP3643559B2 (en) | 2001-01-31 | 2002-01-24 | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001-24859 | 2001-01-31 | ||
| JP2001024859 | 2001-01-31 | ||
| JP2002015854A JP3643559B2 (en) | 2001-01-31 | 2002-01-24 | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2002302751A JP2002302751A (en) | 2002-10-18 |
| JP3643559B2 true JP3643559B2 (en) | 2005-04-27 |
Family
ID=26608720
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2002015854A Expired - Fee Related JP3643559B2 (en) | 2001-01-31 | 2002-01-24 | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3643559B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6704669B1 (en) * | 2019-08-29 | 2020-06-03 | Ｊｆｅ鋼板株式会社 | Hot-dip Al-Zn alloy plated steel sheet having excellent corrosion resistance in worked part and method for producing the same |
-
2002
- 2002-01-24 JP JP2002015854A patent/JP3643559B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JP2002302751A (en) | 2002-10-18 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| TWI511875B (en) | Molten galvanized steel sheet | |
| TWI498455B (en) | A molten Al-Zn plated steel sheet and a method for producing the same | |
| TWI521092B (en) | Hot dip a1-zn plated steel sheet and method of manufacturing the same | |
| KR20150073315A (en) | HOT DIP Zn-Al-Mg ALLOY PLATED STEEL SHEET HAVING EXCELLENT CORROSION RESISTANCE AND METHOD FOR MANUFACTURING THE SAME | |
| JP6704669B1 (en) | Hot-dip Al-Zn alloy plated steel sheet having excellent corrosion resistance in worked part and method for producing the same | |
| JP4555499B2 (en) | Hot-dip Zn-Al-Mg-Si plated steel with excellent surface properties and method for producing the same | |
| JP6509160B2 (en) | Molten Al-Zn based plated steel sheet and manufacturing method thereof | |
| JP2002356759A (en) | HOT DIP Zn-Al-Cr ALLOY PLATED STEEL HAVING EXCELLENT CORROSION RESISTANCE | |
| JP3580541B2 (en) | Surface-treated steel sheet excellent in workability and corrosion resistance of processed part and method for producing the same | |
| JP3654520B2 (en) | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same | |
| JP7393551B2 (en) | Aluminum alloy plated steel sheet with excellent workability and corrosion resistance and its manufacturing method | |
| JP3643559B2 (en) | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same | |
| JP3749487B2 (en) | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part | |
| JP3465688B2 (en) | Hot-dip Zn-Al-based alloy-coated steel sheet excellent in workability and method for producing the same | |
| JPH09209109A (en) | Microspangle hot-dip zinc-aluminium base alloy plated steel sheet and its production | |
| JP2003213396A (en) | Surface-treated steel plate of excellent machinability and corrosion resistance of machined part, and manufacturing method thereof | |
| JP3652996B2 (en) | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same | |
| JP2006207033A (en) | Surface-treated steel sheet excellent in workability and corrosion resistance at worked area | |
| JP3643544B2 (en) | Surface-treated steel sheet excellent in workability and corrosion resistance of machined part and method for producing the same | |
| JP3371819B2 (en) | Hot-dip galvanized steel sheet excellent in blackening resistance and method for producing the same | |
| JP2005290418A (en) | HOT-DIP Al-Zn ALLOY PLATED STEEL SHEET SUPERIOR IN PRESS FORMABILITY, AND MANUFACTURING METHOD THEREFOR | |
| JP3811363B2 (en) | Manufacturing method of surface-treated steel sheet with excellent workability and corrosion resistance of processed parts | |
| JP3811364B2 (en) | Manufacturing method of surface-treated steel sheet with excellent workability and corrosion resistance of processed parts | |
| JP4855290B2 (en) | Hot-dip galvanized steel sheet and method for producing alloyed hot-dip galvanized steel sheet | |
| JP4131577B2 (en) | Manufacturing method of plated steel sheet |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A711 | Notification of change in applicant |
Free format text: JAPANESE INTERMEDIATE CODE: A712 Effective date: 20040629 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20041026 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20050125 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20050128 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| LAPS | Cancellation because of no payment of annual fees |