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WO2025013402A1 - Tuyau sans soudure en acier inoxydable martensitique et procédé de production associé - Google Patents

Tuyau sans soudure en acier inoxydable martensitique et procédé de production associé Download PDF

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Publication number
WO2025013402A1
WO2025013402A1 PCT/JP2024/017796 JP2024017796W WO2025013402A1 WO 2025013402 A1 WO2025013402 A1 WO 2025013402A1 JP 2024017796 W JP2024017796 W JP 2024017796W WO 2025013402 A1 WO2025013402 A1 WO 2025013402A1
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content
stainless steel
martensitic stainless
pipe
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Japanese (ja)
Inventor
広泰 海老名
健一郎 江口
信介 井手
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JFE Steel Corp
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JFE Steel Corp
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Publication of WO2025013402A1 publication Critical patent/WO2025013402A1/fr
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • the present invention relates to martensitic stainless steel seamless pipes and their manufacturing method.
  • CCS carbon capture and storage
  • SCC stress corrosion cracking
  • SSC sulfide stress corrosion cracking
  • Patent Documents 1 and 2 In response to such demands, there are techniques as described in, for example, Patent Documents 1 and 2.
  • the SSC resistance can be improved by setting the Cr content, Mo content, Cu content, and Ni content of the improved 13Cr steel within the range of 11.5 ⁇ Cr+2Mo+2Cu-1.5Ni ⁇ 14.3, and that the SSC resistance can be improved by suppressing the formation of V carbides by setting the Ti content and C content to Ti/C ⁇ 7.5.
  • the SSC resistance can be further improved by setting the size of each intermetallic compound and each Cr oxide that is the starting point of SSC to 5.0 ⁇ m 2 or less, and setting the total area ratio of the intermetallic compound and the Cr oxide to 3.0% or less.
  • the composition of the improved 13Cr steel satisfies -35 ⁇ -109.37C+7.307Mn+6.399Cr+6.329Cu+11.343Ni-13.529Mo+1.276W+2.925Nb+196.775N-2.621Ti-120.307 ⁇ 45, which reduces the amount of residual gamma, thereby reducing hardness and improving SSC resistance.
  • Patent Documents 1 and 2 discuss technologies to improve SSC resistance from the perspective of chemical composition, structure, and precipitates. However, neither document examines the prevention of the growth of localized corrosion, which is the starting point of SSC.
  • the present invention was made in consideration of the above circumstances, and aims to provide a martensitic stainless steel seamless pipe that has a yield strength of 758 MPa or more and excellent local corrosion resistance, and a manufacturing method thereof.
  • the inventors conducted extensive research into the effects of alloying elements on the corrosion rate in an environment simulating the inside of a crevice or pit, where the pH is low and the chloride ion concentration is high, using martensitic stainless steel pipe as the base composition.
  • a method for producing a martensitic stainless steel seamless pipe according to [1] or [2],
  • the steel pipe material having the above-mentioned composition is heated at a heating temperature of 1200 to 1300°C and subjected to pipe-making to obtain a steel pipe;
  • the steel pipe is subjected to a quenching treatment in which the steel pipe is heated to a quenching temperature of 920 to 1200°C and then cooled to room temperature.
  • a tempering treatment is performed at a tempering temperature of 550 to 640°C, in accordance with the method for producing a martensitic stainless steel seamless pipe.
  • the present invention provides a martensitic stainless steel seamless pipe and a manufacturing method thereof that has a yield strength of 758 MPa or more and excellent localized corrosion resistance in low pH and high chloride ion concentration environments in crevice and pitting.
  • a yield strength of 758 MPa or more and excellent localized corrosion resistance in low pH and high chloride ion concentration environments in crevice and pitting.
  • by suppressing localized corrosion it is possible to suppress the occurrence of SCC and SSC that originate from localized corrosion.
  • C 0.050% or less C is an element that enhances hardenability and increases the strength of steel. However, if the C content is too high, the martensite start temperature (Ms point) decreases, martensitic transformation does not occur at room temperature, and as a result, strength cannot be ensured. Therefore, the C content is 0.050% or less.
