JP7482231B2 - 低炭素低コスト超高強度多相鋼板/鋼帯およびその製造方法 - Google Patents
低炭素低コスト超高強度多相鋼板/鋼帯およびその製造方法 Download PDFInfo
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- JP7482231B2 JP7482231B2 JP2022538801A JP2022538801A JP7482231B2 JP 7482231 B2 JP7482231 B2 JP 7482231B2 JP 2022538801 A JP2022538801 A JP 2022538801A JP 2022538801 A JP2022538801 A JP 2022538801A JP 7482231 B2 JP7482231 B2 JP 7482231B2
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- YOBAEOGBNPPUQV-UHFFFAOYSA-N iron;trihydrate Chemical compound O.O.O.[Fe].[Fe] YOBAEOGBNPPUQV-UHFFFAOYSA-N 0.000 description 2
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- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 1
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 1
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
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- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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Description
低コスト超高強多相鋼板/鋼帯であって、その成分重量百分比は、C:0.03~0.07%、Si:0.1~0.5%、Mn:1.3~1.9%、P≦0.02%、S≦0.01%、Al:0.01~0.05%、Cr:0.2~0.5%、さらにTi:0.07~0.14%、(Ni+Nb+Mo+V)<0.03%を含有し、残部は、Feと他の不可避不純物である;かつ同時に以下を満たす:
[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]<3.0;
(Mn+2Cr+4Ti+4Nb+4V+4Mo-Si/3+2C)≦3.0。
本発明にかかる鋼の成分設計において:
炭素(C):炭素は、鋼板/鋼帯の強度、溶接性、成形性、連続鋳造用薄スラブの製造性に直接影響する。炭素の含有量が多いほど、鋼板の強度を向上させることに寄与し、炭素含有量が0.03%より低い場合、鋼板/鋼帯の強度が目標要求に達しない;炭素含有量が0.07%より高い場合、鋼板/鋼帯の強度が高くなりやすく、穴拡げ率が要求に達しないことに繋がる。したがって、本発明には、炭素含有量の範囲を、0.03~0.07%に制御する。
(1)鋼板/鋼帯は、低合金コストを有することを確保するために、[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]<3.0;
(2)鋼板/鋼帯の微細組織には、一定量の炭素化物粒子を析出される、炭素化物を過剰に析出すること、過粗大、過凝集による穴拡げ率の低下を発生しないことを確保するために、(Mn+2Cr+4Ti+4Nb+4V+4Mo-0.5Si+5C)≦3.0。これにより、鋼板/鋼帯は、高い強度と穴拡げ特性を両立することができる。
1)製錬、連続鋳造
上記化学組成に従って製錬し、連続鋳造により鋳造スラブを鋳造し、連続鋳造中のスラブの冷却速度≧5℃/sである;
2)熱間圧延、圧延後の冷却
700℃以上の温度で、スラブを加熱炉に投入し、鋳造スラブを加熱し、加熱温度は1100~1250℃である;熱間圧延の最初、第二パスのパス毎の圧下率≧55%であり、仕上げ圧延・最終圧延の温度は、850~950℃である;
3)圧延後冷却、卷取り
圧延後に、水で冷却し、卷取り温度は550~630℃である;
4)酸洗。
1、常温力学特性:
引張強度≧780MPa、好ましくに≧800MPa;降伏強度≧680MPa、好ましくに≧710MPa;降伏強度比≧0.9。いくつの形態において、引張強度は、780-900MPaで、降伏強度は、680-830MPaである。
A50≧15%又はA5≧19%。
元の穴は抜き穴である場合の穴拡げ率は、>85%、好ましくに≧95%、最高限としては、100%以上になってもよく;一部の実施の形態において、穴拡げ率は、86%から110%までである;
元の穴はリーマ穴である場合の穴拡げ率は、>115%、好ましくに≧120%、最高限としては、130%以上になってもよく;一部の実施の形態において、穴拡げ率は、117%から140%までである;
4、曲げ特性:
180°冷間曲げ、d=0.5a合格。
1.本発明は、合金元素、特に貴金属合金元素の添加を抑えた低コストな組成設計を採用し、多相鋼に非常に低い合金化コストを確保するために、[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]≦3.0、(Nb+V+Mo+Ni)<0.03を要求する。多相鋼の一般的な合金元素の中では、ニオブとバナジウムの合金が最も高価で、グレードを考慮すると、マンガンの単価の20倍に達し、次いで、モリブデンとニッケルがグレードを考慮すると、マンガンの単価の10倍にも達するため、本発明に採用されない。チタン、アルミニウム、マンガン、クロムなどその他の合金元素については、添加量を最小限に抑え、全体のコストを低く抑えるように、最適な成分設計を選択する。
