EP2060644A1 - Martensitischer nichtrostender stahl - Google Patents

Martensitischer nichtrostender stahl Download PDF

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Publication number
EP2060644A1
EP2060644A1 EP07792794A EP07792794A EP2060644A1 EP 2060644 A1 EP2060644 A1 EP 2060644A1 EP 07792794 A EP07792794 A EP 07792794A EP 07792794 A EP07792794 A EP 07792794A EP 2060644 A1 EP2060644 A1 EP 2060644A1
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EP
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Prior art keywords
mpa
stainless steel
martensitic stainless
content
yield stress
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EP07792794A
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English (en)
French (fr)
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EP2060644A4 (de
Inventor
Hideki Takabe
Tomoki Mori
Masakatsu Ueda
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Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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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
    • C22C38/44—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
    • C22C38/001—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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • 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
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes

Definitions

  • the present invention relates to martensitic stainless steel and more specifically to martensitic stainless steel for use in a corroding environment containing a corroding substance such as hydrogen sulfide, carbon dioxide gas, and chlorine ions.
  • a corroding substance such as hydrogen sulfide, carbon dioxide gas, and chlorine ions.
  • oil wells Steel products used as oil country tubular goods in these deep oil wells and gas wells (hereinafter collectively referred to as "oil wells") need high yield stress. Steel materials recently used for oil country tubular goods have a yield stress of 110 ksi grade (at which 0.6% total elongation yield stress is from 758 MPa to 862 MPa).
  • steel containing many alloy components is used for oil wells.
  • SUS420 martensitic stainless steel having carbon dioxide gas corrosion resistance is used for an oil well containing carbon dioxide gas.
  • the SUS420 martensitic stainless steel is not suited for an oil well containing hydrogen sulfide because its SSC resistance against hydrogen sulfide is low.
  • Patent Document 1 JP 5-287455 A discloses martensitic stainless steel for oil wells having high SSC resistance and high carbon dioxide gas corrosion resistance in an oil well containing substances such as hydrogen sulfide and carbon dioxide gas. In order to improve the SSC resistance, it is effective to reduce the tensile stress. Therefore, according to the disclosure of Patent Document 1, the tensile stress of the martensitic stainless steel is reduced, so that high SSC resistance is provided. Furthermore, variation in the tensile stress after tempering is reduced by reducing the tensile stress.
  • the martensitic stainless steel for oil wells disclosed by Patent Document 1 is designed to have low tensile stress. Therefore, when the yield stress of the steel is of 110 ksi grade (from 758 MPa to 832 MPa), the value produced by subtracting the yield stress from the tensile stress is less than 20.7 MPa.
  • a steel product for an oil country tubular good also needs the SSC resistance as described above. If the hardness of the same one steel product greatly varies, the SSC resistance is reduced. Therefore, the hardness variation of a steel product for an oil country tubular good must be suppressed.
  • the inventors produced a plurality of kinds of martensitic stainless steel containing, in percent by mass, 0.010% to 0.030% C, 0.30% to 0.60% Mn, at most 0.040% P, at most 0.0100% S, 10.00% to 15.00% Cr, 2.50% to 8.00% Ni, 1.00% to 5.00% Mo, 0.050% to 0.250% Ti, at most 0.25% V, at most 0.07% N, and at least one kind of at most 0.50% Si, and at most 0.10% Al, the balance consisted of Fe and impurities, and Ti/C was from 7.4 to 10.7.
  • Fig. 1 The result of examination is given in Fig. 1 .
  • the abscissa in Fig. 1 represents Ti/C, and the ordinate represents TS-YS (ksi).