  • the C content is preferably 0.040% or less, and more preferably 0.035% or less. From the viewpoint of ensuring strength, the C content is preferably 0.0050% or more, and more preferably 0.010% or more.
  • Si 1.00% or less Si is an element that acts as a deoxidizer. On the other hand, a Si content of more than 1.00% reduces carbon dioxide corrosion resistance and hot workability. Therefore, the Si content is 1.00% or less. The Si content is preferably 0.30% or less. From the viewpoint of ensuring stable strength, the Si content is preferably 0.10% or more.
  • Mn 1.00% or less Mn is an element that improves hot workability and strength. On the other hand, excessive addition of Mn causes MnS to precipitate, which reduces sulfide stress corrosion cracking resistance. Therefore, the Mn content is 1.00% or less.
  • the Mn content is preferably 0.50% or less, and more preferably 0.40% or less. In order to ensure the strength required in the present invention, the Mn content is preferably 0.10% or more.
  • P 0.030% or less
  • P is an element that reduces carbon dioxide corrosion resistance, and in the present invention, it is desirable to reduce it as much as possible. Therefore, the P content is limited to 0.030% or less.
  • the P content is preferably 0.015% or less. There is no particular lower limit for the P content. However, since an extreme reduction leads to an increase in manufacturing costs, it is preferable that the P content be 0.005% or more.
  • S 0.005% or less
  • S is an element that significantly reduces hot workability, so it is desirable to reduce it as much as possible.
  • the S content is preferably 0.002% or less.
  • the lower limit of the S content is not particularly limited. However, since excessive reduction leads to an increase in manufacturing costs, the S content is preferably 0.0005% or more.
  • Cu 3.00% or less
  • Cu is an element that strengthens the protective coating and improves carbon dioxide corrosion resistance.
  • a Cu content of more than 3.00% reduces hot workability due to precipitation of metallic Cu. Therefore, the Cu content is 3.00% or less.
  • the Cu content is preferably 2.60% or less. From the viewpoint of effectively obtaining the above-mentioned effects, the Cu content is preferably 1.00% or more.
  • Ni 3.00-10.00%
  • Ni is an element that strengthens the protective film, improves the carbon dioxide gas corrosion resistance, and further increases the strength of the steel by dissolving in solid solution. In order to obtain such effects, Ni should be present in a content of 3.00% or more. Ni is required. On the other hand, if the Ni content exceeds 10.00%, the austenite phase becomes energetically stable, which reduces the stability of the martensite phase and decreases the strength. Therefore, The Ni content is limited to 3.00 to 10.00%.
  • the Ni content is preferably 5.00% or more, and more preferably 8.00% or less.
  • the Ni content is more preferably is less than 7.00%.
  • Cr:10.00 ⁇ 20.00% Cr is an element that forms a protective film to improve carbon dioxide corrosion resistance, and a content of 10.00% or more can ensure the carbon dioxide corrosion resistance required for oil well tubular goods and CCS injection tubular goods. If Cr is contained in excess, the Ms point decreases, and the martensite phase cannot be stably maintained, resulting in a decrease in strength. Therefore, the Cr content is limited to 10.00 to 20.00%. The content is preferably 11.00% or more, and more preferably 12.00% or more. The Cr content is preferably 17.00% or less, and more preferably 15.00% or less. .
  • Al 0.100% or less
  • Al is an element that acts as a deoxidizer. In order to obtain such an effect, it is effective to contain 0.01% or more of Al. However, since an Al content exceeding 0.100% adversely affects toughness due to excessive precipitation of oxides, the Al content in the present invention is limited to 0.100% or less.
  • the Al content is preferably 0.040% or less.
  • the Al content is preferably 0.010% or more.
  • the Al content in the present invention means the total Al content.
  • Mo 1.00-4.00%
  • Mo is an element that improves localized corrosion resistance by forming a dense corrosion product film.
  • a Mo content of 1.00% or more is required.
  • Mo should be contained in a range of 1.00 to 4.00%.
  • the Mo content is preferably 1.40% or more, and more preferably 3.00% or more.
  • the Mo content is preferably 3.60% or less.
  • V 1.00% or less
  • V is an element that improves the strength of steel by precipitation strengthening.
  • the V content in the present invention is limited to 1.00% or less.
