WO2024209843A1 - ステンレス継目無鋼管およびその製造方法 - Google Patents

ステンレス継目無鋼管およびその製造方法 Download PDF

Info

Publication number
WO2024209843A1
WO2024209843A1 PCT/JP2024/007195 JP2024007195W WO2024209843A1 WO 2024209843 A1 WO2024209843 A1 WO 2024209843A1 JP 2024007195 W JP2024007195 W JP 2024007195W WO 2024209843 A1 WO2024209843 A1 WO 2024209843A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
ferrite
content
stainless steel
phase
Prior art date
Application number
PCT/JP2024/007195
Other languages
English (en)
French (fr)
Japanese (ja)
Inventor
祐一 加茂
信介 井手
Original Assignee
Ｊｆｅスチール株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to JP2024533288A priority Critical patent/JPWO2024209843A1/ja
Publication of WO2024209843A1 publication Critical patent/WO2024209843A1/ja
Priority to MX2025009739A priority patent/MX2025009739A/es

Links

Images

Classifications

    • 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
    • C22C38/46—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a stainless steel seamless pipe suitable for use in oil wells and gas wells (hereinafter simply referred to as oil wells).
  • the present invention relates to a stainless steel seamless pipe having improved corrosion resistance in high-temperature severe corrosive environments containing carbon dioxide gas (CO 2 ) and chlorine ions (Cl - ), and environments containing hydrogen sulfide (H 2 S), etc.
  • Stainless steel seamless pipes are widely used for applications such as oil well pipes. Excellent yield strength is required for oil well pipes. Furthermore, in light of the expected depletion of energy resources in the near future, there has been active development of oil wells in severe corrosive environments that were not previously considered, such as deep oil fields, environments containing carbon dioxide, and environments containing hydrogen sulfide, known as sour environments. For this reason, oil well pipes are also required to have high corrosion resistance.
  • 13Cr martensitic stainless steel pipe One of the oil well steel pipes used for mining oil and gas fields in environments containing CO2 and Cl- is 13Cr martensitic stainless steel pipe.
  • 13Cr martensitic stainless steel pipe depending on the corrosive environment, the corrosion resistance of 13Cr martensitic stainless steel pipe may be insufficient. Therefore, there is a demand for oil well steel pipes with higher corrosion resistance that can be used in such environments.
  • CCS Carbon Capture and Storage
  • Patent Document 1 proposes a stainless steel for oil wells that contains, by mass%, C: 0.05% or less, Si: 0.5% or less, Mn: 0.01-0.5%, P: 0.04% or less, S: 0.01% or less, Cr: over 16.0% to 18.0%, Ni: over 4.0% to 5.6%, Mo: 1.6-4.0%, Cu: 1.5-3.0%, Al: 0.001-0.10%, and N: 0.05% or less, with the composition satisfying specific relationships between Cr, Ni, Mo, Cu, C, N, and Mn.
  • Patent Document 2 proposes a high-strength stainless steel seamless pipe for oil wells that contains, by mass%, C: 0.005-0.06%, Si: 0.05-0.5%, Mn: 0.2-1.8%, P: 0.03% or less, S: 0.005% or less, Cr: 15.5-18.0%, Ni: 1.5-5.0%, V: 0.02-0.2%, Al: 0.002-0.05%, N: 0.01-0.15%, O: 0.006% or less, and one or more elements selected from Mo: 1.0-3.5%, W: 3.0% or less, and Cu: 3.5% or less, and has a composition in which Cr, Ni, Mo, W, Cu, C, Si, Mn, and N satisfy specific relationships.
  • the composition is, in mass%, C: 0.001-0.06%, Si: 0.05-0.5%, Mn: 0.01-2.0%, P: 0.03% or less, S: less than 0.005%, Cr: 15.5-18.0%, Ni: 2.5-6.0%, V: 0.005-0.25%, Al: 0.05% or less, N: 0.06% or less, O: 0.01% or less, Cu: 0-3.5%, Co: 0-1.5%,
  • a stainless steel has been proposed that contains Nb: 0-0.25%, Ti: 0-0.25%, Zr: 0-0.25%, Ta: 0-0.25%, B: 0-0.005%, Ca: 0-0.01%, Mg: 0-0.01%, and REM: 0-0.05%, and further has a composition in which one or two selected from the group consisting of Mo: 0-3.5% and W: 0-3.5% satisfy a specific relationship.
  • Patent Document 4 also proposes a seamless steel pipe containing, by mass%, C: 0.050% or less, Si: 0.50% or less, Mn: 0.01-0.20%, P: 0.025% or less, S: 0.0150% or less, Cu: 0.09-3.00%, Cr: 15.00-18.00%, Ni: 4.00-9.00%, Mo: 1.50-4.00%, Al: 0.040% or less, N: 0.0150% or less, Ca: 0.0010-0.0040%, Ti: 0.020% or less, Nb: 0.020% or less, V: 0-0.20%, Co: 0-0.30%, and W: 0-2.00%.
  • Patent Documents 1 to 4 produce 17Cr stainless steels that have superior corrosion resistance compared to 13Cr steels.
  • their corrosion resistance, particularly their stress corrosion cracking resistance, is not necessarily sufficient, and it has become clear that there are environments in which they cannot withstand use.
  • the present invention aims to solve these problems of the conventional technology and provide a stainless steel seamless pipe that combines high strength, with a yield strength of 758 MPa (i.e., 110 ksi) or more, and excellent stress corrosion cracking resistance, and a manufacturing method thereof.
  • excellent stress corrosion cracking resistance means that when a test piece is immersed for 720 hours in a 20 mass % NaCl aqueous solution (liquid temperature of the aqueous solution: 200°C) adjusted to pH 4.5 by adding sodium bicarbonate and in contact with CO2 at 50 atmospheres and H2S gas at 0.01 atmospheres in an autoclave, no cracks are generated in the test piece after the test and the corrosion product is removed and the corrosion rate determined by the weight loss method is 0.10 mm/year or less.
  • the inventors have thoroughly investigated the various factors that affect the properties of stainless steel, particularly stress corrosion cracking resistance.
  • elements such as Cr, Mo, and Cu, which are generally known as corrosion-resistant elements, are effective in improving stress corrosion cracking resistance, adding too much of them can make it difficult to obtain a stable amount of martensite phase, which contributes to strength. Therefore, as a completely new approach, the present invention has found that by optimizing the drilling conditions when manufacturing seamless steel pipes and controlling the structural morphology of the steel, it is possible to obtain excellent stress corrosion cracking resistance without the need to add large amounts of corrosion-resistant elements.
  • the structural morphology of the ferrite contained in the steel is controlled as follows. In an optical microscope photograph taken at 400x magnification of the structure on a surface including the longitudinal and thickness directions of the steel pipe, ferrite is extracted by image analysis within an area of actual size: longitudinal: 300 ⁇ m ⁇ thickness: 200 ⁇ m. It was discovered that excellent stress corrosion cracking resistance was achieved by controlling the structural morphology so that the average ferrite filling degree was 0.80 or less. Note that the "average ferrite filling degree" will be described later, so an explanation of this will be omitted here.
  • the "surface including the longitudinal direction and thickness direction of the steel pipe” refers to a cross section in the thickness direction including the pipe axis.
  • the above-mentioned “range of actual dimensions: longitudinal direction: 300 ⁇ m ⁇ thickness direction: 200 ⁇ m” is image-analyzed.
  • the above-mentioned "filling degree” is an index that can be calculated, for example, using ImageJ, a free image analysis software used in the examples of the present invention, and one of the key points of the present invention is the discovery that this index can be used to express a structural morphology with excellent stress corrosion cracking resistance.
