WO2020036090A1 - Tôle d'acier et procédé de production de celle-ci - Google Patents

Tôle d'acier et procédé de production de celle-ci Download PDF

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WO2020036090A1
WO2020036090A1 PCT/JP2019/030769 JP2019030769W WO2020036090A1 WO 2020036090 A1 WO2020036090 A1 WO 2020036090A1 JP 2019030769 W JP2019030769 W JP 2019030769W WO 2020036090 A1 WO2020036090 A1 WO 2020036090A1
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steel
steel sheet
content
toughness
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PCT/JP2019/030769
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Japanese (ja)
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博司 池田
茂樹 木津谷
植田　圭治
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Ｊｆｅスチール株式会社
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Priority to EP19850397.1A priority Critical patent/EP3825436A1/fr
Priority to JP2019568801A priority patent/JP6904438B2/ja
Priority to KR1020217005489A priority patent/KR102497359B1/ko
Priority to CN201980051501.3A priority patent/CN112513309B/zh
Publication of WO2020036090A1 publication Critical patent/WO2020036090A1/fr
Priority to PH12021550314A priority patent/PH12021550314A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D6/00—Heat treatment 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • 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
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    • 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
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
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    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—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 steel sheet which is suitable for structural steel used in a cryogenic environment, such as a tank for a liquefied gas storage tank, and which has excellent corrosion resistance particularly in a salt water corrosion environment, and a method for producing the same.
  • hot-rolled steel sheets for structures such as liquefied gas storage tanks. Since such a structure is used at an extremely low temperature, the hot-rolled steel sheet applied to the structure is required to have not only high strength but also excellent toughness at an extremely low temperature. For example, when a hot-rolled steel sheet is used for a liquefied natural gas storage tank, it is necessary to secure excellent toughness at -164 ° C. or lower, which is the boiling point of liquefied natural gas. If the low-temperature toughness of the steel material is inferior, there is a risk that the safety as a structure for a cryogenic storage tank may not be maintained.
  • an austenitic stainless steel, a 9% Ni steel, or a 5000-type aluminum alloy having an austenitic structure that does not exhibit brittleness at cryogenic temperatures has been used.
  • these metal materials have high alloy costs and high production costs, there is a demand for steel plates that are inexpensive and have excellent cryogenic toughness. Therefore, as a new steel sheet that replaces the conventional cryogenic steel, a high-Mn steel is used as a structural steel sheet in a cryogenic environment by adding a large amount of relatively inexpensive austenitic stabilizing element Mn to form an austenitic structure. That is being considered.
  • Patent Document 1 discloses that the machinability and the Charpy impact characteristics at -196 ° C. of the heat-affected zone due to heat and heat are affected by adding Mn of 15 to 35%, Cu of 5% or less, and C and Cr in appropriate amounts. Are disclosed.
  • Patent Document 2 discloses that C: 0.25 to 0.75%, Si: 0.05 to 1.0%, Mn: more than 20% and 35% or less, and Ni: 0.1% to 7.0. %, Cr: 0.1% or more and less than 8.0% are added to improve the low-temperature toughness, and a high Mn steel material is disclosed.
  • Patent Document 3 discloses that the content of C is 0.001 to 0.80% and Mn is 15 to 35%, and the elements such as Cr, Ti, Si, Al, Mg, Ca, and REM are added.
  • a high Mn steel material with improved cryogenic toughness of the material and welds is disclosed.
  • Patent Literatures 1, 2, and 3 still have room for improvement in terms of manufacturing cost for achieving strength and low-temperature toughness, and corrosion resistance when the above-described austenitic steel material is placed in a salt corrosion environment. There is.
  • the present invention has been made in view of the above problems, and has as its object to provide a high Mn steel having excellent corrosion resistance, particularly in a salt corrosion environment.
  • excellent in corrosion resistance refers to a test based on the Slow Strain Rate Test Method based on NACE Standard TM0111-2011, which is immersed in artificial seawater (chloride ion concentration: 18000 ppm) at a temperature of 23 ° C. : The breaking stress is 600 MPa or more when a constant velocity tensile test is performed at 4 ⁇ 10 ⁇ 7 inch / s.
  • the initial corrosion reaction on the steel sheet surface in a saltwater corrosion environment can be delayed by adding Cr and appropriately controlling the addition amount and the solid solution amount based on the high Mn steel. Thereby, the amount of hydrogen penetrating into the steel can be reduced, and the above-described stress corrosion cracking of the austenitic steel is suppressed.