  • the V content is preferably 0.07% or less. From the viewpoint of effectively obtaining the above-mentioned effects, the V content is preferably 0.01% or more.
  • Ti 0.050% or less
  • Ti is an element that forms TiN and covers oxide-based or sulfide-based inclusions, thereby suppressing the occurrence of pitting corrosion.
  • the Ti content is set to 0.050% or less.
  • the Ti content is preferably 0.020% or less. From the viewpoint of effectively obtaining the above-mentioned effects, the Ti content is preferably 0.001% or more.
  • Nb 0.300% or less
  • Nb is an element that can form carbides, thereby reducing solute carbon and improving the Ms point.
  • excessive Nb content may reduce toughness due to precipitation of carbides and nitrides.
  • the Nb content is set to 0.300% or less.
  • the Nb content is preferably 0.100% or less.
  • the Nb content may be 0%. From the viewpoint of effectively obtaining the above-mentioned effects, the Nb content is preferably 0.005% or more, and more preferably 0.050% or more.
  • N 0.100% or less
  • N is an element that has the effect of increasing strength by dissolving in steel.
  • the N content in the present invention is limited to 0.100% or less.
  • the N content is preferably 0.050% or less. From the viewpoint of effectively obtaining the above-mentioned effects, the N content is preferably 0.005% or more, and more preferably 0.010% or more.
  • W 4.00% or less W is an element that improves local corrosion resistance by generating a dense corrosion product film.
  • excessive W content may precipitate intermetallic compounds and reduce toughness and local corrosion resistance.
  • the W content is set to 4.00% or less.
  • the W content is preferably 3.00% or less, and more preferably 2.00% or less.
  • the W content may be 0%. From the viewpoint of effectively obtaining the above-mentioned action, the W content is preferably 1.0% or more.
  • Co is an element that improves local corrosion resistance by forming a dense corrosion product film, and in order to obtain this effect, a Co content of 0.010% or more is necessary. If Co is added in excess of 4.500%, the manufacturing cost will increase. Therefore, the Co content is set to 0.010 to 4.500%.
  • the Co content is preferably 0.20% or more. and preferably 4.00% or less.
  • the Co content is more preferably 0.40% or more and more preferably 3.00% or less.
  • the contents of C, Cu, Ni, Cr, Mo, Nb, N, W and Co are within the above ranges and each element is contained so as to satisfy the following formula (1). 999.65-2276.19 ⁇ C-17.36 ⁇ Cu-44.80 ⁇ Ni-34.12 ⁇ Cr-23.22 ⁇ Mo+80.11 ⁇ Nb-932.00 ⁇ N-19.18 ⁇ W-1.77 ⁇ Co>35.00...(1)
  • the content (mass%) of the corresponding element is substituted for each element symbol in formula (1), and the content of an element that is not contained is set to zero.
  • Equation (1) is an equation that correlates with the Ms point, and was derived by the inventors as a result of extensive research.
  • the free energy difference between the austenite phase and the martensite phase in the region of 35°C to 300°C becomes greater than the energy required for deformation associated with transformation.
  • martensite transformation occurs even when cooled to room temperature in the quenching process described below, and sufficient strength can be ensured.
  • the value of the left side of equation (1) (the value of "999.65-2276.19 x C-17.36 x Cu-44.80 x Ni-34.12 x Cr-23.22 x Mo + 80.11 x Nb-932.00 x N-19.18 x W-1.77 x Co") is set to be greater than 35.00.
  • the value of the left side of equation (1) is preferably 45.00 or more, and more preferably 55.00 or more. There is no particular upper limit for the value on the left side of formula (1). From the viewpoint of reducing the cost of reducing C and N, the value on the left side of formula (1) is preferably 300.00 or less, and more preferably 200.00 or less.
  • Mo, W and Co are further contained so as to satisfy the following formula (2).
  • the content (mass%) of the corresponding element is substituted for each element symbol in formula (2), and the content of an element that is not contained is set to zero.
  • Equation (2) is an equation that correlates with localized corrosion resistance, and was derived by the inventors as a result of extensive research. By satisfying this equation, a dense corrosion product film is generated, and excellent localized corrosion resistance can be obtained. Therefore, the value on the left side of equation (2) (the value of "1.6 x Mo + 1.35 x W + 2.38 x Co") is set to be greater than 7.50.
