WO2018105510A1 - Tôle d'acier à haute teneur en mn et procédé de production de celle-ci - Google Patents

Tôle d'acier à haute teneur en mn et procédé de production de celle-ci Download PDF

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WO2018105510A1
WO2018105510A1 PCT/JP2017/043245 JP2017043245W WO2018105510A1 WO 2018105510 A1 WO2018105510 A1 WO 2018105510A1 JP 2017043245 W JP2017043245 W JP 2017043245W WO 2018105510 A1 WO2018105510 A1 WO 2018105510A1
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steel sheet
temperature
steel
less
austenite
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PCT/JP2017/043245
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English (en)
Japanese (ja)
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植田　圭治
長谷　和邦
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Ｊｆｅスチール株式会社
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=62490939&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2018105510(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to EP17879107.5A priority Critical patent/EP3553195B1/fr
Priority to BR112019010870-0A priority patent/BR112019010870B1/pt
Priority to CN201780075814.3A priority patent/CN110050082B/zh
Priority to JP2018512637A priority patent/JP6418358B1/ja
Priority to KR1020197015408A priority patent/KR20190077470A/ko
Priority to KR1020217017558A priority patent/KR102309644B1/ko
Publication of WO2018105510A1 publication Critical patent/WO2018105510A1/fr
Priority to PH12019501270A priority patent/PH12019501270A1/en

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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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • 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
    • C21D8/0247—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
    • 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
    • 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
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C22C38/18—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
    • 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
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a high Mn steel sheet suitable for structural steel used in a cryogenic environment, such as a tank for a liquefied gas storage tank, and particularly excellent in stress corrosion cracking resistance in a salt water corrosive environment and a method for producing the same. .
  • Patent Document 1 discloses that when Mn is 15 to 35%, Cu is 5% or less, and C and Cr are added in appropriate amounts, the machinability and Charpy impact characteristics at ⁇ 196 ° C. of the heat and heat affected zone are shown. A steel material with improved is disclosed.
  • Patent Document 2 C: 0.25 to 0.75%, Si: 0.05 to 1.0%, Mn: more than 20% and 35% or less, Ni: 0.1% or more and 7.0 %, And Cr: 0.1% or more and less than 8.0% is added, and a high Mn steel material with improved low temperature toughness is disclosed.
  • Patent Documents 1 and 2 are intended to have strength and low-temperature toughness, and the Charpy impact characteristics at ⁇ 196 ° C. in the heat and heat affected zone are 60 to 135 J ( Only Patent Document 1 is displayed).
  • the cryogenic toughness of the base material is still insufficient, and the cryogenic toughness and the stress corrosion cracking resistance have not been achieved at the same time.
  • the present invention has been made in view of the above problems, and an object thereof is to provide a high-Mn steel sheet excellent in cryogenic toughness and stress corrosion cracking resistance and a method for producing the same.
  • the present inventors have conducted intensive research on various factors that determine the component composition, manufacturing method, and microstructure of a steel sheet for ensuring excellent stress corrosion cracking resistance performance for high-Mn steel sheets. The following findings were obtained.
  • Nb, V, Ti carbides, nitrides, and composite carbonitrides in steel sheets can be further improved in stress corrosion cracking resistance by properly managing their dispersion state. it can.
  • the carbides, nitrides, and composite carbonitrides of Nb, V, and Ti act as diffusible hydrogen trap sites in the steel sheet. That is, it acts as a trap site for diffusible hydrogen generated by the corrosion reaction of the steel material, and has the effect of suppressing stress corrosion cracking.
  • the heating, rolling, and cooling conditions in the hot rolling process affect the dispersion state of Nb, V, and Ti carbides, nitrides, and composite carbonitrides in austenite. Therefore, it is important to manage these manufacturing conditions.
  • P is an element that easily co-segregates with Mn in the solidification process of the steel slab, and lowers the grain boundary strength that intersects the micro-segregation part. Therefore, it is necessary to reduce impurity elements such as P.
  • the present invention has been made by further studying the above knowledge, and the gist thereof is as follows.
  • C 0.20 to 0.70%
  • Si 0.05 to 1.0%
  • Mn 15 to 30%
  • P 0.028% or less
  • S 0.02%
  • Al 0.01 to 0.1%
  • Cr 0.5 to 7.0%
  • Ni 0.03 to 0.30%
  • N 0.0010 to 0.0200%
  • Nb 0.003 to 0.030%
  • V 0.03 to 0.10%
  • Ti 0.003 to 0.040%, or one or more of them
  • It has a component composition, and a microstructure of 0.5 mm below the surface of the steel sheet has austenite as a base phase, of which austenite has an area ratio of 25% or more, a circle equivalent diameter of 10 ⁇ m or more, and a major axis and a minor axis.
  • a high Mn steel sheet having an aspect ratio of 3 or more.
  • the microstructure further includes carbides, nitrides, and carbonitrides containing one or more of Nb, V, and Ti having an equivalent circle diameter of 0.01 to 0.5 ⁇ m in the microstructure.