  • Patent Document 1 which focuses on improving stress corrosion cracking resistance, describes a method for manufacturing stainless steel in which the area reduction rate of the steel material at 850°C to 1250°C is 50% or more.
  • the inventors manufactured steel pipes using the manufacturing method of Patent Document 1.
  • the average ferrite filling degree does not necessarily become 0.80 or less by the control of Patent Document 1 alone, and the stress corrosion cracking resistance targeted by the present invention could not be obtained.
  • the inventors therefore investigated the relationship between the manufacturing conditions for seamless steel pipes and the average value of the ferrite filling degree.
  • the results are shown in Figure 1.
  • the average ferrite filling degree is stably 0.80 or less by performing the piercing process under conditions where the piercing speed, defined based on the length of the blank pipe immediately after piercing is 3.3 m/sec or less.
  • the filling degree of ferrite is a value defined by the following formula for one ferrite grain.
  • the component composition is, in mass%, Nb: 0.3% or less, Ti: 0.3% or less, W: 2.0% or less, Co: 1.0% or less, B: 0.010% or less, Ta: 0.3% or less, Zr: 0.3% or less, Ca: 0.010% or less, REM: 0.3% or less, Mg: 0.01% or less,
  • the martensite phase is 45% or more, the ferrite phase is 15 to 55%, and the retained austenite phase is 30% or less; And, the yield strength is 862 MPa or more.
  • the stainless steel seamless pipe according to [1] or [2].
  • a method for producing a stainless steel seamless pipe according to any one of [1] to [3], When manufacturing a seamless steel pipe from a steel material having the above-mentioned composition, a piercing process is carried out at a piercing speed of 3.3 m/sec or less, Next, the seamless steel pipe is subjected to a quenching treatment in which the seamless steel pipe is heated to a quenching temperature of 850 to 1150°C, and cooled at a cooling rate of 0.01°C/sec or more until the surface temperature of the steel pipe reaches a cooling stop temperature of 50°C or less; The stainless steel seamless pipe is then subjected to a tempering treatment at a tempering temperature of 500 to 650°C.
  • a stainless steel seamless pipe that combines high strength, with a yield strength of 758 MPa or more, and excellent stress corrosion cracking resistance. Furthermore, according to the manufacturing method of the present invention, a stainless steel seamless pipe that combines the above-mentioned properties can be manufactured by optimizing the drilling conditions in the drilling process.
  • FIG. 1 is a graph showing the relationship between the manufacturing conditions of a seamless steel pipe and the average value of the filling degree of ferrite.
  • the stainless steel seamless pipe of the present invention has the above-mentioned composition. First, the reasons for limiting the composition will be explained. Hereinafter, unless otherwise specified, “mass %” will be simply written as "%”.
  • C 0.06% or less C is an element that is inevitably contained in the steelmaking process. If the C content exceeds 0.06%, the corrosion resistance decreases. For this reason, the C content is set to 0.06% or less.
  • the C content is preferably set to 0.05% or less, more preferably set to 0.04% or less, and even more preferably set to 0.03% or less. From the viewpoint of corrosion resistance, the lower the C content, the better, so the lower limit of the C content is not particularly limited. However, from the viewpoint of decarburization cost, the C content is preferably set to 0.002% or more, more preferably set to 0.003% or more, and even more preferably set to 0.005% or more.
  • corrosion resistance includes carbon dioxide corrosion resistance, sulfide stress cracking resistance (SSC resistance), and stress corrosion cracking resistance (SCC resistance).
  • Si 1.0% or less
  • Si is an element that acts as a deoxidizer. However, if the Si content exceeds 1.0%, the hot workability and corrosion resistance are reduced. Therefore, the Si content is set to 1.0% or less.
  • the Si content is preferably set to 0.7% or less, more preferably set to 0.5% or less, and even more preferably set to 0.4% or less.
  • the lower limit of the Si content is not particularly limited, but from the viewpoint of enhancing the deoxidizing effect, the Si content is preferably set to 0.03% or more, more preferably set to 0.05% or more, and even more preferably set to 0.10% or more.
  • Mn 0.01-1.0%
  • Mn is an element that acts as a deoxidizer and a desulfurizer and improves hot workability.
  • the Mn content is set to 0.
  • the Mn content is preferably 0.03% or more, more preferably 0.05% or more, and further preferably 0.10% or more.
  • the Mn content is set to 1.0% or less.
  • the Mn content is preferably set to 0.8% or less, and more preferably set to 0.6% or less. More preferably, it is set to 0.4% or less.
  • P 0.05% or less
  • P is an element that reduces carbon dioxide corrosion resistance and SSC resistance.
  • the P content is set to 0.05% or less.
  • the P content is preferably set to 0.04% or less, and more preferably set to 0.03% or less.
  • the lower limit of the P content is not particularly limited and may be 0%. From the viewpoint of manufacturing costs, the P content is more preferably set to 0.005% or more.
  • S 0.005% or less
  • S is an element that significantly reduces hot workability and inhibits stable operation of the hot pipe making process.
  • S exists as sulfide-based inclusions in steel and reduces corrosion resistance. Therefore, the S content is set to 0.005% or less.
  • the S content is preferably set to 0.004% or less, more preferably set to 0.003% or less, and further preferably set to 0.002% or less.
  • the lower limit of the S content is not particularly limited and may be 0%. From the viewpoint of manufacturing cost, the S content is more preferably set to 0.0005% or more.
  • Cr 15.2-18.0%
  • Cr is an element that forms a protective film on the surface of the steel pipe, thereby contributing to improving corrosion resistance. If the Cr content is less than 15.2%, the desired stress corrosion cracking resistance cannot be ensured. Gas corrosion resistance is also reduced. Furthermore, Cr is an element that stabilizes the ferrite phase, but if the Cr content is less than 15.2%, the ferrite phase fraction becomes small, and it is difficult to obtain a steel with a desired phase fraction. Therefore, the Cr content is set to 15.2% or more.
  • the Cr content is preferably set to 15.5% or more, more preferably set to 16.0% or more, and further preferably set to 16.3% or more.
  • the Cr content is preferably 17.5% or less, more preferably 17.2% or less, and further preferably 17.0% or less.
  • Mo 1.5-4.3% Mo stabilizes the protective film on the steel pipe surface and increases resistance to pitting corrosion caused by Cl- or low pH, thereby improving corrosion resistance.
  • the Mo content The Mo content is set to 1.5% or more. Mo is an element that stabilizes the ferrite phase, but if the Mo content is less than 1.5%, the ferrite phase fraction becomes small, and it is difficult to obtain a steel with a desired phase fraction.
  • the Mo content is preferably 1.8% or more, more preferably 2.0% or more, and further preferably 2.3% or more.
  • the Mo content is 4.3%, If the Mo content exceeds 4.3%, the ferrite phase fraction and the residual austenite phase fraction become too high, making it impossible to ensure the desired strength. Therefore, the Mo content is set to 4.3% or less.
