JP2016130355A - めっき性、加工性、および耐遅れ破壊特性に優れた高強度めっき鋼板、並びにその製造方法 - Google Patents
めっき性、加工性、および耐遅れ破壊特性に優れた高強度めっき鋼板、並びにその製造方法 Download PDFInfo
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- JP2016130355A JP2016130355A JP2015159212A JP2015159212A JP2016130355A JP 2016130355 A JP2016130355 A JP 2016130355A JP 2015159212 A JP2015159212 A JP 2015159212A JP 2015159212 A JP2015159212 A JP 2015159212A JP 2016130355 A JP2016130355 A JP 2016130355A
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- steel sheet
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- strength
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Classifications
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- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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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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- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- C—CHEMISTRY; METALLURGY
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C—ALLOYS
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22C—ALLOYS
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- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C—CHEMISTRY; METALLURGY
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Abstract
Description
(A)内部酸化層:SiおよびMnよりなる群から選択される少なくとも一種の酸化物を含む層である。内部酸化層の平均深さdは、4μm以上、後記する(B)に記載の軟質層の平均深さD未満である。
(B)軟質層:上記内部酸化層を含み、上記素地鋼板の板厚をtとしたとき、ビッカース硬さが、上記素地鋼板のt/4部におけるビッカース硬さの90%以下を満足する。軟質層の平均深さDは、20μm以上である。
(C)硬質層:マルテンサイトおよびベイナイト:60面積%以上95面積%未満と、ポリゴナルフェライト:5面積%超40面積%以下と、を含む組織で構成される。
まず、めっき層1と素地鋼板2の界面に直接接する部分は、平均深さdが4μm以上の内部酸化層3を有する。ここで、平均深さとは、上記界面からの平均深さを意味し、その詳細な測定方法は、後記する実施例の欄において図2を用いて説明する。
本発明において軟質層4は、図1に示すように、上記(A)の内部酸化層3の領域を含む層であって、且つ、ビッカース硬さが、素地鋼板2のt/4部におけるビッカース硬さの90%以下を満足するものである。上記ビッカース硬さの詳細な測定方法は、後記する実施例の欄で説明する。