  • Ti/C and TS-YS indicated a negative correlation. More specifically, as Ti/C was reduced, TS-YS increased. Based on this new finding, the inventors found that TS-YS ⁇ 20.7 MPa (3 ksi) can be satisfied by satisfying the following Expression (A): Ti / C ⁇ 10.1 where the element symbols represent the contents of these elements (% by mass).
  • the inventors newly found that when Ti/C is too small, the hardness greatly varies. More specifically, they found that when Ti/C is in an appropriate range, TS-YS is not less than 20.7 MPa and the hardness variation can be reduced.
  • Martensitic stainless steel according to the invention includes, in percent by mass, 0.010% to 0.030% C, 0.30% to 0.60% Mn, at most 0.040% P, at most 0.0100% S, 10.00% to 15.00% Cr, 2.50% to 8.00% Ni, 1.00% to 5.00% Mo, 0.050% to 0.250% Ti, at most 0.25% V, at most 0.07% N, and at least one of at most 0.50% Si and at most 0.10% Al, and the balance consists of Fe and impurities.
  • the martensitic stainless steel according to the present invention further satisfies Expression (1) and has a yield stress in the range from 758 MPa to 862 MPa.
  • the yield stress herein means 0.6% total elongation yield stress according to the ASTM standards. 6.0 ⁇ Ti / C ⁇ 10.1 where the symbols of the elements represent the contents of the elements in percent by mass.
  • the martensitic stainless steel preferably includes at least one of at most 0.25% Nb and at most 0.25% Zr instead of part of the Fe.
  • the martensitic stainless steel preferably further includes at most 1.00% Cu instead of part of the Fe.
  • the martensitic stainless steel preferably further includes at least one of at most 0.005% Ca, at most 0.005% Mg, at most 0.005% La, and at most 0.005% Ce instead of part of the Fe.
  • Martensitic stainless steel according to the embodiment of the invention has the following composition.
  • “%” related to elements means “% by mass.”
  • An excessive carbon (C) content raises the hardness after tempering too high, which increases the sulfide stress corrosion cracking sensitivity.
  • C content is from 0.010% to 0.030%, preferably from 0.012% to 0.018%.
  • Mn 0.30% to 0.60%
  • Manganese (Mn) improves the hot workability. However, with an excessive Mn content, the effect is saturated. Therefore, the Mn content is from 0. 30% to 0.60%. P: 0.040% or less
  • Phosphorus (P) is an impurity and lowers the SSC resistance. Therefore, the P content is not more than 0.040%. S: 0.0100% or less
  • S Sulfur
  • Cr 10.00% to 15.00%
  • Chromium (Cr) improves the carbon dioxide gas corrosion resistance. An excessive Cr content however prevents the structure after tempering from attaining a martensitic phase. Therefore, the Cr content is from 10.00% to 15.00%. Ni: 2.50% to 8.00%
  • Nickel (Ni) effectively allows the structure after tempering to mainly attain a martensitic phase.
  • the Ni content is from 2.50% to 8.00%, preferably from 4.00% to 7.00%.
  • Mo 1.00% to 5.00%
  • Molybdenum (Mo) improves the SSC resistance of high strength steel in an environment containing hydrogen sulfide. However, with an excessive Mo content, the effect is saturated. Therefore, the Mo content is from 1.00% to 5.00%. Ti: 0.050% to 0.250%
  • Titanium (Ti) improves the toughness by suppressing the structure from being coarse-grained.
  • an excessive Ti content prevents the structure after tempering from mainly attaining a martensitic phase, so that the toughness and the corrosion resistance (the SSC resistance and the carbon dioxide gas corrosion resistance) are lowered. Therefore, the Ti content is from 0.050% to 0.250%, preferably from 0.050% to 0.150%. N: 0.07% or less
  • N Nitrogen
  • V 0.25% or less
  • Vanadium (V) fixes C in the steel by forming a carbide and thus raises the tempering temperature and enhances the SSC resistance.
  • an excessive V content prevents a martensitic phase from being attained. Therefore, the V content is not more than 0.25%.
  • the lower limit for the V content is preferably 0.01%.
  • the martensitic stainless steel according to the embodiment contains at least one of Si and Al. Si: 0.50% or less Al: 0.10% or less
  • Si Silicon
  • Al aluminum
  • Si Silicon (Si) and aluminum (Al) both effectively work as a deoxidizing agent.
  • an excessive Si content lowers the toughness and the hot workability.
  • An excessive Al content causes a lot of inclusions to be produced in the steel, which lowers the corrosion resistance. Therefore, the Si content is not more than 0.50% and the Al content is not more than 0.10%.