  • the value on the left side of equation (2) is preferably 7.80 or more, and more preferably 8.00 or more. There is no particular upper limit for the value on the left side of equation (2). Since excessive alloy addition promotes the precipitation of intermetallic compounds, the value on the left side of equation (2) is preferably 20.00 or less.
  • the present invention uses a test liquid of 5.4 mass% CrCl3 solution (pH: 2.1, liquid temperature: 25°C, H2S : 0.1 bar, CO2 : 0.9 bar). That is, in the present invention, a corrosion rate of 2.5 mm/y or less when a test piece is immersed in this environment (i.e., in this test liquid) for 24 hours is considered to be "excellent in local corrosion resistance.” The method for measuring this corrosion rate will be described in detail in the examples below.
  • the remainder other than the above components consists of Fe and unavoidable impurities.
  • the above-mentioned components are the basic components, and the martensitic stainless steel seamless steel pipe of the present invention can obtain the desired characteristics with these basic components.
  • the present invention can contain the following optional elements as necessary.
  • the following Ta and REM components can be contained as necessary, so these components may be 0%.
  • Ta 1.00% or less and REM: 0.200% or less
  • Ta 1.00% or less
  • Ta is an element that suppresses the occurrence of pitting corrosion by precipitating nitrides together with Ti and covering oxide-based or sulfide-based inclusions, and can be selectively included as necessary.
  • the Ta content is 1.00% or less.
  • the Ta content is preferably 0.70% or less.
  • the Ta content is preferably 0.10% or more.
  • REM 0.200% or less
  • REM rare earth metal
  • the REM content is set to 0.200% or less.
  • the REM content is preferably 0.100% or less, and more preferably 0.060% or less.
  • the REM content is preferably 0.001% or more.
  • the steel pipe structure of the present invention has martensite as the main phase.
  • “main phase” refers to a volume fraction of 55% or more of the entire steel pipe structure.
  • the volume fraction is preferably 95% or less.
  • the steel pipe structure may contain a ferrite phase having a volume fraction of 40% or less in addition to the martensite phase. Since the ferrite phase is soft, if the volume fraction of the ferrite phase exceeds 40%, the strength of the steel decreases.
  • the volume fraction of the ferrite phase is preferably 30% or less, and more preferably 10% or less. There is no particular lower limit for the ferrite phase, but for stable production, the volume fraction is preferably 0.1% or more, and more preferably 1.0% or more.
  • the steel may also contain a retained austenite phase having a volume fraction of 40% or less. Since the austenite phase is soft, if the volume fraction of the retained austenite phase exceeds 40%, the strength of the steel decreases.
  • the volume fraction of the retained austenite phase is preferably 30% or less, and more preferably 20% or less. There is no particular lower limit for the retained austenite phase, but for stable production, the volume fraction is preferably 1% or more, and more preferably 5% or more.
  • the temperature (°C) refers to the surface temperature of the steel pipe material and the steel pipe (i.e., the seamless steel pipe after pipe making) unless otherwise specified. These surface temperatures can be measured with a radiation thermometer, etc.
  • a steel pipe material having the above-mentioned composition is used.
  • the manufacturing method of the steel pipe material it is preferable to melt molten steel having the above-mentioned composition using a melting method such as a converter, and then turn it into a steel pipe material such as a billet using a method such as continuous casting or ingot casting and blooming rolling.
  • the above steel pipe material is heated, and in the pipe-making process, the heated steel pipe material is made into a hollow blank tube using a piercing machine using the Mannesmann plug mill method or the Mannesmann mandrel mill method, and then hot processed and made into a pipe.
  • a seamless steel pipe with the above-mentioned chemical composition and the desired dimensions i.e., specified shape
  • seamless steel pipes can also be made by hot extrusion using a press method.
