WO2009119048A1 - Acier inoxydable destiné à être utilisé dans un tuyau de puits de pétrole - Google Patents

Acier inoxydable destiné à être utilisé dans un tuyau de puits de pétrole Download PDF

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WO2009119048A1
WO2009119048A1 PCT/JP2009/001238 JP2009001238W WO2009119048A1 WO 2009119048 A1 WO2009119048 A1 WO 2009119048A1 JP 2009001238 W JP2009001238 W JP 2009001238W WO 2009119048 A1 WO2009119048 A1 WO 2009119048A1
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stainless steel
less
steel
content
scc
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PCT/JP2009/001238
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English (en)
Japanese (ja)
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天谷尚
近藤邦夫
高部秀樹
大江太郎
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住友金属工業株式会社
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Priority to AU2009230545A priority Critical patent/AU2009230545B2/en
Priority to BRPI0909042A priority patent/BRPI0909042B8/pt
Priority to MX2010010435A priority patent/MX2010010435A/es
Priority to CN2009801107412A priority patent/CN101981215A/zh
Priority to EP09726339.6A priority patent/EP2256225B1/fr
Priority to JP2010505320A priority patent/JP4577457B2/ja
Priority to CA2717104A priority patent/CA2717104C/fr
Priority to ES09726339.6T priority patent/ES2674255T3/es
Publication of WO2009119048A1 publication Critical patent/WO2009119048A1/fr
Priority to US12/892,045 priority patent/US20110014083A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the present invention relates to stainless steel, and more particularly to stainless steel used for oil well pipes used in gas wells and oil wells.
  • Oil and natural gas produced from oil wells and gas wells contain corrosive associated gases such as carbon dioxide and hydrogen sulfide. Therefore, oil well pipes used for the production of oil and natural gas are required to have excellent corrosion resistance.
  • Patent Document 1 sets the Cr content of the stainless steel pipe to 15.5 to 18%, which is higher than that of the conventional 13% Cr steel. Also, by making Cr + Mo + 0.3Si-43.5C-0.4Mn-Ni-0.3Cu-9N ⁇ 11.5, the steel structure becomes a two-phase structure of ferrite phase and martensite phase, and hot working of oil well pipes Improve sexiness. Although the two-phase structure may decrease the corrosion resistance, the oil well pipe can contain Ni, Mo, and Cu to improve the corrosion resistance so that Cr + 0.65Ni + 0.6Mo + 0.55Cu-20C ⁇ 19.5. Prevents the deterioration of corrosion resistance.
  • Patent Document 2 also sets the Cr content of stainless steel to 15.5 to 18%, and further contains Ni that improves corrosion resistance.
  • the chemical composition of the stainless steel disclosed in this document is similar to that of Patent Document 1, but Mo is not an essential element and has an alloy design that suppresses costs. Furthermore, Cu is also an optional element.
  • the stainless steel disclosed in Patent Document 3 contains 14 to 18% Cr and contains Ni, Mo, and Cu, and thus has high corrosion resistance. Further, the steel structure contains a martensite phase and an austenite phase with a volume ratio of 3 to 15%, so that the toughness is improved.
  • the stainless steels disclosed in the above-mentioned Patent Documents 1 to 3 contain more Cr than the conventional 13% Cr-based steel and contain alloy elements such as Ni, Mo, and Cu. Corrosion rate decreases in high temperature corrosive environment.
  • the corrosion rate (mm / yr) was investigated using a 20 wt% NaCl aqueous solution at 230 ° C. in a 100 atmospheres CO 2 gas atmosphere, and a decrease in the corrosion rate was proved. (See Table 2 in Patent Document 1).
  • An object of the present invention is to provide an oil well pipe stainless steel having excellent corrosion resistance in a high temperature chloride aqueous solution environment containing carbon dioxide gas at 150 ° C. or higher. More specifically, it is to provide a stainless steel for oil country tubular goods having a low corrosion rate and excellent SCC resistance in a high-temperature chloride aqueous solution environment containing carbon dioxide gas.
  • the present inventors In order to reduce the corrosion rate in a high-temperature chloride aqueous solution environment containing carbon dioxide gas at 150 ° C. or higher, the present inventors contain 16% or more Cr by mass and a small amount of Mo in the steel. I thought it was necessary. However, since Cr and Mo are ferrite forming elements, if 16% or more of Cr and a slight amount of Mo are contained, most of the steel structure becomes a ferrite phase, and high strength cannot be obtained.
  • Ni which is an austenite forming element
  • the austenite phase at a high temperature is stabilized, so that a martensite phase is formed by quenching and a high strength steel structure is obtained.
  • Ms point martensite transformation start temperature
  • the Ni content is appropriately adjusted, a structure mainly including a martensite phase and a ferrite phase having a volume ratio of about 10% or more is formed, and high strength can be obtained.
  • Cu is effective for strengthening the ferrite phase, a high-strength structure can be obtained if Cu is contained. Cu further reduces the corrosion rate in a high-temperature chloride aqueous solution environment and improves the SCC resistance.
