JP6477980B1 - ホットスタンプ成形体 - Google Patents
ホットスタンプ成形体 Download PDFInfo
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- JP6477980B1 JP6477980B1 JP2018535454A JP2018535454A JP6477980B1 JP 6477980 B1 JP6477980 B1 JP 6477980B1 JP 2018535454 A JP2018535454 A JP 2018535454A JP 2018535454 A JP2018535454 A JP 2018535454A JP 6477980 B1 JP6477980 B1 JP 6477980B1
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
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Abstract
Description
Cは、2000MPa以上の引張強さを得るために重要な元素である。0.35%未満では、マルテンサイトが軟らかく、2000MPa以上の引張強さを確保することが困難であるので、Cは0.35%以上とする。好ましくは0.37%以上である。要求される強度と早期破断抑制のバランスを鑑みて、上限を0.75%とする。
Siは、変形能を高めて衝撃吸収能の向上に寄与する元素である。0.005%未満では変形能が乏しく衝撃吸収能が劣化するため、0.005%以上添加する。好ましくは0.01%以上である。一方、0.25%を超えると、炭化物への固溶量が増加して炭化物が溶解しにくくなり旧オーステナイトの粒径を3μmに制御できなくなるため、上限を0.25%とする。好ましくは0.22%以下である。
Mnは、固溶強化で強度の向上に寄与する元素である。0.5%未満では固溶強化能が乏しくマルテンサイトが軟らかくなり、2000MPa以上の引張強さを確保することが困難であるので、0.5%以上添加する。好ましくは0.7%以上である。一方、3.0%を超えて添加すると、炭化物への固溶量が増加して炭化物が溶解しにくくなり旧オーステナイトの粒径を3μm以下に制御できなくなるため、3.0%を上限とする。好ましくは、2.5%以下である。
Alは、溶鋼を脱酸して鋼を健全化する作用をなす元素である。0.0002%未満では、脱酸が十分で粗大な酸化物が生成して早期破断を引き起こすため、sol.Alは0.0002%以上とする。好ましくは0.0010%以上である。一方、3.0%を超えて添加すると、粗大な酸化物が生成し早期破断を引き起こすため、3.0%以下とする。好ましくは2.5%以下である。
Crは、固溶強化で強度の向上に寄与する元素である。0.05%未満では固溶強化能が乏しくマルテンサイトが軟らかくなり、2000MPa以上の引張強さを確保することが困難であるので、0.05%以上添加する。好ましくは0.1%以上である。一方、1.00%を超えて添加すると、炭化物への固溶量が増加して炭化物が溶解しにくくなり旧オーステナイトの粒径を3μm以下に制御できなくなるため、1.00%を上限とする。好ましくは、0.8%以下である。
Bは、固溶強化で強度の向上に寄与する元素である。0.0005%未満では固溶強化能が乏しくマルテンサイトが軟らかくなり、2000MPa以上の引張強さを確保することが困難であるので、0.0005%以上添加する。好ましくは0.0008%以上である。一方、0.010%を超えて添加すると、炭化物への固溶量が増加して炭化物が溶解しにくくなり旧オーステナイトの粒径を3μm以下に制御できなくなるため、0.010%を上限とする。好ましくは、0.007%以下である。
Nbは、旧オーステナイトの粒界に固溶して粒界の強度を上昇させる元素である。また、Nbは、粒界に固溶することでPの粒界偏析を阻害するため、粒界の脆化強度を向上させる。そのため、0.01%以上添加する。好ましくは0.030%以上である。一方、0.15%を超えて添加すると、炭化物として析出しやすくなり、粒界への固溶量が低下してしまうため0.15%以下とする。好ましくは0.12%以下である。
Moは、旧オーステナイトの粒界に固溶して粒界の強度を上昇させる元素である。また、Moは、粒界に固溶することでPの粒界偏析を阻害するため、粒界の脆化強度を向上させる。そのため、0.005以上添加する。好ましくは0.030%以上である。一方、1.00%を超えて添加すると、炭化物として析出しやすくなり、粒界への固溶量が低下してしまうため1.00%以下とする。好ましくは0.80%以下である。
Tiは、必須の元素ではないが、固溶強化で強度の向上に寄与する元素であるため、必要に応じて添加してもよい。Tiを添加する場合、添加の効果を得るためには、0.01%以上とするのが好ましい。好ましくは0.02%である。一方、0.15%を超えて添加すると、粗大な炭化物や窒化物を形成して早期破断を引き起こすため、0.15%以下とする。好ましくは0.12%以下である。
