WO2008023702A1 - Martensitic stainless steel - Google Patents
Martensitic stainless steel Download PDFInfo
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- WO2008023702A1 WO2008023702A1 PCT/JP2007/066194 JP2007066194W WO2008023702A1 WO 2008023702 A1 WO2008023702 A1 WO 2008023702A1 JP 2007066194 W JP2007066194 W JP 2007066194W WO 2008023702 A1 WO2008023702 A1 WO 2008023702A1
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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
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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
- 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")
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—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 particularly to martensitic stainless steel used in a corrosive environment containing corrosive substances such as hydrogen sulfide, carbon dioxide, and chlorine ions.
- oil wells In recent years, deepening of oil and gas fields has been progressing. Since these oil wells and gas wells (hereinafter collectively referred to as oil wells) are deep, high yield strength is required for steel materials used as oil well pipes in these wells. Recently, steel with a yield strength of l lOksi class (0.6% total elongation yield of 758 MPa to 862 MPa) has been used as an oil well pipe.
- the oil well contains hydrogen sulfide, carbon dioxide, and chlorine ions. Therefore, steel materials for oil well pipes are required to have excellent SSC (Sulfide stress corrosion cracking) resistance and carbon dioxide gas corrosion resistance.
- SSC Sulfide stress corrosion cracking
- SUS420 martensitic stainless steel with carbon dioxide corrosion resistance is used for oil wells containing carbon dioxide.
- SUS420 martensitic stainless steel is not suitable for oil wells containing hydrogen sulfide. This is because the SSC resistance to hydrogen sulfide is low.
- Patent Document 1 discloses martensitic stainless steel for oil wells having high SSC resistance and carbon dioxide gas corrosion resistance in oil wells containing hydrogen sulfide, carbon dioxide gas, and the like. ing. In order to improve SSC resistance, it is effective to reduce the tensile strength. Therefore, in Patent Document 1 described above, high S / S resistance is obtained by reducing the bow I tension strength of martensitic stainless steel. Furthermore, by reducing the tensile strength, the variation in tensile strength after tempering is reduced.
- the martensitic stainless steel for oil wells disclosed in Patent Document 1 is designed to have a low tensile strength. Therefore, when the yield strength of steel is llOksi class (758MPa ⁇ 832MPa), there is a problem that the value obtained by subtracting the yield strength from the tensile strength is less than 20.7MPa.
- the steel material for oil country tubular goods is also required to have SSC resistance. If the hardness of the same steel material is large, the SSC resistance decreases. Therefore, it is necessary to suppress the hardness variation in the steel material for oil well pipes.
- An object of the present invention is a martensite of llOksi class (yield strength is 758MPa to 862MPa) having a value obtained by subtracting yield strength from tensile strength of 20.7MPa or more and capable of suppressing variation in hardness. Is to provide stainless steel.
- the present inventors calculated the yield strength (Yield Stress) from the ratio of Ti content to C content in steel (hereinafter also referred to as Ti / C) and tensile strength (hereinafter also referred to as TS). : We have newly found that there is a correlation with the value (hereinafter also referred to as TS-YS) minus (hereinafter also referred to as YS). Hereinafter, this knowledge will be described.
- the present inventors in mass%, C: 0.010-0.030%, Mn: 0.30-0.60%, P: 0.0 40% or less, S: 0.0100% or less, Cr: 10.00-15.00%, Ni: 2.50 —8.00%, Mo: l.00—5.00%, Ti: 0.050—0.250%, V: 0.25% or less, N: 0.07% or less, Si: 0.50% or less, A1: 0.10% or less A plurality of martensitic stainless steels with the balance of Fe and impurities and Ti / C of 7-4-10.7 were manufactured.
- FIG. 1 shows the survey results.
- the horizontal axis in Fig. 1 is Ti / C, and the vertical axis is TS—YS (ksi).
- TS—YS ksi
- Ti / C and TS—YS showed a negative correlation. Specifically, TS-YS became larger as Ti / C became smaller. Based on this new finding, the present inventors have found that TS-YS ⁇ 20.7 MPa (3 ksi) can be satisfied by satisfying the equation (A).
- the element symbol in a formula is content (mass%) of each element.
- the present inventors have also newly found that if Ti / C is too small, the variation in hardness becomes large. In other words, it was found that by setting Ti / C within an appropriate range, the TS-YS force is 3 ⁇ 40.7 MPa or more, and the force S can be suppressed to suppress variation in hardness.
