JP2022513695A - 水素脆性に対する抵抗性に優れた熱間プレス成形部材及びその製造方法 - Google Patents
水素脆性に対する抵抗性に優れた熱間プレス成形部材及びその製造方法 Download PDFInfo
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- JP2022513695A JP2022513695A JP2021531411A JP2021531411A JP2022513695A JP 2022513695 A JP2022513695 A JP 2022513695A JP 2021531411 A JP2021531411 A JP 2021531411A JP 2021531411 A JP2021531411 A JP 2021531411A JP 2022513695 A JP2022513695 A JP 2022513695A
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Abstract
Description
部材を厚さ方向に切断した断面から観察したときに、上記気孔の分率は、全合金めっき層の面積に対して3%以上の比率を有することができる。気孔の分率を上述の比率とすることで、十分な水素集積効果を奏することができる。しかし、気孔の比率が高すぎる場合には、合金めっき層が弱くなるという問題があるため、本発明の例示的な一実施形態では、上記気孔の分率を30%以下にすることができる。本発明の他の例示的な一実施形態では、上記気孔の分率を5~20%にしてもよい。
水素の集積サイトを提供するために、上記気孔は5×103個/mm2以上存在することが好ましい。しかし、気孔の個数が過多である場合には、合金めっき層が弱くなるという問題があるため、本発明の例示的な一実施形態では、上記気孔の個数を2×106個/mm2以下に制限することができる。本発明において、上記気孔の数密度は、気孔の個数を合金めっき層の面積で除した値を意味する。本発明の他の例示的な一実施形態では、上記気孔の数密度を9×103~1×106個/mm2にすることができる。
上記Cは、熱処理部材の強度を向上させるための必須元素であり、適正量で添加することができる。すなわち、熱処理部材の強度を十分に確保するために、上記Cを0.04%以上添加することができる。好ましくは、上記Cの含量の下限は0.1%以上であってもよい。しかし、その含量が高すぎる場合には、冷延材の生産時に熱延材の冷間圧延を行う際に、熱延材の強度が過度に高くて冷間圧延性が大きく低下するだけでなく、スポット溶接性を大きく低下させるため、十分な冷間圧延性とスポット溶接性を確保するために、0.5%以下添加することができる。また、上記Cの含量は0.45%以下、より好ましくは0.4%以下にその含量を制限してもよい。
上記Siは、製鋼において脱酸剤として添加される必要があり、熱間プレス成形部材の強度に最も大きい影響を与える炭化物の生成を抑える役割を果たす。本発明では、熱間プレス成形において、マルテンサイトの生成後にマルテンサイトのラス(lath)粒界に炭素を濃化させることで残留オーステナイトを確保するために、0.01%以上の含量を添加することができる。また、圧延後の鋼板にアルミニウムめっきを行うときに十分なめっき性を確保するために、上記Siの含量の上限を2%に決定することができる。好ましくは、上記Siの含量を1.5%以下に制限してもよい。
上記Mnは、固溶強化の効果を確保することができるだけでなく、熱間プレス成形部材においてマルテンサイトを確保するための臨界冷却速度を下げるために、0.1%以上の含量を添加することができる。また、鋼板の強度を適切に維持することで、熱間プレス成形工程の作業性を確保し、製造原価を低減し、スポット溶接性を向上させるという点から、上記Mnの含量は5%以下に制限することができる。
上記Pは、鋼中に不純物として存在し、できる限りその含量が少ないほど有利である。したがって、本発明において、Pの含量を0.05%以下に制限することができ、好ましくは、0.03%以下に制限してもよい。Pは、少ないほど有利な不純物元素であるため、その含量の上限を特に決定する必要はない。しかし、Pの含量を過度に減少させると製造コストが上昇する恐れがあるため、これを考慮すると、その下限を0.001%にすることができる。
