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WO2023162571A1 - Tôle en acier, et procédé de fabrication de celle-ci - Google Patents

Tôle en acier, et procédé de fabrication de celle-ci Download PDF

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Publication number
WO2023162571A1
WO2023162571A1 PCT/JP2023/002491 JP2023002491W WO2023162571A1 WO 2023162571 A1 WO2023162571 A1 WO 2023162571A1 JP 2023002491 W JP2023002491 W JP 2023002491W WO 2023162571 A1 WO2023162571 A1 WO 2023162571A1
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WIPO (PCT)
Prior art keywords
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steel sheet
hardness
steel
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2023/002491
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English (en)
Japanese (ja)
Inventor
恭野 安田
和彦 塩谷
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to EP23759577.2A priority Critical patent/EP4458993A4/fr
Priority to US18/836,002 priority patent/US20250115972A1/en
Priority to CN202380020301.8A priority patent/CN118647744A/zh
Priority to JP2023523653A priority patent/JP7601218B2/ja
Priority to AU2023223720A priority patent/AU2023223720B2/en
Priority to KR1020247023941A priority patent/KR20240124991A/ko
Publication of WO2023162571A1 publication Critical patent/WO2023162571A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • 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
    • 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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
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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
    • C21D8/0263—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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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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    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/008—Martensite
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a high-strength steel sheet with excellent toughness and corrosion resistance, particularly suitable for structural members such as tanks used in a low-temperature, liquid-ammonia environment.
  • the present invention relates to a steel sheet for low temperature use and a method for manufacturing the same.
  • tanks may carry liquid ammonia as well as LPG.
  • hydrogen carriers for liquid ammonia and liquid ammonia fuel has been promoted, and thus the size of tanks for transportation and storage of liquefied ammonia has been increased.
  • ammonia SCC Stress Corrosion Cracking
  • Patent Documents 1 and 2 disclose techniques for satisfying the low-temperature toughness and the predetermined strength range required for liquefied gas storage tanks as described above.
  • high low-temperature toughness and predetermined strength properties are achieved by heat-treating a steel plate that has been cooled after hot-rolling, or by heat-treating a steel plate that has been water-cooled after hot-rolling several times. is realized.
  • Patent Literatures 1 and 2 above had the economic problem of requiring multiple heat treatments, which required high equipment and energy costs.
  • the present invention solves the above problems and provides a high-strength steel sheet with excellent ammonia SCC resistance and low-temperature toughness, which is used for storage tanks used for storing liquefied gas in energy transport ships, and a method for producing the same. for the purpose.
  • the present inventors used the TMCP process and an online induction heating device to extensively study various factors affecting the low-temperature toughness and strength characteristics of steel sheets.
  • the steel sheet contains a predetermined amount of elements such as C, Si, Mn, and Al, and the metal structure is controlled so that the volume fraction of the bainite structure at a position 0.5 mm from the surface of the steel sheet is 90% or more.
  • the average hardness is 230 HV0.1 or less
  • the variation in hardness is 30 HV0.1 or less
  • the maximum hardness in the thickness direction is the surface of the steel sheet
  • the present invention was made based on the above findings, and the gist of the present invention is as follows. 1. in % by mass, C: 0.010 to 0.200%, Si: 0.01 to 0.50%, Mn: 0.50-2.50%, Al: 0.010 to 0.060%, N: 0.0010% or more and 0.0100% or less, P: 0.020% or less, A steel sheet having a chemical composition containing S: 0.0100% or less and O: 0.0100% or less, with the balance being Fe and inevitable impurities, At a depth of 0.5 mm from the surface of the steel sheet, the average hardness is 230 HV0.1 or less, the hardness variation is 30 HV0.1 or less, and the maximum hardness in the thickness direction is the steel sheet.
  • the component composition further, in mass %, Cu: 0.01-0.50%, Ni: 0.01 to 2.00%, Cr: 0.01 to 1.00%, Sn: 0.01 to 0.50%, Sb: 0.01 to 0.50%, Mo: 0.01-0.50% and W: 0.01-1.00% 2.
