KR840007899A - Low alloy steel sheet and manufacturing method - Google Patents

Low alloy steel sheet and manufacturing method Download PDF

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KR840007899A
KR840007899A KR1019840001338A KR840001338A KR840007899A KR 840007899 A KR840007899 A KR 840007899A KR 1019840001338 A KR1019840001338 A KR 1019840001338A KR 840001338 A KR840001338 A KR 840001338A KR 840007899 A KR840007899 A KR 840007899A
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steel sheet
low alloy
alloy steel
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copper
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제이 제시맨 라드니
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원본미기재
암코 인코포레이팃드
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • 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
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

내용 없음.No content.

Description

저합금 강판과 그 제조방법Low alloy steel sheet and manufacturing method

본 내용은 요부공개 건이므로 전문내용을 수록하지 않았음Since this is an open matter, no full text was included.

제1도는 ASTM A710 등급A의 본 발명 강철과 거의 몰리브덴을 함유치 않은 유사한 강철에 있어서 인장 특성대판 두께의 도표비교이다.FIG. 1 is a graphical comparison of tensile properties plate thickness for the inventive steels of ASTM A710 grade A and similar steels containing almost no molybdenum.

제2도는 ASTM A710 등급 A의 본 발명 강철과, 거의 몰리브덴을 함유치 않은 유사한 강철에 있어서 연성 취성전이온도 대 판 두께의 도표 비교이다.FIG. 2 is a graphical comparison of ductile brittle transition temperature vs. plate thickness for the inventive steels of ASTM A710 class A and similar steels containing almost no molybdenum.

제3도 및 4도는 본 발명 강철의 고온 압연판의 배율 200현미경 도표이다.3 and 4 are magnification 200 micrographs of a hot rolled sheet of steel of the present invention.

Claims (14)

