EP2256225B1 - 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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EP2256225B1
EP2256225B1 EP09726339.6A EP09726339A EP2256225B1 EP 2256225 B1 EP2256225 B1 EP 2256225B1 EP 09726339 A EP09726339 A EP 09726339A EP 2256225 B1 EP2256225 B1 EP 2256225B1
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steel
stainless steel
scc
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EP2256225A1 (fr
EP2256225A4 (fr
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Hisashi Amaya
Kunio Kondo
Hideki Takabe
Taro Ohe
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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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 specifically to stainless steel used for oil country tubular goods for use in gas wells or oil wells.
  • Oil or natural gas produced from oil wells or gas wells contains associated corroding gas as such as carbon dioxide gas and hydrogen sulfide. Therefore, oil country tubular goods used for producing oil or natural gas need high corrosion resistance.
  • Carbon steel or low alloy steel has been used as a steel for oil country tubular goods. As the goods have come to be used in a tougher corroding environment in an oil well or a gas well, SUS420 martensitic stainless steel (13% Cr-based steel) having a Cr content of about 13% or stainless steel having high corrosion resistance such as improved 13% Cr-based steel produced by adding Ni to the 13% Cr-based steel has been used.
  • Patent Document 1 JP 2005-336595 A
  • Patent Document 2 JP 2006-16637 A
  • Patent Document 3 JP 2007-332442 A
  • the Cr content of the stainless steel pipe is from 15.5% to 18% which is greater than that of the conventional 13% Cr-based steel.
  • the steel has a two-phase structure including a ferrite phase and a martensite phase, so that the hot workability of the oil country tubular good is improved.
  • the two-phase structure could lower the corrosion resistance, while when Ni, Mo, and Cu that improve the corrosion resistance are added such that Cr+0.65Ni+0.6Mo+0.55Cu-20C ⁇ 19.5 is established, the reduction in the corrosion resistance of the oil country tubular good is prevented.
  • the Cr content of the stainless steel is from 15.5% to 18% and Ni that improves the corrosion resistance is contained.
  • the chemical composition of the stainless steel disclosed by the document is similar to that in Patent Document 1, but Mo is not an essential element, and therefore a less costly alloy design is proposed.
  • Cu is also an optional element.
  • the stainless steel disclosed by Patent Document 3 contains 14% to 18% Cr as well as Ni, Mo, and Cu, so that high corrosion resistance is obtained. Furthermore, the steel includes a martensite phase and 3% to 15% austenite phase by volume, and therefore the toughness improves.
  • Patent Documents 1 to 3 surely contain a larger amount of Cr than the conventional 13% Cr-based steel and alloy elements such as Ni, Mo, and Cu are added, so that the corrosion rate in a high temperature corroding environment is reduced.
  • the corrosion rate (mm/yr) was examined and it was established that the corrosion rate was reduced (see Table 2 in Patent Document 1).
  • EP-A1-1,683,885 discloses a highly corrosion resistant high strength stainless steel pipe for linepipe, having a composition containing 0.001 to 0.015% C, 0.01 to 0.5% Si, 0.1 to 1.8% Mn, 0.03% or less P, 0.005% or less S, 15 to 18% Cr, 0.5% or more and less than 5.5% Ni, 0.5 to 3.5% Mo, 0.02 to 0.2% V, 0.001 to 0.015% N, and 0.006% or less O, by mass, so as to satisfy [Cr + 0.65Ni + 0.6Mo + 0.55Cu - 20C ⁇ 18.5],[Cr + Mo + 0.3Si - 43.5C - 0.4Mn - Ni - 0.3Cu - 9N ⁇ 11.5] and[C + N ⁇ 0.025].
  • Cr and Mo are ferrite forming elements and therefore if at least 16 mass % Cr and a small amount of Mo are contained, a major part of the structure of the steel becomes a ferrite phase and therefore high strength cannot be obtained.
  • an austenite phase at high temperatures is stabilized by adding Ni that is an austenite forming element, so that a martensite phase is formed by quenching and a high strength steel structure is obtained.
  • Ni an austenite forming element
  • Ms point the starting temperature for martensite transformation
  • a structure mainly including a martensite phase and about at least 10% ferrite phase by volume is formed and high strength can be provided.
  • the copper (Cu) effectively enhances a ferrite phase, and therefore a high strength structure can be provided by adding Cu.
  • Cu reduces the corrosion rate in a high temperature chloride aqueous solution environment and improves the SCC resistance.
  • stainless steel having prescribed strength and reduced corrosion rate can be provided when the steel contains 16% to 18% Cr, more than 2% and not more than 4% Mo, 3.5% to 7% Ni, and 1.5% to 4% Cu.