  • P is an element that tends to segregate together with Mn in the process of solidifying the steel slab, and lowers the grain boundary strength at a portion where such a segregated portion intersects. Therefore, it is necessary to reduce impurity elements such as P.
  • B is an element that enhances the strength of the austenite grain boundary. By adding B in addition to reducing impurity elements such as P, it is possible to further effectively suppress grain boundary destruction.
  • the present invention has been made by further studying the above findings, and the gist thereof is as follows. 1. In mass%, C: 0.20% or more and 0.70% or less, Si: 0.05% or more and 1.00% or less, Mn: 15.0% or more and 35.0% or less, P: 0.030% or less, S: 0.0200% or less, Al: 0.010% to 0.100%, Cr: 0.5% or more and 8.0% or less, N: 0.0010% or more and 0.0300% or less and B: 0.0003% or more and 0.0100% or less, and has a component composition of the balance of Fe and unavoidable impurities. Steel plate that is molten Cr.
  • the component composition further includes, in mass%, Nb: 0.003% or more and 0.030% or less, 2.
  • the component composition further includes, in mass%, Cu: 0.01% or more and 0.50% or less, Ni: 0.01% or more and 0.50% or less, Sn: 0.01% or more and 0.30% or less, Sb: 0.01% or more and 0.30% or less, 3.
  • the component composition further includes, in mass%, Ca: 0.0005% or more and 0.0050% or less, 4.
  • hot rolling is performed at a finishing temperature: 750 ° C. or more and a material to be rolled: 950 ° C. or less.
  • a method for producing a steel sheet in which the residence time at 600 ° C. or more is set to 30 minutes or less, and then cooling is performed at a cooling rate of 3 ° C./s or more in a temperature range of 700 ° C. to 600 ° C.
  • the present invention it is possible to provide a steel sheet having excellent corrosion resistance, especially in a salt corrosion environment. Therefore, by using the steel sheet of the present invention for a steel structure used in an extremely low temperature environment, such as a tank for a liquefied gas storage tank, for example, the safety and life of the steel structure are greatly improved. Will bring about the effect. Further, since the steel sheet of the present invention is inexpensive as compared with existing materials, it also has the advantage of being economical.
  • the steel sheet of the present invention will be described in detail. Note that the present invention is not limited to the following embodiments.
  • the component composition of the steel sheet of the present invention in order to ensure excellent corrosion resistance, the component composition of the steel sheet is specified as follows. Note that “%” representing the component composition means “% by mass” unless otherwise specified.
  • C 0.20% or more and 0.70% or less C is effective for increasing the strength, is an inexpensive austenite stabilizing element, and is an important element for obtaining austenite. To obtain the effect, C needs to be contained at 0.20% or more. On the other hand, when the content exceeds 0.70%, excessive precipitation of Cr carbide and Nb, V, and Ti-based carbides is promoted, and these precipitates become a starting point of corrosion and lower the low-temperature toughness. Therefore, C is set to 0.20% or more and 0.70% or less. Preferably, the content is 0.25% or more and 0.60% or less.
  • Si acts as a deoxidizing material and is not only necessary for steelmaking, but also has the effect of forming a solid solution in steel and strengthening the steel sheet by solid solution strengthening. .
  • the content of Si needs to be 0.05% or more.
  • Si is set to 0.05% or more and 1.00% or less. Preferably, it is 0.07% or more and 0.50% or less.
  • Mn 15.0% or more and 35.0% or less
  • Mn is a relatively inexpensive austenite stabilizing element. In the present invention, it is an important element for achieving both strength and toughness at extremely low temperatures. In order to obtain the effect, Mn needs to be contained at 15.0% or more. On the other hand, when the content exceeds 35.0%, the effect of improving the toughness at a very low temperature is saturated, which causes an increase in alloy cost. Also, the weldability and the cuttability deteriorate. Further, it causes the segregation of Mn to promote the occurrence of stress corrosion cracking. Therefore, Mn is set to 15.0% or more and 35.0% or less. Preferably, it is in the range of 18.0% or more and 28.0% or less.
  • P 0.030% or less
  • the content of P is preferably 0.024% or less, more preferably 0.020% or less.
  • the content of P is less than 0.001%, a large cost is required for steel making and the economic efficiency is impaired. Therefore, the content of 0.001% or more is allowable from the viewpoint of economic efficiency.