  • the Mo content is preferably It is set to 4.0% or less, more preferably 3.5% or less, and further preferably 3.0% or less.
  • Cu 0.5-3.5%
  • Cu has the effect of strengthening the protective film on the steel pipe surface and enhancing corrosion resistance, particularly carbon dioxide corrosion resistance.
  • the Cu content is 0.5
  • the Cu content is preferably 0.8% or more, more preferably 1.5% or more, and further preferably 2.0% or more.
  • the Cu content is too high, the steel The hot workability of the pipe is reduced, and surface defects are generated during pipe making, making it impossible to obtain the desired stress corrosion cracking resistance.
  • Cu is an austenite phase stabilizing element, so if it is added in excess, the ferrite phase fraction is reduced. Therefore, the Cu content is set to 3.5% or less.
  • the Cu content is preferably set to 3.2% or less, and more preferably set to 3.0% or less. % or less, and more preferably 2.7% or less.
  • Ni 3.5-5.2%
  • Ni maintains the austenite phase fraction at high temperatures and contributes to ensuring strength by obtaining the required amount of martensite phase in the present invention.
  • the Ni content is 3.5%.
  • Ni is an element that stabilizes the austenite phase. If the Ni content is less than 3.5%, the austenite phase fraction at high temperatures becomes small, and the desired phase fraction of the martensite phase that is transformed from austenite is not obtained.
  • the Ni content is preferably 3.8% or more, more preferably 4.0% or more, and further preferably 4.3% or more.
  • the Ni content exceeds 5.2%, If the steel contains Cr, the austenite phase fraction becomes too large, which reduces the hot workability of the steel, making it more susceptible to defects during hot rolling, and the desired stress corrosion cracking resistance may not necessarily be obtained. In addition, since the austenite forming ability increases, the ferrite phase fraction decreases accordingly, and steel with the desired phase fraction cannot be obtained. For this reason, the Ni content is set to 5.2% or less. Ni Content is preferably 5.0% or less.
  • V 0.5% or less
  • V is an element that increases strength without impairing toughness by forming carbonitrides.
  • V easily forms carbonitrides, so it suppresses the reduction in the effective amount of corrosion resistance of corrosion-resistant elements such as Cr by forming carbonitrides, thereby obtaining excellent corrosion resistance, particularly the desired stress corrosion cracking resistance.
  • the V content is set to 0.5% or less.
  • the V content is preferably set to 0.2% or less, more preferably set to 0.1% or less.
  • the lower limit of the V content is not particularly limited, but the V content is preferably set to 0.01% or more, and more preferably set to 0.03% or more.
  • Al 0.10% or less
  • Al is an element that acts as a deoxidizer. However, if the Al content exceeds 0.10%, the corrosion resistance decreases. Therefore, the Al content is set to 0.10% or less.
  • the Al content is preferably set to 0.07% or less, and more preferably set to 0.05% or less.
  • the lower limit of the Al content is not particularly limited, but from the viewpoint of enhancing the deoxidizing effect, the Al content is preferably set to 0.005% or more, more preferably set to 0.010% or more, and even more preferably set to 0.015% or more.
  • N 0.10% or less
  • N is an element that is inevitably contained in the steelmaking process, but it also increases the strength of steel.
  • the N content is set to 0.10% or less.
  • the N content is preferably set to 0.07% or less, more preferably set to 0.05% or less, and even more preferably set to 0.03% or less.
  • the lower limit of the N content is not particularly limited, but an extreme reduction in the N content leads to an increase in the steelmaking cost. Therefore, the N content is preferably set to 0.002% or more, more preferably set to 0.003% or more, and even more preferably set to 0.005% or more.
  • O oxygen
  • oxygen exists as an oxide in steel and has a detrimental effect on various properties. For this reason, in the present invention, it is desirable to reduce the O content as much as possible. In particular, if the O content exceeds 0.010%, the hot workability and corrosion resistance decrease. For this reason, the O content is set to 0.010% or less.
  • the lower limit of the O content is not particularly limited and may be 0%. Since an extreme reduction in the O content leads to an increase in steelmaking costs, it is more preferable that the O content is 0.0005% or more.
  • the stainless steel seamless pipe of the present invention has a composition containing the above components, with the remainder being Fe and unavoidable impurities.
  • the components described above are the basic components, and the stainless steel seamless pipe of the present invention can achieve the desired characteristics with these basic components.
  • the present invention can optionally contain one or more elements selected from the group consisting of Nb, Ti, W, Co, B, Ta, Zr, Ca, REM, Mg, Sn, and Sb. Since Nb, Ti, W, Co, B, Ta, Zr, Ca, REM, Mg, Sn, and Sb are steel components that can be optionally contained, the content of these elements may be 0%.
  • Nb 0.3% or less
  • Nb is an element that forms carbonitrides and improves strength and corrosion resistance, and can be contained as necessary. However, since Nb carbonitrides tend to reduce low-temperature toughness, when Nb is added, the Nb content is set to 0.3% or less.
  • the Nb content is preferably set to 0.2% or less, and more preferably set to 0.1% or less.
  • the Nb content is more preferably set to 0.01% or more.
  • Ti 0.3% or less
  • Ti is an element that increases strength and corrosion resistance, and can be contained as necessary. However, if Ti is contained in an amount exceeding 0.3%, low-temperature toughness decreases. Therefore, when Ti is added, the Ti content is set to 0.3% or less.
  • the Ti content is preferably set to 0.2% or less, and more preferably set to 0.1% or less.
  • the Ti content is preferably set to 0.001% or more, and more preferably set to 0.01% or more.
  • W 2.0% or less W is an element that contributes to improving the strength of steel and stabilizes the protective film on the steel pipe surface to increase corrosion resistance, and can be contained as necessary. However, if W is contained in an amount exceeding 2.0%, the ferrite phase fraction becomes too high and the desired strength cannot be ensured. For this reason, when W is added, the W content is set to 2.0% or less.
  • the W content is preferably set to 1.5% or less, more preferably set to 1.2% or less.
  • the W content is more preferably set to 0.3% or more, and even more preferably set to 0.5% or more.
  • Co 1.0% or less
  • Co is an element that improves corrosion resistance and can be contained as necessary. However, even if Co is contained in an amount exceeding 1.0%, the effect is saturated. Therefore, when Co is added, the Co content is 1.0% or less.
  • the Co content is preferably 0.5% or less, more preferably 0.3% or less, and even more preferably 0.1% or less.
  • the Co content is more preferably 0.01% or more.
  • B 0.010% or less
  • B is an element that contributes to improving hot workability and has the effect of suppressing the occurrence of cracks and fractures during the pipe-making process, and can be contained as necessary. However, if the B content exceeds 0.010%, the low-temperature toughness decreases. Therefore, when B is added, the B content is set to 0.010% or less.