  • the lower limit for the Si content is preferably 0.10%, and the lower limit for the Al content is preferably 0.001%. Note that if the Si and/or Al content is less than the described lower limits, the above-described effect is provided to some extent.
  • the balance of the martensitic stainless steel according to the embodiment includes Fe. Note that impurities other than the above-described impurities may be contained for various causes.
  • the Ti content and the C content in the chemical composition described above satisfy the following Expression (1): 6.0 ⁇ Ti / C ⁇ 10.1 where the element symbols represent the contents of the elements (% by mass).
  • Hmax and Hmin are measured by the following method.
  • the Rockwell hardness C scale (which is hereinafter simply referred to as "Rockwell hardness” and expressed in the unit HRC) is measured at the thickness central parts P1 to P4 at intervals of 90° in the circumferential direction.
  • the maximum value is Hmax and the minimum value is Hmin.
  • the SSC resistance tends to decrease.
  • Ti/C is not less than 6.0
  • the hardness variation is less than 2.5 and can be suppressed. While the reason is not clearly determined, this may be for the following reason. If Ti/C is too small, the Ti content in the steel is small. Therefore, a plurality of VCs are deposited during tempering. The deposited VCs have unequal sizes depending on where they are deposited in the steel pipe. As a result, the hardness greatly varies. On the other hand, if Ti/C is large, the Ti content in the steel is large. Therefore, TiC is deposited during tempering and the deposition of VCs is suppressed. Consequently, the hardness variation is reduced.
  • the martensitic stainless steel according to the invention satisfies Expression (1), so that TS-YS is not less than 20.7 MPa and the hardness variation is less than 2.5.
  • the upper limit for Ti/C is preferably 9.6, more preferably 9.0.
  • the martensitic stainless steel according to the embodiment further contains at least one of Nb and Zr instead of part of Fe as required.
  • Nb 0.25% or less
  • Zr 0.25% or less
  • Niobium (Nb) and Zirconium (Zr) are both optional elements. These elements both form a carbide to fix C in the steel and reduce the hardness variation after tempering. However, excessive contents of these elements prevent the tempered structure from mainly attaining a martensitic phase. Therefore, the Nb content and the Zr content are both not more than 0.25%. The preferred lower limits for the Nb content and the Zr content are each 0.005%. Note that when the Nb and Zr contents are each less than 0.005%, the above-described effect can be provided to some extent.
  • the martensitic stainless steel according to the embodiment further contains Cu instead of part of Fe as required.
  • Cu 1.00% or less
  • Copper (Cu) is an optional element. Similarly to Ni, Cu effectively allows the structure after tempering to attain a martensitic phase. However, an excessive Cu content lowers the hot workability. Therefore, the Cu content is not more than 1.00%. The lower limit for the Cu content is preferably 0.05%. Note that if the Cu content is less than 0.05%, the above-described effect can be provided to some extent.
  • the martensitic stainless steel according to the embodiment further contains at least one of Ca, Mg, La, and Ce instead of part of Fe as required.
  • Ca 0.005% or less Mg: 0.005% or less La: 0.005% or less Ce: 0.005% or less
  • Calcium (Ca), magnesium (Mg), lanthanum (La) and cerium (Ce) are optional elements. These elements improve the hot workability. However, if these elements are excessively contained, coarse oxides are produced, and the corrosion resistance is lowered. Therefore, the contents of these elements are each not more than 0.005%.
  • the lower limit for each of these elements is preferably 0.0002%. Note that if the contents of Ca, Mg, La, and Ce are less than 0.0002%, the above-described effect can be provided to some extent.
  • Ca and/or La is preferably contained.
  • molten steel having the chemical composition described in the above 1. is made into a slab or billet by a method such as continuous casting.
  • the molten steel is made into an ingot by ingot-making.
  • the slab or ingot is subjected to hot working by a method such as blooming and made into a billet.