Niは、必須の元素ではないが、固溶強化で強度の向上に寄与する元素であるため、必要に応じて添加してもよい。Niを添加する場合、添加の効果を得るためには、0.01%以上とするのが好ましい。好ましくは0.02%である。一方、3.00%を超えて添加すると、鋼が脆くなり早期破断を引き起こすため、3.00%以下とする。好ましくは2.00%以下である。
Pは不純物元素であり、粒界に偏析しやすく、粒界の脆化強度を低下させる元素である。0.10%を超えると、粒界の脆化強度が著しく低下し、早期破断を引き起こすため、Pは0.10%以下とする。好ましくは0.050%以下である。下限は、特に限定しないが、0.0001%未満に低減すると、脱Pコストが大幅に上昇し、経済的に不利になるので、実用鋼板上、0.0001%が実質的な下限である。
Sは不純物元素であり、介在物を形成する元素である。0.10%を超えると、介在物が生成し早期破断を引き起こすため、Sは0.10%以下とする。好ましくは0.0050%以下である。下限は、特に限定しないが、0.0015%未満に低減すると、脱Sコストが大幅に上昇し、経済的に不利になるので、実用鋼板上、0.0015%が実質的な下限である。
Nは不純物元素であり、窒化物を形成して早期破断を引き起こすため、0.010%以下とする。好ましくは0.0075%以下である。下限は、特に限定しないが、0.0001%未満に低減すると、脱Nコストが大幅に上昇し、経済的に不利になるので、実用鋼板上、0.0001%が実質的な下限である。
次に、本発明に係るホットスタンプ成形体、およびホットスタンプ成形体の製造に用いるホットスタンプ用鋼板を得るための製造方法の形態を説明するが、本発明は、以下に説明するような形態に限定されない。
上述の化学組成を有する溶鋼を連続鋳造法により、鋼片(スラブ)にする。この連続鋳造工程では、単位時間当たりの溶鋼鋳込み量を6ton/分以下とすることが好ましい。連続鋳造時に溶鋼の単位時間あたりの鋳込み量(鋳込み速度)が6ton/分を超えると、Mnのミクロ偏析が増加するとともに、MoやNbを主体とする析出物の核生成量が増加してしまう。鋳込み量を5ton/分を以下とすることがさらに好ましい。鋳込み量の下限は特に限定されないが、操業コストの観点から、0.1ton/分以上であることが好ましい。
上述の鋼片を熱間圧延して鋼板とする。その際、式(2)で定義されるA3変態温度+10℃以上かつA3変態温度+200℃以下の温度域で熱間圧延を終了し、その際の最終段圧下率を12%以上とし、仕上げ圧延終了後から1秒以内に冷却を開始し、仕上げ圧延終了温度から550℃までの温度域を100℃/秒以上の冷却速度で冷却し、500℃未満の温度で巻き取る。
軟化層の表面上に、耐食性の向上等を目的として、めっき層を形成してもよい。めっき層は、電気めっき層及び溶融めっき層のいずれでもよい。電気めっき層としては、電気亜鉛めっき層、電気Zn−Ni合金めっき層等が例示される。溶融めっき層としては、溶融亜鉛めっき層、合金化溶融亜鉛めっき層、溶融アルミニウムめっき層、溶融Zn−Al合金めっき層、溶融Zn−Al−Mg合金めっき層、溶融Zn−Al−Mg−Si合金めっき層等が例示される。めっき層の付着量は、特に制限されず一般的な付着量でよい。
ホットスタンプ用鋼板の製造においては、その他、酸洗、冷間圧延、調質圧延等、公知の製法を含んでもよい。
Claims (2)
- 成分組成が、質量%で、
C :0.35%以上、0.75%以下、
Si:0.005%以上、0.25%以下、
Mn:0.5%以上、3.0%以下、
sol.Al:0.0002%以上、3.0%以下、
Cr:0.05%以上、1.00%以下、
B :0.0005%以上、0.010%以下、
Nb:0.01%以上、0.15%以下、
Mo:0.005%以上、1.00%以下、
Ti:0%以上、0.15%以下、
Ni:0%以上、3.00%以下、
P :0.10%以下、
S :0.10%以下、
N :0.010%以下
を含有し、残部がFe及び不可避的不純物であり、
ミクロ組織が、
旧オーステナイトを含み、さらに、
下部ベイナイト、マルテンサイト、及び焼戻しマルテンサイトの少なくとも1種を、面積率で90%以上含み、
前記旧オーステナイトの平均結晶粒径が3μm以下であり、
Z=(粒界におけるNb及びMoの1種又は2種の質量%)/(溶解時のNb及びMoの1種又は2種の質量%)で定義される粒界固溶比Zが0.3以上であり、
引張強度が2000MPa以上である
ことを特徴とするホットスタンプ成形体。 - めっき層を有することを特徴とする請求項1に記載のホットスタンプ成形体。
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