  • the component composition further, in mass %, V: 0.01 to 1.00%, Ti: 0.005 to 0.100%, Co: 0.01 to 1.00%, Nb: 0.005 to 0.100%, B: 0.0001 to 0.0100%, Ca: 0.0005 to 0.0200%, Mg: 0.0005-0.0200% and REM: 0.0005-0.0200% 3.
  • V 0.01 to 1.00%
  • Ti 0.005 to 0.100%
  • Co 0.01 to 1.00%
  • Nb 0.005 to 0.100%
  • B 0.0001 to 0.0100%
  • Ca 0.0005 to 0.0200%
  • Mg 0.0005-0.0200%
  • REM 0.0005-0.0200% 3.
  • a method for producing a steel sheet comprising : In the accelerated cooling, the cooling stop temperature is in the range of 200 to 600 ° C., and the cooling rate at the 1/4 position of the plate thickness of the steel plate is 20 to 120 ° C./s, The reheating is performed until the temperature reached at a position 1/4 of the plate thickness of the steel plate is 500 ° C. or less, and the temperature reached at a depth of 0.5 mm from the surface of the steel plate is in the range of 400 to 680 ° C.
  • the steel plate manufacturing method.
  • the chemical composition of the steel material is further, in mass%, Cu: 0.01-0.50%, Ni: 0.01 to 2.00%, Cr: 0.01 to 1.00%, Sn: 0.01 to 0.50%, Sb: 0.01 to 0.50%, Mo: 0.01-0.50% and W: 0.01-1.00% 4.
  • the chemical composition of the steel material is further, in mass%, V: 0.01 to 1.00%, Ti: 0.005 to 0.100%, Co: 0.01 to 1.00%, Nb: 0.005 to 0.100%, B: 0.0001 to 0.0100%, Ca: 0.0005 to 0.0200%, 6.
  • a steel sheet having excellent low-temperature toughness that is, low-temperature impact resistance and ammonia SCC resistance, and having high strength suitable for structural members such as tanks used in a low-temperature and liquid ammonia environment.
  • a steel sheet having excellent low-temperature toughness that is, low-temperature impact resistance and ammonia SCC resistance, and having high strength suitable for structural members such as tanks used in a low-temperature and liquid ammonia environment.
  • % representing the content of the following components (elements) means “% by mass” unless otherwise specified.
  • C 0.010-0.200% C is the most effective element for increasing the strength of steel sheets produced by cooling according to the present invention.
  • the C content is specified to be 0.010% or more.
  • the C content is preferably 0.013% or more from the viewpoint of reducing the content of other alloying elements and manufacturing at a lower cost.
  • the C content is specified at 0.200% or less.
  • the C content is preferably 0.170% or less from the viewpoint of toughness and weldability.
  • Si 0.01-0.50% Si is added for deoxidation.
  • the Si content is specified to be 0.01% or more. Furthermore, it is preferable to make it 0.03% or more.
  • the Si content is specified to be 0.50% or less. Furthermore, the Si content is preferably 0.40% or less from the viewpoint of toughness and weldability.
  • Mn 0.50-2.50%
  • Mn is an element that has the effect of increasing the hardenability of steel, and is one of the important elements that need to be added in order to achieve high strength as in the present invention.
  • the Mn content is specified to be 0.50% or more.
  • the content of Mn is preferably 0.70% or more from the viewpoint of reducing the content of other alloying elements and manufacturing at a lower cost.
  • the Mn content is specified at 2.50% or less.
  • the Mn content is preferably 2.30% or less from the viewpoint of suppressing deterioration of toughness and weldability.
  • Al acts as a deoxidizing agent.
  • the Al content is specified to be 0.010% or more.
  • the Al content exceeds 0.060%, the oxide inclusions increase to lower the cleanliness and toughness. Therefore, the Al content is specified at 0.060% or less.
  • the Al content is preferably 0.050% or less from the viewpoint of further preventing toughness deterioration.
  • N 0.0010 to 0.0100% N contributes to the refinement of the structure and improves the toughness of the steel sheet.