  • the inventors also found that by adding at least a prescribed amount of an earth rare metal (REM) in the chemical composition described above, high SCC resistance results even in a carbon dioxide gas contained, high temperature chloride aqueous solution environment. Now, this will be described in detail.
  • REM earth rare metal
  • the chemical compositions are the same except for REM.
  • the REM content is different among the numbered stainless steel grades in the range from 0.0001% to 0.03%.
  • these numbered stainless steel grades were subjected to quenching-tempering such that the yield stress of each kind of stainless steel was adjusted in the range from 860 MPa to 900 MPa.
  • the structures of these numbered stainless steel grades include, in volume percentage, 60% martensite phase, 30% ferrite phase, and 10% austenite phase.
  • a specimen for four-point bending test having a length of 75 mm, a width of 10 mm, and a thickness of 2 mm was sampled from each of the numbered stainless steel grades.
  • the sampled specimens were subjected to a bending load by four-point bending.
  • the bending amount of each specimen was determined according to ASTM G39 such that stress applied on each specimen was equal to the yield stress of each specimen.
  • Each bent specimen was immersed for one month in a 25 wt% NaCl aqueous solution in an autoclave at 204°C (400F) having CO 2 enclosed therein under a pressure of 30 atm. After the immersion for one month, each specimen was examined for the presence of SCC. More specifically, a longitudinal section of each specimen was observed with a 100x magnification optical microscope and determined for the presence/absence of SCC by visual inspection.
  • Fig. 1 The test result is given in Fig. 1 .
  • the abscissa represents the REM content (% by mass) and the ordinate represents the presence/absence of SCC.
  • Fig. 1 “ ⁇ " in the "SCC present” on the ordinate indicates the presence of SCC, while “ ⁇ ” in the “no SCC” indicates the absence of SCC.
  • the REM content was not less than 0.001%, no SCC was generated even in a carbon dioxide contained, high temperature chloride aqueous solution environment. While how REM improves the SCC resistance is not clearly known, this may be for the following reason.
  • the inventors have completed the following invention based on the foregoing findings.
  • Stainless steel used for an oil country tubular goods consists of, in percent by mass, 0.001% to 0.05% C, 0.05% to 1% Si, at most 2% Mn, at most 0.03% P, less than 0.002% S, 16% to 18% Cr, 3.5% to 7% Ni, more than 2% and at most 4% Mo, 1.5% to 4% Cu, 0.001% to 0.3% earth metal, 0.001% to 0.1% sol.
  • the steel has a structure including, in percent by volume, 10% to 60% ferrite phase and 2% to 10% residual austenite phase and has a yield stress of at least 654 MPa.
  • the stainless steel according to the invention preferably further includes, at least one selected from the group consisting of 0.005% to 0.5% Ti, 0.005% to 0.5% Zr, 0.005% to 0.5% Hf, 0.0055 to 0.5% V, and 0.005% to 0.5% Nb.
  • Fig. 1 is a graph showing the relation between the contents of rare earth metals in stainless steel and SCC.
  • Stainless steel according to the invention is applicable to oil country tuber goods for use in a carbon dioxide gas contained, high temperature chloride aqueous solution environment at 150°C or more.
  • this carbon dioxide gas contained, high temperature chloride aqueous solution environment at 150°C or more will be simply referred to as "high temperature chloride aqueous solution environment.”
  • the stainless steel according to the invention has the following chemical composition.
  • % related to elements means “% by mass.”
  • Carbon (C) forms carbide with Cr and lowers the corrosion resistance of steel in a high temperature chloride aqueous solution environment. Therefore, the C content is preferably as small as possible. Therefore, the upper limit for the C content is 0.05%. Note that the lower limit for the C content that can substantially be controlled is 0.001%.
  • Si 0.05% to 1%.
  • Si deoxidizes steel in refining process.
  • the lower limit for the Si content is 0.05%.
  • an excessive Si content not only saturates the deoxidizing effect but also lowers the hot workability of the steel. Therefore, the upper limit for the Si content is 1%.
  • Manganese (Mn) improves the strength of the steel.
  • an excessive Mn content is more likely to cause segregation in the steel.
  • the segregation in the steel lowers the toughness of the steel and also lowers the SCC resistance in a high temperature chloride aqueous solution environment. Therefore, the Mn content is not more than 2%.
  • the Mn content is preferably not less than 0.2% in order to improve the strength. However, if the Mn content is less than 0.2%, the strength of the steel is improved to some extent.
  • Phosphorus (P) is an impurity and lowers the SSC (sulfide stress cracking) resistance and the SCC resistance in a high temperature chloride aqueous solution environment. Therefore, the P content is preferably as small as possible. The P content is therefore not more than 0.03%.
  • S Sulfur
  • Mn or the like Sulfur (S) combines with Mn or the like and forms an inclusion.