  • T Nb (° C.) 7500 / ⁇ 3.0 ⁇ log 10 ([% Nb] ⁇ [% C]) ⁇ ⁇ 273 (1)
  • T V (° C.) 10800 / ⁇ 7.2-log 10 ([% V] ⁇ [% C]) ⁇ ⁇ 273 (2)
  • T Ti (° C.) 7000 / ⁇ 2.8 ⁇ log 10 ([% Ti] ⁇ [% C]) ⁇ ⁇ 273 (3)
  • [% Nb], [% V], [% Ti] and [% C] indicate the contents (mass%) of Nb, V, Ti and C in the steel, respectively. In the case of an element not included, the element symbol in the formula is calculated as 0.
  • “high strength” means a material having a yield strength of 400 MPa or more.
  • “very low temperature toughness” means low temperature toughness, that is, the absorbed energy vE ⁇ 196 of the Charpy impact test at ⁇ 196 ° C. is 50 J or more.
  • “excellent in stress corrosion cracking resistance” is a test in accordance with the Narrow Standard TM0111-2011 standard Slow Strain Rate Test Method, which is artificial seawater (chloride ion concentration) at a temperature of 23 ° C. immersed in 18000ppm), strain rate:. when performing a constant velocity tensile test at 4 ⁇ 10 -7 inch / sec, refers to breaking stress is more than 500 MPa.
  • a high Mn steel sheet having excellent cryogenic toughness and stress corrosion cracking resistance can be obtained.
  • the high Mn steel plate of this invention contributes greatly to the improvement of the safety
  • C 0.20 to 0.70%
  • carbonized_material and Nb, V Ti type carbide
  • C is 0.25% or more.
  • C is 0.60% or less. More preferably, C is 0.30% or more. More preferably, C is 0.55% or less.
  • Si acts as a deoxidizer and is not only necessary for steelmaking, but also has the effect of increasing the strength of the steel sheet by solid solution and solid solution strengthening. In order to acquire such an effect, Si needs to contain 0.05% or more. On the other hand, when it contains exceeding 1.0%, weldability will deteriorate. It also affects the SCC resistance. For this reason, Si is made 0.05 to 1.0%. Preferably, Si is 0.07% or more. Preferably, Si is 0.50% or less. More preferably, Si is 0.15% or more. More preferably, Si is 0.45% or less.
  • Mn 15-30% Mn is a relatively inexpensive austenite stabilizing element. In the present invention, it is an important element for achieving both strength and cryogenic toughness. In order to acquire the effect, Mn needs to contain 15% or more. On the other hand, even if the content exceeds 30%, the effect of improving the cryogenic toughness is saturated, leading to an increase in alloy cost. In addition, the weldability and cutability are deteriorated. Furthermore, segregation is promoted and stress corrosion cracking is promoted. Therefore, Mn is set to 15 to 30%. Preferably, Mn is 18% or more. Preferably, Mn is 28% or less. More preferably, Mn is 20% or more. More preferably, Mn is 27% or less.
  • P 0.028% or less
  • P 0.028% or less
  • P is 0.005% or more.
  • P is 0.024% or less.
  • S 0.02% or less Since S deteriorates the low-temperature toughness and ductility of the base material, 0.02% is the upper limit and it is desirable to reduce it as much as possible. Therefore, S is set to 0.02% or less. In addition, since excessive S reduction raises refining cost and becomes economically disadvantageous, it is desirable to set it as 0.001% or more. Preferably, S is 0.002% or more. Preferably, S is 0.018% or less. More preferably, S is 0.010% or less.
  • Al acts as a deoxidizer and is most commonly used in the molten steel deoxidation process of steel sheets. Moreover, it has the effect which suppresses the coarsening of a crystal grain by fixing the solid solution N in steel and forming AlN. At the same time, it has the effect of suppressing toughness deterioration due to the reduction of solute N. In order to acquire such an effect, Al needs to contain 0.01% or more. On the other hand, if Al is contained in an amount exceeding 0.1%, it is mixed into the weld metal part during welding and deteriorates the toughness of the weld metal. For this reason, Al is made 0.01 to 0.1%. Preferably, Al is 0.02% or more. Preferably, Al is 0.07% or less.
  • Cr 0.5 to 7.0% Cr is an element that stabilizes austenite by addition of an appropriate amount and is effective in improving cryogenic toughness and base material strength. Further, in the present invention, it is an important element that improves the stress corrosion cracking resistance by reducing the amount of hydrogen penetration into the steel sheet through the effect of densifying rust generated on the surface of the base material in a salt water environment. . In order to acquire such an effect, Cr needs to contain 0.5% or more. On the other hand, if the content exceeds 7.0%, the low temperature toughness and stress corrosion cracking resistance decrease due to the formation of Cr carbide. Therefore, Cr is 0.5 to 7.0%. Cr is preferably 1.0% or more, more preferably 1.2% or more, and further preferably 2.5% or more. Cr is preferably 6.0% or less, more preferably 5.7% or less, and still more preferably 5.5% or less.