  • the N content is specified to be 0.0010% or more. Preferably, it is 0.0020% or more.
  • the N content is specified at 0.0100% or less.
  • the N content is preferably 0.0080% or less from the viewpoint of further suppressing deterioration of toughness and weldability.
  • Ti when Ti is present, N can bond with Ti and precipitate as TiN.
  • P 0.020% or less
  • P has an adverse effect, such as lowering toughness and weldability, by segregating at grain boundaries. Therefore, it is desirable to make the P content as low as possible, but a P content of 0.020% or less is acceptable.
  • the lower limit of the P content is not particularly limited, and may be 0%. However, since P is an element that can industrially remain in steel, it may exceed 0%. Moreover, since excessive reduction causes a rise in refining cost, it is preferable to set the P content to 0.0005% or more from the viewpoint of cost.
  • S 0.0100% or less S is present in steel as sulfide-based inclusions such as MnS, and is an element that exerts adverse effects, such as deteriorating the toughness of the steel sheet by becoming the origin of fracture. Therefore, it is desirable that the S content be as low as possible, but a content of 0.0100% or less is permissible.
  • the lower limit of the S content is not particularly limited, and may be 0%. However, since S is an element that can industrially remain in steel, it may exceed 0%. Moreover, since an excessive reduction causes a rise in refining cost, it is preferable to set the S content to 0.0005% or more from the viewpoint of cost.
  • O 0.0100% or less
  • O is an element that forms an oxide, becomes a starting point of fracture, and has an adverse effect such as lowering the toughness of the steel sheet.
  • the O content is preferably 0.0050% or less, more preferably 0.0030% or less.
  • the lower limit of the O content is not particularly limited, and may be 0%. However, since O is an element that can industrially remain in steel, it may exceed 0%. Moreover, since an excessive reduction causes a rise in refining cost, it is preferable to set the O content to 0.0010% or more from the viewpoint of cost.
  • the balance other than the above components is Fe and unavoidable impurities.
  • the above component composition can contain the elements described below, if necessary.
  • Cu 0.01-0.50%, Ni: 0.01-2.00%, Cr: 0.01-1.00%, Sn: 0.01-0.50%, Sb: 0.01- 0.50%, Mo: 0.01 to 0.50%, and W: one or more selected from 0.01 to 1.00% Cu, Ni, Cr, Sn, Sb, Mo and W are It is an element that improves strength and ammonia SCC resistance, and one or more of these elements can be contained.
  • the Cu content is 0.01% or more, when Ni is contained, the Ni content is 0.01% or more, and when Cr is contained, When the Cr content is 0.01% or more, the Sn content is 0.01% or more when Sn is contained, and the Sb content is 0.01% or more when Sb is contained.
  • Mo is contained, the Mo content is preferably adjusted to 0.01% or more, and when W is contained, the W content is preferably adjusted to 0.01% or more.
  • an excessive Ni content causes deterioration of weldability and an increase in alloy cost.
  • the Cu content is 0.50% or less
  • the Ni content is 2.00% or less
  • the Cr content is 1.00% or less
  • the Sn content is 0.50% or less
  • the Sb content is It is preferable to adjust the Mo content to 0.50% or less
  • the W content is 0.50% or less
  • the W content is 1.00% or less.
  • the Cu content is 0.40% or less
  • the Ni content is 1.50% or less
  • the Cr content is 0.80% or less
  • the Sn content is 0.40% or less
  • the Sb content is The amount is adjusted to 0.40% or less
  • the Mo content to 0.40% or less
  • the W content to 0.80% or less.
  • V 0.01-1.00%
  • V is an element that has the effect of improving the strength of the steel sheet, and can be optionally added.
  • the V content is preferably 0.01% or more.
  • the V content is preferably 1.00% or less. More preferably, the lower limit of V content is 0.05% and the upper limit is 0.50%.
  • Ti 0.005-0.100%
  • Ti is an element that has a strong tendency to form nitrides and has the action of fixing N and reducing solid solution N, and can be added arbitrarily.