  • the present inventors have found that if a rare earth metal (REM) is contained in the above chemical composition in a predetermined amount or more, excellent SCC resistance can be obtained even in a high-temperature chloride aqueous solution environment containing carbon dioxide gas. It was. Hereinafter, this point will be described in detail.
  • REM rare earth metal
  • the present inventors prepared stainless steels having the chemical composition shown in Table 1, and conducted a test for evaluating the SCC resistance of each stainless steel.
  • the chemical components other than REM were the same. Further, the REM has a different content for each number in the range of 0.0001% to 0.03%. Further, each number of stainless steel was quenched and tempered, and the yield stress of each stainless steel was adjusted within the range of 860 to 900 MPa. All stainless steel structures contained 60% martensite phase, 30% ferrite phase and 10% austenite phase in volume fraction.
  • a 4-point bending specimen having a length of 75 mm, a width of 10 mm, and a thickness of 2 mm was collected from each number of stainless steel. Deflection due to 4-point bending was loaded on each collected specimen. At this time, in accordance with ASTM G39, the amount of deflection of each test piece was determined so that the stress applied to each test piece was equal to the yield stress of each test piece.
  • test piece loaded with deflection was immersed in an aqueous solution of NaCl at 25% by weight for one month in an autoclave at 204 ° C. (400 F) containing 30 atm of CO 2 under pressure. After immersion for 1 month, it was investigated whether or not SCC occurred in each test piece. Specifically, the longitudinal section of the test piece was observed with an optical microscope having a 100-fold field of view, and the presence or absence of SCC was judged visually.
  • the test results are shown in FIG.
  • the horizontal axis in FIG. 1 indicates the REM content (% by mass), and the vertical axis indicates whether or not SCC is generated.
  • a point “ ⁇ ” on “with SCC” on the vertical axis indicates that an SCC has occurred.
  • ⁇ indicates that no SCC has occurred.
  • FIG. 1 it was found that when the REM content is 0.001% or more, SCC does not occur even in a high-temperature chloride aqueous solution environment containing carbon dioxide gas. The reason why REM improves the SCC resistance is not clear, but the following reason is estimated.
  • the stainless steel according to the present invention is used for oil well pipes.
  • the stainless steel of the present invention is, in mass%, C: 0.001 to 0.05%, Si: 0.05 to 1%, Mn: 2% or less, P: 0.03% or less, S: 0.002 %: Cr: 16-18%, Ni: 3.5-7%, Mo: more than 2% and 4% or less, Cu: 1.5-4%, rare earth metal: 0.001-0.3%, sol.
  • Ti 0.5% or less
  • Zr 0.5% or less
  • Hf 0.5% or less
  • V 0.5% or less
  • a part of Fe And Nb one or more selected from the group consisting of 0.5% or less.
  • the above-mentioned stainless steel has a structure including a ferrite phase of 10 to 60% and a residual austenite phase of 2 to 10% by volume fraction.
  • the stainless steel according to the present invention has a yield stress of 654 MPa or more.
  • the stainless steel according to the present invention can be used for oil well pipes used in a high temperature chloride aqueous solution environment containing carbon dioxide gas at 150 ° C. or higher.
  • a high-temperature chloride aqueous solution environment containing carbon dioxide and having a temperature of 150 ° C. or higher is simply referred to as a high-temperature chloride aqueous solution environment.
  • the stainless steel according to the present invention has the following chemical composition.
  • % related to elements means “% by mass”.
  • Carbon (C) forms carbides with Cr and reduces the corrosion resistance of steel in a high temperature chloride aqueous solution environment. For this reason, the C content is preferably as low as possible. Therefore, the upper limit of the C content is 0.05%. The lower limit of the C content that can be substantially controlled is 0.001%.
  • Si deoxidizes steel in the refining process.
  • the lower limit of the Si content is set to 0.05%.
  • the upper limit of Si content is 1%.
  • Manganese (Mn) improves the strength of steel. However, if Mn is contained excessively, segregation is likely to occur in the steel. Segregation in steel reduces the toughness of the steel and further reduces the SCC resistance in a high-temperature chloride aqueous solution environment. Therefore, the Mn content is 2% or less. In order to obtain the effect of improving the strength, the preferable Mn content is 0.2% or more. However, even if the Mn content is less than 0.2%, the strength of the steel is improved to some extent.
  • Phosphorus (P) is an impurity. P decreases SSC (sulfide stress cracking) resistance and SCC resistance in a high-temperature chloride aqueous solution environment. For this reason, the P content is preferably as low as possible. Therefore, the P content is set to 0.03% or less.
  • S Sulfur
  • Mn or the like Sulfur (S) combines with Mn or the like to form inclusions.
  • the formed inclusion becomes a starting point of pitting corrosion and SCC, and reduces the corrosion resistance of steel.
  • S reduces the hot workability of steel. Therefore, the S content is preferably as low as possible. Therefore, the S content is less than 0.002%.