  • Ni 0.03-0.30%
  • Ni is a typical austenite stabilizing element, and is an element effective for improving cryogenic toughness and base metal strength. In the present invention, it is an important element that improves the stress corrosion cracking resistance by reducing the amount of hydrogen entering the steel sheet through the effect of densifying the rust generated on the surface of the base material in a salt water environment. . In order to acquire such an effect, Ni needs to contain 0.03% or more. On the other hand, when the content exceeds 0.30%, the alloy cost increases and the effect of improving the stress corrosion cracking resistance is saturated. For this reason, Ni is made 0.03 to 0.30%.
  • Ni is 0.25% or less.
  • it is 0.04% or more. More preferably, Ni is 0.23% or less. More preferably, Ni is 0.05% or more. More preferably, Ni is 0.21% or less.
  • N 0.0010 to 0.0200%
  • N is an austenite stabilizing element and is an element effective for improving cryogenic toughness. Moreover, it combines with Nb, V, and Ti, precipitates as nitride or carbonitride, and has an effect of suppressing stress corrosion cracking as a diffusible hydrogen trap site. In order to acquire such an effect, N needs to contain 0.0010% or more. On the other hand, if the content exceeds 0.0200%, the nitride or carbonitride becomes coarse and the toughness decreases. For this reason, N is made 0.0010 to 0.0200%.
  • N is 0.0020% or more.
  • N is 0.0150% or less. More preferably, N is 0.0030% or more. More preferably, N is 0.0170% or less.
  • Nb 0.003 to 0.030%
  • V 0.03 to 0.10%
  • Ti 0.003 to 0.040%
  • Nb is an element that precipitates as carbonitride (including carbide), and the produced carbonitride is effective at the trap site of diffusible hydrogen and has the effect of suppressing stress corrosion cracking. In order to acquire such an effect, Nb needs to contain 0.003% or more.
  • Nb exceeds 0.030%, coarse carbonitride precipitates, which may be the starting point of destruction. Further, the precipitates may become coarse and the base material toughness may be deteriorated. Therefore, when Nb is contained, the content is made 0.003 to 0.030%.
  • Nb is preferably 0.005% or more, more preferably 0.007% or more.
  • Nb is preferably 0.025% or less, more preferably 0.022% or less.
  • V 0.03-0.10%
  • V is an element which precipitates as carbonitride and the produced carbonitride is effective at the trap site of diffusible hydrogen and has the effect of suppressing stress corrosion cracking. In order to acquire such an effect, V needs to contain 0.03% or more.
  • V exceeds 0.10%, coarse carbonitride precipitates and may become a starting point of fracture. Further, the precipitates may become coarse and the base material toughness may be deteriorated. Therefore, when V is contained, the content is made 0.03 to 0.10%.
  • V is preferably 0.04% or more, more preferably 0.05% or more.
  • V is preferably 0.09% or less, more preferably 0.08% or less, and still more preferably 0.07% or less.
  • Ti 0.003-0.040%
  • Ti precipitates as nitride or carbonitride, and the generated nitride or carbonitride is an element effective for diffusible hydrogen trap sites and has the effect of suppressing stress corrosion cracking. In order to acquire such an effect, Ti needs to contain 0.003% or more.
  • Ti is contained in an amount exceeding 0.040%, the precipitates are coarsened and the base material toughness may be deteriorated. In addition, coarse carbonitrides may precipitate and become the starting point of fracture. Therefore, when Ti is contained, the content is made 0.003 to 0.040%.
  • Ti is preferably 0.005% or more, more preferably 0.007% or more.
  • Ti is preferably 0.035% or less, more preferably 0.032% or less.
  • the balance is iron and inevitable impurities.
  • Inevitable impurities include O and H, and a total of 0.01% or less is acceptable.
  • O and S are preferably defined as follows.
  • O 0.0005 to 0.0070% If O is contained in an amount exceeding 0.0070%, it forms coarse inclusions with Al and lowers the low temperature toughness. Therefore, the upper limit of O is 0.0070%, and it is desirable to reduce it as much as possible. Preferably, O is 0.0060% or less. In addition, excessive O reduction increases the refining cost and is economically disadvantageous, so it is 0.0005% or more. Preferably, O is 0.0008% or more.
  • O / S ⁇ 1 The balance of O and S forms oxides, sulfides, and composite precipitates thereof with Al, Ti, and Mn, and effectively acts as a trapping site for diffusible hydrogen to improve stress corrosion cracking. In order to obtain this effect, O / S ⁇ 1.
  • O / S ⁇ 1 When O / S ⁇ 1, coarse oxysulfides are formed, and the low-temperature toughness may be lowered. Therefore, in the present invention, O / S ⁇ 1 is set to ensure low temperature toughness.
  • the target characteristics of the present invention can be obtained.
  • the following elements can be contained as required in addition to the above essential elements.