  • Ti can improve the toughness of the base material and the weld zone.
  • the Ti content is preferably 0.005% or more. Furthermore, it is more preferable to make it 0.007% or more.
  • the Ti content exceeds 0.100%, the toughness rather decreases. Therefore, when adding Ti, the Ti content is preferably 0.100% or less. Furthermore, the Ti content is more preferably 0.090% or less.
  • Co 0.01-1.00%
  • Co is an element that has the effect of improving the strength of the steel sheet, and can be optionally added.
  • the Co content is preferably 0.01% or more.
  • the Co content is preferably 1.00% or less. More preferably, the Co content has a lower limit of 0.05% and an upper limit of 0.50%.
  • Nb 0.005-0.100%
  • Nb is an element that has the effect of reducing the grain size of prior austenite and improving the toughness by precipitating as a carbonitride.
  • the Nb content is preferably 0.005% or more. Furthermore, it is more preferable to make it 0.007% or more.
  • the Nb content exceeds 0.100%, a large amount of NbC precipitates, resulting in a decrease in toughness. Therefore, when Nb is added, the Nb content is preferably 0.100% or less. Furthermore, it is more preferable to make it 0.060% or less.
  • B 0.0001 to 0.0100%
  • B is an element that has the effect of significantly improving hardenability even when added in a very small amount. That is, the strength of the steel sheet can be improved.
  • the B content is preferably 0.0001% or more.
  • the B content exceeds 0.0100%, the weldability deteriorates. Therefore, when B is added, the B content is preferably 0.0100% or less. More preferably, the B content has a lower limit of 0.0010% and an upper limit of 0.0030%.
  • Ca 0.0005-0.0200%
  • Ca is an element that binds to S and has the effect of suppressing the formation of MnS or the like elongated in the rolling direction. That is, by adding Ca, it is possible to control the morphology of the sulfide-based inclusions so that they exhibit a spherical shape, and improve the toughness of the weld zone and the like.
  • the Ca content is preferably 0.0005% or more.
  • the Ca content exceeds 0.0200%, the cleanliness of the steel is lowered. A decrease in cleanliness leads to a decrease in toughness. Therefore, when Ca is added, the Ca content is preferably 0.0200% or less. More preferably, the Ca content has a lower limit of 0.0020% and an upper limit of 0.0100%.
  • Mg: 0.0005-0.0200% Mg, like Ca is an element that binds to S and has the effect of suppressing the formation of MnS or the like elongated in the rolling direction. That is, by adding Mg, it is possible to control the morphology of the sulfide-based inclusions so that they exhibit a spherical shape, and improve the toughness of the weld zone and the like. In order to obtain such an effect, when Mg is added, the Mg content is preferably 0.0005% or more. On the other hand, when the Mg content exceeds 0.0200%, the cleanliness of the steel is lowered. A decrease in cleanliness leads to a decrease in toughness. Therefore, when Mg is added, the Mg content is preferably 0.0200% or less. More preferably, the Mg content has a lower limit of 0.0020% and an upper limit of 0.0100%.
  • REM 0.0005-0.0200%
  • REM rare earth metal
  • the REM content is preferably 0.0005% or more.
  • the REM content exceeds 0.0200%, the cleanliness of the steel deteriorates. A decrease in cleanliness leads to a decrease in toughness. Therefore, when REM is added, the REM content is preferably 0.0200% or less. More preferably, the REM content has a lower limit of 0.0020% and an upper limit of 0.0100%.
  • the steel sheet of the present invention has the above chemical composition, and in addition, the average The hardness is 230 HV0.1 or less, the variation in hardness at the 0.5 mm position is 30 HV0.1 or less, and the maximum hardness in the thickness direction is 1.0 mm or more from the surface of the steel sheet. 4 or less, and has a hardness characteristic in which the variation in hardness in the plate thickness direction is 70HV1 or less. Further, the steel sheet of the present invention has a metal structure in which the volume fraction of bainite structure (hereinafter also simply referred to as bainite) at the 0.5 mm position is 90% or more.