本発明において硬質層は、図1に示すように、上記(B)の軟質層4の素地鋼板2側に形成され、且つ、マルテンサイトおよびベイナイト:60面積%以上95面積%未満と、ポリゴナルフェライト:5面積%超40面積%以下と、を含む組織で構成される。上記硬質層5のマルテンサイトは焼き戻しされていても良い。ベイナイトとマルテンサイトの合計面積率が多い程(すなわち、フェライトの面積率が少ない程)強度が向上し、ベイナイトとマルテンサイトの合計面積率が少ない程(すなわち、フェライトの面積率が多い程)延性が向上する傾向にある。また、フェライトの面積率が少なくなると強度と伸びのバランスが悪くなる。よって、これら組織の好ましい面積比率は、所望とする特性との関係を考慮して適宜設定することが推奨される。例えば強度向上の観点から、ベイナイトとマルテンサイトの合計面積率は80面積%以上、フェライトの合計面積率は20面積%以下であることが好ましい。また、強度と伸びのバランス向上を考慮すれば、ベイナイトとマルテンサイトの合計面積率は70面積%以下、フェライトの合計面積率は30面積%以上であることが好ましい。
Cは、焼入れ性を向上させ、またマルテンサイトの硬質化効果により、鋼の高強度化に重要な元素である。このような効果を有効に発揮させるため、C量の下限を0.05%以上とする。C量の好ましい下限は0.08%以上であり、より好ましくは0.10%以上である。しかし、Cを過剰に添加すると、軟質相と硬質相の硬度差が大きくなり、加工性および耐遅れ破壊特性が低下するため、C量の上限を0.25%とする。C量の好ましい上限は0.2%以下であり、より好ましくは0.18%以下である。
Siは固溶強化により鋼の強度を高め、加工性向上にも有効な元素である。また、内部酸化層を生成し、水素脆化の抑制作用も有する。このような効果を有効に発揮させるため、Si量の下限を0.25%以上とする。Si量の好ましい下限は0.3%以上であり、より好ましくは0.5%以上、更に好ましくは0.7%以上である。しかし、Siはフェライト生成元素であり、Siを過剰に添加すると、フェライトの生成を抑制できず、軟質相と硬質相の硬度差が大きくなり、加工性が低下する。更には、めっき性も悪くなるため、Si量の上限を3%とする。Si量の好ましい上限は2.5%以下であり、より好ましくは2.0%以下である。
Mnは、焼入れ性向上元素であり、フェライトおよびベイナイトを抑制し、マルテンサイトを生成させて高強度化に寄与する。このような効果を有効に発揮させるため、Mn量の下限を1.5%以上とする。Mn量の好ましい下限は1.8%以上であり、より好ましくは2.0%以上である。しかし、Mnを過剰に添加すると、めっき性が低下し、また偏析も著しくなる。更に、Pの粒界偏析を助長する虞がある。そのため、Mn量の上限を4%とする。Mn量の好ましい上限は3.5%以下である。
Pは、固溶強化元素として鋼の強化に有用な元素である。このような効果を有効に発揮させるため、P量の下限を0%超とする。しかし、過剰に添加すると、加工性のほか、溶接性、靱性を劣化させる虞があるため、その上限を0.1%以下とする。P量は少ない方が良く、好ましくは0.03%以下、より好ましくは0.015%以下である。
Sは、不可避的に含有する元素であり、MnSなどの硫化物を形成し、割れの起点なり、加工性を劣化させる虞がある。そのため、S量の上限を0.05%以下とする。S量は少ない方が良く、好ましくは0.01%以下、より好ましくは0.008%以下である。
Alは、脱酸剤として作用する。またAlはNと結合してAlNとなり、オーステナイト粒径の微細化により加工性および耐遅れ破壊特性も向上する。このような作用を有効に発揮させるため、Al量の下限を0.005%以上とする。Al量の好ましい下限は0.01%以上であり、より好ましくは0.02%以上である。しかし、Alを過剰に添加すると、アルミナなどの介在物が増加して加工性が劣化するほか、靱性も劣化するようになる。そのため、Al量の上限を1%とする。Al量の好ましい上限は0.8%以下であり、より好ましくは0.6%以下である。
Nは、不可避的に含有する元素であるが、過剰に含まれると加工性が劣化する。また、鋼中にB(ホウ素)を添加した場合には、BN析出物が生成し、Bによる焼入れ性向上作用を阻害するため、Nはできるだけ低減する方が良い。そのため、N量の上限を0.01%以下とする。N量の好ましい上限は0.008%以下であり、より好ましくは0.005%以下である。