  • Mo 0.05 to 2.0%
  • W 0.05 to 2.0%
  • Mo 0.05 to 2.0%
  • Mo is an element useful for increasing the strength of the base material, and can be contained as necessary.
  • Mo preferably contains 0.05% or more.
  • Mo is preferably made 2.0% or less.
  • Mo is 0.07% or more.
  • Mo is 1.7% or less.
  • W 0.05-2.0% W is an element useful for increasing the strength of the base material, and can be contained as necessary. In order to obtain such an effect, W preferably contains 0.05% or more. On the other hand, if the content exceeds 2.0%, the toughness and weld crack resistance may be adversely affected, so W is preferably set to 2.0% or less. Therefore, when W is contained, the content is made 0.05 to 2.0%. More preferably, the content is 0.07% or more. More preferably, it is 1.5% or less.
  • Ca 0.0005 to 0.0050%
  • Mg 0.0005 to 0.0050%
  • REM 0.0010 to 0.0200%
  • Ca 0.0005 to 0.0050%
  • the inclusion shape control means that the expanded sulfide inclusion is a granular inclusion. Ductility, toughness, and resistance to sulfide stress corrosion cracking are improved through shape control of the inclusions.
  • Ca preferably contains 0.0005% or more.
  • the content is made 0.0005 to 0.0050%. More preferably, it is 0.0010% or more. More preferably, it is 0.0040% or less.
  • Mg 0.0005 to 0.0050%
  • Mg is useful as an element that contributes to the improvement of resistance to sulfide stress corrosion cracking, and can be contained if necessary.
  • Mg preferably contains 0.0005% or more.
  • the content is made 0.0005 to 0.0050%. More preferably, it is 0.0010% or more. More preferably, it is 0.0040% or less.
  • REM 0.0010 to 0.0200% REM is useful as an element that contributes to the improvement of resistance to sulfide stress corrosion cracking, and can be contained as necessary.
  • REM preferably contains 0.0010% or more.
  • the content is 0.0020% or more. More preferably, it is 0.0150% or less.
  • the microstructure of 0.5 mm below the surface of the steel sheet has austenite as a base phase, and the area ratio of the austenite is 25% or more, the equivalent circle diameter is 10 ⁇ m or more, and the aspect ratio of major axis and minor axis is 3 or more.
  • the base phase having a microstructure of 0.5 mm below the surface of the steel sheet is austenite.
  • the grain boundary in the vicinity of the steel sheet surface layer is obtained by having an area ratio of 25% or more of austenite having an equivalent circle diameter of 10 ⁇ m or more and an aspect ratio of major axis to minor axis of 3 or more.
  • the deformation zone in the crystal grains effectively acts as a diffusible hydrogen trap site and effectively acts on the stress corrosion cracking property. Thereby, suppression of stress corrosion cracking can be remarkably improved.
  • the yield strength is improved.
  • the area ratio is 30% or more.
  • the area ratio exceeds 95%, the strength of the steel material becomes excessive, and the base material toughness may be deteriorated.
  • it is 95% or less, More preferably, you may be 94% or less. More preferably, it is 90% or less. More preferably, it is 85% or less.
  • the equivalent circle diameter is less than 10 ⁇ m, or the aspect ratio of the major axis to the minor axis is less than 3, the desired yield strength cannot be obtained, and a deformation band within the crystal grains that effectively acts as a trapping site for diffusible hydrogen can be obtained. Therefore, the stress corrosion cracking property is lowered, and the above-described effects cannot be obtained.
  • the circle equivalent diameter of the above-mentioned austenite, an area ratio, and an aspect ratio can be measured by the method as described in the Example mentioned later.
  • 0.5 mm below the surface of the steel sheet means a cross section parallel to the rolling direction at a position 0.5 mm in the thickness direction from the front and back surfaces of the steel sheet.
  • 0.5 mm below the surface of the steel sheet means that the above-mentioned micro is formed in a cross section parallel to the rolling direction in any of ⁇ 5% from the position of 0.5 mm from the front and back surfaces of the steel sheet in the thickness direction.
  • the microstructure 0.5 mm below the surface of the steel sheet further includes carbides and nitrides containing one or more of Nb, V, and Ti having an equivalent circle diameter of 0.01 to 0.5 ⁇ m in the structure. And a total of 2 ⁇ 10 2 pieces / mm 2 or more of carbonitrides Carbide containing one or more of Nb, V, Ti in the microstructure at 0.5 mm below the surface of the steel sheet of the present invention.
  • Nb, V, and Ti-based precipitates The existence state of nitrides and carbonitrides (hereinafter referred to as Nb, V, and Ti-based precipitates) will be described.
  • Carbides, nitrides, and carbonitrides containing one or more of Nb, V, and Ti are carbides containing one or more of Nb, V, and Ti, Nb, V, A nitride containing one or more of Ti, and a carbonitride containing one or more of Nb, V, and Ti.
  • the particle diameter of the Nb, V, and Ti-based precipitates is 0.01 to 0.5 ⁇ m in terms of equivalent circle diameter.