  • the formed inclusion becomes an origin for a pit or SCC and lowers the corrosion resistance of the steel.
  • S lowers the hot workability of the steel. Therefore, the S content is preferably as small 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 for the Cr content is 16%.
  • Cr is a ferrite forming element
  • an excessive Cr content increases the ratio of a ferrite phase in the steel structure and lowers the strength of the steel. Furthermore, it lowers the ratio of a residual austenite phase, which lowers the toughness of the steel. Therefore, the upper limit for the Cr content is 18%.
  • the Cr content is preferably from 16.5% to 17.5%.
  • Nickel (Ni) improves the corrosion resistance in a high temperature chloride aqueous solution environment and also improves the toughness of the steel. In order to obtain these effects, the lower limit for the Ni content is 3.5%.
  • Ni is an austenite forming element and an excessive Ni content increases the ratio of a residual austenite phase in the structure of the steel, which lowers the strength of the steel. Therefore, the upper limit for the Ni content is 7%.
  • the Ni content is preferably from 3.5% to 6.5%, more preferably from 3.8% to 5.8%.
  • Copper (Cu) lowers the dissolution rate of the steel in a high temperature chloride aqueous solution environment and also improves the SCC resistance of the steel. In addition, Cu strengthens a ferrite phase in the structure of the steel. In order to obtain these effects, the lower limit for the Cu content is 1.5%. On the other hand, an excessive Cu content lowers the hot workability of the steel. Therefore, the upper limit for the Cu content is 4%.
  • the Cu content is preferably from 1.5% to 3.0%, more preferably from 1.5% to 2.5%.
  • Molybdenum (Mo) improves the pitting corrosion resistance and the SCC resistance of the steel when it coexists with Cr. In order to obtain the effects, the Mo content is more than 2%. On the other hand, Mo is a ferrite forming element and therefore an excessive Mo content increases the ratio of a ferrite phase in the structure of the steel, which lowers the strength. Therefore, the Mo content is not more than 4%.
  • the Mo content is preferably from 2.1% to 3.3%, more preferably from 2.3% to 3.0%.
  • the Al content in the specification means the content of acid soluble aluminum (sol. Al).
  • the lower limit for the Ca content is 0.0001%.
  • an excessive Ca content causes a large amount of an inclusion such as CaO to be generated in the steel, which lowers the toughness of the steel.
  • the inclusion such as CaO forms an origin for a pit. Therefore, the upper limit for the Ca content is 0.01%.
  • N Nitrogen
  • the N content is not more than 0.05%.
  • the lower limit for the N content is preferably 0.005%.
  • Oxygen (O) is an impurity and combines with another element to form oxide, which lowers the toughness and the corrosion resistance of the steel. Therefore, the O content is preferably as small as possible. Therefore, the O content is not more than 0.05%.
  • Rare earth metals are important elements according to the invention.
  • the REM improve the SCC resistance in a high temperature chloride aqueous solution environment as described above.
  • the lower limit for the REM content is 0.001%.
  • an excessive REM content saturates the effect. Therefore, the upper limit for the REM content is 0.3%.
  • the REM content is preferably from 0.001% to 0.1%, more preferably from 0.001% to 0.01%.
  • the REM according to the invention refer to yttrium (Y) with atomic number 39 and lanthanoids from lanthanum (La) with atomic number 57 to lutetium (Lu) with atomic number 71.
  • the stainless steel according to the invention contains at least one of the above REM. Therefore, the REM content means the total content of at least one selected from the plurality of REM described above.
  • the balance of the chemical composition consists of Fe and impurities.
  • the stainless steel according to the invention contains at least one selected from the group consisting of Ti, Zr, Hf, V, and Nb in place of a part of Fe if necessary.
  • Titanium (Ti), zirconium (Zr), hafnium (Hf), vanadium (V), and niobium (Nb) are not essential elements and added as optional elements. These elements each fix C and reduce the generation of Cr carbide. Therefore, the generation of a pit attributable to a Cr depleted layer formed around Cr carbide is reduced and the SCC sensitivity is reduced. However, an excessive content of any of these elements lowers the toughness of the steel. Therefore, the upper limits for the contents of these elements are each 0.5%. In order to effectively obtain the above-described effect, the lower limits for the contents of these elements are each preferably 0.005%. Note however that if the contents of these elements are less than the preferable lower limit, the above-described effect is obtained to some extent.
  • the stainless steel according to the invention can have the following structure by carrying out quenching-tempering as heat treatment, so that the corrosion resistance as intended and strength necessary when it is used as oil country tubular goods can be provided. Now, a method of manufacturing a stainless steel pipe according to the invention will be described by way of example.
  • Steel having the above-described chemical composition is melted and made into a billet.
  • the produced billet is subjected to hot working and made into a stainless steel pipe.