용접물의 열작용 구역에서 보유된 인성을 포함하는 우수한 용접성과 함께, 고온 수축된 조건에서 실내 온도로 적어도 56㎏/㎟의 항복강도와 -46℃에서 적어도 27주울의 종방향 샤르피 V노치충격강도를 나타내는 적어도 4.8m 두께의 저합금강판을 제조하는 방법에 있어서, 중량 백분율로 탄소 약 0.02-0.07%, 망간 1.2-2.0%, 황 최대 0.020%, 규소 0.5% 미만, 몰리브덴 0.1-0.4%, 니오브 0.01-0.1%, 산용해성 알루미늄 0.01-0.10%, 구리 약 0.8-2.0%, 니켈 약 0.4-2.0%, 잉여 크롬, 그리고 우연한 불순물을 제외한 나머지 철로 필수 구성되는 강철 시발 물질을 제공하고 ; 오오스테나이트의 실질적인 재결정화를 피하고 주로 크게 변형된 오오스테나이트상을 얻도록, 약 760-927℃의 온도 범위 내에서 적어도 3090의 총두께 수축을 갖게 상기 시발 물질을 원하는 최종 두께로 열 수축시키고 ; 상기 오오스테나이트상을 주로 미세한 바늘상 페라이트와 하부 베이나이트상으로 변형하는 속도로 냉각하는 ; 단계들을 특징으로 하는 저합금 강판 제조방법.Exhibits a yield strength of at least 56 kg / mm2 at room temperature and a longitudinal Charpy V notch impact strength of at least 27 joules at -46 ° C, with good weldability including toughness retained in the thermal zone of the weldment. A method for producing a low alloy steel sheet having a thickness of at least 4.8 m, wherein the weight percentage is about 0.02-0.07% carbon, 1.2-2.0% manganese, up to 0.020% sulfur, less than 0.5% silicon, 0.1-0.4% molybdenum, 0.01-0.05 Providing a steel starting material consisting essentially of iron excluding 0.1%, 0.01-0.10% acid soluble aluminum, about 0.8-2.0% copper, about 0.4-2.0% nickel, excess chromium, and accidental impurities; Heat shrinking the starting material to the desired final thickness with a total thickness shrinkage of at least 3090 within a temperature range of about 760-927 ° C. to avoid substantial recrystallization of the austenite and to obtain a predominantly modified austenite phase. ; Cooling the austenite phase to a rate mainly transforming into fine needle-like ferrite and lower bainite phase; A low alloy steel sheet manufacturing method characterized by the steps. 제1항에 있어서, 상기 총 두께 수축은 760-871℃의 온도 범위내에서 적어도 50%인 방법.The method of claim 1, wherein the total thickness shrinkage is at least 50% within a temperature range of 760-871 ° C. 제1항에 있어서, 실대온도에서 적어도 60㎏/㎟의 항복강도와 -46℃에서 적어도 27주울의 종방향 샤르피 V 노치 충격강도를 갖는 강판을 얻기 위해 약 482℃와 ACI 점 사이의 범위내에서 가열하므로서 침전경화하는 단계를 더 포함하는 방법.The method of claim 1, wherein the steel sheet has a yield strength of at least 60 kg / mm 2 at ambient temperature and a longitudinal Charpy V notch impact strength of at least 27 joules at −46 ° C., within a range between about 482 ° C. and the ACI point. The method further comprises the step of curing the precipitation by heating. 제3항에 있어서, 상기 침전 경화는 약 538-649℃ 사이의 범위내에서 가열하는 것을 포함하는 방법.The method of claim 3, wherein the precipitation curing comprises heating within a range between about 538-649 ° C. 5. 제1항에 있어서, 상기 강철 시발물질은 필수적으로 탄소 약 0.03-0.05%, 망간 1.3-1.65%, 황 최대 0.001%, 규소 약 0.15-0.40%, 몰리브덴 약 0.15-0.30%, 니오브 약 0.02-0.05%, 산용해성 알루미늄 약 0.02-0.06%, 구리 약 1.0-1.3%, 니켈 약 0.7-1.0%, 크롬 0.25% 이하, 그리고 우연한 불순물을 제외한 나머지 철로 구성되는 방법.The method of claim 1, wherein the steel starting material is essentially about 0.03-0.05% carbon, 1.3-1.65% manganese, up to 0.001% sulfur, about 0.15-0.40% silicon, about 0.15-0.30% molybdenum, about 0.02-0.05 niobium %, About 0.02-0.06% of acid-soluble aluminum, about 1.0-1.3% copper, about 0.7-1.0% nickel, 0.25% or less chromium, and the rest of iron except accidental impurities. 용접물의 열 작용 지역에 보유된 인성을 포함하여 우수한 용접성과 함께, 오오스테나이트되고, 담금질되고 침전 경화된 조건에서 실내온도로 적어도 56㎏/㎟의 항복강도와, -62℃에서 적어도 68주울의 종방향 샤르피 V노치 충격강도를 나타내는 적어도 4.8m 두께의 저합금 강판을 제조하는 방법에 있어서, 중량 백분율로 탄소 약 0.02-0.07%, 망간 1.2-2.0%, 황 최대 0.020%, 규소 0.5% 미만, 몰리브덴 0.1-0.4%, 니오브 0.01-0.1%, 산용해성 알루미늄 약 0.01-0.10%, 구리 0.8-2.0%, 니켈 0.4-2.0%, 잉여 크롬, 그리고 우연한 불순물을 제외한 나머지 철로 필수 구성되는 강철시발 물질을 제공하고 ; 상기 시발 물질을 소기의 최종 두께로 고온 수축하고 ; 강철이 페라이트로 바뀌는 온도로 냉각하고 ; 상기 페라이트를 오오스테나이트로 바꾸도록 오오스테나이트화 범위내에서 그리고 약 871-982℃의 온도로 열수축된 판을 재가열하고 ; 실질적으로 상기 모든 오오스테나이트를 주로 미세한 바늘상 페라이트와 하부 베이나이트상으로 변형하고, 구리 풍부한 입자들의 실질적인 침전을 피하는 범위에서 담금질하고 ; 약 482℃와 ACI점 사이의 범위내에서 가열하여 침전경화하는 ; 단계들을 특징으로 하는 저합금 강판 제조방법.Yield strength of at least 56 kg / mm2 at room temperature under austenitic, quenched and precipitation hardened conditions, with good weldability including toughness retained in the thermally active zone of the weldment, and at least 68 joules at -62 ° C. A method of making at least 4.8 m thick low alloy steel sheet exhibiting longitudinal Charpy V notch impact strength, wherein the weight percentage is about 0.02-0.07% carbon, 1.2-2.0% manganese, 0.020% sulfur, less than 0.5% silicon, Steel starting materials consisting essentially of iron other than molybdenum 0.1-0.4%, niobium 0.01-0.1%, acid-soluble aluminum about 0.01-0.10%, copper 0.8-2.0%, nickel 0.4-2.0%, excess chromium, and accidental impurities To provide; Hot shrinking the starting material to the desired final thickness; Cooling to the temperature at which the steel turns to ferrite; Reheat the heat-shrinkable plate within the austenitization range and at a temperature of about 871-982 ° C. to convert the ferrite into austenite; Substantially transforming all of the austenite into mainly fine needle-like ferrites and lower bainite phases and quenching in a range that avoids substantial precipitation of copper rich particles; Precipitation hardening by heating within a range between about 482 ° C. and an ACI point; A low alloy steel sheet manufacturing method characterized by the steps. 제6항에 있어서, 상기 고온 수축된 강판은 약 899-927℃의 온도로 재가열도고, 상기 침전 경화는 약 538-649℃ 범위 내에서 가열하는 것으로 구성되는 방법.The method of claim 6, wherein the hot shrinked steel sheet is reheated to a temperature of about 899-927 ° C., and the precipitation hardening consists of heating within a range of about 538-649 ° C. 8. 제6항에 있어서, 상기 강철은, 탄소 약 0.03-0.05%, 망간 약 1.3-1.65%, 황 최대 약 0.01%, 규소 약 0.15-0.40%, 몰리브덴 약 0.15-0.30%, 니오브 약 0.02-0.05%, 산용해성 알루미늄 약 0.02-0.06%, 구리 약 1.0-1.3%, 니켈 약 0.7-1.0%, 크롬 0.25% 미만, 그리고 우연한 불순물을 제외한 나머지 철로 필수 구성되는 방법.The method of claim 6, wherein the steel is about 0.03-0.05% carbon, about 1.3-1.65% manganese, about 0.01% sulfur maximum, about 0.15-0.40% silicon, about 0.15-0.30% molybdenum, about 0.02-0.05% niobium Consisting of about 0.02-0.06% acid soluble aluminum, about 1.0-1.3% copper, about 0.7-1.0% nickel, less than 0.25% chromium, and iron, excluding accidental impurities. 제6항에 있어서, 사기 고온 수축단계는 약 760-927℃의 온도범위내에서 적어도 30%의 두께 수축을 포함하고, 그리하여 오오스테나이트의 실질적인 재결정화를 피하고, 주로 크게 변형된 오오스테나이트상을 얻는 방법.The method according to claim 6, wherein the high temperature shrinkage step comprises at least 30% thickness shrinkage within a temperature range of about 760-927 ° C., thus avoiding substantial recrystallization of the austenite, mainly with a largely deformed austenite phase. How to get it. 용접물의 열 작용구역에서 보유된 인성을 포함하여 우수한 용접성과 함께, 고온 수축된 조건에서 실내온도로 적어도 56㎏/㎟의 항복강도와, -46℃에서 적어도 27주울의 종방향 샤르피 V노치 충격강도를 나타대는 적어도 4.8m 두께의 저합금 강판에 있어서, 상기 강철은 중량 백분율로 탄소 약 0.02-0.07%, 망간 1.2-2.0%, 황 최대 0.020%, 규소 0.5% 미만, 몰리브덴 0.1-0.4%, 니오브 0.01-0.1%, 산용해성 알루미늄 약 0.01-0.10%, 구리 약 0.8-2.0%, 니켈 약 0.4-2.0%, 잉여 크롬 그리고 우연인 불순물을 제외한 나머지 철로 필수 구성되고, 주로 바늘상 페라이트 및 하부 베이나이트 현미경 조직이 특징인 저합금 강판.Yield strength of at least 56 kg / mm2 at room temperature, and longitudinal Charpy V notch impact strength of at least 27 joules at -46 ° C, with good weldability including toughness retained in the thermal zone of the weldment. In a low alloy steel sheet having a thickness of at least 4.8 m, the steel has a weight percentage of about 0.02-0.07% carbon, 1.2-2.0% manganese, up to 0.020% sulfur, less than 0.5% silicon, 0.1-0.4% molybdenum, and niobium. Essentially 0.01-0.1%, acid-soluble aluminum about 0.01-0.10%, copper about 0.8-2.0%, nickel about 0.4-2.0%, excess chromium and iron other than incidental impurities, mainly needle-like ferrite and lower bainite Low alloy steel plate characterized by microscopic structure. 제10항에 있어서, 상기 강철은, 탄소 약 0.03-0.05%, 망간 약 1.3-1.65%, 황 최대 2.01%, 규소 약 0.15-0.40%, 몰리브덴 약 0.15-0.30%, 니오브 약 0.02-0.05%, 산수용성 알루미늄, 약 0.02-0.06%, 구리 약 1.0-1.3%, 니켈 0.7-1.0%, 크롬 0.25% 미만, 나머지 철로 필수 구성되는 저합금 강판.The method of claim 10, wherein the steel comprises about 0.03-0.05% carbon, about 1.3-1.65% manganese, up to 2.01% sulfur, about 0.15-0.40% silicon, about 0.15-0.30% molybdenum, about 0.02-0.05% niobium, Low alloy steel sheet consisting essentially of acid-soluble aluminum, about 0.02-0.06%, copper about 1.0-1.3%, nickel 0.7-1.0%, chromium less than 0.25% and the remaining iron. 제10항에 있어서, 침전 경화된 조건에서 실대온도로 적어도 60㎏/㎟의 항복강도가 특징인 저합금 강판.The low alloy steel sheet of claim 10 characterized by a yield strength of at least 60 kg / mm 2 at actual temperature under precipitation hardened conditions. 제10항에 있어서, 오오스테나이트화, 담금질 및 침전경화 후에 -62℃에서 적어도 68주울의 종방향 샤르피 V 노치 충격강도가 특징인 저합금 강판.The low alloy steel sheet of claim 10 characterized by a longitudinal Charpy V notch impact strength of at least 68 joules at −62 ° C. after austenitization, quenching and precipitation hardening. 제10항에 있어서, 적어도 50mm 이하의 두께를 갖는 고온압연된 판의 형태인 저합금 강판.The low alloy steel sheet of claim 10 in the form of a hot rolled plate having a thickness of at least 50 mm or less. ※참고사항 : 최초출원 내용에 의하여 공개하는 것임.※ Note: It is to be disclosed based on the initial application.
KR1019840001338A 1983-03-17 1984-03-16 Low alloy steel sheet and manufacturing method KR840007899A (en)