  • the thickness is less than 0.01 ⁇ m, the effect of suppressing hydrogen embrittlement cracking as a diffusible hydrogen trap site is saturated.
  • a manufacturing load will increase extremely and manufacturing cost will rise.
  • it exceeds 0.5 ⁇ m the low temperature toughness is lowered.
  • the effect of suppressing hydrogen embrittlement cracking as a trapping site for diffusible hydrogen cannot be obtained.
  • it is 0.03 ⁇ m or more.
  • it is 0.4 micrometer or less.
  • the total of the Nb, V, and Ti-based precipitates having the above particle diameter is less than 2 ⁇ 10 2 pieces / mm 2 in a microstructure of 0.5 mm below the surface of the steel sheet, it acts as a diffusible hydrogen trap site. Since the precipitates are insufficient, the effect of suppressing hydrogen embrittlement cracking as a diffusible hydrogen trap site cannot be obtained. For this reason, it is set to 2 ⁇ 10 2 pieces / mm 2 or more. Preferably, it is 5 ⁇ 10 2 pieces / mm 2 or more.
  • the number density and equivalent circle diameter of the Nb, V, and Ti-based precipitates described above can be measured by the method described in the examples described later.
  • the low temperature toughness decreases. For this reason, austenite shall be 90% or more.
  • the area ratio of the structure such as martensite is small.
  • the structures such as martensite are martensite, bainite, ferrite, and pearlite.
  • the total area ratio of each structure with respect to the entire steel sheet is preferably 10% or less.
  • the steel sheet is manufactured by hot rolling at a temperature of 1000 ° C. or less and then the average cooling rate on the surface of the steel plate from the lower one of (finishing finish temperature ⁇ 50 ° C.) or the cooling start temperature to 650 ° C. is 1.0. It can be obtained by cooling at a temperature of ° C / s or higher.
  • the “° C.” display relating to the temperature means the temperature on the surface of the steel plate or the surface of the steel material.
  • the high Mn steel sheet according to the present invention can be produced by melting a molten steel having the above-described composition by a known melting method such as a converter or an electric furnace. Further, secondary refining may be performed in a vacuum degassing furnace. Thereafter, a steel material such as a slab having a predetermined size is preferably formed by a known casting method such as a continuous casting method or an ingot-bundling rolling method.
  • Tx (° C) defined by the formulas (1) to (3) and is heated to a temperature range of (Tx-50) ° C to (Tx + 200) ° C.
  • Nb (°C) 7500 / ⁇ 3.0-log 10 ([% Nb] ⁇ [% C]) ⁇ - 273 ⁇ (1)
  • T V (° C.) 10800 / ⁇ 7.2-log 10 ([% V] ⁇ [% C]) ⁇ ⁇ 273 (2)
  • T Ti (° C.) 7000 / ⁇ 2.8 ⁇ log 10 ([% Ti] ⁇ [% C]) ⁇ ⁇ 273 (3)
  • [% Nb], [% V], [% Ti] and [% C] indicate the contents (mass%) of Nb, V, Ti and C in the steel, respectively. In the case of an element not included, the element symbol in the formula is calculated as 0.
  • the heating temperature is less than (Tx-50) ° C.
  • the deformation resistance in hot rolling becomes high and the amount of reduction per pass cannot be made large, so the number of rolling passes increases and the rolling efficiency decreases.
  • a casting defect in a steel material (slab) cannot be crimped.
  • the crystallized material containing Nb, V and Ti that has been crystallized non-uniformly in the steel in the melting stage remains in the steel plate after the rolling, and a precipitate containing the desired Nb, V and Ti is obtained.
  • the stress corrosion cracking resistance decreases.
  • the heating temperature exceeds (Tx + 200) ° C.
  • Tx + 200 surface flaws are likely to occur due to the scale during heating, and the maintenance load after rolling increases.
  • the surface of the steel material is excessively decarburized, the surface of the steel sheet after rolling becomes martensite, and bendability and hydrogen embrittlement are reduced.
  • the target microstructure cannot be obtained due to coarsening of austenite grains.
  • the heating temperature of the steel material is set to (Tx-50) ° C. or higher and (Tx + 200) ° C. or lower.
  • the temperature is (Tx-30) ° C. or higher.
  • it is set to (Tx + 180) ° C. or lower.
  • hot rolling is started when the steel material is (Tx-50) ° C. or higher and (Tx + 200) ° C. or lower.
  • any of Tx (° C.) defined by the formulas (1) to (3) “When heated to a temperature range where the surface temperature of the steel material is (Tx ⁇ 50) ° C. or higher and (Tx + 200) ° C. or lower” with two or more of Nb and V as the above component composition, for example.
  • the heating temperature should satisfy at least one of (T Nb ⁇ 50) ° C. or more and (T Nb +200) ° C. or (T V ⁇ 50) ° C. or more and (T V +200) ° C. or less. Means. That is, either heating temperature may be selected.