- the martensitic stainless steel according to the present invention is, in mass%, C: 0.010—0.030%, Mn: 0.30—0.60%, P: 0.040% or less, S: 0.0100% or less, Cr: 10.00—15.0% , Ni: 2.50—8.00%, ⁇ : 1.00—5.00%, Ti: 0.050—0.250%, V: 0.25% or less, N: 0.07% or less, Si: 0.50% or less, A1: 0.10% or less One or more of them, and the balance consists of Fe and impurities.
- the martensitic stainless steel of the present invention further satisfies the formula (1) and has a yield strength of 758 to 862 MPa. Yield strength here refers to 0.6% total elongation resistance based on ASTM standards.
- the element symbol in a formula is content (mass%) of each element.
- the martensitic stainless steel further includes Nb: 0.25 instead of a part of Fe.
- Zr contain one or more of 0.25% or less.
- FIG. 1 is a graph showing the relationship between Ti / C and the value obtained by subtracting the yield strength from the tensile strength.
- FIG. 2 is a cross-sectional view of a steel pipe for explaining hardness measurement points.
- the martensitic stainless steel according to the embodiment of the present invention has the following composition.
- % related to elements means mass%.
- C carbon
- TS—YS ⁇ 20.7 MPa TS—YS ⁇ 20.7 MPa cannot be satisfied when the yield strength of steel is at least lOksi class (758 MPa to 862 MPa). Therefore, the C content shall be 0.0010-0.030%.
- a preferable C content is 0.012 to 0.018%.
- Manganese ( ⁇ ) improves hot workability. However, if ⁇ is contained excessively, the effect is saturated. Therefore, the ⁇ content is 0.30-0.60%.
- Phosphorus ( ⁇ ) is an impurity. ⁇ reduces SSC resistance. Therefore, the soot content is not more than 0.040%.
- S Sulfur
- S is an impurity. S decreases hot workability. Therefore, the lower the S content, the better.
- the S content is not more than 0.0100%.
- Chromium (Cr) improves carbon dioxide corrosion resistance. However, excessive Cr content prevents the tempered structure from becoming a martensite phase. Therefore, the Cr content is set to 10.00-15.00%.
- Nickel (Ni) is effective to make the structure after tempering mainly martensite. . If the Ni content is too low, many ferrite phases will precipitate in the tempered structure. On the other hand, if the Ni content is too large, the structure after tempering mainly becomes an austenite phase. Was once, Ni content (or 2. 50-8. To 00 0/0. Is preferably Rere Ni content (or 4. 00-7. 00%.
- Molybdenum (Mo) improves the SSC resistance of high-strength steel in environments containing hydrogen sulfide. However, if Mo is contained excessively, the effect is saturated. Therefore, the Mo content should be 1.00-5.00%.
- Titanium (Ti) improves toughness by suppressing the coarsening of the structure.
- excessive Ti content prevents the structure after tempering from becoming a martensite phase, and as a result, toughness and corrosion resistance (SSC resistance and carbon dioxide corrosion resistance) decrease. Therefore, the Ti content is set to 0.05-0.250%.
- the preferred Ti content is between 0.050 and 0.150%
- N 0.07% or less
- N Nitrogen
- the N content is 0.07% or less.
- the N content is 0.03% or less, more preferably the N content is 0.02% or less. More preferably, the N content is 0.01% or less.
- V 0.25% or less
- V Vanadium (V) fixes carbides in steel by forming carbides, raises the tempering temperature, and improves SSC resistance.
- excessive addition of V has the effect of preventing the martensitic phase. Therefore, the V content is 0.25% or less.
- a preferable lower limit of the V content is 0.01%.
- the martensitic stainless steel according to the present embodiment further contains at least one of Si and A1.
- Si 0.50% or less
- Si silicon
- Al aluminum
- the balance of the martensitic stainless steel according to the present embodiment is made of Fe. Note that impurities other than the above-described impurities may be included due to various factors.
- the Ti content and the C content in the chemical composition satisfy the formula (1).
- the element symbol in a formula is content (mass%) of each element.
- TS-YS increases as Ti / C decreases. If Ti / C exceeds 10 ⁇ 1, TS -YS ⁇ 20. 7MPa cannot be satisfied! / ,.
- Hardness variation (HRC) specified in (2) is 2.5 or more.