これらの元素は、鋼板の強度上昇に有効な元素である。これらの元素は単独で添加しても良いし、二種以上を併用しても良い。
これらの元素は、組織微細化による加工性および耐遅れ破壊特性向上に有効な元素である。これらの元素は単独で添加しても良いし、二種以上を併用しても良い。
CuおよびNiは、高強度化に有効な元素である。これらの元素は単独で添加しても良いし、併用しても良い。
本発明に係る第一の製造方法は、熱延工程と、酸洗、冷延工程と、連続溶融Znめっきライン(CGL(Continuous Galvanizing Line))での酸化工程、還元工程、およびめっき工程とに大別される。そして本発明の特徴部分は、上記鋼中成分を満足する鋼板を、600℃以上の温度で巻取ることにより内部酸化層を形成した熱延鋼板を得る熱延工程と;内部酸化層の平均深さdが4μm以上残るように酸洗・冷間圧延する工程と;酸化帯にて、0.9〜1.4の空気比で酸化する工程と;還元帯にて、(Ac1点+50℃)〜(Ac3点+20℃)の範囲で保持して均熱する工程と;均熱後、冷却停止温度までの範囲を5℃/秒以上の平均冷却速度で冷却する工程と;を、この順序で含むところにある。
Ac1(℃)=723−10.7×[Mn]−16.9×[Ni]+29.1×[Si]+16.9×[Cr]+290×[As]+6.38×[W]・・・(i)
Ac3(℃)=910−203×[C]1/2−15.2×[Ni]+44.7×[Si]+104×[V]+31.5×[Mo]+13.1×[W]−{30×[Mn]+11×[Cr]+20×[Cu]−700×[P]−400×[Al]−120×[As]−400×[Ti]} ・・・(ii)
本発明に係る第二の製造方法は、上記鋼中成分を満足する熱延鋼板を、500℃以上の温度で巻取る熱延工程と;500℃以上の温度で80分以上保温する工程と;内部酸化層の平均深さdが4μm以上残るように酸洗・冷間圧延する工程と;酸化帯にて、0.9〜1.4の空気比で酸化する工程と;還元帯にて、(Ac1点+50℃)〜(Ac3点+20℃)の範囲で保持して均熱する工程と;均熱後、冷却停止温度までの範囲を5℃/秒以上の平均冷却速度で冷却する工程と;を、この順序で含むところに特徴がある。前述した第一の製造方法と対比すると、上記第二の製造方法では、熱延後巻取温度の下限を500℃以上にしたこと、熱延工程の後に保温工程を設けたことの二点でのみ上記第一の製造方法と相違する。よって、以下では、当該相違点のみ説明する。上記第一の製造方法と一致する工程は、上記第一の製造方法を参照すればよい。
酸洗液:10%塩酸、温度:82℃、酸洗時間:表2のとおり。
めっき鋼板の板幅をWとしたとき、W/4部からサイズ50mm×50mmの試験片を採取した後、グロー放電発光分析法[GD−OES(Glow Discharge−Optical Emission Spectroscopy)]にて、めっき層表面からのO量、Fe量、およびZn量をそれぞれ分析し、定量した。詳細には、堀場製作所製GD−PROFILER2型GDA750のGD−OES装置を用いて、上記試験片の表面を、Arグロー放電領域内で高周波スパッタリングし、スパッタされるO、Fe、Znの各元素のArプラズマ内における発光線を連続的に分光することによって、素地鋼板の深さ方向における各元素量プロファイル測定した。スパッタ条件は以下のとおりであり、測定領域は、めっき層表面から深さ50μmまでとした。
パルススパッタ周波数:50Hz
アノード径(分析面積):直径6mm
放電電力:30W
Arガス圧:2.5hPa
酸洗・冷間圧延後の素地鋼板を用いたこと以外は上記(1)と同様にして、内部酸化層の平均深さを算出した。
めっき鋼板の板幅W方向に対して垂直な断面であるW/4部を露出させ、サイズ20mm×20mmの試験片を採取した後、樹脂に埋め込み、めっき層と素地鋼板の界面から素地鋼板の板厚t内部に向かってビッカース硬さを測定した。測定はビッカース硬度計を用い、荷重3gfにて行った。詳細には図3に示すように、めっき層1と素地鋼板2の界面から板厚内部深さ10μmの測定位置から、板厚内部に向かって5μmピッチごとに測定を行い、深さ100μmまでビッカース硬さを測定した。測定点同士の間隔;すなわち図3中、×と×の距離は、最低でも15μm以上とした。各深さでn=1ずつビッカース硬さを測定し、板厚内部方向の硬さ分布を調査した。更に、素地鋼板のt/4部におけるビッカース硬さを、ビッカース硬度計を用いて荷重1kgfにて測定した(n=1)。素地鋼板のt/4部と比較してビッカース硬さが90%以下の領域を軟質層とし、その深さを計算した。同様の処理を、同じ試験片で10箇所実施し、その平均を軟質層の平均深さDとした。