  • bainite volume fraction of bainite structure
  • the average hardness is 230HV0.1 or less, and the variation in hardness is 30HV0.1 or less
  • the average hardness is set to 230 HV0.1 or less
  • the variation in hardness is set to 30 HV0.1 or less.
  • the average hardness at the 0.5 mm position is 230 HV0.1 or less, and the hardness variation is 30 HV0.1 or less by adjusting the hardness characteristics.
  • the lower limit of the average hardness at the 0.5 mm position is not particularly limited, it is preferably about 130HV0.1.
  • the lower limit of the variation in hardness at the 0.5 mm position may be 0HV0.1, but industrially it is about 10HV0.1.
  • the average hardness can be calculated by measuring Vickers hardness at a plurality of points (for example, 100 points) at a position of 0.5 mm. Further, the variation in hardness means the standard deviation of the Vickers hardness measured to obtain the average hardness.
  • the maximum hardness in the plate thickness direction is located at a position of 1.0 mm or more and 1/4 or less of the plate thickness from the surface of the steel plate]
  • the maximum hardness of the steel sheet exists at a position distant from the surface to some extent, the hardness of only the surface layer can be reduced while maintaining the hardness of most of the steel sheet. That is, it is possible to ensure excellent ammonia SCC resistance while maintaining the strength of the steel sheet.
  • the maximum value is located at a position less than 1.0 mm from the surface of the steel sheet, the hardness at the 0.5 mm position cannot be sufficiently reduced.
  • the maximum value is at a position exceeding 1/4 of the plate thickness from the surface of the steel plate, the steel plate itself cannot ensure sufficient strength.
  • the maximum value of the hardness in the plate thickness direction is defined as being at a position of 1.0 mm or more and 1/4 or less of the plate thickness from the surface of the steel plate. .
  • the variation in hardness in the plate thickness direction is specified to be 70HV1 or less.
  • the variation is calculated by measuring the Vickers hardness (HV1) at a pitch of 0.5 mm in the plate thickness direction and obtaining the difference between the maximum value and the minimum value.
  • bainite includes a structure called bainitic ferrite or granular ferrite that transforms during or after accelerated cooling that contributes to transformation strengthening, and a structure obtained by tempering them.
  • the remaining structure occupying 10% or less in volume fraction may include a martensite structure in addition to the ferrite, pearlite, and austenite structures.
  • the fraction of each structure in the remaining structure is not particularly limited, but the remaining structure is preferably a pearlite structure.
  • the volume fraction of various metal structures can be measured by the method described in Examples below.
  • the manufacturing conditions of the steel material need not be particularly limited. It is preferable to use a steel material such as a slab of predetermined dimensions in the method. It should be noted that there is no problem in making a steel material such as a slab having a predetermined size by the ingot casting-decomposition rolling method.
  • the steel material thus obtained is directly hot-rolled without cooling or hot-rolled after reheating.
  • Hot rolling is performed with a rolling end temperature equal to or higher than the Ar 3 transformation point, then accelerated cooling from a cooling start temperature equal to or higher than the Ar 3 transformation point is performed under predetermined conditions, and then reheating is performed under predetermined conditions.
  • the heating temperature of the steel material is not particularly limited, but if the heating temperature is too low, the deformation resistance increases, the load on the hot rolling mill increases, and hot rolling may become difficult. On the other hand, if the temperature exceeds 1300° C., the oxidation becomes significant, the oxidation loss increases, and the yield increases. For these reasons, the heating temperature is preferably 950° C. or higher and 1300° C. or lower.
  • hot rolling [Rolling end temperature: Ar 3 transformation point or higher]
  • the rolling end temperature is set to the Ar 3 transformation point or higher.
  • the rolling end temperature is more preferably Ar 3 transformation point +10°C or higher.
  • the rolling end temperature exceeds 950°C, the structure may coarsen and the toughness may deteriorate, so the rolling end temperature is preferably 950°C or less.
  • each element indicates the content of the element in steel (% by mass).