  • the B content is preferably set to 0.007% or less, and more preferably set to 0.005% or less.
  • the B content is more preferably set to 0.0005% or more, and even more preferably set to 0.0010% or more.
  • Ta 0.3% or less Ta is an element that has the effect of increasing strength and improving corrosion resistance, and can be contained as necessary. However, even if Ta is contained in an amount exceeding 0.3%, the effect is saturated. Therefore, when Ta is added, the Ta content is set to 0.3% or less. It is more preferable that the Ta content is set to 0.001% or more.
  • Zr 0.3% or less
  • Zr is an element that increases strength and can be contained as necessary.
  • Zr also has the effect of improving SSC resistance. However, even if Zr is contained in an amount exceeding 0.3%, the effect is saturated. Therefore, when Zr is added, the Zr content is set to 0.3% or less.
  • the Zr content is preferably set to 0.0005% or more.
  • Ca 0.010% or less
  • Ca is an element that improves hot workability through morphological control of sulfides, and also has the effect of suppressing the occurrence of cracks and fractures in the pipe-making process, and can be contained as necessary.
  • the Ca content is 0.001% or more.
  • the Ca content is preferably 0.002% or more, more preferably 0.003% or more, and even more preferably 0.005% or more.
  • the Ca content is 0.010% or less.
  • the Ca content is preferably 0.008% or less, and more preferably 0.007% or less.
  • REM 0.3% or less REM (rare earth metal) is an element that contributes to improving stress corrosion cracking resistance through morphology control of sulfides, and can be contained as necessary. However, even if REM is contained in an amount exceeding 0.3%, the effect is saturated and an effect commensurate with the content cannot be expected. For this reason, when REM is added, the REM content is set to 0.3% or less.
  • the REM content is preferably set to 0.0005% or more.
  • REM refers to scandium (Sc) with atomic number 21, yttrium (Y) with atomic number 39, and lanthanoids from lanthanum (La) with atomic number 57 to lutetium (Lu) with atomic number 71.
  • the composition of the stainless steel seamless pipe of the present invention can optionally contain at least one of the above REMs. Therefore, the REM content in the present invention is the total content of the above elements.
  • Mg 0.01% or less Mg is an element that improves corrosion resistance and can be contained as necessary. However, even if the Mg content exceeds 0.01%, the effect is saturated and an effect commensurate with the content cannot be expected. Therefore, when Mg is added, the Mg content is set to 0.01% or less. The Mg content is preferably set to 0.0005% or more.
  • Sn 1.0% or less Sn is an element that improves corrosion resistance, and can be contained as necessary. However, even if the Sn content exceeds 1.0%, the effect is saturated and an effect commensurate with the content cannot be expected. Therefore, when Sn is added, the Sn content is 1.0% or less.
  • the Sn content is preferably 0.001% or more.
  • Sb 1.0% or less Sb is an element that improves corrosion resistance and can be contained as necessary. However, even if the Sb content exceeds 1.0%, the effect is saturated and an effect commensurate with the content cannot be expected. Therefore, when Sb is added, the Sb content is set to 1.0% or less. The Sb content is preferably set to 0.001% or more.
  • the structure of the stainless steel seamless pipe is, by volume, 40% or more martensite phase, 15-55% ferrite phase, and 40% or less retained austenite phase, and the average filling rate of ferrite in the plane including the longitudinal direction and wall thickness direction of the steel pipe described below is 0.80 or less.
  • Martensite phase 40% or more in volume fraction If the volume fraction of the martensite phase is less than 40%, the desired strength cannot be ensured. Therefore, the volume fraction of the martensite phase is set to 40% or more.
  • the volume fraction of the martensite phase is preferably set to 45% or more, more preferably set to 50% or more, and even more preferably set to 60% or more.
  • the upper limit of the volume fraction of the martensite phase is not particularly limited, but the volume fraction of the martensite phase is preferably set to 90% or less, and more preferably set to 85% or less.
  • the volume fraction of the ferrite phase 15 to 55% by volume
  • the volume fraction of the ferrite phase is preferably set to 50% or less, more preferably set to 45% or less, and even more preferably set to 40% or less.
  • the volume fraction of the ferrite phase is set to 15% or more.
  • the volume fraction of the ferrite phase is preferably set to 20% or more, and more preferably set to 25% or more.
  • Retained austenite phase 40% or less in volume
  • the presence of the retained austenite phase improves ductility and low-temperature toughness.
  • the volume fraction of the retained austenite phase is set to 40% or less.
  • the volume fraction of the retained austenite phase is preferably 30% or less, and more preferably 25% or less.
  • the lower limit of the volume fraction of the retained austenite phase is not particularly limited, but the volume fraction of the retained austenite phase is preferably 3% or more, and more preferably 5% or more.
  • volume fraction of each of the above phases can be measured by the following method.
  • a piece of steel is cut from a surface of the stainless steel seamless pipe including the longitudinal direction and the wall thickness direction, and the piece is embedded in resin and mirror polished to prepare a sample for microstructural observation.
  • the observation surface is electrolytically etched in a KOH solution (i.e., a mixture of 35 g of KOH and 100 g of pure water) at a current density of 3 A/cm2 for 35 seconds, and then etched in a Villela reagent (i.e., a mixture of 2 g of picric acid, 5 ml of hydrochloric acid, and 50 ml of ethanol, respectively) for 30 seconds.
  • a Villela reagent i.e., a mixture of 2 g of picric acid, 5 ml of hydrochloric acid, and 50 ml of ethanol, respectively
  • An image is cut from an arbitrary position in the obtained optical microscope photograph in the range of 300 ⁇ m in the longitudinal direction of the steel pipe ⁇ 200 ⁇ m in the wall thickness direction of the steel pipe in actual size, and analyzed using image analysis software (ImageJ 1.52p, National Institute of Health) to calculate the structure fraction (area fraction (%)) of the ferrite phase.
  • the ferrite phase can be extracted by using the Weka Trainable Segmentation function for the optical microscope photograph, using three locations each of the bright ferrite parts and the dark martensite parts as teacher data, and automatically classifying the other locations using the above-mentioned Segmentation function.
  • the area fraction of the ferrite phase extracted in this way is defined as the volume fraction (%) of the ferrite phase.
  • a test piece for X-ray diffraction taken from the stainless steel seamless pipe is ground and polished so that a cross section perpendicular to the pipe axis direction (i.e., C cross section) becomes the measurement surface, and the structural fraction of the retained austenite ( ⁇ ) phase is measured using an X-ray diffraction method.