  • the finish rolling finish temperature in finish rolling is set to 750 ° C. or more and 1000 ° C. or less to obtain a steel plate having a desired thickness.
  • the finish rolling finish temperature of hot rolling exceeds 1000 ° C., the steel plate surface The recrystallization of the nearby austenite proceeds easily, the desired microstructure cannot be obtained, and the stress corrosion cracking resistance is lowered.
  • the finish rolling finish temperature is less than 750 ° C., the hot deformation resistance becomes excessively high, and the load on the rolling mill increases. In addition, the rolling efficiency is reduced, and the manufacturing cost is increased.
  • the finish rolling finish temperature of hot rolling shall be 750 degreeC or more and 1000 degrees C or less.
  • the temperature is 800 ° C. or higher.
  • the temperature is preferably 950 ° C. or lower. More preferably, it is set to 940 ° C. or lower.
  • Cumulative rolling reduction in the temperature range of 850 ° C. or higher (Tx ⁇ 50) ° C. or lower in finish rolling 10% to 50% (preferred condition) If the cumulative rolling reduction in the temperature range of 850 ° C. or higher (Tx-50) ° C. or lower is less than 10%, the target microstructure may not be obtained. On the other hand, if it exceeds 50%, the efficiency during rolling decreases. Moreover, there exists a possibility that intensity may become excessive and low-temperature toughness may fall.
  • the cumulative reduction ratio is the sum of the reduction ratios in each rolling pass in the temperature range of 850 ° C. or more (Tx ⁇ 50) ° C. in finish rolling.
  • Cumulative rolling reduction of 5% to 60% (more suitable conditions) in the non-recrystallization temperature range (960 ° C. or less) in finish rolling If the cumulative rolling reduction in the non-recrystallization temperature range is less than 5%, the target strength may not be obtained. On the other hand, if it exceeds 60%, the yield strength becomes excessive and the low-temperature toughness may be lowered.
  • the cumulative reduction ratio is the sum of the reduction ratios in each rolling pass that is in the non-recrystallization temperature range in finish rolling.
  • the average cooling rate is preferably 1.0 ° C./s or more. More preferably, it is set to 2.0 ° C./s or more.
  • the average cooling rate is preferably 150.0 ° C./s or less.
  • the average cooling rate is more preferably 120.0 ° C./s or less. More preferably, it shall be 100.0 degrees C / s or less.
  • the average cooling rate is the average of the cooling rates from the lower temperature of (finishing rolling finishing temperature ⁇ 50 ° C.) or the cooling start temperature to 650 ° C. after finishing rolling.
  • controlling the average cooling rate in cooling is effective in suppressing Cr carbide precipitation during cooling, thereby improving the stress corrosion cracking resistance.
  • the average cooling rate in the temperature range from the finish rolling finish temperature to (finish finish finish temperature ⁇ 50 ° C.) is not particularly specified, but is 1.0 ° C./s because precipitation of Nb, V, and Ti-based precipitates can be promoted. The following is preferable.
  • the average cooling rate below 650 degreeC is not prescribed
  • regulated it is preferable to set it as less than 100.0 degreeC / s from a viewpoint of preventing the distortion of a steel plate. More preferably, it is 80.0 ° C./s or less.
  • the obtained hot-rolled steel sheet having a thickness of 12 mm to 80 mm was subjected to a microstructure investigation, a base material tensile test, a base material toughness, and a stress corrosion cracking test in the following manner.
  • the microstructure was examined by taking a sample for microstructural observation of a cross section parallel to the rolling direction at a position 0.5 mm below the surface of the thickness of each steel sheet, and adding a sodium pyrosulfite aqueous solution (10 g Na After immersion corrosion with 2 S 2 O 5 +95 ml water solution, 5 fields of the optical microscope tissue were photographed at a magnification of 500 times. Thereafter, the area ratio, equivalent circle diameter, and aspect ratio of the austenite were obtained from the obtained tissue image using an image analysis apparatus.
  • Austenite area ratio The austenite area ratio is austenite etched, the structure is photographed at 500 times, the austenite grain boundary is traced, and by image analysis, the area of austenite is 10 ⁇ m or more relative to the total area of austenite The percentage was determined.
  • Austenite equivalent circle diameter The crystal grain size of austenite, that is, the equivalent circle diameter of austenite, was measured for the area of each austenite using image analysis on the above-described structure image. The equivalent circle diameter was calculated from each area.
  • Austenite grain aspect ratio The austenite grain aspect ratio is determined by observing the structure of the austenite grain boundary by the above-mentioned corrosion using an optical microscope. The ratio of the widest width (minor axis) was calculated.
  • Equivalent circle diameter of Nb, V, and Ti-based precipitates The investigation of equivalent circle diameter of Nb, V, and Ti-based precipitates was conducted on a cross section parallel to the rolling direction at a position 0.5 mm below the surface of each steel plate. Ten fields of view were taken with a scanning electron microscope at a magnification of 50000 times, and the area of each Nb, V, Ti-based precipitate was measured using image analysis on the tissue image. The equivalent circle diameter of the Nb, V, and Ti-based precipitates was calculated from each area.