  • the manufactured billet is heated in a heating furnace, and the billet extracted from the heating furnace is axially pierced by a piercing mill. Then, the strand or billet is made into a seamless steel pipe having a prescribed size by a mandrel mill, a reducer, or the like. Then, heat treatment (quenching and tempering) is carried out. At the time, the quenching and tempering temperatures are adjusted so that the 0.6% total elongation yield stress of the tempered martensitic stainless steel is in the range from 758 MPa to 862 MPa (110 ksi grade).
  • Seamless steel pipes having various chemical compositions were produced and the produced seamless steel pipes were examined for TS-YS and hardness variation.
  • quenching and tempering was carried out so that the 0.6% total elongation yield stress of each of the manufactured seamless steel pipes was within the range from 758 MPa to 862 MPa. More specifically, the quenching temperature was 910°C and the tempering temperature was adjusted in the range from 560°C to 630°C.
  • each of the seamless steel pipes was cut in the transverse direction in the center.
  • the Rockwell hardness C scale (HRC) was measured at the thick center parts P1 to P4 at intervals of 90° in the circumferential direction.
  • the maximum value was represented by Hmax and the minimum value by Hmin.
  • Hmax and Hmin the hardness variation (HRC) was obtained from Expression (2).
  • Ti/C is the ratio of the Ti content (% by mass) to the C content (% by mass) for each of the specimens with the test numbers.
  • TS represents the tensile stress (MPa) of each of the specimens with the test numbers
  • YS represents the 0.6% total elongation yield stress (MPa).
  • TS-YS represents the value (MPa) obtained by subtracting the 0.6% total elongation yield stress from the tensile stress.
  • hardness variation represents hardness variation (HRC) obtained by Expression (2). Note that the underlined numerical values are outside the range defined by the invention.
  • the 0.6% total elongation yield stress (YS) was in the range from 758 MPa to 862 MPa.
  • TS-YS was not less than 20.7 MPa and the hardness variation (HRC) was less than 2.5 for any of the seamless steel pipes.
  • the seamless steel pipes with Nos. 50 and 51 had chemical compositions within the range defined by the invention, but their Ti/C values did not satisfy Expression (1) or Ti/C exceeded 10.1 for each of the pipes. Therefore, TS-YS was less than 20.7 MPa.
  • the seamless steel pipes with Nos. 70 to 73 had chemical compositions within the range defined by the invention but their Ti/C values were all less than 6.0. Therefore, the hardness variation was not less than 2.5.
  • the seamless steel pipes with Nos. 1 to 49 and 70 to 73 in Table 1 were subjected to SSC tests and appreciated for their SSC resistance. More specifically, a tensile test specimen with a parallel part having a diameter of 6.3 mm and a length of 25.4 mm was produced from each of the seamless steel pipes. Using the produced tensile test specimens, proof ring tests were carried out according to the NACE TM0177-96 Method A. At the time, the specimens were immersed for 720 hours in a 20% NaCl aqueous solution saturated with '0.03 atm H 2 S (CO 2 bal.). The pH of the NaCl aqueous solution was 4.5 and the temperature of the aqueous solution was kept at 25°C during the tests. After the tests, the specimens were examined for cracks by visual inspection.
  • Martensitic stainless steel according to the invention is widely applicable as steel products for use in a corroding environment containing a corroding substance such as hydrogen sulfide, carbon dioxide gas, and chlorine ions. More specifically, the steel is suitably used for steel products for use in a production facility for oil or natural gas, a carbon dioxide removing device, and geothermal power generation installment. The steel is particularly suitably used as an oil country tubular good used in an oil well and a gas well.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Rigid Pipes And Flexible Pipes (AREA)
EP07792794.5A 2006-08-22 2007-08-21 Martensitischer nichtrostender stahl Withdrawn EP2060644A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2006225261 2006-08-22
PCT/JP2007/066194 WO2008023702A1 (fr) 2006-08-22 2007-08-21 Acier inoxydable martensitique