  • the hot-rolled steel sheet is subjected to accelerated cooling from a cooling start temperature equal to or higher than the Ar 3 transformation point. If the cooling start temperature is less than the Ar 3 transformation point, ferrite is excessively formed and the cooling rate increases, so it coexists with the martensitic structure or bainite, which has a large difference in strength, resulting in insufficient strength and deterioration of toughness. is generated, and further the ammonia SCC resistance deteriorates. Therefore, the cooling start temperature should be the Ar 3 transformation point or higher.
  • the cooling rate at the 1/4 position of the plate thickness of the steel plate is specified to be 120° C./s or less.
  • the cooling rate can be increased by active cooling operation such as water cooling, and can be controlled by intermittently performing the cooling operation as appropriate (providing a period in which the cooling operation is stopped). .
  • the temperature in the thickness cross section The distribution, particularly the temperature at the 1/4 position of the plate thickness, can be obtained in real time.
  • cooling stop temperature 200 to 600°C
  • a predetermined accelerated cooling is performed to a cooling stop temperature arbitrarily set in the range of 200 to 600 ° C., so that ferrite and bainite are reduced to a predetermined volume ratio at the center of the plate thickness. It is possible to improve strength and toughness satisfactorily.
  • the cooling stop temperature is less than 200° C., the volume fraction of the island-shaped martensite structure becomes too large, resulting in a decrease in toughness.
  • the cooling stop temperature exceeds 600° C., ferrite and pearlite structures are excessively formed, resulting in insufficient strength and deterioration of toughness. Therefore, the cooling stop temperature is specified in the range of 200 to 600°C. Further, the cooling stop temperature in the present invention is the temperature at the 1/4 position of the plate thickness of the steel plate.
  • reheat [Attainment temperature at 0.5 mm position from the surface is 400 to 680 ° C.]
  • Accelerated cooling of a thick steel plate increases the cooling rate of the surface layer of the steel plate and cools the surface layer of the steel plate to a lower temperature than the inside of the steel plate. Therefore, a hard structure such as martensite is likely to form in the surface layer of the steel sheet, and the ammonia SCC resistance may be deteriorated. Therefore, in the present invention, the surface layer portion of the steel sheet is reheated after accelerated cooling. This is because the hardness of the surface layer portion can be reduced. Preferably, reheating is performed immediately after accelerated cooling.
  • the temperature reached at a position 0.5 mm from the surface during reheating after accelerated cooling is specified in the range of 400 to 680.degree.
  • induction heating it is preferable to use induction heating as the reheating means after accelerated cooling.
  • high-frequency induction heating so that the heating concentrates on the surface layer of the steel sheet.
  • cooling can be performed as appropriate. Cooling after reheating is not particularly limited, but in a thick steel plate having a thickness exceeding about 40 mm, the cooling rate becomes slow, and there is a concern that toughness is deteriorated due to agglomeration and coarsening of carbides. In such a case, water cooling or mist cooling may be performed after the reheating treatment.
  • the steel sheet thus obtained has excellent strength characteristics and toughness, and is excellent in ammonia SCC resistance.
  • the excellent strength characteristics are yield strength YS (yield point YP when there is a yield point, 0.2% yield strength ⁇ 0.2 when there is no yield point): 450 MPa or more, tensile strength (TS): 570 MPa or more and uniform elongation (uEl): 10% or more.
  • excellent toughness means that vTrs conforming to JIS Z 2241 is -30°C or less.
  • a steel sheet having these properties is the steel sheet of the present invention having excellent ammonia SCC resistance.
  • any item not described in this specification can be used by a conventional method.
  • a slab is formed by continuous casting of steel having the chemical composition shown in Table 1 (steel grades A to AI, the balance being Fe and unavoidable impurities), and hot rolling, accelerated cooling, and reheating are sequentially performed under the conditions shown in Table 2, Thick steel plates (No. 1 to 50) with a thickness of 30 mm were obtained.
  • the obtained steel sheet was subjected to measurement of the metal structure fraction at a position of 0.5 mm from the surface of the steel sheet, evaluation of hardness characteristics, evaluation of strength characteristics and toughness, and evaluation of ammonia SCC resistance. Each test method is as follows. These results are also shown in Table 2.