  • Number density of Nb, V, and Ti-based precipitates The number density of Nb, V, and Ti-based precipitates was determined by examining transmission electron for a cross section parallel to the rolling direction at a position 0.5 mm below the surface of each steel plate. Ten fields of view were taken with a microscope at 50000 times, and the number of Nb, V, and Ti-based precipitates having an equivalent circle diameter of 0.01 to 0.5 ⁇ m per 1 mm 2 was examined. The total number density of precipitates was determined.
  • (2) Base material tensile properties JIS No. 5 tensile test specimens were collected from each of the obtained steel plates, and subjected to a tensile test in accordance with the default of JIS Z 2241 (1998) to investigate the tensile properties.
  • a yield strength of 400 MPa or more is assumed to have excellent base material tensile properties (within the scope of the present invention).
  • what was excellent in the base material tensile characteristics of this invention was the tensile strength of 800 MPa or more and the total elongation of 30% or more.
  • Base material toughness JIS Z 2202 (1998) from the direction perpendicular to the rolling direction of the plate thickness 1/4 position of each steel plate exceeding 20 mm thickness or the plate thickness 1/2 position of each steel plate thickness 20 mm or less.
  • Charpy V-notch test specimens were collected in accordance with the provisions of JIS Z 2242, and three Charpy impact tests were performed on each steel sheet in accordance with the provisions of JIS Z 2242 (1998), and the absorbed energy at -196 ° C And the toughness of the base material was evaluated.
  • the average value of three absorbed energy (vE -196) is more than 50J was excellent in base metal toughness (within the scope of the present invention). More preferably, the average value of absorbed energy (vE ⁇ 196 ) is 100 J or more.
  • Stress Corrosion Cracking Test The stress corrosion cracking test was carried out in accordance with the Narrow Standard TM0111-2011 standard Slow Strain Rate Test Method.
  • the shape of the specimen is a Type A round bar notched specimen, immersed in artificial seawater (chloride ion concentration 18000 ppm) at a temperature of 23 ° C., and subjected to a constant velocity tensile test at a strain rate of 4 ⁇ 10 ⁇ 7 inch / sec. Carried out.
  • the fracture stress is 500 MPa or more and is excellent in stress corrosion cracking resistance (within the scope of the present invention). More preferably, the breaking stress is 600 MPa or more.
  • the present invention is, target performance of the above (yield strength of the base material is more than 400 MPa, 50 J or more in the average value of the low-temperature toughness absorbed energy (vE -196), more 500MPa stress corrosion cracking resistance in breaking stress) satisfies Confirmed to do.
  • Yield strength of the base material is more than 400 MPa, 50 J or more in the average value of the low-temperature toughness absorbed energy (vE -196), more 500MPa stress corrosion cracking resistance in breaking stress
  • any one or more of the base material strength, the low temperature toughness, and the stress corrosion cracking resistance cannot satisfy the above target performance.
  • the steel plate No. Nos. 12 and 36 have a stable austenite because C is out of the range of the present invention, but there are a lot of unstable austenites. Therefore, the average equivalent circle diameter is 10 ⁇ m or more and the aspect ratio of major axis to minor axis is 3 The area ratio of the above austenite was 70%.

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Abstract

L'invention concerne une tôle d'acier à haute teneur en Mn et un procédé de production de celle-ci. La composition de cette tôle d'acier à haute teneur en Mn est la suivante, en % en masse : 0,20 à 0,70 % de C ; 0,05 à 1,0 % de Si ; 15 à 30 % de Mn ; une proportion inférieure ou égale à 0,028 % de P ; une proportion inférieure ou égale à 0,02 % de S ; 0,01 à 0,1 % d'Al ; 0,5 à 7,0 % de Cr ; 0,03 à 0,30 % de Ni ; et 0,0010 à 0,0200 % de N ; la tôle d'acier contient en outre un ou plusieurs des constituants suivants : 0,003 à 0,030 % de Nb, 0,03 à 0,10 % de V et 0,003 à 0,040 % de Ti, le reste étant du Fe et des impuretés inévitables. Cette tôle d'acier à haute teneur en Mn présente une microstructure, à 0,5 mm au-dessous de la surface de la tôle d'acier, qui comporte une phase matricielle d'austénite ; et une proportion supérieure ou égale à 25 % de l'austénite, en termes de rapport de surface, présente un diamètre de cercle équivalent de 10 µm ou plus et un rapport d'aspect longueur/largeur supérieur ou égal à 3.