  • the volume fraction of the retained austenite phase is calculated from the integrated intensities of the (220) plane of austenite and the (211) plane of ferrite using the following formula.
  • V ⁇ (%) 100/(1+(I ⁇ R ⁇ /I ⁇ R ⁇ ))
  • V ⁇ volume fraction of retained austenite phase
  • I ⁇ integrated intensity of the (211) plane of ferrite
  • I ⁇ integrated intensity of the (220) plane of austenite
  • R ⁇ the theoretically calculated crystallographic value of ⁇ (34.15)
  • R ⁇ the theoretically calculated crystallographic value of ⁇ (22.33).
  • the remainder other than the ferrite phase and the residual gamma phase determined by the above measurement method is the martensite phase fraction.
  • the observation method for each of the above structures is also described in detail in the examples below.
  • the structure of the stainless steel seamless pipe of the present invention consists of a martensite phase, a ferrite phase, and a retained austenite phase.
  • the stainless steel seamless pipe of the present invention has a microstructure in which the average value of the ferrite packing degree is expressed as 0.80 or less.
  • the average value of the ferrite filling degree is determined by the following method.
  • the segmented image i.e., one image at the "any one position" described above
  • the number of ferrite grains and the feature values of each ferrite grain are obtained by using the Analyze Particle function for the ferrite portion.
  • the solidity in the ImageJ output corresponds to the filling degree of each individual ferrite.
  • the average value of the solidity of all ferrite grains is defined as the average value of the ferrite filling degree in this invention.
  • the ferrite phase which is rich in corrosion-resistant elements such as Cr and Mo, acts as a barrier against the occurrence of pitting corrosion, which is the starting point of stress corrosion cracking.
  • the degree of filling is high, that is, when the proportion of ferrite phase in the convex hull surrounding the ferrite grains is high, pitting corrosion is less likely to occur in the ferrite part, but the structure is not one in which the martensite phase and ferrite phase are intertwined. In other words, the structure is one in which the martensite phase is densely packed. Therefore, pitting corrosion is likely to occur and grow in this martensite part, which becomes a weak point for stress corrosion cracking.
  • the average ferrite filling degree is 0.80 or less. Since a smaller average filling degree is expected to improve stress corrosion cracking resistance, the average ferrite filling degree is preferably 0.75 or less, and more preferably 0.70 or less.
  • the lower limit of the average ferrite filling degree is preferably 0.2 or more.
  • the average ferrite filling degree is more preferably 0.4 or more.
  • yield strength 758 MPa or more
  • the stainless steel seamless pipe of the present invention has a yield strength of 758 MPa or more.
  • the upper limit of the yield strength is not particularly limited, but it is preferably 1034 MPa or less.
  • the yield strength can be measured by the method described in the examples.
  • the stainless steel seamless pipe of the present invention preferably has a yield strength of 862 MPa or more.
  • the volume fraction of each of the above phases at this yield strength is 45% or more for martensite phase, 15 to 55% for ferrite phase, and 30% or less for retained austenite phase.
  • the stainless steel seamless pipe of the present invention can be used for any purpose without being particularly limited.
  • the stainless steel seamless pipe of the present invention can be used extremely preferably for oil wells, and can also be used preferably as a CO2 injection pipe in the above-mentioned CCS.
  • the stainless steel seamless pipe of the present invention can be manufactured by forming a seamless steel pipe from a steel material and subjecting the seamless steel pipe to a quenching and tempering treatment under specific conditions.
  • the above-mentioned steel material is not particularly limited and any material can be used.
  • a billet is used as the steel material, and the composition of the steel material has the above-mentioned composition.
  • the manufacturing method of the above steel material is not particularly limited, and it can be manufactured by any method.
  • molten steel having the above-mentioned composition is melted by a melting method using a converter or the like, and then made into a round billet-shaped steel material by a method such as a continuous casting method or an ingot making-blooming rolling method.
  • the steel material in the round billet shape can be directly manufactured by casting it into a cylindrical shape.
  • the above-mentioned steel material thus obtained is made into a seamless steel pipe.
  • the pipe is made by hot working. Specifically, in the hot working, the steel material is heated, and the heated steel material is made into a blank pipe (i.e., a hollow blank pipe) by a piercing machine, and the blank pipe is rolled, such as formed, to obtain a seamless steel pipe of a desired dimension.
  • the method of hot working the steel material to obtain a seamless steel pipe is not particularly limited, and any method can be used.
  • a seamless steel pipe can be obtained by using either the Mannesmann plug mill method or the Mannesmann mandrel mill method.
  • the heating temperature in the heating in this hot working is not particularly limited, but it is preferably 1100 to 1350°C from the viewpoint of achieving both high levels of hot workability during pipe making and low-temperature toughness of the final product. After the heating, a piercing process is performed to make holes in the steel material.
  • the temperature (unit: °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.
  • the piercing process is controlled so that the piercing speed, which is determined based on the length of the mother pipe immediately after the piercing process is completed and before the subsequent rolling process is completed, is 3.3 m/sec or less. This is because, by appropriately controlling the piercing speed in the piercing process so as to satisfy the above range, the average filling degree of ferrite can be set to 0.80 or less.
  • the piercing speed is calculated by dividing the length of the blank pipe immediately after piercing by the piercing time.
  • blade pipe length immediately after piercing refers to the total longitudinal length (unit: m) of the blank pipe immediately after the piercing process is completed.
  • piercing time refers to the time (unit: seconds) required from the point when the roll load of the piercing machine is applied to the steel material to the point when the roll load is no longer applied to the steel material after piercing.
  • the state in which the roll load is applied refers to the state in which the roll load changes over time in the piercing mill relative to the level when the steel material is not in contact with the roll.
  • the state in which the roll load is not applied refers to the state in which the roll load returns to the above level in the above-mentioned change over time.
  • an index that changes when the steel material is in contact with the roll such as the roll displacement or torque value, can be used instead of the roll load.