  • the heating temperature is preferably in the range of 1200 to 1300°C. If the heating temperature is less than 1200°C, large stress is required for deformation, making it difficult to manufacture steel pipes. On the other hand, if the heating temperature exceeds 1300°C and becomes too high, the amount of ferrite becomes excessive, reducing the workability of the steel, making it difficult to manufacture steel pipes. Also, from the viewpoint of temperature uniformity and heating costs, it is preferable to set the heating time at the heating temperature to 10 to 200 minutes.
  • the above heating process may be carried out one or more times during the pipe-making process.
  • the seamless steel pipe After pipe making, it is preferable to cool the seamless steel pipe to room temperature at a cooling rate faster than air cooling. This causes martensitic transformation and allows the desired strength to be obtained.
  • the seamless steel pipe (hereinafter referred to as “steel pipe”) is subjected to quenching and tempering treatments.
  • Quenching treatment Specifically, the steel pipe is subjected to a quenching treatment in which the steel pipe is heated to a quenching temperature of 920° C. to 1200° C., held at that temperature for a predetermined period of time, and then cooled until the surface temperature of the steel pipe reaches room temperature.
  • the quenching temperature is less than 920°C, the melting temperature of the precipitated intermetallic compounds may not be reached, and the desired local corrosion resistance cannot be achieved. Therefore, the quenching temperature is limited to 920°C or higher.
  • the quenching temperature is preferably 950°C or higher. If the quenching temperature exceeds 1200°C, the structure becomes coarse and the strength of the steel decreases. Therefore, the quenching temperature is limited to 1200°C or lower.
  • the quenching temperature is preferably 1170°C or lower.
  • This holding time is preferably 300 minutes or less.
  • cooling can be performed by air cooling or water cooling.
  • air cooling refers to a cooling rate of 0.05°C/sec or more and 20°C/sec or less
  • water cooling refers to a cooling rate of 5°C/sec or more and 100°C/sec or less.
  • the quenched steel pipe is subjected to a tempering treatment. Specifically, the steel pipe is heated to a temperature of 550° C. to 640° C. (i.e., the tempering temperature), held for a predetermined time, and then air-cooled.
  • a tempering treatment Specifically, the steel pipe is heated to a temperature of 550° C. to 640° C. (i.e., the tempering temperature), held for a predetermined time, and then air-cooled.
  • the tempering temperature is limited to 640°C or lower.
  • the tempering temperature is preferably 620°C or lower. If the tempering temperature is lower than 550°C, carbides will precipitate, reducing pitting corrosion resistance. Therefore, the tempering temperature is limited to 550°C or higher.
  • the tempering temperature is preferably 580°C or higher.
  • the above tempering temperature for 10 minutes or more. This holding time is preferably 200 minutes or less.
  • test specimens were immersed in a test liquid: a 5.4 mass% CrCl3 aqueous solution (pH: 2.1, liquid temperature: 25°C, H2S : 0.1 bar, CO2 : 0.9 bar), and the test period (immersion period) was set to 24 hours.
  • This corrosion test simulates the environment inside a crevice or pitting corrosion, which has a low pH and a high chloride ion concentration.
  • the weight of the test specimens after the test was measured, and the corrosion rate was calculated from the weight loss before and after the corrosion test.
  • a corrosion rate of 2.50 mm/y or less was considered to be pass, and a corrosion rate of more than 2.50 mm/y was considered to be fail.
  • a test piece for microstructure observation was prepared from each test material, and each structure was measured.
  • the observation surface of the structure was a cross section (C cross section) perpendicular to the rolling direction.
  • the test piece for microstructure observation was corroded with Villela's reagent (specifically, a reagent in which picric acid, hydrochloric acid, and ethanol were mixed in the ratio of 2 g, 10 ml, and 100 ml, respectively), and the structure was photographed with an optical microscope. At this time, the magnification was set to 400 times.
  • the structure fraction (area %) of the ferrite phase was calculated using an image analyzer.
  • the area ratio of the ferrite phase was regarded as the volume fraction (%) of the ferrite phase.
  • the X-ray diffraction specimen was ground and electrolytically polished so that the cross section (C cross section) perpendicular to the rolling direction was the measurement surface, and the amount of retained austenite ( ⁇ ) was measured using an X-ray diffraction method.
  • the amount of retained austenite was calculated by measuring the integrated intensity of diffracted X-rays from the (200), (220), and (311) faces of ⁇ and the (200) and (211) faces of ⁇ (ferrite), and converting it using the following formula.