  • the determination when obtaining the fraction of the metal structure of the sample was performed as follows. That is, in the photographed images described above, the polygonal ferrite is discriminated as ferrite, and the bainite (Table 2 It was determined as B) in
  • HV0.1 Vickers hardness
  • the Vickers hardness (HV1) was measured in the plate thickness direction, and the position in the plate thickness direction (distance from the surface) where the maximum value exists was measured. Further, the difference between the maximum value and the minimum value of Vickers hardness (HV1) in such measurement was calculated and used as variation in hardness in the plate thickness direction.
  • Ammonia SCC resistance was evaluated by an accelerated test in which a four-point bending test was performed in a test solution and constant potential anodic electrolysis was performed to promote corrosion. Specifically, we performed the following steps: A test piece having a thickness of 5 mm ⁇ 15 mm ⁇ 115 mm was taken from the surface of the steel plate, subjected to ultrasonic degreasing in acetone for 5 minutes, and stress equal to the yield strength of each steel plate was applied by four-point bending.
  • the invention examples all have a yield strength YS of 450 MPa or more, a tensile strength TS of 570 MPa or more, and a uniform elongation uEl of 10% or more, vTrs is -30 ° C. or less, A steel sheet excellent in low-temperature toughness and ammonia SCC resistance is obtained.
  • the chemical composition of the steel is outside the range of the present invention, so the yield strength YS, tensile strength TS, toughness at low temperatures, or ammonia SCC resistance are inferior.
  • the chemical composition of the steel may be considered as the chemical composition of the steel sheet.

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Abstract

L'invention fournit une tôle en acier hautement résistante qui à son tour fournit un réservoir de stockage mis en œuvre dans le chargement d'un gaz liquéfié à bord d'un navire de transport d'énergie, et qui se révèle excellente en termes de résistance à la fissuration par corrosion sous contrainte provoquée par l'ammoniac et de résilience aux basses températures. La tôle en acier de l'invention présente une composition prédéfinie. Cette tôle en acier présente également des caractéristiques de dureté telles que la dureté moyenne en une position à 0,5mm de profondeur à partir de sa surface est inférieure ou égale à ２３０ＨＶ０,１, la variation de dureté est inférieure ou égale à ３０ＨＶ０, la valeur maximale de la dureté dans une direction épaisseur de tôle se trouve en une position à 1,0mm ou plus à partir de la surface à 1/4 ou moins de l'épaisseur de tôle, et la variation de dureté dans la direction épaisseur de tôle est inférieure ou égale à ７０ＨＶ１. Enfin, cette tôle en acier présente une structure métallique dans laquelle le rapport en volume d'une structure de bainite en une position à une profondeur de 0,5mm à partir de la surface, est supérieur ou égal à 90%.
PCT/JP2023/002491 2022-02-24 2023-01-26 Tôle en acier, et procédé de fabrication de celle-ci Ceased WO2023162571A1 (fr)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2025060169A1 (fr) * 2023-09-21 2025-03-27 南京钢铁股份有限公司 Acier de tôle navale à ductilité élevée de fh40-hd50 présentant une structure multiphase, et son procédé de préparation

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN120818747B (zh) * 2025-09-17 2025-11-18 鞍钢股份有限公司 一种350MPa级低屈强比抗冲击零部件用钢、制造方法及零部件渗碳处理方法

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008025014A (ja) * 2006-07-25 2008-02-07 Sumitomo Metal Ind Ltd Ｌｐｇ・アンモニア運搬船用タンクに用いられる鋼材
JP2013139630A (ja) * 2011-12-09 2013-07-18 Jfe Steel Corp 鋼板内の材質均一性に優れた耐サワーラインパイプ用高強度鋼板とその製造方法
WO2018181564A1 (fr) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de fabrication, et tuyau en acier haute résistance utilisant une tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