  • the drilling speed is preferably 2.0 m/s or less, more preferably 1.0 m/s or less, and even more preferably 0.5 m/s or less. It is believed that the average ferrite filling degree decreases as the drilling speed decreases, so no lower limit is set for the drilling speed. However, an extremely low drilling speed reduces manufacturing efficiency, so the drilling speed is preferably 0.05 m/s or more, more preferably 0.10 m/s or more, and even more preferably 0.2 m/s or more.
  • a cooling process may be performed after the pipe is made.
  • the cooling process can be performed under any conditions without any particular restrictions.
  • An average cooling rate faster than air cooling means 0.01°C/second or faster.
  • a seamless steel pipe is heated to a quenching temperature of 850 to 1150° C., and the heated seamless steel pipe is cooled to a cooling stop temperature of 50° C. or less at an average cooling rate of 0.01° C./sec or more.
  • Quenching temperature 850 to 1150°C If the heating temperature in the quenching process (i.e., the quenching temperature) is less than 850°C, reverse transformation from martensite to austenite does not occur, and transformation from austenite to martensite does not occur during cooling, and as a result, the desired strength cannot be ensured. Therefore, the quenching temperature is set to 850°C or higher. The quenching temperature is preferably set to 900°C or higher. On the other hand, if the quenching temperature is higher than 1150°C, the crystal grains become coarse, and as a result, the low-temperature toughness deteriorates. Therefore, the quenching temperature is set to 1150°C or lower. The quenching temperature is preferably set to 1100°C or lower.
  • the seamless steel pipe may be heated to the above quenching temperature, and then a soaking treatment may be performed to hold the pipe at the quenching temperature.
  • a soaking treatment By performing the soaking treatment, the temperature of the seamless steel pipe in the thickness direction can be made uniform, and material variations can be reduced.
  • the time for which the pipe is held at the quenching temperature i.e., the soaking time
  • it is preferably 5 to 30 minutes.
  • Average cooling rate 0.01° C./sec or more If the average cooling rate in the quenching treatment is less than 0.01° C./sec, the desired structure cannot be obtained. Therefore, the average cooling rate is set to 0.01° C./sec or more.
  • the average cooling rate is preferably 1.0° C./sec or more, more preferably 5.0° C./sec or more, and even more preferably 10.0° C./sec or more.
  • the above cooling can be performed by any method without any particular limitation.
  • the cooling is preferably performed by at least one of air cooling and water cooling, and more preferably by water cooling.
  • Cooling stop temperature 50°C or less If the cooling stop temperature is higher than 50°C, the desired structure cannot be obtained. If the cooling stop temperature is high, the transformation from austenite to martensite does not occur sufficiently, and the residual austenite fraction becomes excessive. Therefore, the cooling stop temperature in the above quenching treatment is set to 50°C or less.
  • the cooling stop temperature is the surface temperature of the seamless steel pipe.
  • Tempering temperature 500-650°C If the tempering temperature is less than 500°C, a sufficient tempering effect cannot be obtained, and as a result, low-temperature toughness deteriorates. Therefore, the tempering temperature is set to 500°C or more.
  • the tempering temperature is preferably 520° C. or higher.
  • the tempering temperature is set to 650° C. or lower.
  • the return temperature is preferably 630° C. or less.
  • the seamless steel pipe can be heated to the above tempering temperature and then held at the tempering temperature.
  • the time it is held at the tempering temperature i.e., holding time. From the viewpoint of making the temperature uniform in the wall thickness direction and preventing material variations, it is preferable for the holding time to be 5 to 90 minutes.
  • the stainless steel seamless pipe of the present invention can also have excellent low-temperature toughness.
  • a steel material was cast using molten steel having the composition shown in Table 1.
  • the steel material was then heated and hot-worked using a model seamless rolling mill to produce a seamless steel pipe with an outer diameter of 177.8 mm and a wall thickness of 16.0 mm, which was then air-cooled.
  • the heating temperature of the steel material before hot working was 1250°C.
  • the piercing speed was as shown in Table 2.
  • the obtained seamless steel pipe was subjected to quenching and tempering treatment under the following conditions to obtain a stainless steel seamless steel pipe.
  • the seamless steel pipe obtained was subjected to quenching treatment under the conditions shown in Table 2. Specifically, the seamless steel pipe was heated to the quenching temperature shown in Table 2 and held at the quenching temperature for the soaking time shown in Table 2. Next, it was cooled to a cooling stop temperature of 5°C. The cooling was performed by water cooling. In the water cooling, the average cooling rate from when the seamless steel pipe was put into water until the temperature reached 50°C or less was 20°C/sec.
  • Test pieces were taken from the obtained stainless steel seamless pipe and the following methods were used to perform (1) microstructural observation, (2) tensile testing, and (3) stress corrosion cracking testing.
  • the average ferrite filling level was also calculated using the method described above.
  • a test piece of 5 mm thick x 15 mm wide x 115 mm long was prepared by machining, and a four-point bending test was performed.
  • the four-point bending test was performed by immersing the above test piece in a 20 mass% NaCl aqueous solution (liquid temperature: 200°C, 50 atm CO 2 -0.01 atm H 2 S gas atmosphere) held in an autoclave, to which NaHCO 3 was added so that the pH was 4.5, for a period of 30 days (i.e., 720 hours).
  • the load stress was the same as the yield stress at 200°C.
  • the corrosion products were removed, and the presence or absence of cracks was determined by observing the surface of the test piece.
  • those without cracks were considered to pass, and those with cracks were considered to fail, and in the "Presence or Absence of Cracks" column in Table 2, pass was indicated by the symbol " ⁇ " and fail was indicated by the symbol " ⁇ ".
  • the weight of the corrosion test piece after removing the corrosion products was measured, and the weight loss due to the corrosion test was calculated by subtracting the weight of the test piece before the corrosion test, which had been measured in advance.
  • the weight loss was divided by the surface area of the test piece used and the immersion period described above to obtain the weight loss per unit time and unit area.
  • This weight loss per unit time and unit area was then divided by the density of the steel to convert it into the corrosion thickness per unit time and unit area.
  • the corrosion thickness (mm/year) per unit time and unit area obtained in this way was taken as the corrosion rate.
  • a corrosion rate of 0.10 mm/year or less was deemed to pass, and a corrosion rate of more than 0.10 mm/year was deemed to fail.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
PCT/JP2024/007195 2023-04-06 2024-02-28 ステンレス継目無鋼管およびその製造方法 WO2024209843A1 (ja)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP2024533288A JPWO2024209843A1 (enrdf_load_stackoverflow) 2023-04-06 2024-02-28
MX2025009739A MX2025009739A (es) 2023-04-06 2025-08-18 Tuberia de acero inoxidable sin costura y metodo para fabricar la misma