  • Chromium (Cr) is an essential element that improves the corrosion resistance in a high-temperature chloride aqueous solution environment.
  • the lower limit of the Cr content is 16%.
  • Cr is a ferrite-forming element, if it is contained excessively, the proportion of the ferrite phase increases in the steel structure, and the strength of the steel decreases. Furthermore, since the ratio of a retained austenite phase falls, the toughness of steel falls. Therefore, the upper limit of the Cr content is 18%.
  • a preferable Cr content is 16.5 to 17.5%.
  • Nickel (Ni) improves the corrosion resistance in a high temperature chloride aqueous solution environment. Ni further improves the toughness of the steel. In order to obtain these effects, the lower limit of the Ni content is 3.5%.
  • Ni is an austenite forming element, if it is excessively contained, the proportion of the retained austenite phase is excessively increased in the steel structure, and the strength of the steel is lowered. Therefore, the upper limit of the Ni content is 7%.
  • a preferable Ni content is 3.5 to 6.5%, and a more preferable Ni content is 3.8 to 5.8%.
  • Copper (Cu) reduces the elution rate of steel in a high temperature chloride aqueous solution environment. Cu further improves the SCC resistance of the steel. Cu also strengthens the ferrite phase in the steel structure. In order to obtain these effects, the lower limit of the Cu content is 1.5%. On the other hand, if Cu is contained excessively, the hot workability of the steel is lowered. Therefore, the upper limit of the Cu content is 4%. A preferable Cu content is 1.5 to 3.0%, and a more preferable Cu content is 1.5 to 2.5%.
  • Molybdenum (Mo) improves the pitting corrosion resistance and SCC resistance of steel in the presence of Cr. In order to obtain this effect, the Mo content is more than 2%.
  • Mo is a ferrite-forming element, if Mo is contained excessively, the proportion of the ferrite phase in the steel structure increases and the strength decreases. Therefore, the Mo content is 4% or less.
  • a preferable Mo content is 2.1 to 3.3%, and a more preferable Mo content is 2.3 to 3.0%.
  • Al deoxidizes steel in the refining process.
  • the lower limit of the Al content is 0.001%.
  • the upper limit of the Al content is 0.1%.
  • Al content said by this specification means content of acid-soluble Al (Sol.Al:Soluble Aluminum).
  • N Nitrogen
  • N stabilizes the austenite phase. N further improves pitting corrosion resistance.
  • the N content is 0.05% or less. The minimum with preferable N content for acquiring the above-mentioned effect effectively is 0.005%.
  • Oxygen (O) is an impurity. O combines with other elements to form oxides, reducing the toughness and corrosion resistance of the steel. Therefore, it is preferable that the O content is as small as possible. Therefore, the O content is 0.05% or less.
  • Rare earth metals are important elements in the present invention. As described above, REM improves the SCC resistance in a high-temperature chloride aqueous solution environment. In order to obtain this effect, the lower limit of the REM content is 0.001%. On the other hand, even if REM is excessively contained, the effect is saturated. Therefore, the upper limit of the REM content is 0.3%. A preferable REM content is 0.001 to 0.1%, and a more preferable REM content is 0.001 to 0.01%.
  • REM as used in the field of this invention is lanthanoid from yttrium (Y) of atomic number 39 and lanthanum (La) of atomic number 57 to lutetium (Lu) of 71.
  • the stainless steel according to the present invention contains one or more of the above-mentioned REMs. Accordingly, the REM content is a total content of one or more selected from the above-described plurality of REMs.
  • the balance of the chemical composition is Fe and impurities.
  • the stainless steel of the present invention further contains one or more selected from the group consisting of Ti, Zr, Hf, V and Nb, instead of part of Fe, if necessary.
  • Titanium (Ti), zirconium (Zr), hafnium (Hf), vanadium (V) and niobium (Nb) are not essential elements but are elements that are arbitrarily added. All of these elements fix C and suppress the formation of Cr carbides. Therefore, the occurrence of pitting caused by the Cr-deficient layer formed around the Cr carbide is suppressed, and the SCC sensitivity is reduced. However, if these elements are contained excessively, the toughness of the steel is lowered. Accordingly, the upper limit of the content of these elements is 0.5%. In order to obtain the above-mentioned effects remarkably, the lower limit of the content of these elements is preferably 0.005% for all elements. However, even if the content of these elements is less than the preferable lower limit, the above-described effects can be obtained to some extent.
  • the stainless steel according to the present invention can have the structure described later by performing a heat treatment of quenching and tempering, and can obtain the desired corrosion resistance and the strength necessary for oil well pipe use.
  • the manufacturing method of the stainless steel pipe of this invention is demonstrated as an example.
  • ⁇ Steel with the above chemical composition is melted to produce billets.
  • the manufactured billet is hot-worked into a stainless steel pipe.