めっき鋼板の板幅W方向に対して垂直な断面であるW/4部を露出させ、この断面を研磨し、更に電解研磨した後、ナイタールで腐食させたものをSEM(Scanning Electron Microscope)観察した。観察位置は素地鋼板の板厚をtとしたときt/4位置とし、観察倍率は2000倍、観察領域は40μm×40μmとした。SEMで撮影した金属組織写真を画像解析し、マルテンサイトとベイナイト(両者は区別せず)、およびフェライトの面積率を夫々測定した。表3中、α=フェライト、(B+M)=(ベイナイト+マルテンサイト)を意味する。また、表3中、「その他」の組織の面積分率は、100面積%から、マルテンサイトとベイナイト、およびフェライトの各面積率を引いて算出した。観察は任意に3視野について行い、平均値を算出した。
めっき鋼板の圧延方向に垂直な方向と試験片の長手方向が平行になるようにJIS 13号B引張試験片を採取し、JIS Z2241に従ってC方向の引張強度(TS)、降伏応力(YS)、および伸び(EL)を測定した。TSおよびYSより、降伏比YR(YS/TS)を算出した。
めっき鋼板の圧延方向に垂直な方向と試験片の長手方向が平行になるようにめっき鋼板から切り出した20mm×70mmの試験片を用意し、曲げ稜線が長手方向となるように90°V曲げ試験を行った。曲げ半径Rを適宜変化させて試験を実施し、試験片に割れが発生することなく曲げ加工できる最小曲げ半径Rminを求めた。
TSが1080MPa以上、1180MPa未満の場合、Rmin/t<2.5を合格
TSが1180MPa以上の場合、Rmin/t<3.2を合格
めっき鋼板の板幅W方向に対して垂直な断面であるW/4部を露出させ、150mm(W)×30mm(L)の試験片を切り出し、最小曲げ半径にてU曲げ加工を行った後、ボルトで締め付け、U曲げ加工試験片の外側表面に1000MPaの引張応力を負荷した。引張応力の測定は、U曲げ加工試験片の外側に歪ゲージを貼り付け、歪を引張応力に換算して行った。その後、U曲げ加工試験片のエッジ部をマスキングし、電気化学的に水素をチャージさせた。水素チャージは、試験片を、0.1M−H2SO4(pH=3)と0.01M−KSCNの混合溶液中に浸漬し、室温且つ100μA/mm2の定電流の条件で行
なった。
日本鉄鋼連盟規格JFST1001に準じて穴拡げ試験を実施し、λを測定した。詳細には、めっき鋼板に直径10mmの穴を打ち抜いた後、周囲を拘束した状態で60°円錐のポンチを穴に押し込み、亀裂発生限界における穴の直径を測定した。下記式から限界穴拡げ率λ(%)を求め、λが20%以上を合格、すなわち穴拡げ性に優れると評価した。限界穴拡げ率λ(%)={(Df−D0)/D0}×100
式中、Dfは亀裂発生限界における穴の直径(mm)、D0は初期穴の直径(mm)
めっき鋼板の外観を目視で観察し、不めっきの発生の有無に基づいてめっき性を評価した。
2 素地鋼板
3 内部酸化層
4 軟質層
5 硬質層
Claims (7)
- 素地鋼板の表面に、溶融亜鉛めっき層または合金化溶融亜鉛めっき層を有するめっき鋼板であって、
(1)前記素地鋼板は、質量%で、
C :0.05〜0.25%、
Si:0.25〜3%、
Mn:1.5〜4%、
P :0%超0.1%以下、
S :0%超0.05%以下、
Al:0.005〜1%、および
N :0%超0.01%以下を含有し、
残部が鉄および不可避不純物からなり、
(2)前記素地鋼板と前記めっき層との界面から素地鋼板側に向って順に、
SiおよびMnよりなる群から選択される少なくとも一種の酸化物を含む内部酸化層と、
前記内部酸化層を含む層であって、且つ、前記素地鋼板の板厚をtとしたとき、ビッカース硬さが、前記素地鋼板のt/4部におけるビッカース硬さの90%以下を満足する軟質層と、
マルテンサイトおよびベイナイト:60面積%以上95面積%未満と、ポリゴナルフェライト:5面積%超40面積%以下と、を含む硬質層と、