上記Sは、鋼中に不純物として存在し、部材の延性、衝撃特性、及び溶接性を阻害する元素であるため、最大含量を0.02%に制限し、好ましくは0.01%以下に制限することができる。また、その最小含量が0.0001%未満である場合には製造コストが上昇する恐れがあるため、その含量の下限を0.0001%にすることができる。
上記Alは、Siとともに製鋼で脱酸作用を行って鋼の清浄度を高めることができ、上記効果を得るために、0.001%以上の含量を添加することができる。また、Ac3温度が過度に高くならないようにし、熱間プレス成形時に必要な加熱を適切な温度範囲で行うことができるように、上記Alの含量は1%以下に制限することができる。
上記Nは、鋼中に不純物として含まれる元素であり、スラブの連鋳時にクラックの発生に対する敏感度を減少させ、衝撃特性を確保するためには、その含量が低いほど有利であるため、0.02%以下含むことができる。下限を特に決定する必要はないが、製造コストの上昇などを考慮すると、Nの含量を0.001%以上に決定してもよい。
上記Bは、少量添加しても硬化能を向上させることができるだけでなく、旧オーステナイト結晶粒界に偏析され、P及び/またはSの粒界偏析による熱間プレス成形部材の脆性を抑えることができる元素である。したがって、Bを0.0001%以上添加することができる。しかし、0.01%を超える場合には、その効果が飽和するだけでなく、熱間圧延で脆性をもたらすため、その上限を0.01%にし、好ましくは上記Bの含量を0.005%以下にすることができる。
上記Crは、Mnと同様に、固溶強化の効果、及び熱間成形時の硬化能の向上のために添加する元素であり、上記効果を得るために0.01%以上添加することができる。但し、部材の溶接性を確保するために、その含量を1%以下に制限することができる。また、1%を超える場合には、添加量に比べて硬化能の向上効果も微小であるため、原価の点からも不利である。
上記Tiは、微細析出物の形成による熱処理部材の強度上昇、及び結晶粒の微細化による部材の衝突性能向上に効果があるだけでなく、Bが添加される場合には、Nと先に反応してBの添加効果を極大化させる効果がある。上記効果を得るために、Tiを0.001%以上添加することができる。しかし、Tiの含量の増加に起因する粗大なTiNの形成は部材の衝突性能を低下させるため、その含量を0.2%以下に制限することができる。
本発明の例示的な一実施形態によると、アルミニウムめっき鋼板を用いる通常の熱間プレス成形工程とは異なって、アルミニウム-鉄合金めっき鋼板を熱間プレス成形工程に用いることで、本発明の有利な熱間プレス成形部材を提供することができる。このように、本発明の熱間プレス成形部材に適したアルミニウム-鉄合金めっき鋼板は、熱間圧延または冷間圧延された素地鋼板を準備し、上記素地鋼板の表面に溶融アルミニウムめっきを行った後、めっき鋼板に合金化のための焼鈍処理を行うことで得ることができる。以下、各工程毎に詳細に説明する。
上述の合金組成を有する素地鋼板を準備し、上記素地鋼板の表面に適切な条件でアルミニウムめっきを行い、これを巻き取ることで、アルミニウムめっき鋼板(コイル)を得ることができる。
アルミニウムめっきされた鋼板に対して、次のような条件で焼鈍処理を行うことにより、アルミニウム-鉄合金めっき鋼板を得ることができる。
上述の製造方法により製造された熱間成形用アルミニウム-鉄合金めっき鋼板に対して熱間プレス成形を行うことで、熱間プレス成形部材を製造することができる。この際、熱間プレス成形には、当該技術分野で一般に用いられる方法を利用することができ、非制限的な例示的な一実施形態として、Ac3~950℃の温度範囲で1~15分間熱処理した後、熱間プレス成形することができる。
先ず、素地鋼板として、下記表1の組成(Ac3:830℃)を有する熱間プレス成形用冷間圧延鋼板を準備し、鋼板の表面に、Al-8%Si-2.5%Feの組成を有するtype Iめっき浴で鋼板の表面をめっきした。めっき時のめっき量は、片面当たり65g/m2に調節し、アルミニウムめっき後に、250℃までの冷却速度を8℃/秒として冷却した後、巻取張力を2.4kg/mm2に調節して巻き取ることで、アルミニウムめっき鋼板を得た。