  • ⁇ (volume ratio) 100/(1+(I ⁇ R ⁇ /I ⁇ R ⁇ ))
  • I ⁇ is the integrated intensity of ⁇
  • R ⁇ is the theoretically calculated value of ⁇
  • I ⁇ is the integrated intensity of ⁇
  • R ⁇ is the theoretically calculated value of ⁇
  • All of the examples of the present invention had a yield strength (YS) of 758 MPa or more, and were excellent in localized corrosion resistance in a low pH and high chloride ion concentration environment.
  • the comparative examples outside the range of the present invention did not achieve the desired value for at least one of the yield strength (YS) and localized corrosion resistance.
  • the steel material of this invention is useful as an oil well pipe material and a CCS injection pipe material, which require high strength and localized corrosion resistance.

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Abstract

L'invention concerne un tuyau sans soudure en acier inoxydable martensitique et son procédé de production. Le tuyau sans soudure en acier inoxydable martensitique selon la présente invention est composé de manière à contenir C, Si, Mn, P, S, Cu, Ni, Cr, Al, Mo, V, Ti, Nb, N, W et Co, et satisfait les formules (1) et (2), le reste étant du Fe et des impuretés inévitables, et a une limite d'élasticité supérieure ou égale à 758 MPa. (1) : 999,65-2276,19 × C-17,36 × Cu-44,80 × Ni-34,12 × Cr-23,22 × Mo + 80,11 × Nb-932,00 × N-19,18 × W-1,77 × Co > 35,00 (2) : 1,6 × Mo + 1,35 × W + 2,38 × Co > 7,50
PCT/JP2024/017796 2023-07-07 2024-05-14 Tuyau sans soudure en acier inoxydable martensitique et procédé de production associé Pending WO2025013402A1 (fr)

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WO2018020886A1 (fr) * 2016-07-27 2018-02-01 Ｊｆｅスチール株式会社 Tube en acier inoxydable sans soudure de haute résistance destiné aux puits de pétrole et son procédé de production
JP2018524472A (ja) * 2015-06-29 2018-08-30 ヴァルレック オイル アンド ガス フランス 耐食鋼、耐食鋼の製造方法、及び使用
WO2018181404A1 (fr) 2017-03-28 2018-10-04 新日鐵住金株式会社 Matériau en acier inoxydable martensitique
WO2019225280A1 (fr) 2018-05-25 2019-11-28 Ｊｆｅスチール株式会社 Tube en acier sans soudure en acier inoxydable martensitique pour tubes de puits de pétrole, et son procédé de production
WO2020202957A1 (fr) * 2019-03-29 2020-10-08 Ｊｆｅスチール株式会社 Tuyau en acier inoxydable sans soudure
WO2024063108A1 (fr) * 2022-09-21 2024-03-28 日本製鉄株式会社 Matériau en acier inoxydable martensitique

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JP2018524472A (ja) * 2015-06-29 2018-08-30 ヴァルレック オイル アンド ガス フランス 耐食鋼、耐食鋼の製造方法、及び使用
WO2018020886A1 (fr) * 2016-07-27 2018-02-01 Ｊｆｅスチール株式会社 Tube en acier inoxydable sans soudure de haute résistance destiné aux puits de pétrole et son procédé de production
CN106756605A (zh) * 2016-12-13 2017-05-31 中国石油化工股份有限公司 一种高强度抗腐蚀管线管及其制造方法
WO2018181404A1 (fr) 2017-03-28 2018-10-04 新日鐵住金株式会社 Matériau en acier inoxydable martensitique
WO2019225280A1 (fr) 2018-05-25 2019-11-28 Ｊｆｅスチール株式会社 Tube en acier sans soudure en acier inoxydable martensitique pour tubes de puits de pétrole, et son procédé de production
WO2020202957A1 (fr) * 2019-03-29 2020-10-08 Ｊｆｅスチール株式会社 Tuyau en acier inoxydable sans soudure
WO2024063108A1 (fr) * 2022-09-21 2024-03-28 日本製鉄株式会社 Matériau en acier inoxydable martensitique

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