を有し、且つ、
前記軟質層の平均深さDが20μm以上、および
前記内部酸化層の平均深さdが4μm以上、前記D未満
を満足し、引張強度が980MPa以上である高強度めっき鋼板。 - 前記素地鋼板が、更に、質量%で、
Cr:0%超1%以下、
Mo:0%超1%以下、および
B :0%超0.01%以下よりなる群から選択される少なくとも一種を含有する請求項1に記載の高強度めっき鋼板。 - 前記素地鋼板が、更に、質量%で、
Ti:0%超0.2%以下、
Nb:0%超0.2%以下、および
V :0%超0.2%以下よりなる群から選択される少なくとも一種を含有する請求項1または2に記載の高強度めっき鋼板。 - 前記素地鋼板が、更に、質量%で、
Cu:0%超1%以下、および
Ni:0%超1%以下よりなる群から選択される少なくとも一種を含有する請求項1〜3のいずれかに記載の高強度めっき鋼板。 - 前記内部酸化層の平均深さdと前記軟質層の平均深さDは、D>2dの関係を満足する請求項1〜4のいずれかに記載の高強度めっき鋼板。
- 請求項1〜5のいずれかに記載の高強度めっき鋼板を製造する方法であって、
前記素地鋼板の鋼中成分を満足する鋼板を、600℃以上の温度で巻取る熱延工程と、
内部酸化層の平均深さdが4μm以上残るように酸洗・冷間圧延する工程と、
酸化帯にて、0.9〜1.4の空気比で酸化する工程と、
還元帯にて、(Ac1点+50℃)〜(Ac3点+20℃)の範囲で保持して均熱する工程と、
均熱後、冷却停止温度までの範囲を5℃/秒以上の平均冷却速度で冷却する工程と、
を、この順序で含む高強度めっき鋼板の製造方法。 - 請求項1〜5のいずれかに記載の高強度めっき鋼板を製造する方法であって、
前記素地鋼板の鋼中成分を満足する鋼板を、500℃以上の温度で巻取る熱延工程と、
500℃以上の温度で80分以上保温する工程と、
内部酸化層の平均深さdが4μm以上残るように酸洗・冷間圧延する工程と、
酸化帯にて、0.9〜1.4の空気比で酸化する工程と、
還元帯にて、(Ac1点+50℃)〜(Ac3点+20℃)の範囲で保持して均熱する工程と、
均熱後、冷却停止温度までの範囲を5℃/秒以上の平均冷却速度で冷却する工程と、
を、この順序で含む高強度めっき鋼板の製造方法。
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WO2021251276A1 (ja) | 2020-06-08 | 2021-12-16 | 日本製鉄株式会社 | 鋼板及びその製造方法 |
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EP3584344A4 (en) | 2017-02-20 | 2020-08-05 | Nippon Steel Corporation | HIGH RESISTANCE STEEL SHEET |
WO2020162556A1 (ja) * | 2019-02-06 | 2020-08-13 | 日本製鉄株式会社 | 溶融亜鉛めっき鋼板およびその製造方法 |
KR102231344B1 (ko) * | 2019-05-17 | 2021-03-24 | 주식회사 포스코 | 구멍확장성 및 연성이 우수한 초고강도 강판 및 이의 제조방법 |
EP4108799A4 (en) * | 2020-02-18 | 2023-08-02 | Posco | STEEL SHEET WITH EXCELLENT SURFACE QUALITY AND PROCESS FOR ITS PRODUCTION |
WO2021176249A1 (en) * | 2020-03-02 | 2021-09-10 | Arcelormittal | High strength cold rolled and galvannealed steel sheet and manufacturing process thereof |
CN113789482A (zh) * | 2021-09-01 | 2021-12-14 | 安徽金亿新材料股份有限公司 | 一种高吸能嫦娥钢、气门座圈及其制备方法 |
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