Claims (10)
- 素地鋼板と、前記素地鋼板の表面に形成された合金めっき層と、を含む熱間プレス成形部材であって、
前記部材を厚さ方向に切断した断面からみたときに、
前記合金めっき層は、合金めっき層の面積に対する、サイズ5μm以下の気孔が占める面積の比率が3~30%になるように気孔を含む、水素脆性に対する抵抗性に優れた熱間プレス成形部材。 - 素地鋼板と、前記素地鋼板の表面に形成された合金めっき層と、を含む熱間プレス成形部材であって、
前記部材を厚さ方向に切断した断面からみたときに、
前記合金めっき層は、合金めっき層の面積を、サイズ5μm以下の気孔の個数で除した値である気孔の数密度が5×103~2×106個/mm2になるように気孔を含む、水素脆性に対する抵抗性に優れた熱間プレス成形部材。 - 面積を基準として、サイズ5μm以下の全体気孔のうち70%以上の気孔が合金めっき層の表層部に存在する、請求項1に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材。
- 面積を基準として、サイズ5μm以下の全体気孔のうち70%以上の気孔が合金めっき層の表層部に存在する、請求項2に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材。
- 前記部材を厚さ方向に切断した断面からみたときに、
前記合金めっき層は、合金めっき層の面積に対する、サイズ5μm以下の気孔が占める面積の比率が3~30%になるように気孔を含む、請求項2に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材。 - 前記素地鋼板は、重量%で、C:0.04~0.5%、Si:0.01~2%、Mn:0.1~5%、P:0.001~0.05%、S:0.0001~0.02%、Al:0.001~1%、N:0.001~0.02%、残部Fe、及びその他の不純物を含む、請求項1~5の何れか一項に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材。
- 前記素地鋼板は、重量%で、B:0.0001~0.01%、Cr:0.01~1%、Ti:0.001~0.2%のうち1種以上をさらに含む、請求項6に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材。
- 素地鋼板の表面をアルミニウムめっきし、巻き取ってアルミニウムめっき鋼板を得る段階と、
アルミニウムめっき鋼板を焼鈍してアルミニウム-鉄合金めっき鋼板を得る段階と、
熱間成形用アルミニウム-鉄合金めっき鋼板をAc3~950℃の温度範囲で1~15分間熱処理した後、熱間プレス成形する段階と、を含む、熱間プレス成形部材の製造方法であって、
前記アルミニウムめっき量は、鋼板の片面を基準として30~200g/m2であり、
アルミニウムめっき後、250℃までの冷却速度を20℃/秒以下とし、
巻き取り時における巻取張力を0.5~5kg/mm2とし、
前記焼鈍は、水素を体積分率で50%以上含む箱焼鈍炉において、550~750℃の加熱温度範囲で30分~50時間行い、
前記焼鈍時に、常温から前記加熱温度まで加熱する時に、平均昇温速度を10~100℃/hとし、かつ400~500℃区間の平均昇温速度を1~15℃/hとし、
前記箱焼鈍炉内の雰囲気温度と鋼板温度との差を5~80℃とする、水素脆性に対する抵抗性に優れた熱間プレス成形部材の製造方法。 - 前記素地鋼板は、重量%で、C:0.04~0.5%、Si:0.01~2%、Mn:0.1~5%、P:0.001~0.05%、S:0.0001~0.02%、Al:0.001~1%、N:0.001~0.02%、残部Fe、及びその他の不純物を含む、請求項8に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材の製造方法。
- 前記素地鋼板は、重量%で、B:0.0001~0.01%、Cr:0.01~1%、Ti:0.001~0.2%のうち1種以上をさらに含む、請求項9に記載の水素脆性に対する抵抗性に優れた熱間プレス成形部材の製造方法。
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