WO2018179512A1 (fr) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 Plaque d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de fabrication, et tuyau en acier haute résistance utilisant une plaque d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
WO2020067210A1 (fr) * 2018-09-28 2020-04-02 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de production, et tuyau en acier haute résistance utilisant une tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
WO2020067209A1 (fr) * 2018-09-28 2020-04-02 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de production, et tuyau en acier haute résistance utilisant une tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
JP2020193375A (ja) * 2019-05-29 2020-12-03 Ｊｆｅスチール株式会社 耐サワーラインパイプ用溶接鋼管及びその製造方法
JP2020193374A (ja) * 2019-05-29 2020-12-03 Ｊｆｅスチール株式会社 耐サワーラインパイプ用溶接鋼管及びその製造方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3802626B2 (ja) 1996-11-12 2006-07-26 新日本製鐵株式会社 溶接性および低温靭性の優れた低降伏比高張力鋼の製造方法
JP3848415B2 (ja) 1996-12-11 2006-11-22 新日本製鐵株式会社 溶接性および低温靭性の優れた低降伏比高張力鋼の製造方法
CA2977017C (fr) * 2015-03-31 2020-02-04 Jfe Steel Corporation Tole d'acier a resistance et tenacite elevees et procede pour la produire
CN112585290B (zh) * 2018-08-22 2022-05-24 杰富意钢铁株式会社 高强度钢板及其制造方法
WO2020080493A1 (fr) * 2018-10-17 2020-04-23 日本製鉄株式会社 Tôle d'acier et procédé de fabrication d'une tôle d'acier
WO2020137812A1 (fr) * 2018-12-26 2020-07-02 Ｊｆｅスチール株式会社 Acier pour environnements à hydrogène gazeux à haute pression, structure en acier pour environnements à hydrogène gazeux à haute pression et procédé de production d'acier pour environnements à hydrogène gazeux à haute pression
EP3943624B1 (fr) * 2019-03-22 2025-06-04 Nippon Steel Corporation Tôle d'acier à haute résistance et son procédé de production
KR102691589B1 (ko) * 2019-11-27 2024-08-05 제이에프이 스틸 가부시키가이샤 강판 및 그 제조 방법

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008025014A (ja) * 2006-07-25 2008-02-07 Sumitomo Metal Ind Ltd Ｌｐｇ・アンモニア運搬船用タンクに用いられる鋼材
JP2013139630A (ja) * 2011-12-09 2013-07-18 Jfe Steel Corp 鋼板内の材質均一性に優れた耐サワーラインパイプ用高強度鋼板とその製造方法
WO2018181564A1 (fr) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de fabrication, et tuyau en acier haute résistance utilisant une tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
WO2018179512A1 (fr) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 Plaque d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de fabrication, et tuyau en acier haute résistance utilisant une plaque d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
WO2020067210A1 (fr) * 2018-09-28 2020-04-02 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de production, et tuyau en acier haute résistance utilisant une tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
WO2020067209A1 (fr) * 2018-09-28 2020-04-02 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité, son procédé de production, et tuyau en acier haute résistance utilisant une tôle d'acier haute résistance pour tuyau de canalisation résistant à l'acidité
JP2020193375A (ja) * 2019-05-29 2020-12-03 Ｊｆｅスチール株式会社 耐サワーラインパイプ用溶接鋼管及びその製造方法
JP2020193374A (ja) * 2019-05-29 2020-12-03 Ｊｆｅスチール株式会社 耐サワーラインパイプ用溶接鋼管及びその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4458993A4 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2025060169A1 (fr) * 2023-09-21 2025-03-27 南京钢铁股份有限公司 Acier de tôle navale à ductilité élevée de fh40-hd50 présentant une structure multiphase, et son procédé de préparation

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AU2023223720A1 (en) 2024-06-20
AU2023223720B2 (en) 2025-09-18
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JP7601218B2 (ja) 2024-12-17
US20250115972A1 (en) 2025-04-10
EP4458993A1 (fr) 2024-11-06
TW202336240A (zh) 2023-09-16
TWI826257B (zh) 2023-12-11
JPWO2023162571A1 (fr) 2023-08-31
CN118647744A (zh) 2024-09-13

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