- Hmax and Hmin are measured by the following method.
- the Rockwell hardness C scale hereinafter simply referred to as Rockwell hardness
- HRC the Rockwell hardness C scale
- the hardness variation is 2.5 or more, the SSC resistance tends to decrease. If Ti / C is 6.0 or more, the hardness variation is less than 2.5, and the strength S can be suppressed. The reason for this is not clear, but the following reason is presumed. If Ti / C is too small, the Ti content in the steel is low. Therefore, multiple VCs precipitate during tempering. The size of each deposited VC is non-uniform depending on the deposition location in the steel pipe. As a result, the hardness variation increases. On the other hand, if Ti / C is large, the Ti content in the steel is large. Therefore, TiC precipitates during tempering and VC precipitation is suppressed. As a result, the hardness variation is reduced. [0041] The martensitic stainless steel according to the present invention satisfies the formula (1), so that TS-YS is 20.7 MPa or more and the hardness variation is less than 2.5.
- a preferable upper limit value of Ti / C is 9.6, and a more preferable upper limit value of Ti / C is 9.0.
- the martensitic stainless steel according to the present embodiment further contains at least one of Nb and Zr instead of a part of Fe, if necessary.
- Nb 0.25% or less
- Niobium (Nb) and zirconium (Zr) are both selective elements. Together, these elements reduce the strength variation after tempering by forming carbides and fixing C in the steel. However, excessive inclusion of these elements prevents the structure after tempering from becoming mainly martensitic. Therefore, the Nb content and Zr content are 0.25% or less, respectively. The lower limit of the preferred Nb content and the lower limit of the Zr content are each 0.05%. Note that the above effect can be obtained to some extent even if it contains less than 0.005% Nb and Zr.
- the martensitic stainless steel according to the present embodiment further contains Cu instead of a part of Fe, if necessary.
- Copper (Cu) is a selective element.
- Cu like Ni, is effective in making the structure after tempering mainly martensite.
- Cu content should be 1.00% or less.
- the preferred lower limit of Cu content is 0.05%. Note that the above effect can be obtained to some extent even if it contains less than 0.05% of Cu.
- the martensitic stainless steel according to the present embodiment further contains at least one of Ca, Mg, La, and Ce instead of part of Fe, if necessary.
- Calcium (Ca), magnesium (Mg), lanthanum (La) and cerium (Ce) are all selective elements. All of these elements improve hot workability. However, if these elements are contained excessively, coarse oxides are formed, and as a result, the corrosion resistance decreases. Therefore, the content of these elements should be 0.005% or less. The preferable lower limit of the content of these elements is 0.0002%. Even if Ca, Mg, La, Ce is contained in less than 0.0002%, the above effect can be obtained to some extent. Preferably, among these elements, Ca and / or La is contained.
- the molten steel having the chemical composition described in 1 above is formed into a slab or billet by a continuous forging method or the like.
- molten steel is made into an ingot by the ingot-making method. Slabs and ingots are hot-worked by ingot rolling, etc. to form billets.
- the manufactured billet is heated in a heating furnace, and the steel piece or steel piece extracted from the heating furnace is drilled in the axial direction by a punching machine. After that, it is processed into a seamless steel pipe of a predetermined size by a mandrel mill and reducer. After processing, heat treatment (quenching and tempering) is performed. At this time, the quenching temperature and the tempering temperature are adjusted so that the 0.6% total elongation yield strength of the martensitic stainless steel after tempering falls within the range of 758 to 862 MPa (110 ksi class).
- the above-described manufacturing method is a method for manufacturing a martensitic stainless steel seamless steel pipe! /
- the force described in the above is a method for manufacturing a martensitic stainless steel welded steel pipe by a known manufacturing method. Also good.
- Billets were manufactured by melting steel having the chemical composition shown in Table 1 for each test number in Table 1. Each billet produced was hot forged and hot rolled to produce a seamless steel pipe.
- quenching and tempering were carried out so that the 0.6% total elongation yield strength of each manufactured seamless steel pipe was within the range of 758 MPa 862 MPa. Specifically, the quenching temperature was 910 ° C, and the tempering temperature was adjusted within the range of 560 ° C and 630 ° C.
- each steel pipe After quenching and tempering, each steel pipe has a 0.6% total elongation resistance (YS) and tensile strength (TS) was measured.