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Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0288054B1 (en) * 1987-04-24 1993-08-11 Nippon Steel Corporation Method of producing steel plate with good low-temperature toughness
DE4033700C1 (en) * 1990-10-19 1992-02-06 Stahlwerke Peine-Salzgitter Ag, 3150 Peine, De
JP2634961B2 (en) * 1991-03-06 1997-07-30 新日本製鐵株式会社 Manufacturing method of 80kgf / mm2 class high strength steel with excellent weldability
CH687879A5 (en) * 1993-12-01 1997-03-14 Met Cnam Paris Max Willy Tisch Reinforcement, machine, apparatus and Metallbaustaehle in fines Dumaguete with stable anticorrosive coating.
WO1996017099A1 (en) * 1994-11-28 1996-06-06 Tischhauser Max Willy Process for producing high quality, close-grained structural steel with a stable anticorrosive layer for metal structures apparatus, machines and armouring
US6264767B1 (en) 1995-06-07 2001-07-24 Ipsco Enterprises Inc. Method of producing martensite-or bainite-rich steel using steckel mill and controlled cooling
US5810951A (en) * 1995-06-07 1998-09-22 Ipsco Enterprises Inc. Steckel mill/on-line accelerated cooling combination
US6309482B1 (en) 1996-01-31 2001-10-30 Jonathan Dorricott Steckel mill/on-line controlled cooling combination
CN100335670C (en) 2002-02-07 2007-09-05 杰富意钢铁株式会社 High strength steel plate and method for production thereof
MY157870A (en) * 2007-05-06 2016-07-29 Bluescope Steel Ltd A thin cast strip product with microalloy additions, and method for making the same
CN115838904A (en) * 2022-12-20 2023-03-24 衡阳华菱钢管有限公司 Method for manufacturing 850 MPa-grade high-strength high-toughness seamless steel pipe