  • the Mannesmann method is performed to manufacture a seamless steel pipe.
  • a preferable quenching temperature is 900 to 1200 ° C.
  • a preferable tempering temperature is 450 to 650 ° C.
  • the structure of stainless steel manufactured by the above-described manufacturing method includes 10-60% ferrite phase and 2-10% residual austenite phase in volume fraction.
  • the volume fraction of the ferrite phase is obtained by the following method.
  • the test piece whose surface has been polished is etched using a mixed solution of aqua regia and glycerin.
  • the area ratio of the ferrite phase on the specimen surface is measured by a point calculation method based on JISG0555. Let the measured area ratio be the volume fraction.
  • the volume fraction of the retained austenite phase is measured by an X-ray diffraction method.
  • the part other than the ferrite phase and the retained austenite phase is mainly a tempered martensite phase.
  • carbides, nitrides, borides, and Cu phases may be included.
  • the stainless steel according to the present invention has the above-described structure, so that the yield stress becomes 654 MPa (corresponding to 95 ksi) or more. Furthermore, it can be adjusted to 758 MPa (corresponding to 110 ksi) or more, and further to 862 MPa (corresponding to 125 ksi) or more.
  • the yield stress here is 0.2% offset proof stress based on the ASTM standard.
  • the stainless steel of the present invention has high toughness because it contains the retained austenite phase having the above volume fraction in the structure.
  • a plurality of stainless steels having various chemical compositions were manufactured, and the SCC resistance in a high temperature chloride aqueous solution environment was investigated.
  • Each numerical value in Table 2 indicates the content (% by mass) of the corresponding element. Moreover, among the chemical composition of each steel, the remainder other than the elements described in Table 1 is Fe and impurities.
  • Symbols a) to c) next to the numerical values in the “REM” column indicate the type of REM contained in each steel. Specifically, a) indicates that the contained REM is neodymium (Nd). b) shows that the contained REM is yttrium (Y). c) shows that the contained REM is misch metal. Misch metal is composed of 51.0% cerium (Ce), 25.5% lanthanum (La), 18.6% neodymium (Nd), and 4.8% praseodymium (Pr). 0.1% samarium (Sm).
  • the chemical compositions of the steels with numbers 1 to 12 were all within the range defined in the present invention.
  • the Mo content was less than the lower limit of the range defined in the present invention.
  • the Cr content was less than the lower limit of the range defined in the present invention.
  • the Cu content was less than the lower limit of the range defined in the present invention.
  • REM was not contained.
  • the Ni content was less than the lower limit of the range defined in the present invention.
  • each number was hot forged and hot rolled to produce a 12 mm thick steel plate. Quenching and tempering were performed on each number of steel plates. In the quenching treatment, each numbered steel plate was heated at a quenching temperature of 980 to 1200 ° C. for 15 minutes and then cooled with water. In the tempering treatment, the tempering temperature was set to 500 to 650 ° C. Through the above steps, the yield strength of each steel sheet was adjusted to be in the range of 800 to 950 MPa.
  • a round bar tensile test piece was collected from each number of steel plates and subjected to a tensile test.
  • the longitudinal direction of the round bar tensile test piece was the rolling direction of the steel plate, the diameter of the parallel part of the round bar tensile test piece was 14 mm, and the length was 20 mm.
  • the tensile test was performed at room temperature.
  • Each test piece loaded with deflection was immersed in an aqueous solution of NaCl at 25% by weight for one month in an autoclave at 204 ° C. (400 F) containing 30 atm of CO 2 under pressure. After immersion for 1 month, it was investigated whether or not SCC occurred in each test piece. Specifically, the longitudinal section of the test piece was observed with an optical microscope having a 100-fold field of view, and the presence or absence of SCC was judged visually. Moreover, the weight of each test piece before and after the test was measured. The corrosion weight loss of each test piece was obtained from the change in the measured weight, and the corrosion rate was obtained based on the corrosion weight loss.
  • the “YS” column in Table 3 indicates the yield stress (MPa) of each numbered steel plate obtained by a tensile test.
  • the volume fractions (%) of the ferrite phase and the retained austenite phase of the steel plates of the respective numbers are shown.
  • “No SCC” in the “SCC evaluation result” column indicates that no SCC occurred in the four-point bending test piece, and “SCC present” indicates that SCC occurred.
  • “ ⁇ 0.1” in the “Corrosion Rate” column indicates that the corrosion rate was less than 0.1 g / (m 2 ⁇ hr), and “ ⁇ 0.1” indicates that the corrosion rate was 0.1 g. / (M 2 ⁇ hr) or more.
  • stainless steel can be used as an oil well pipe, and is particularly suitable for use in an oil well pipe used in a high temperature chloride aqueous solution environment containing carbon dioxide gas at 150 ° C. or higher.