- YS total elongation resistance
- TS tensile strength
- Tensile tests were performed on the collected round bar specimens at room temperature, and 0.6% total elongation resistance YS (MPa) and tensile strength TS (MPa) based on ASTM standards were measured. After the measurement, TS-YS was determined for each test number.
- each seamless steel pipe was cut at the center in the transverse direction.
- the Rockwell hardness C scale (HRC) of the central thickness P1-P4 was measured every 90 ° in the circumferential direction.
- HRC Rockwell hardness C scale
- Table 1 shows the survey results.
- Ti / C in the table is the ratio of the Ti content (mass%) to the C content (mass%) of each test number.
- TS in the table indicates the tensile strength (MPa) of each test number, and “YS” indicates the 0.6% total elongation resistance (MPa) of each test number.
- TS—YS in the table indicates the value (MPa) obtained by subtracting 0.6% total elongation resistance from tensile strength.
- Hardness variation in the table indicates the hardness variation (HRC) obtained by equation (2). It should be noted that numerical values with an underlined bow in the table are outside the scope of the present invention.
- the seamless steel pipes having test numbers 1 to 49 had a chemical composition within the scope of the present invention, and Ti / C satisfied the formula (1). Therefore, TS-YS of all seamless steel pipes was 20 ⁇ 7MPa or more. Furthermore, the hardness variation (HRC) of all seamless steel pipes was less than 2.5.
- the seamless steel pipes having test numbers 70 to 73 all had a chemical composition within the scope of the present invention, but had a Ti / C of less than 6.0. Therefore, the hardness variation was 2.5 or more.
- the martensitic stainless steel according to the present invention is widely applied to steel materials used in corrosive environments containing corrosive substances such as hydrogen sulfide, carbon dioxide, and chlorine ions. Specifically, it is suitable for steel materials used in oil and natural gas production facilities, carbon dioxide removal equipment, and geothermal power generation facilities. Especially suitable for oil well pipes used in oil wells and gas wells.
Abstract
Description
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Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2008530919A JP5124857B2 (en) | 2006-08-22 | 2007-08-21 | Martensitic stainless steel |
BRPI0719904A BRPI0719904B1 (en) | 2006-08-22 | 2007-08-21 | martensitic stainless steel |
EP07792794.5A EP2060644A4 (en) | 2006-08-22 | 2007-08-21 | Martensitic stainless steel |
MX2009001836A MX2009001836A (en) | 2006-08-22 | 2007-08-21 | Martensitic stainless steel. |
NO20090712A NO20090712L (en) | 2006-08-22 | 2009-02-13 | Martensitic stainless steel |
US12/379,395 US20090162239A1 (en) | 2006-08-22 | 2009-02-20 | Martensitic stainless steel |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2006225261 | 2006-08-22 | ||
JP2006-225261 | 2006-08-22 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US12/379,395 Continuation US20090162239A1 (en) | 2006-08-22 | 2009-02-20 | Martensitic stainless steel |
Publications (1)
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WO2008023702A1 true WO2008023702A1 (en) | 2008-02-28 |
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ID=39106787
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2007/066194 WO2008023702A1 (en) | 2006-08-22 | 2007-08-21 | Martensitic stainless steel |
Country Status (9)
Country | Link |
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US (1) | US20090162239A1 (en) |
EP (1) | EP2060644A4 (en) |
JP (1) | JP5124857B2 (en) |
CN (1) | CN101506400A (en) |
BR (1) | BRPI0719904B1 (en) |
MX (1) | MX2009001836A (en) |
NO (1) | NO20090712L (en) |
RU (1) | RU2416670C2 (en) |
WO (1) | WO2008023702A1 (en) |
Cited By (8)
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WO2018079111A1 (en) | 2016-10-25 | 2018-05-03 | Jfeスチール株式会社 | Seamless pipe of martensitic stainless steel for oil well pipe, and method for producing seamless pipe |
WO2019065116A1 (en) | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | Oil well pipe martensitic stainless seamless steel pipe and production method for same |
WO2019065114A1 (en) | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | Oil well pipe martensitic stainless seamless steel pipe and production method for same |
