JP7167025B2 - 加工部耐食性に優れたアルミニウム系合金めっき鋼板 - Google Patents
加工部耐食性に優れたアルミニウム系合金めっき鋼板 Download PDFInfo
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Description
[式1]t/5≦g≦t
Siは、加工性及び耐酸化性を向上させる役割を果たす。本発明では、かかる効果を得るために、Si含有量を3%以上に制御することが好ましい。但し、その含有量が15%を超えると、めっき浴温度の過度な上昇がもたらされるか、または粗大なSi初晶が晶出するという問題がある。
Mgは、耐食性を向上させ、未めっきを減少させる役割を果たす。本発明では、かかる効果を得るために、Mg含有量を0.1%以上に制御することが好ましい。但し、その含有量が10%を超えると、その効果が飽和するだけでなく、コストが急増するため好ましくない。
界面合金層を形成するとき、素地鋼板中のアルミニウムとめっき中のアルミニウムとの反応に参加するようになる。素地鋼板中のアルミニウム含有量が高いほど、界面合金層中のアルミニウム含有量が高い傾向がある。界面合金層中のアルミニウム含有量は、少ないほど加工性に有利であり、高いほど界面合金層の均一性がよい。したがって、界面合金層の均一性を考慮して、40%以上とし、加工性の観点から70%以下に制限する。
界面合金層を形成するとき、反応に参加するマンガンは、素地鋼板中に含有されるマンガンであって、鉄とマンガンの反応は、鉄-アルミニウム反応よりも遅い傾向を示す。界面合金層中のマンガン含有量は、素地鋼板中のマンガン含有量の変化に鈍感に変化する傾向がある。界面合金層中のマンガン含有量が高いほど、加工性には有利である。但し、高すぎると、加工に不利な相が生成されるためよくない。したがって、少なくとも界面合金層中のマンガン含有量は、加工性を考慮して、3%以上10%以下に制限する。
Siは、界面合金層の成長を抑制することを目的にアルミニウム系めっき浴中に添加されるものであって、3~15%添加する。合金層を形成するとき、鉄-シリコンの反応で鉄-アルミニウム反応を抑制する役割を果たすことで、めっき浴中のSi含有量がめっき層の加工性に影響を与えるようになる。界面合金層中のSi含有量は、めっき浴中のSi含有量、反応温度及び時間などの影響を受ける。したがって、界面合金層が効果的に抑制された場合、Si含有量は2%以上であり、13%を超えてもそれ以上の追加的な効果を得ることができないため、13%に限定する。
界面合金層の成分のうちMn含有量の適切な制御が要求される。Mnは、Feと同様の性質を有する金属であって、素地鋼板と溶融アルミニウム系めっき液が反応したとき、界面合金相の成長を促進するものと考えられる。界面合金層中のMn含有量は、素地鋼板内のMn含有量を調節するか、めっき層内のMnを微量添加することにより制御することができる。界面合金層中のMnの好ましい含有量範囲は、上述したとおりである。
界面合金層上に凹凸が形成される場合、Mg-Si系合金相の核が界面合金層の近くで優先的に生成される。これは、界面合金層上に凹凸が形成される場合には、アルミニウム系めっき層の熱を素地鋼板にさらに簡単に且つ多く伝達させるためであると考えられる。
めっき後の冷却速度は、Mg-Si系合金相の位置分布に大きな影響を与える。本発明で目標とする組織を確保するためには、Mg-Si系合金相の晶出温度範囲に限って徐冷を行うことによりMg-Si系合金相のめっき層の表層部の形成を防止する必要がある。この場合、Mg-Si系合金相の晶出温度範囲外では、比較的急冷を行うことにより、比較的温度の低いめっき層の表層部における残留液相のめっき層の凝固を誘導する必要がある。Mg-Si系合金相の晶出温度範囲は、組成系に応じて異なり、約556℃~1085℃である。本発明の組成範囲内では、約556℃~640℃である。本発明者らの研究結果では、Mg-Si系合金相の晶出温度が640℃である場合には、640℃から610℃までの温度範囲(すなわち、晶出温度から約20~40℃程度低い温度までの範囲)では5℃/sec以下の速度で徐冷し、それ以降の温度範囲では10℃/sec以上の速度で急冷する場合、目標とするMg-Si系合金相の位置分布を確保するのに有利であることが確認できる。
下記表1のようなMn含有量を有する鋼スラブ(すべてのスラブにおいてMn以外には、C:0.76%、Si:0.65%、P:0.013%、S:0.0050%、Cr:0.25%、Al:2.28%、Ti:0.08%を含み、各成分の含有量範囲は大差がないように調節した)を設けた。次に、鋼スラブを1200℃の温度範囲で加熱してから熱間圧延を行い、特に860℃で熱間仕上げ圧延を行った後、620℃で巻取りし、空冷した。その後、HCl溶液で鋼板表面の酸化物を除去した後、70%の圧下率で冷間圧延して1.2mmの冷延鋼板を製造した。続いて、冷延鋼板を脱脂し、サンドペーパーでその表面を研磨することにより、粗さを0.3μmに調節した後、800℃のN2-10vol%、H2雰囲気下で90秒間焼鈍熱処理し、その後、600~680℃で維持されるSi:9重量%、Mg:5重量%を含むアルミニウム系めっき浴に浸漬して冷延鋼板の表面にアルミニウム系めっき層を形成した。このとき、アルミニウム系めっき浴に浸漬される冷延鋼板の温度はめっき浴に対して15℃以下の温度で管理した。その後、各成分系のMg-Si系合金相晶出温度に対して30℃以下の温度までは3℃/secの速度、それ以降の温度では15℃/secの速度で冷却を行った。
Claims (7)