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3539404A (en) * 1967-05-15 1970-11-10 Youngstown Sheet And Tube Co Method of making a low alloy steel
US3726723A (en) * 1970-05-11 1973-04-10 American Metal Climax Inc Hot-rolled low alloy steels
CA952415A (en) * 1970-05-20 1974-08-06 Eiji Miyoshi Process and apparatus for manufacture of strong tough steel plates
JPS5215523B1 (en) * 1970-11-18 1977-04-30
GB1436846A (en) * 1973-03-16 1976-05-26 Int Nickel Ltd Steels
CA988751A (en) * 1974-07-22 1976-05-11 Madhavarao Krishnadev Extra low-carbon copper-manganese - columbium high strength steel
US3955971A (en) * 1974-12-11 1976-05-11 United States Steel Corporation Alloy steel for arctic service
JPS5933168B2 (en) * 1977-06-10 1984-08-14 新日本製鐵株式会社 Manufacturing method for high-strength, high-toughness special-shaped steel pipes
JPS6017806B2 (en) * 1977-06-10 1985-05-07 新日本製鐵株式会社 Manufacturing method for specially shaped steel pipes with excellent toughness
JPS5421917A (en) * 1977-07-20 1979-02-19 Nippon Kokan Kk <Nkk> Method of manufacturing non-quenched high-tensile steel having high toughness

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EP0123406A2 (en) 1984-10-31
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ES530726A0 (en) 1985-03-01
CA1207639A (en) 1986-07-15
JPS605822A (en) 1985-01-12
BR8401222A (en) 1984-10-23

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