  • S 0.0200% or less Since S deteriorates the low-temperature toughness and ductility of the base material, the upper limit is set to 0.0200%, and it is desirable to reduce as much as possible. Therefore, S is set to 0.0200% or less, preferably 0.0180% or less. On the other hand, if the content is less than 0.0001%, a large cost is required for steel making and the economic efficiency is impaired. Therefore, the content of 0.0001% or more is allowable from the viewpoint of economic efficiency.
  • Al acts as a deoxidizing agent and is most commonly used in a molten steel deoxidizing process.
  • solid solution N in steel to form AlN
  • Al needs to be contained at 0.01% or more.
  • the content exceeds 0.100%, a coarse nitride is formed, which becomes a starting point of corrosion and destruction, and the stress corrosion cracking resistance may be reduced.
  • Al is set to 0.100% or less.
  • it is 0.020% or more and 0.070% or less.
  • Cr 0.5% or more and 8.0% or less and 60% or more of Cr is a solid solution
  • Cr Cr has an effect of delaying an initial corrosion reaction on the surface of a steel sheet in a saltwater corrosion environment when contained in an appropriate amount. This effect is an important element that reduces the amount of hydrogen penetrating into the steel sheet and improves stress corrosion cracking resistance. In order to obtain such an effect, the content needs to be 0.5% or more. On the other hand, when the content of Cr exceeds 8.0%, the above-mentioned effect obtained is saturated, and on the contrary, economic efficiency is impaired. Therefore, the Cr content is set to 0.5% or more and 8.0% or less. Preferably, it is at least 1.0%.
  • the solid solution component of the added Cr contributes to the improvement of the stress corrosion cracking resistance, but the precipitated component may hinder the improvement of the stress corrosion cracking resistance. It is important that at least 60% be solid solution Cr. That is, when the amount of the solid solution Cr is 60% or more of the contained Cr amount, the above-described effects can be obtained, and the improvement of the stress corrosion cracking resistance by adding Cr can be realized.
  • the solute Cr is preferably at least 70% of the Cr content, more preferably 100%.
  • Solute solution Cr refers to a state in which a solute atom exists in an atomic state without forming a precipitate or the like. Specifically, the amount of solute Cr was determined by extracting a test piece for electrolytic extraction from a steel sheet and extracting it by an electrolytic extraction method using a 10% AA (10% acetylacetone-1% tetramethylammonium chloride-methanol) solution. The precipitate can be determined by measuring the amount of Cr in the precipitate by ICP emission spectrometry and subtracting it from the total Cr in the test piece.
  • N 0.0010% or more and 0.0300% or less
  • N is an austenite stabilizing element and is an element effective for improving the cryogenic toughness.
  • Nb, V and Ti combines with Nb, V and Ti and finely precipitates as nitride or carbonitride, and has an effect of suppressing stress corrosion cracking as a trap site for diffusible hydrogen.
  • N needs to be contained at 0.0010% or more.
  • N is set to 0.0010% or more and 0.0300% or less.
  • it is 0.0020% or more and 0.0150% or less.
  • B 0.0003% or more and 0.0100% or less
  • B is an element that increases the strength of the austenite grain boundary, and is an element that suppresses cracking at the grain boundary and is effective in improving stress corrosion cracking resistance.
  • B needs to be contained at 0.0003% or more.
  • it is at least 0.0005%, more preferably more than 0.0007% and more than 0.0010%.
  • the content exceeds 0.0100%, this effect is saturated. Therefore, B is limited to the range of 0.0100% or less. Preferably, it is 0.0070% or less.
  • Nb 0.003% to 0.030%
  • V 0.01% to 0.10.
  • Ti 0.003% to 0.040%.
  • Nb is an element having the effect of suppressing stress corrosion cracking because it precipitates as carbonitride and the deposited carbonitride functions as a trap site for diffusible hydrogen. .
  • Nb is preferably contained at 0.003% or more.
  • the content is preferably set to 0.003% or more and 0.030% or less. More preferably, it is 0.005% or more and 0.025% or less, furthermore, 0.007% or more and 0.022% or less.
  • V 0.01% or more and 0.10% or less
  • V is an element having an effect of suppressing stress corrosion cracking because V is precipitated as carbonitride and the generated carbonitride functions as a trap site for diffusible hydrogen. .
  • V is preferably contained at 0.01% or more.
  • the content exceeds 0.10%, coarse carbonitrides may precipitate and become a starting point of fracture. Further, the precipitates may be coarsened and the toughness of the base material may be deteriorated.
  • the content is preferably set to 0.01% or more and 0.10% or less. More preferably, it is 0.02% or more and 0.09% or less, and further more preferably 0.03% or more and 0.08% or less.