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  • Rigid Pipes And Flexible Pipes (AREA)

Abstract

L'invention porte sur un acier inoxydable pour un tuyau de puits de pétrole, lequel inclut les composants suivants (en masse) : C : de 0,001 à 0,05 %, Si : de 0,05 à 1 %, Mn : 2 % ou moins, P : 0,03 % ou moins, S : moins de 0,002 %, Cr : de 16 à 18 %, Ni : de 3,5 à 7 %, Mo : plus de 2 % et pas plus de 4 %, Cu : de 1,5 à 4 %, un lanthanide : de 0,001 à 0,3 %, Al.sol : de 0,001 à 0,1 %, Ca : de 0,0001 à 0,01 %, O : 0,05 % ou moins et N : 0,05 % ou moins, le reste étant Fe et des impuretés. L'acier inoxydable contient un lanthanide et peut par conséquent présenter une excellente résistance à la corrosion fissurante sous tension (SCC), même dans une solution aqueuse de chlorure présentant une température élevée.
PCT/JP2009/001238 2008-03-28 2009-03-19 Acier inoxydable destiné à être utilisé dans un tuyau de puits de pétrole WO2009119048A1 (fr)

Priority Applications (9)

Application Number Priority Date Filing Date Title
AU2009230545A AU2009230545B2 (en) 2008-03-28 2009-03-19 Stainless steel for use in oil well tube
BRPI0909042A BRPI0909042B8 (pt) 2008-03-28 2009-03-19 aço inoxidável usado para produtos tubulares empregados nos campos petrolíferos
MX2010010435A MX2010010435A (es) 2008-03-28 2009-03-19 Acero inoxidable usado para material tubular destinado a pozos petroleros.
CN2009801107412A CN101981215A (zh) 2008-03-28 2009-03-19 油井管用不锈钢
EP09726339.6A EP2256225B1 (fr) 2008-03-28 2009-03-19 Acier inoxydable destiné à être utilisé dans un tuyau de puits de pétrole
JP2010505320A JP4577457B2 (ja) 2008-03-28 2009-03-19 油井管に用いられるステンレス鋼
CA2717104A CA2717104C (fr) 2008-03-28 2009-03-19 Acier inoxydable destine a etre utilise dans un tuyau de puits de petrole
ES09726339.6T ES2674255T3 (es) 2008-03-28 2009-03-19 Acero inoxidable para su uso en tubo de pozo de petróleo
US12/892,045 US20110014083A1 (en) 2008-03-28 2010-09-28 Stainless steel used for oil country tubular goods