- 素地鋼板と、界面合金層と、Mg-Si系合金相を含むアルミニウム系めっき層と、を含み、
前記アルミニウム系めっき層に含まれるMg-Si系合金相の面積率をaとし、前記アルミニウム系めっき層の厚さ方向に下部20%の領域に含まれるMg-Si系合金相の面積率をbとしたとき、b/aが1~5であり、
前記素地鋼板は5~35重量%のMnを含み、
前記界面合金層は、重量%で、Al:40~70%、Mn:3~10%、Si:2~13%、残部Fe及び不可避不純物からなり、
前記界面合金層に含まれるMnは前記素地鋼板から流入された成分であり、
前記Mg-Si系合金相の少なくとも一部は、前記界面合金層と接して形成され、
前記界面合金層と接して形成されるMg-Si系合金相を前記素地鋼板と界面合金層の界面に投影した長さの平均をeとし、前記界面合金層と接して形成されるMg-Si系合金相の高さの平均をfとするとき、f/eが0.2~3である、アルミニウム系合金めっき鋼板。 - 前記界面合金層と接して形成されるMg-Si系合金相を前記素地鋼板と界面合金層の界面に投影した長さの合計をcとし、前記素地鋼板と界面合金層の界面の長さをdとするとき、c/dが0.2~0.8である、請求項1に記載のアルミニウム系合金めっき鋼板。
- 前記界面合金層と接して形成されるMg-Si系合金相の平均硬度は、400~600Hvである、請求項1に記載のアルミニウム系合金めっき鋼板。
- 前記界面合金層と接して形成されるMg-Si系合金相の平均間隔をgとし、前記アルミニウム系めっき層及び前記界面合金層の厚さをtとするとき、下記式1を満たす、請求項1に記載のアルミニウム系合金めっき鋼板。
[式1]t/5≦g≦t - 前記界面合金層は0.1~10μmの厚さを有する、請求項1に記載のアルミニウム系合金めっき鋼板。
- 前記アルミニウム系めっき層は、重量%で、Si:3~15%、Mg:0.1~10%、残部Al及び不可避不純物からなる、請求項1に記載のアルミニウム系合金めっき鋼板。
- 前記アルミニウム系めっき層は、重量%で、Ca:0.001~5%、Sr:0.005~2%、Mn:0.01~2%、Cr:0.01~2%、Mo:0.01~2%、Sn:0.1~10%の1種または2種以上をさらに含む、請求項6に記載のアルミニウム系合金めっき鋼板。
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KR1020160177538A KR101839253B1 (ko) | 2016-12-23 | 2016-12-23 | 가공부 내식성이 우수한 알루미늄계 합금 도금강판 |
KR10-2016-0177538 | 2016-12-23 | ||
PCT/KR2017/015415 WO2018117770A1 (ko) | 2016-12-23 | 2017-12-22 | 가공부 내식성이 우수한 알루미늄계 합금 도금강판 |
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EP3889312A4 (en) * | 2018-11-30 | 2021-10-27 | Posco | AL-FE CLADED STEEL SHEET FOR HOT FORMING WITH EXCELLENT CORROSION RESISTANCE AND POINT WELDABILITY AND PROCESS FOR ITS MANUFACTURING |
WO2020111881A1 (ko) * | 2018-11-30 | 2020-06-04 | 주식회사 포스코 | 내식성 및 용접성이 우수한 열간 프레스용 알루미늄-철계 도금 강판 및 그 제조방법 |
KR102311502B1 (ko) * | 2019-12-20 | 2021-10-13 | 주식회사 포스코 | 가공성 및 내식성이 우수한 알루미늄계 합금 도금강판 및 이의 제조방법 |
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- 2017-12-22 US US16/471,920 patent/US10837094B2/en active Active
- 2017-12-22 EP EP17882328.2A patent/EP3561139B1/en active Active
- 2017-12-22 CN CN201780080005.1A patent/CN110100039B/zh active Active
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EP3561139A4 (en) | 2020-02-19 |
JP2020504238A (ja) | 2020-02-06 |
US10837094B2 (en) | 2020-11-17 |
KR101839253B1 (ko) | 2018-03-15 |
EP3561139A1 (en) | 2019-10-30 |
US20190382877A1 (en) | 2019-12-19 |
CN110100039B (zh) | 2021-12-03 |
WO2018117770A1 (ko) | 2018-06-28 |
CN110100039A (zh) | 2019-08-06 |
ES2875890T3 (es) | 2021-11-11 |
EP3561139B1 (en) | 2021-03-24 |
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