  • Ti 0.003% or more and 0.040% or less Ti precipitates as nitride or carbonitride, and the generated nitride or carbonitride functions as a trap site for diffusible hydrogen. It is an element that has an effect. In order to obtain such an effect, it is preferable that Ti is contained at 0.003% or more. On the other hand, if the content exceeds 0.040%, the precipitates may be coarsened and the base material toughness may be deteriorated. In addition, coarse carbonitrides may precipitate and serve as starting points for destruction. Therefore, when Ti is contained, the content is preferably set to 0.003% or more and 0.040% or less. More preferably, it is 0.005% or more and 0.035% or less, furthermore, 0.007% or more and 0.032% or less.
  • Cu 0.01% to 0.50%
  • Ni 0.01% to 0.50%
  • Sn 0.01% to 0.30%
  • Sb 0.01% to 0.30%
  • Mo 0.01% or more and 2.0% or less
  • W 0.01% or more and 2.0% or less
  • Cu, Ni, Sn, Sb, Mo, and W are elements that improve the corrosion resistance of a high Mn steel in a saltwater corrosion environment by being combined with Cr.
  • Cu, Sn, and Sb have an effect of suppressing a hydrogen generation reaction, which is a cathode reaction, by increasing a hydrogen overvoltage of a steel material.
  • Ni forms a precipitate coating on the steel material surface, Cl - physically inhibit the transmission of the corrosive anions such as base steel.
  • Cu, Ni, Sn, Sb, Mo and W are liberated as metal ions from the surface of the steel material during the corrosion, and the corrosion products are densified, whereby the corrosion to the steel interface (the interface between the rust layer and the ground iron) is reduced.
  • Mo and W are liberated as Mo 4 2 ⁇ and WO 4 2 ⁇ , respectively, and imparted to the cation selective permeability by being adsorbed in the corrosion product or on the steel sheet surface, and the permeation of corrosive anions to the iron base Is electrically suppressed.
  • the Cu content is in the range of 0.01% to 0.50%
  • the Ni content is in the range of 0.01% to 0.50%
  • the Sn content is in the range of 0.01% to 0.30%
  • the Sb content is in the range of 0.01% to 0.30%
  • the Mo content is in the range of 0.01% to 2.0%
  • the W content is in the range of 0.01% to 2.0%. Is preferred.
  • the Cu content is 0.02% to 0.40%
  • the Ni content is 0.02% to 0.40%
  • the Sn content is 0.02% to 0.25%
  • the Sb content is 0%.
  • Mo amount is 0.02% or more and 0.40% or less
  • W amount is 0.02% or more and 0.40% or less.
  • Ca 0.0005% or more and 0.0050% or less
  • Mg 0.0005% or more and 0.0100% or less
  • REM 0.0010% or more and 0.0200% or less.
  • Ca, Mg and REM are useful elements for controlling the morphology of inclusions, and can be contained as necessary.
  • the morphological control of inclusions means that expanded sulfide-based inclusions are used as granular inclusions. Through control of the inclusion morphology, ductility, toughness and sulfide stress corrosion cracking resistance can be improved.
  • Ca and Mg are contained at 0.0005% or more and REM is contained at 0.0010% or more.
  • REM is contained at 0.0010% or more.
  • the Ca content is 0.0010% to 0.0040%
  • the Mg content is 0.0010% to 0.0040%
  • the REM content is 0.0020% to 0.0150%.
  • the temperature of the material to be rolled in the hot rolling step and the cooling rate in the subsequent cooling step mean the temperature and the cooling rate measured on the surface of the rolled material. That is, after the steel material having the above-described composition is heated to 1000 ° C. or more and 1300 ° C. or less, hot rolling is performed at a reduction ratio of 3 or more and 30 or less and a finishing temperature of 750 ° C. or more and a material to be rolled: 950 ° C.
  • the steel sheet is manufactured by performing the cooling at a temperature of 700 ° C. or more and 600 ° C. or more at an average cooling rate of 3 ° C./s or more.
  • Step material heating temperature 1000 ° C to 1300 ° C
  • the reason why the steel material is heated to 1000 ° C. or higher is to make the carbonitride in the structure form a solid solution and make the crystal grain size and the like uniform. That is, if the heating temperature is lower than 1000 ° C., desired characteristics cannot be obtained because the carbonitride does not sufficiently form a solid solution. Further, when heating is performed at more than 1300 ° C., in addition to material deterioration due to coarsening of the crystal grain size, excessive energy is required and productivity is reduced. Therefore, the upper limit of the heating temperature is 1300 ° C.