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2023-062295 2023-04-06
JP2023062295 2023-04-06

Publications (1)

Publication Number Publication Date
WO2024209843A1 true WO2024209843A1 (ja) 2024-10-10

Family

ID=92972114

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2024/007195 WO2024209843A1 (ja) 2023-04-06 2024-02-28 ステンレス継目無鋼管およびその製造方法

Country Status (4)

Country Link
JP (1) JPWO2024209843A1 (enrdf_load_stackoverflow)
AR (1) AR132300A1 (enrdf_load_stackoverflow)
MX (1) MX2025009739A (enrdf_load_stackoverflow)
WO (1) WO2024209843A1 (enrdf_load_stackoverflow)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2025150315A1 (ja) * 2024-01-12 2025-07-17 日本製鉄株式会社 ステンレス鋼材

Citations (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001340904A (ja) * 2000-05-29 2001-12-11 Sumitomo Metal Ind Ltd 継目無鋼管の穿孔圧延方法
WO2010134498A1 (ja) 2009-05-18 2010-11-25 住友金属工業株式会社 油井用ステンレス鋼、油井用ステンレス鋼管及び油井用ステンレス鋼の製造方法
JP2013249516A (ja) 2012-05-31 2013-12-12 Jfe Steel Corp 油井管用高強度ステンレス鋼継目無管およびその製造方法
WO2016079922A1 (ja) * 2014-11-18 2016-05-26 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管の製造方法
WO2016079920A1 (ja) * 2014-11-19 2016-05-26 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管
WO2016113794A1 (ja) * 2015-01-15 2016-07-21 Ｊｆｅスチール株式会社 油井用継目無ステンレス鋼管およびその製造方法
JP2016145372A (ja) * 2015-02-06 2016-08-12 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管の製造方法
WO2017010036A1 (ja) * 2015-07-10 2017-01-19 Ｊｆｅスチール株式会社 高強度ステンレス継目無鋼管およびその製造方法
WO2017022374A1 (ja) 2015-08-04 2017-02-09 新日鐵住金株式会社 ステンレス鋼及び油井用ステンレス鋼材
JP2017039998A (ja) * 2015-08-18 2017-02-23 Ｊｆｅスチール株式会社 油井用継目無ステンレス鋼管およびその製造方法
WO2017138050A1 (ja) * 2016-02-08 2017-08-17 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2018020886A1 (ja) * 2016-07-27 2018-02-01 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2018131340A1 (ja) * 2017-01-13 2018-07-19 Ｊｆｅスチール株式会社 高強度ステンレス継目無鋼管およびその製造方法
WO2018155041A1 (ja) * 2017-02-24 2018-08-30 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2019035329A1 (ja) * 2017-08-15 2019-02-21 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2020013197A1 (ja) 2018-07-09 2020-01-16 日本製鉄株式会社 継目無鋼管及びその製造方法
WO2020202957A1 (ja) * 2019-03-29 2020-10-08 Ｊｆｅスチール株式会社 ステンレス継目無鋼管
WO2021065262A1 (ja) * 2019-10-01 2021-04-08 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法
WO2021065263A1 (ja) * 2019-10-01 2021-04-08 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法
WO2021187331A1 (ja) * 2020-03-19 2021-09-23 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびステンレス継目無鋼管の製造方法
WO2021187330A1 (ja) * 2020-03-19 2021-09-23 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびステンレス継目無鋼管の製造方法
WO2022009598A1 (ja) * 2020-07-06 2022-01-13 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法