Publications (2)

Publication Number Publication Date
EP2060644A1 true EP2060644A1 (de) 2009-05-20
EP2060644A4 EP2060644A4 (de) 2016-02-17

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EP07792794.5A Withdrawn EP2060644A4 (de) 2006-08-22 2007-08-21 Martensitischer nichtrostender stahl

Country Status (9)

Country Link
US (1) US20090162239A1 (de)
EP (1) EP2060644A4 (de)
JP (1) JP5124857B2 (de)
CN (1) CN101506400A (de)
BR (1) BRPI0719904B1 (de)
MX (1) MX2009001836A (de)
NO (1) NO20090712L (de)
RU (1) RU2416670C2 (de)
WO (1) WO2008023702A1 (de)

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EP2128278A1 (de) * 2007-03-26 2009-12-02 Sumitomo Metal Industries Limited Verfahren zur herstellung eines bogenrohrs für ein leitungsrohr und bogenrohr für ein leitungsrohr
EP3460087A4 (de) * 2016-05-20 2019-11-06 Nippon Steel Corporation Stahlstab für bohrlochelement sowie bohrlochelement
EP3690072A4 (de) * 2017-09-29 2020-08-05 JFE Steel Corporation Ölbohrrohr aus martensitischem edelstahl und verfahren zu seiner herstellung

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CN101956146A (zh) * 2010-10-12 2011-01-26 西安建筑科技大学 一种油气管线用高强韧超级马氏体不锈钢及其制备方法
JP6049331B2 (ja) * 2012-07-03 2016-12-21 株式会社東芝 蒸気タービンの動翼、蒸気タービンの動翼の製造方法および蒸気タービン
BR102014005015A8 (pt) 2014-02-28 2017-12-26 Villares Metals S/A aço inoxidável martensítico-ferrítico, produto manufaturado, processo para a produção de peças ou barras forjadas ou laminadas de aço inoxidável martensítico-ferrítico e processo para a produção de tudo sem costura de aço inoxidável martensítico-ferrítico
WO2018079111A1 (ja) 2016-10-25 2018-05-03 Ｊｆｅスチール株式会社 油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法
CN108624809B (zh) * 2017-03-24 2020-07-28 宝山钢铁股份有限公司 优良的耐海水腐蚀、抗疲劳性能及抗环境脆性的超高强度钢板及其制造方法
RU2718019C1 (ru) * 2017-03-28 2020-03-30 Ниппон Стил Корпорейшн Продукт из мартенситной нержавеющей стали
JP6540920B1 (ja) 2017-09-29 2019-07-10 Ｊｆｅスチール株式会社 油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法
BR112020004793A2 (pt) 2017-09-29 2020-09-24 Jfe Steel Corporation tubo sem costura de aço inoxidável martensítico para produtos tubulares para regiões petrolíferas, e método para sua fabricação
EP3767000A4 (de) 2018-05-25 2021-03-03 JFE Steel Corporation Nahtloses stahlrohr aus martensitischem edelstahl für erdölbohrrohre und verfahren zu seiner herstellung
US11773461B2 (en) 2018-05-25 2023-10-03 Jfe Steel Corporation Martensitic stainless steel seamless pipe for oil country tubular goods, and method for manufacturing same
US20220074009A1 (en) * 2018-11-05 2022-03-10 Jfe Steel Corporation Martensitic stainless steel seamless pipe for oil country tubular goods, and method for manufacturing same
CN113584407A (zh) * 2020-04-30 2021-11-02 宝山钢铁股份有限公司 一种高强度耐高温腐蚀马氏体不锈钢及其制造方法
EP4286542A1 (de) 2021-03-24 2023-12-06 Nippon Steel Corporation Martensitisches edelstahlmaterial

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BRPI0719904B1 (pt) 2018-11-21
RU2009110199A (ru) 2010-09-27
JPWO2008023702A1 (ja) 2010-01-14
US20090162239A1 (en) 2009-06-25
WO2008023702A1 (fr) 2008-02-28
RU2416670C2 (ru) 2011-04-20
JP5124857B2 (ja) 2013-01-23
NO20090712L (no) 2009-05-19
MX2009001836A (es) 2009-04-30
BRPI0719904A2 (pt) 2014-06-10
EP2060644A4 (de) 2016-02-17
CN101506400A (zh) 2009-08-12

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