WO2019065115A1 (en) | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | Oil well pipe martensitic stainless seamless steel pipe and production method for same |
WO2019225281A1 (en) | 2018-05-25 | 2019-11-28 | Jfeスチール株式会社 | Martensitic stainless steel seamless steel tube for oil well pipes, and method for producing same |
WO2019225280A1 (en) | 2018-05-25 | 2019-11-28 | Jfeスチール株式会社 | Martensitic stainless steel seamless steel tube for oil well pipes, and method for producing same |
WO2020095559A1 (en) | 2018-11-05 | 2020-05-14 | Jfeスチール株式会社 | Seamless martensite stainless steel tube for oil well pipes, and method for manufacturing same |
WO2022202913A1 (en) | 2021-03-24 | 2022-09-29 | 日本製鉄株式会社 | Martensite stainless steel material |
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JP5045178B2 (en) | 2007-03-26 | 2012-10-10 | 住友金属工業株式会社 | Method for manufacturing bend pipe for line pipe and bend pipe for line pipe |
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WO2004057050A1 (en) * | 2002-12-20 | 2004-07-08 | Sumitomo Metal Industries, Ltd. | High-strength martensitic stainless steel with excellent resistances to carbon dioxide gas corrosion and sulfide stress corrosion cracking |
JP2006144069A (en) * | 2004-11-19 | 2006-06-08 | Sumitomo Metal Ind Ltd | Martensitic stainless steel |
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JP2730090B2 (en) * | 1988-10-13 | 1998-03-25 | 住友金属工業株式会社 | High yield ratio martensitic stainless steel |
CA2481009C (en) * | 2002-04-12 | 2011-07-26 | Sumitomo Metal Industries, Ltd. | Method for producing martinsitic stainless steel |
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2007
- 2007-08-21 RU RU2009110199/02A patent/RU2416670C2/en active
- 2007-08-21 BR BRPI0719904A patent/BRPI0719904B1/en active IP Right Grant
- 2007-08-21 MX MX2009001836A patent/MX2009001836A/en active IP Right Grant
- 2007-08-21 JP JP2008530919A patent/JP5124857B2/en active Active
- 2007-08-21 WO PCT/JP2007/066194 patent/WO2008023702A1/en active Application Filing
- 2007-08-21 EP EP07792794.5A patent/EP2060644A4/en not_active Withdrawn
- 2007-08-21 CN CNA2007800311494A patent/CN101506400A/en active Pending
-
2009
- 2009-02-13 NO NO20090712A patent/NO20090712L/en not_active Application Discontinuation
- 2009-02-20 US US12/379,395 patent/US20090162239A1/en not_active Abandoned
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Cited By (11)
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WO2018079111A1 (en) | 2016-10-25 | 2018-05-03 | Jfeスチール株式会社 | Seamless pipe of martensitic stainless steel for oil well pipe, and method for producing seamless pipe |
WO2019065116A1 (en) | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | Oil well pipe martensitic stainless seamless steel pipe and production method for same |
WO2019065114A1 (en) | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | Oil well pipe martensitic stainless seamless steel pipe and production method for same |
WO2019065115A1 (en) | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | Oil well pipe martensitic stainless seamless steel pipe and production method for same |
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 |
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 |
WO2019225281A1 (en) | 2018-05-25 | 2019-11-28 | Jfeスチール株式会社 | Martensitic stainless steel seamless steel tube for oil well pipes, and method for producing same |
WO2019225280A1 (en) | 2018-05-25 | 2019-11-28 | Jfeスチール株式会社 | Martensitic stainless steel seamless steel tube for oil well pipes, and method for producing same |
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 |
WO2020095559A1 (en) | 2018-11-05 | 2020-05-14 | Jfeスチール株式会社 | Seamless martensite stainless steel tube for oil well pipes, and method for manufacturing same |
WO2022202913A1 (en) | 2021-03-24 | 2022-09-29 | 日本製鉄株式会社 | Martensite stainless steel material |
Also Published As
Publication number | Publication date |
---|---|
EP2060644A1 (en) | 2009-05-20 |
BRPI0719904A2 (en) | 2014-06-10 |
CN101506400A (en) | 2009-08-12 |
NO20090712L (en) | 2009-05-19 |
RU2416670C2 (en) | 2011-04-20 |
BRPI0719904B1 (en) | 2018-11-21 |
US20090162239A1 (en) | 2009-06-25 |
MX2009001836A (en) | 2009-04-30 |
JP5124857B2 (en) | 2013-01-23 |
EP2060644A4 (en) | 2016-02-17 |
JPWO2008023702A1 (en) | 2010-01-14 |
RU2009110199A (en) | 2010-09-27 |
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