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EP3604591A1 - Matériau en acier inoxydable martensitique - Google Patents

Matériau en acier inoxydable martensitique Download PDF

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Publication number
EP3604591A1
EP3604591A1 EP18774332.3A EP18774332A EP3604591A1 EP 3604591 A1 EP3604591 A1 EP 3604591A1 EP 18774332 A EP18774332 A EP 18774332A EP 3604591 A1 EP3604591 A1 EP 3604591A1
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EP
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content
intermetallic compounds
oxides
steel product
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EP18774332.3A
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German (de)
English (en)
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EP3604591A4 (fr
Inventor
Daisuke Matsuo
Yusaku TOMIO
Hideki Takabe
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Nippon Steel Corp
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Nippon Steel Corp
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Publication of EP3604591A1 publication Critical patent/EP3604591A1/fr
Publication of EP3604591A4 publication Critical patent/EP3604591A4/fr
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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B23/00—Tube-rolling not restricted to methods provided for in only one of groups B21B17/00, B21B19/00, B21B21/00, e.g. combined processes planetary tube rolling, auxiliary arrangements, e.g. lubricating, special tube blanks, continuous casting combined with tube 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • hydrogen sulfide causes sulfide stress cracking (hereunder, referred to as "SSC") in steel pipes for oil well made of 13Cr steel with a high strength of, for example, 724 MPa or more.
  • 13Cr steel that has a high strength of 724 MPa or more has a higher susceptibility to SSC compared to low-alloy steel, and in the 13 Cr steel, SSC occurs even at a comparatively low hydrogen sulfide partial pressure (for example, less than 0.1 atm). Therefore, 13Cr steel is not suitable for use in the above-described highly corrosive environments containing carbon dioxide gas and hydrogen sulfide.
  • duplex stainless steel is expensive in comparison to 13Cr steel. Consequently, there is a required for a steel pipe for oil well casing, tubing and drilling that has a high yield strength of 724 MPa or more and high SSC resistance that can be used in highly corrosive environments.
  • Patent Literature 1 Japanese Patent Application Publication No. 10-503809
  • Patent Literature 2 Japanese Patent Application Publication No. 2003-003243
  • Patent Literature 4 International Application Publication No. WO 2004/057050
  • Patent Literature 5 Japanese Patent Application Publication No. 2000-192196
  • Patent Literature 6 Japanese Patent Application Publication No. 11-310855
  • Patent Literature 7 Japanese Patent Application Publication No. 08-246107
  • Patent Literature 8 Japanese Patent Application Publication No. 2012-136742
  • An objective of the present disclosure is to provide a martensitic stainless steel product having a yield strength of 724 MPa or more and having excellent SSC resistance.
  • the present inventors found for the first time that in a highly corrosive environment such as described above, strengthening a film by Ni decreases a hydrogen diffusion coefficient in the steel. If the hydrogen diffusion coefficient in the steel decreases, hydrogen is liable to stay in the steel product. Consequently, the SSC resistance of the steel product decreases.
  • the present inventors conducted further studies regarding Cr, Mo, Cu and Ni which are elements that influence SSC resistance. As a result, the present inventors discovered that excellent SSC resistance is obtained if, in a steel product having a chemical composition consisting of, in mass%, C: 0.030% or less, Si: 1.00% or less, Mn: 1.00% or less, P: 0.030% or less, S: 0.005% or less, Al: 0.0010 to 0.0100%, N: 0.0500% or less, Ni: 5.00 to 6.50%, Cr: 10.00 to 13.40%, Cu: 1.80 to 3.50%, Mo: 1.00 to 4.00%, V: 0.01 to 1.00%, Ti: 0.050 to 0.300%, Co: 0.300% or less and W: 0 to 1.50%, with the balance being Fe and impurities, a Cr content, a Mo content, a Cu content and a Ni content satisfy the following Formula (1): 11.5 ⁇ Cr + 2 ⁇ Mo + 2 ⁇ Cu ⁇ 1.5 ⁇ Ni ⁇ 14.
  • F1 is defined as being equal to Cr+2Mo+2Cu-1.5Ni.
  • FIG. 1 was obtained by means of examples that are described later.
  • the symbol “ ⁇ ” in FIG. 1 indicates that SSC did not occur in an SSC resistance evaluation test in the examples that are described later.
  • the symbol “ ⁇ ” in FIG. 1 indicates that SSC occurred in an SSC resistance evaluation test in the examples that are described later.
  • F1 is less than 11.5 or when F1 is more than 14.3, SSC resistance decreases. Accordingly, F1 is from 11.5 to 14.3.
  • the present inventors discovered that, in the steel product having the aforementioned chemical composition that satisfies Formula (1) and Formula (2), if the size of each intermetallic compound and the size of each Cr oxide in the microstructure is 5.0 ⁇ m 2 or less and the gross area fraction of the intermetallic compounds and the Cr oxides is 3.0% or less, the SSC resistance is further increased in the steel product having the aforementioned chemical composition that satisfies Formula (1) and Formula (2).
  • the intermetallic compounds and the Cr oxides can be identified by structural observation using an extraction replica method.