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2008-087643 2008-03-28
JP2008087643 2008-03-28

Related Child Applications (1)

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US12/892,045 Continuation US20110014083A1 (en) 2008-03-28 2010-09-28 Stainless steel used for oil country tubular goods

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WO2009119048A1 true WO2009119048A1 (fr) 2009-10-01

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PCT/JP2009/001238 WO2009119048A1 (fr) 2008-03-28 2009-03-19 Acier inoxydable destiné à être utilisé dans un tuyau de puits de pétrole

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US (1) US20110014083A1 (fr)
EP (1) EP2256225B1 (fr)
JP (1) JP4577457B2 (fr)
CN (1) CN101981215A (fr)
AR (1) AR070745A1 (fr)
AU (1) AU2009230545B2 (fr)
BR (1) BRPI0909042B8 (fr)
CA (1) CA2717104C (fr)
ES (1) ES2674255T3 (fr)
MX (1) MX2010010435A (fr)
RU (1) RU2449046C1 (fr)
WO (1) WO2009119048A1 (fr)

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EP2565287A4 (fr) * 2010-04-28 2017-03-15 Nippon Steel & Sumitomo Metal Corporation Acier inoxydable haute résistance pour puits de pétrole et tube d'acier inoxydable haute résistance pour puits de pétrole

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CN103484785A (zh) * 2013-08-16 2014-01-01 广东华鳌合金新材料有限公司 一种含稀土元素的高强度的合金及其制备方法
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
WO2016113794A1 (fr) 2015-01-15 2016-07-21 Ｊｆｅスチール株式会社 Tube d'acier inoxydable sans soudure pour puits de pétrole, et son procédé de fabrication
EP3333276A4 (fr) * 2015-08-04 2019-01-09 Nippon Steel & Sumitomo Metal Corporation Acier inoxydable et matériau en acier inoxydable pour puits de pétrole
US11066718B2 (en) 2016-01-13 2021-07-20 Nippon Steel Corporation Method of manufacturing stainless pipe for oil wells and stainless steel pipe for oil wells
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US20210138550A1 (en) * 2019-10-21 2021-05-13 Desktop Metal, Inc. Binder compositions for additive manufacturing comprising low molecular weight polymers including acrylic acid repeat units
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2565287A4 (fr) * 2010-04-28 2017-03-15 Nippon Steel & Sumitomo Metal Corporation Acier inoxydable haute résistance pour puits de pétrole et tube d'acier inoxydable haute résistance pour puits de pétrole
WO2013146046A1 (fr) * 2012-03-26 2013-10-03 新日鐵住金株式会社 Acier inoxydable pour puits de pétrole et tuyau en acier inoxydable pour puits de pétrole
JP5348354B1 (ja) * 2012-03-26 2013-11-20 新日鐵住金株式会社 油井用ステンレス鋼及び油井用ステンレス鋼管
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WO2014030392A1 (fr) 2012-08-24 2014-02-27 エヌケーケーシームレス鋼管株式会社 Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion

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CA2717104A1 (fr) 2009-10-01
EP2256225A1 (fr) 2010-12-01
CA2717104C (fr) 2014-01-07
CN101981215A (zh) 2011-02-23
AR070745A1 (es) 2010-05-05
EP2256225A4 (fr) 2017-01-04
BRPI0909042A2 (pt) 2016-06-07
BRPI0909042B8 (pt) 2020-05-05
AU2009230545A1 (en) 2009-10-01
ES2674255T3 (es) 2018-06-28
MX2010010435A (es) 2010-11-05
JP4577457B2 (ja) 2010-11-10
US20110014083A1 (en) 2011-01-20
JPWO2009119048A1 (ja) 2011-07-21
AU2009230545B2 (en) 2011-12-15
RU2449046C1 (ru) 2012-04-27
EP2256225B1 (fr) 2018-04-25
BRPI0909042B1 (pt) 2020-03-24

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