PCT/JP2017/043245 2016-12-08 2017-12-01 Tôle d'acier à haute teneur en mn et procédé de production de celle-ci WO2018105510A1 (fr)

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EP17879107.5A EP3553195B1 (fr) 2016-12-08 2017-12-01 Tôle d'acier à haute teneur en mn et procédé de production de celle-ci
BR112019010870-0A BR112019010870B1 (pt) 2016-12-08 2017-12-01 Placa de aço de alto mn e método de fabricação para a mesma
CN201780075814.3A CN110050082B (zh) 2016-12-08 2017-12-01 高Mn钢板及其制造方法
JP2018512637A JP6418358B1 (ja) 2016-12-08 2017-12-01 高Ｍｎ鋼板およびその製造方法
KR1020197015408A KR20190077470A (ko) 2016-12-08 2017-12-01 고 Mn 강판 및 그 제조 방법
KR1020217017558A KR102309644B1 (ko) 2016-12-08 2017-12-01 고 Mn 강판 및 그 제조 방법
PH12019501270A PH12019501270A1 (en) 2016-12-08 2019-06-06 HIGH-Mn STEEL PLATE AND MANUFACTURING METHOD THEREFOR

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PCT/JP2016/005080 WO2018104984A1 (fr) 2016-12-08 2016-12-08 TÔLE D'ACIER À TENEUR ÉLEVÉE EN Mn ET SON PROCÉDÉ DE PRODUCTION
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WO2020027211A1 (fr) * 2018-08-03 2020-02-06 Ｊｆｅスチール株式会社 Acier à haute teneur en manganèse et son procédé de production
WO2020166538A1 (fr) * 2019-02-12 2020-08-20 Ｊｆｅスチール株式会社 Acier à haute teneur en mn et procédé de fabrication d'un tel acier
EP3835445A4 (fr) * 2018-08-28 2021-08-18 JFE Steel Corporation Tôle d'acier et procédé pour la production de celle-ci
WO2022168686A1 (fr) * 2021-02-08 2022-08-11 Ｊｆｅスチール株式会社 Matériau d'acier et son procédé de production, ainsi que réservoir et son procédé de production

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WO2020035917A1 (fr) * 2018-08-15 2020-02-20 Ｊｆｅスチール株式会社 Tôle d'acier et procédé de production de celle-ci
WO2020054553A1 (fr) * 2018-09-12 2020-03-19 Ｊｆｅスチール株式会社 Matériau en acier et son procédé de fabrication
KR20210105418A (ko) * 2019-03-19 2021-08-26 제이에프이 스틸 가부시키가이샤 고망간강 주편의 제조 방법, 고망간강 강편 및 고망간강 강판의 제조 방법
CN114302977B (zh) 2019-08-21 2022-12-06 杰富意钢铁株式会社 钢及其制造方法
US20230077573A1 (en) * 2020-02-27 2023-03-16 Nippon Steel Stainless Steel Corporation Stainless steel for metal foils, stainless steel foil, and methods for producing them
CN112853194B (zh) * 2021-01-06 2022-05-13 鞍钢股份有限公司 一种可控氮的高锰钢钒合金化方法
CN116926443A (zh) * 2022-04-07 2023-10-24 南京钢铁股份有限公司 超低温钢及其热处理工艺和应用

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WO2020027211A1 (fr) * 2018-08-03 2020-02-06 Ｊｆｅスチール株式会社 Acier à haute teneur en manganèse et son procédé de production
JPWO2020027211A1 (ja) * 2018-08-03 2020-08-06 Ｊｆｅスチール株式会社 高Ｍｎ鋼およびその製造方法
KR20210027412A (ko) * 2018-08-03 2021-03-10 제이에프이 스틸 가부시키가이샤 고 Mn 강 및 그 제조 방법
KR102492352B1 (ko) 2018-08-03 2023-01-27 제이에프이 스틸 가부시키가이샤 고 Mn 강 및 그 제조 방법
US11959157B2 (en) 2018-08-03 2024-04-16 Jfe Steel Corporation High-Mn steel and method of producing same
EP3835445A4 (fr) * 2018-08-28 2021-08-18 JFE Steel Corporation Tôle d'acier et procédé pour la production de celle-ci
WO2020166538A1 (fr) * 2019-02-12 2020-08-20 Ｊｆｅスチール株式会社 Acier à haute teneur en mn et procédé de fabrication d'un tel acier
JPWO2020166538A1 (ja) * 2019-02-12 2021-03-11 Ｊｆｅスチール株式会社 高Ｍｎ鋼およびその製造方法
WO2022168686A1 (fr) * 2021-02-08 2022-08-11 Ｊｆｅスチール株式会社 Matériau d'acier et son procédé de production, ainsi que réservoir et son procédé de production
JPWO2022168686A1 (fr) * 2021-02-08 2022-08-11
JP7338792B2 (ja) 2021-02-08 2023-09-05 Ｊｆｅスチール株式会社 鋼材およびその製造方法、タンクおよびその製造方法

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EP3553195B1 (fr) 2021-05-19
BR112019010870B1 (pt) 2023-04-11
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JP6418358B1 (ja) 2018-11-07
TWI653343B (zh) 2019-03-11
KR20190077470A (ko) 2019-07-03
BR112019010870A2 (pt) 2019-10-01
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CN110050082A (zh) 2019-07-23
WO2018104984A1 (fr) 2018-06-14

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