  • the total of the areas of the identified intermetallic compounds and the identified Cr oxides is taken as the gross area ( ⁇ m 2 ) of the intermetallic compounds and the Cr oxides.
  • the proportion of the gross area of the intermetallic compounds and the Cr oxides with respect to the area of the overall observation region is taken as the gross area fraction (%) of intermetallic compounds and the Cr oxides.
  • the microstructure contains martensite having an area fraction of 80% or more, the size of each intermetallic compounds and the size of each Cr oxides in the microstructure is 5.0 ⁇ m 2 or less and the gross area fraction of the intermetallic compounds and the Cr oxides in the microstructure is 3.0% or less, the strength of the steel product is adjustable to 724 to 860 MPa.
  • the chemical composition of the aforementioned martensitic stainless steel product may contain W: 0.10 to 1.50%.
  • Carbon (C) is unavoidably contained. That is, the C content is more than 0%. C increases the hardenability and raises the strength of the steel product. However, if the C content is too high, the strength of the steel product will be too high and the SSC resistance will decrease. Accordingly, the C content is 0.030% or less. It is preferable to make the C content as low as possible. However, if the C content is excessively reduced, the production cost increases. Therefore, when taking into consideration industrial production, a preferable lower limit of the C content is 0.0001%, and more preferably is 0.0005%. From the viewpoint of the strength of the steel product, a preferable lower limit of the C content is 0.002%, and more preferably is 0.005%. A preferable upper limit of the C content is 0.020%, and more preferably is 0.015%.
  • Co Cobalt
  • the Co content is more than 0%.
  • the ductility and toughness decrease if the Co content is too high. Accordingly, the Co content is 0.300% or less.
  • a preferable upper limit of the Co content is 0.270%, and more preferably is 0.250%.
  • the Co content is as low as possible. However, if the Co content is excessively reduced, the production cost increases. Therefore, when taking into consideration industrial production, a preferable lower limit of the Co content is 0.0001%, and more preferably is 0.0005%.
  • the chemical composition of the martensitic stainless steel product according to the present embodiment may further contain W in lieu of a part of Fe.
  • Tungsten (W) is an optional element, and need not be contained. That is, the W content may be 0%. If W is contained, W stabilizes the passive film and improve corrosion resistance. However, if the W content is too high, W binds with C to form fine carbides. The fine carbides raise the strength of the steel product by fine precipitation hardening, and as a result, lower the SSC resistance. Accordingly, the W content is 0 to 1.50%. A preferable lower limit of the W content is 0.10%, and more preferably is 0.20%. A preferable upper limit of the W content is 1.00%, and more preferably is 0.50%.
  • F1 is defined as being equal to Cr+2Mo+2Cu-1.5Ni.
  • F1 is an index of the SSC resistance of the steel product having the aforementioned chemical composition. Referring to FIG. 1 , the SSC resistance decreases if F1 is less than 11.5. It is considered that the reason the SSC resistance decreases in this case is that the Ni content which reduces the diffusion coefficient of hydrogen in the steel is too high relative to the content of Cr, Mo and Cu that dissolve and increase the SSC resistance. On the other hand, when F1 is more than 14.3, the SSC resistance also decreases.
  • F1 is from 11.5 to 14.3.
  • a preferable lower limit of F1 is 11.7.
  • a preferable upper limit of F1 is 14.0.
  • F2 is less than 7.5
  • the Ti content is too low relative to the C content. In that case, Ti is consumed to form nitrides such as TiN, and TiC cannot be formed sufficiently. Consequently, C is used for formation of VC, and the strength of the steel product is too high.
  • F2 is 7.5 or more
  • the Ti content is sufficiently high relative to the C content. As a result, Ti consumes C, and forms TiC with priority over VC. By this means, formation of VC can be suppressed. Therefore, the strength of the steel product can be kept from becoming too high. As a result, it can have excellent SSC resistance.
  • the yield strength of the martensitic stainless steel of the present embodiment is 724 to 860 MPa. If the yield strength is less than 724 MPa, the strength will not be sufficient for steel product that can be applied to a highly corrosive environment. On the other hand, if the yield strength is more than 860 MPa, as illustrated in FIG. 1 , SSC resistance decreases in the steel product having the aforementioned chemical composition. Accordingly, the yield strength of the martensitic stainless steel of the present embodiment is 724 to 860 MPa. A preferable upper limit of the yield strength is 850 MPa, and more preferably is 840 MPa. A preferable lower limit of the yield strength is 730 MPa, and more preferably is 740 MPa. In the present description, the term "yield strength" means a 0.2% proof stress.
  • intermetallic compound refers to a precipitate of an alloying element that precipitates after tempering.
  • the intermetallic compounds are, for example, Laves phase such as Fe 2 Mo, sigma phase ( ⁇ phase), or chi phase ( ⁇ phase).