  • the steel material it is preferable to use a steel material such as a slab or a billet by a conventionally known method such as an ingot-making method, in addition to the continuous casting slab. Needless to say, a process such as ladle refining and vacuum degassing may be added to the molten steel.
  • Cooling after hot rolling is performed when the average cooling rate at 700 ° C or lower and 600 ° C or higher is less than 3 ° C / s, since a large amount of precipitates such as Cr carbides are generated, the average cooling rate is 3 ° C / s or higher. limit. Preferably, it is in the range of 10 ° C / s or more and 150 ° C / s or less.
  • the residence time in a temperature range of 950 ° C. or lower and 600 ° C. or higher is restricted to 30 minutes or less, since it decreases to cause a decrease in corrosion resistance and a decrease in cryogenic toughness.
  • it is in the range from 5 minutes to 25 minutes.
  • the length of the material to be rolled is 5000 mm or less, and the reduction ratio in hot rolling from the material to be rolled is 30 or less. Is preferable. That is, if the length of the material to be rolled is 5000 mm or less and the rolling reduction is 30 or less, the rolling time is shortened, and as a result, the residence time in the range of 950 ° C. or less and 600 ° C. or more can be 30 minutes or less. .
  • the upper limit of the reduction ratio in hot rolling is preferably 30 or less.
  • the reduction ratio in hot rolling is less than 3, the effect of promoting recrystallization and reducing the size of the grains is reduced, so that coarse austenite grains remain, and the parts are preferentially oxidized, so that the corrosion resistance is reduced. There is a risk of deterioration. Therefore, it is preferable to set the reduction ratio in hot rolling to 3 or more.
  • the reduction ratio is defined as (the thickness of the rolled material to be subjected to hot rolling) / (the thickness of the steel sheet after hot rolling).
  • the corrosion resistance test was performed in accordance with the Slow Strain Rate Test Method (hereinafter, SSRT test) based on NACE Standard TM0111-2011. That is, the test piece was a Type A round bar notched test piece, 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 / s. Was carried out.
  • a rupture stress of 600 MPa or more is considered to be excellent in stress corrosion cracking resistance.
  • Table 2 shows the results obtained as described above.
  • the steel sheet according to the present invention (sample Nos. 1 to 42) had a corrosion resistance satisfying 600 MPa or more as a breaking stress in the SSRT test.
  • the comparative examples (sample Nos. 43 to 65) out of the range of the present invention do not satisfy the above-mentioned target performance in the stress corrosion cracking resistance.

Abstract

L'invention concerne un acier à teneur en Mn élevée, lequel présente une excellente résistance à la corrosion, et plus particulièrement à la corrosion dans un environnement de corrosion due au sel.　Cette tôle contient: de 0,20 à 0,70% de C, de 0,05 à 1,00% de Si, de 15,0 à 35,0% de Mn, au plus 0,030% de P, au plus 0,020% de S, de 0,010 à 0,100% de Al, de 0,5 à 8,0% de Cr, et de 0,0010 à 0,0300% de N, le reste étant constitué de Fe et d'inévitables impuretés, et au moins 60% du Cr susmentionné étant du Cr solide.
PCT/JP2019/030769 2018-08-15 2019-08-05 Tôle d'acier et procédé de production de celle-ci WO2020036090A1 (fr)

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EP19850397.1A EP3825436A1 (fr) 2018-08-15 2019-08-05 Tôle d'acier et procédé de production de celle-ci
JP2019568801A JP6904438B2 (ja) 2018-08-15 2019-08-05 鋼板およびその製造方法
KR1020217005489A KR102497359B1 (ko) 2018-08-15 2019-08-05 강판 및 그 제조 방법
CN201980051501.3A CN112513309B (zh) 2018-08-15 2019-08-05 钢板及其制造方法
PH12021550314A PH12021550314A1 (en) 2018-08-15 2021-02-11 Steel plate and method of producing same

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PH12021550314A1 (en) 2021-10-11
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CN112513309B (zh) 2022-04-26
KR20210035867A (ko) 2021-04-01
TWI702296B (zh) 2020-08-21
EP3825436A4 (fr) 2021-05-26
JPWO2020036090A1 (ja) 2020-08-20
EP3825436A1 (fr) 2021-05-26
WO2020035917A1 (fr) 2020-02-20
KR102497359B1 (ko) 2023-02-08
CN112513309A (zh) 2021-03-16

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