Patent Citations (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001340904A (ja) * 2000-05-29 2001-12-11 Sumitomo Metal Ind Ltd 継目無鋼管の穿孔圧延方法
WO2010134498A1 (ja) 2009-05-18 2010-11-25 住友金属工業株式会社 油井用ステンレス鋼、油井用ステンレス鋼管及び油井用ステンレス鋼の製造方法
JP2013249516A (ja) 2012-05-31 2013-12-12 Jfe Steel Corp 油井管用高強度ステンレス鋼継目無管およびその製造方法
WO2016079922A1 (ja) * 2014-11-18 2016-05-26 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管の製造方法
WO2016079920A1 (ja) * 2014-11-19 2016-05-26 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管
WO2016113794A1 (ja) * 2015-01-15 2016-07-21 Ｊｆｅスチール株式会社 油井用継目無ステンレス鋼管およびその製造方法
JP2016145372A (ja) * 2015-02-06 2016-08-12 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管の製造方法
WO2017010036A1 (ja) * 2015-07-10 2017-01-19 Ｊｆｅスチール株式会社 高強度ステンレス継目無鋼管およびその製造方法
WO2017022374A1 (ja) 2015-08-04 2017-02-09 新日鐵住金株式会社 ステンレス鋼及び油井用ステンレス鋼材
JP2017039998A (ja) * 2015-08-18 2017-02-23 Ｊｆｅスチール株式会社 油井用継目無ステンレス鋼管およびその製造方法
WO2017138050A1 (ja) * 2016-02-08 2017-08-17 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2018020886A1 (ja) * 2016-07-27 2018-02-01 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2018131340A1 (ja) * 2017-01-13 2018-07-19 Ｊｆｅスチール株式会社 高強度ステンレス継目無鋼管およびその製造方法
WO2018155041A1 (ja) * 2017-02-24 2018-08-30 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2019035329A1 (ja) * 2017-08-15 2019-02-21 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管およびその製造方法
WO2020013197A1 (ja) 2018-07-09 2020-01-16 日本製鉄株式会社 継目無鋼管及びその製造方法
WO2020202957A1 (ja) * 2019-03-29 2020-10-08 Ｊｆｅスチール株式会社 ステンレス継目無鋼管
WO2021065262A1 (ja) * 2019-10-01 2021-04-08 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法
WO2021065263A1 (ja) * 2019-10-01 2021-04-08 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法
WO2021187331A1 (ja) * 2020-03-19 2021-09-23 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびステンレス継目無鋼管の製造方法
WO2021187330A1 (ja) * 2020-03-19 2021-09-23 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびステンレス継目無鋼管の製造方法
WO2022009598A1 (ja) * 2020-07-06 2022-01-13 Ｊｆｅスチール株式会社 ステンレス継目無鋼管およびその製造方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2025150315A1 (ja) * 2024-01-12 2025-07-17 日本製鉄株式会社 ステンレス鋼材

Also Published As

Publication number Publication date
JPWO2024209843A1 (enrdf_load_stackoverflow) 2024-10-10
AR132300A1 (es) 2025-06-11
MX2025009739A (es) 2025-09-02

Similar Documents

Publication Publication Date Title
JP6399259B1 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP6384636B1 (ja) 高強度ステンレス継目無鋼管およびその製造方法
JP5967066B2 (ja) 耐食性に優れた油井用高強度ステンレス継目無鋼管およびその製造方法
RU2599936C2 (ru) Бесшовная труба из высокопрочной нержавеющей стали с высокой коррозионной стойкостью для нефтяной скважины и способ её изготовления
JP4363327B2 (ja) 油井用ステンレス鋼管およびその製造方法
WO2017138050A1 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP7156536B2 (ja) ステンレス継目無鋼管およびステンレス継目無鋼管の製造方法
JP6156609B1 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP7156537B2 (ja) ステンレス継目無鋼管およびステンレス継目無鋼管の製造方法
WO2014112353A1 (ja) 油井用ステンレス継目無鋼管およびその製造方法
JP2008081793A (ja) 高靭性でかつ耐食性に優れた油井用高強度ステンレス鋼管
JP7201094B2 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP7315097B2 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP7226675B1 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP4470617B2 (ja) 耐炭酸ガス腐食性に優れる油井用高強度ステンレス鋼管
WO2024209843A1 (ja) ステンレス継目無鋼管およびその製造方法
WO2023053743A1 (ja) 油井用高強度ステンレス継目無鋼管およびその製造方法
JP7626229B2 (ja) ステンレス継目無鋼管およびその製造方法
JP7409569B1 (ja) ステンレス継目無鋼管およびその製造方法
JP7347714B1 (ja) 油井用高強度ステンレス継目無鋼管
WO2024247508A1 (ja) 油井用高強度ステンレス継目無鋼管
WO2024009564A1 (ja) ステンレス継目無鋼管およびその製造方法
JP7279863B2 (ja) ステンレス鋼管およびその製造方法
JP7226571B2 (ja) ステンレス継目無鋼管およびその製造方法
WO2025013402A1 (ja) マルテンサイト系ステンレス継目無鋼管及びその製造方法

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 2024533288

Country of ref document: JP

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 24784639

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 2024784639

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 2024784639

Country of ref document: EP

Effective date: 20250717