  • size of an intermetallic compound refers to the area ( ⁇ m 2 ) of the intermetallic compound that is observed by a measurement that is described later.
  • intermetallic compounds other than the Laves phase, the ⁇ phase, and the ⁇ phase are extremely small, so there is no problem ignoring them.
  • Cr oxide refers to chromia (Cr 2 O 3 ).
  • size of a Cr oxide refers to the area ( ⁇ m 2 ) of the Cr oxide that is observed by a measurement that is described later.
  • each intermetallic compound and the size of each Cr oxide is 5.0 ⁇ m 2 or less, the intermetallic compounds and Cr oxides do not affect the SSC resistance.
  • the size of the intermetallic compounds and the size of each Cr oxide is 1.0 ⁇ m 2 , 2.0 ⁇ m 2 , or even 5.0 ⁇ m 2 , the intermetallic compounds and Cr oxides do not affect the SSC resistance.
  • the size of each intermetallic compound and Cr oxide is 5.0 ⁇ m 2 or less, if the gross area fraction of intermetallic compounds and Cr oxides is more than 3.0%, the intermetallic compounds and Cr oxides remarkably affect the SSC resistance.
  • a test specimen having dimensions of 15 mm ⁇ 15 mm ⁇ 15 mm is extracted from a center position in the thickness direction of the martensitic stainless steel product.
  • the term "center position in the thickness direction” refers to a center position with respect to the plate thickness
  • the term "center position in the thickness direction” refers to a center position with respect to the wall thickness.
  • One test specimen is extracted from a front end portion (top portion) and one test specimen is extracted from a rear end portion (bottom portion) in the longitudinal direction of the steel product.
  • the term “front end portion” refers to, in a case where the steel product is divided equally into 10 sections in the longitudinal direction, the section at the front end, and the term “rear end portion” refers to the section at the rear end.
  • the extraction replica film is a disk shape with a diameter of 3 mm.
  • An arbitrary region of 10 ⁇ m 2 is observed at four places (four visual fields) at a magnification of 20,000 times on each extraction replica film using a TEM (transmission electron microscope). In other words, regions at eight places are observed for each steel product.
  • a test specimen having dimensions of 15 mm ⁇ 15 mm ⁇ a thickness of 2 mm was extracted from each plate material.
  • the volume ratio (%) of retained austenite was determined by the aforementioned X-ray diffraction method, and a value obtained when the volume ratio of retained austenite was subtracted from 100% was defined as the volume ratio (%) of martensite.
  • a test specimen having dimensions of 15 mm ⁇ 15 mm ⁇ 15 mm was extracted from a center position of the thickness of each plate.
  • One of the aforementioned test specimens was extracted from a front end portion (top portion) and one of the test specimens was extracted from a rear end portion (bottom portion) in the longitudinal direction of the plate.
  • the term "front end portion” refers to, in a case where the steel product is divided equally into 10 sections in the longitudinal direction, the section at the front end, and the term “rear end portion” refers to the section at the rear end.
  • Intermetallic compounds were identified based on contrast that was distinguished by means of backscattered electron images of the respective observation regions.
  • the respective areas ( ⁇ m 2 ) of the identified intermetallic compounds and the respective Cr oxides were taken as the sizes of the respective intermetallic compounds and the respective Cr oxides.
  • the total of the areas of the identified intermetallic compounds and the identified Cr oxides was taken as the gross area ( ⁇ m 2 ) of the intermetallic compounds and Cr oxides.
  • the ratio of the gross area of the intermetallic compounds and the Cr oxides with respect to the gross area (80 ⁇ m 2 ) of the overall observation region was defined as the gross area fraction (%) of the intermetallic compounds and the Cr oxides.
  • TM indicates that the volume ratio of martensite in the microstructure was 80% or more, the size of each intermetallic compound in the microstructure was 5.0 ⁇ m 2 or less, the size of each Cr oxide in the microstructure was 5.0 ⁇ m 2 or less and the gross area fraction of intermetallic compounds and Cr oxides in the microstructure was 3.0% or less.
  • TM+I indicates that although the volume ratio of martensite in the microstructure was 80% or more, intermetallic compounds or Cr oxides having a size that was more than 5.0 ⁇ m 2 were present in the microstructure and/or the gross area fraction of intermetallic compounds and Cr oxides in the microstructure was more than 3.0%.
  • the Ni content was high, the Cu content was low, and the tempering temperature was too low. Consequently, an intermetallic compound more than 5.0 ⁇ m 2 was observed and the gross area fraction of the intermetallic compounds and Cr oxides was more than 3.0%. As a result, the yield strength was 860 MPa or more and the SSC resistance was low.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
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  • Manufacturing & Machinery (AREA)
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EP18774332.3A 2017-03-28 2018-03-27 Matériau en acier inoxydable martensitique Pending EP3604591A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2017062539 2017-03-28
PCT/JP2018/012601 WO2018181404A1 (fr) 2017-03-28 2018-03-27 Matériau en acier inoxydable martensitique