表1に示される異なる組成の鋼を製錬してから、表2に示されるように加熱+熱間圧延プロセスを実行し、厚さが4mm未満の鋼板を得た。長手方向に50mmゲージ長と5mmゲージ長の引張サンプルを採取し、降伏、引張強度および伸びを測定し,鋼板中央部に穴拡げ率と180°曲げ特性を測定した;試験データを表2に示す。ただし、穴拡げ率は、中央部に穴のある試料をパンチ金型でダイ金型に押し込み、板の穴縁部がくびれたり貫通亀裂が生じたりするまで、試料の中央部の穴を拡げるといった穴拡げ試験で測定した。試料中央部の元の穴の製造方法は穴拡げ率の計測結果に大きな影響を与えるため、抜き穴およびリーマ穴によってそれぞれ試料中央部の元の穴を製造し、後段の試験および計測方法は、ISO/DIS 16630規格に規定される穴広げ率の計測方法に沿って行われた。180°曲げ試験は、GB/T232-2010基準の曲げ性能の測定方法で行った。
Claims (13)
- 成分重量百分比は、C:0.03~0.07%、Si:0.1~0.5%、Mn:1.3~1.9%、P≦0.02%、S≦0.01%、Al:0.01~0.05%、Cr:0.2~0.5%、Ti:0.07~0.14%、(Ni+Nb+Mo+V)<0.03%を含有し、残部は、Feと他の不可避不純物である;かつ同時に以下を満たすことを特徴とする超高強多相鋼板/鋼帯であって、
[Mn+1.5Cr+5(Ti+Al+Cu)+10(Mo+Ni)+20(Nb+V)]≦3.0;
(Mn+2Cr+4Ti+4Nb+4V+4Mo-Si/3+2C)≦3.0、
前記鋼板/鋼帯の微細組織はフェライトおよび下部ベイナイトを含有し、フェライト含有量≦70%、フェライト+下部ベイナイト含有量≧90%であり、
前記鋼板/鋼帯の引張強度≧780MPa、降伏強度≧680MPa、伸び≧15%、降伏強度比≧0.9、元の穴が抜き穴である場合の穴拡げ率≧85%;元の穴がリーマ穴である場合の穴拡げ率≧115%;180°曲げ実験の角径が0.5板厚(d=0.5a)に等しい際に割れない、超高強多相鋼板/鋼帯。 - 重量百分比で、前記のC含有量は、0.04~0.06%であることを特徴とする請求項1に記載された超高強多相鋼板/鋼帯。
- 重量百分比で、前記のSi含有量は、0.1~0.27%であることを特徴とする請求項1に記載された超高強多相鋼板/鋼帯。
- 重量百分比で、前記のMn含有量は、1.45~1.75%であることを特徴とする請求項1に記載された超高強多相鋼板/鋼帯。
- 重量百分比で、前記のCr含有量は、0.35~0.50%であることを特徴とする請求項1に記載された超高強多相鋼板/鋼帯。
- 重量百分比で、前記の化学成分には、Nb+Mo+V<0.03%であることを特徴とする請求項1に記載された超高強多相鋼板/鋼帯。
- 前記微細組織は、さらに炭素化物析出相、介在物相及び/又は微量マルテンサイト相を含有することを特徴とする請求項1~6のいずれか一つに記載された超高強多相鋼板/鋼帯。
- 前記の鋼板/鋼帯の微細組織には、さらにTiN粒子を含有し、且つ単一粒子の最長辺の長さ<10μm又は面積<50μm2であることを特徴とする請求項1~7のいずれか一つに記載された超高強多相鋼板/鋼帯。
- フェライト晶粒平均直径<6μmで、又は粒度レベルASTMグレード判定>11.8であることを特徴とする請求項1~7のいずれか一つに記載された超高強多相鋼板/鋼帯。
- 以下のステップを含む、請求項1~9のいずれか一つに記載された超高強多相鋼板/鋼帯を製造する方法:
1)製錬、連続鋳造
請求項1~6のいずれか一つに記載された化学組成に従って製錬し、連続鋳造により鋳造スラブを鋳造し、連続鋳造中の冷却速度≧5℃/sである;
2)スラブ熱送、圧延、圧延後の冷却、卷取り
700℃以上の温度で、スラブを加熱炉に投入し、スラブを加熱し、加熱温度は1100~1250℃である;スラブの熱間圧延の最初二回のパスの圧下率≧55%である;仕上げ圧延・最終圧延の温度は、850~950℃である;卷取り温度は550~630℃である;
3)酸洗。 - ステップ3)の酸洗の後に、溶融亜鉛めっき焼鈍プロセスも含み、これによって、熱間圧延溶融亜鉛めっき鋼板完成品を得ることを特徴とする請求項10に記載された超高強多相鋼板/鋼帯を製造する方法。
- ステップ1)には、前記のスラブ鋳造状態組織では、柱状結晶の割合≦10%で、又は柱状結晶区域の厚み<40mmであることを特徴とする請求項10に記載された超高強多相鋼板/鋼帯を製造する方法。
- 前記の鋼板/鋼帯の厚みは、0.7~4.0mmであることを特徴とする請求項10に記載された超高強多相鋼板/鋼帯を製造する方法。
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KR20220115575A (ko) | 2022-08-17 |
AU2020416427A1 (en) | 2022-07-21 |
WO2021136352A1 (zh) | 2021-07-08 |
BR112022010497A2 (pt) | 2022-09-06 |
JP2023507528A (ja) | 2023-02-22 |
EP4086363A4 (en) | 2023-06-14 |
CN113122770B (zh) | 2022-06-28 |
US20230052592A1 (en) | 2023-02-16 |
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