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EP3604591A1 true EP3604591A1 (fr) 2020-02-05
EP3604591A4 EP3604591A4 (fr) 2020-09-02

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EP (1) EP3604591A4 (fr)
JP (1) JP6787483B2 (fr)
CN (1) CN110462085A (fr)
MX (1) MX2019011443A (fr)
RU (1) RU2718019C1 (fr)
WO (1) WO2018181404A1 (fr)

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EP3845680A4 (fr) * 2018-11-05 2021-12-01 JFE Steel Corporation Tube en acier inoxydable martensitique sans soudure pour tuyaux de puits de pétrole, et son procédé de fabrication
US11401570B2 (en) 2017-09-29 2022-08-02 Jfe Steel Corporation Martensitic stainless steel seamless pipe for oil country tubular goods, and method for manufacturing same
EP3533892B1 (fr) * 2016-10-25 2022-11-02 JFE Steel Corporation Seamless pipe of martensitic stainless steel for oil well pipe, and method for producing seamless pipe
EP4130317A4 (fr) * 2020-04-01 2023-05-17 Nippon Steel Corporation Matériau en acier
US11827949B2 (en) 2017-09-29 2023-11-28 Jfe Steel Corporation Martensitic stainless steel seamless pipe for oil country tubular goods, and method for manufacturing same
EP4137591A4 (fr) * 2020-04-13 2025-03-05 Nippon Steel Corporation Acier inoxydable martensitique, et procédé de production d'acier inoxydable martensitique
EP4134462A4 (fr) * 2020-04-07 2025-03-12 Nippon Steel Corporation Tuyau d'acier inoxydable martensitique sans soudure

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Publication number Priority date Publication date Assignee Title
MX2020002857A (es) * 2017-09-29 2020-07-24 Jfe Steel Corp Tubo sin costura de acero inoxidable martensitico para productos tubulares de region petrolifera, y metodo para la fabricacion del mismo.
WO2020071344A1 (fr) * 2018-10-02 2020-04-09 日本製鉄株式会社 Tuyau sans soudure en acier inoxydable à base de martensite
EP3862455A4 (fr) * 2018-10-02 2022-06-15 Nippon Steel Corporation Tuyau sans soudure en acier inoxydable à base de martensite
JP7200869B2 (ja) * 2019-07-24 2023-01-10 日本製鉄株式会社 ステンレス鋼管の製造方法
EP4006177B1 (fr) * 2019-07-24 2024-02-28 Nippon Steel Corporation Tuyau en acier inoxydable martensitique et procédé de fabrication de tuyau en acier inoxydable martensitique
JP7215369B2 (ja) * 2019-07-24 2023-01-31 日本製鉄株式会社 マルテンサイト系ステンレス鋼管の製造方法
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JPWO2018181404A1 (ja) 2019-12-12
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JP6787483B2 (ja) 2020-11-18
WO2018181404A1 (fr) 2018-10-04

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