  • a Mannesmann method for example is employed as the hot working to make a seamless steel pipe. Note that the hot working may be hot extruding or hot forging.
  • the produced stainless steel pipe is subjected to quenching and tempering.
  • the preferable quenching temperature is from 900°C to 1200°C
  • the preferable tempering temperature is from 450°C to 650°C.
  • the structure of the stainless steel produced by the above-described method includes, in percent by volume, 10% to 60% ferrite phase and 2% to 10% residual austenite phase.
  • the volume percentage of the ferrite phase is obtained by the following method.
  • a specimen having its surface polished is etched using a mixture solution of aqua regia and glycerin.
  • the area ratio of the ferrite phase at the specimen surface is measured by a point-counting method according to JISG0555. The measured area ratio is used as a volume percentage.
  • the volume percentage of the residual austenite phase is measured by X-ray diffraction.
  • the portion other than the ferrite phase and the residual austenite phase is mainly a tempered martensite phase.
  • Carbide, nitride, boride and a Cu phase may be included other than the martensite phase.
  • the stainless steel according to the invention has the above-described structure, so that the yield stress is not less than 654 MPa (that corresponds to 95 ksi).
  • the yield stress may be adjusted to 758 MPa (that corresponds to 110 ksi) or more and further to 862 MPa (that corresponds to 125 ksi) or more.
  • the yield stress in this specification refers to 0.2% offset yield stress based on the ASTM standard.
  • the stainless steel according to the invention has high toughness since it contains the residual austenite phase as much as the above-described volume percentage in the structure.
  • a plurality of kinds of stainless steel having various chemical compositions were produced and examined for their SCC resistance in a high temperature chloride aqueous solution environment.
  • the numerical values in Table 2 refer to the contents of corresponding elements (% by mass). Among these chemical compositions, the balance other than the elements described in Table 1 is Fe and impurities.
  • the symbols a) to c) attached to the numerical values in the "REM" column each represent the kind of REM included in the steel. More specifically, a) means that the contained REM is neodymium (Nd). Similarly, b) means that the contained REM is yttrium (Y) and c) means that the contained REM is misch metal.
  • the misch metal contains, in percent by mass, 51.0% cerium (Ce), 25.5% lanthanum (La), 18.6% neodymium (Nd), 4.8% praseodymium (Pr) and 0.1% samarium (Sm).
  • the steel kinds with Nos. 1 to 12 each had a chemical composition within the range defined by the invention.
  • its Mo content was less than the lower limit defined by the invention.
  • its Cr content was less than the lower limit defined by the invention.
  • its Cu content was less than the lower limit defined by the invention.
  • the steel with No. 16 contained no REM.
  • its Ni content was less than the lower limit defined by the invention.
  • the numbered steel plates were subjected to hot forging and hot rolling, and a steal plate having a thickness of 12 mm was produced.
  • the numbered steel plates were subjected to quenching and tempering. In the quenching processing, the steel plates were each heated for 15 minutes at a quenching temperature from 980°C to 1200°C and then cooled with water. In the tempering processing, the tempering temperature was from 500°C to 650°C. Through these steps, the yield stress of each steel plate was adjusted to be in the range from 800 MPa to 950 MPa.
  • the volume percentage (%) of the ferrite phase and the residual austenite phase of each steel plate was obtained by the measuring method described in 3.
  • a round rod tensile test specimen was sampled from each of the steel plates and subjected to a tensile test.
  • the length-wise direction of the round rod tensile test specimen was arranged in the direction of rolling the steel plate and the parallel part of the round rod tensile test specimen had a diameter of 14 mm, and a length of 20 mm.
  • the tensile tests were carried out at room temperatures.
  • a four-point bending specimen having a length of 75 mm, a width of 10 mm, and a thickness of 2 mm was sampled from each of the steel plates. Each of the sampled specimens was bent by four-point bending. At the time, according to ASTM G39, the amount of bending of each of the specimens was determined so that stress applied on each of the specimens was equal to the yield stress of each of the specimens.
  • the bent specimens were each immersed for one month in a 25 wt% NaCl aqueous solution in an autoclave at 204°C (400F) having CO 2 enclosed therein under a pressure of 30 atm. After the immersion for one month, the specimens were examined for the presence of SCC. More specifically, a longitudinal section of each specimen was observed with a 100x magnification optical microscope and examined for the presence/absence of SCC by visual inspection. The weight of each specimen was measured before and after the test. From the difference between the measured weights, the weight loss of each specimen caused by corrosion was obtained and the corrosion rate was calculated based on the weight loss.
  • the “YS” column in Table 3 represents the yield stress (MPa) of each of the numbered steel plates obtained by the tensile tests.
  • the "ferrite phase” and “residual austenite phase” columns represent the volume percentages (%) of the ferrite phase and the residual austenite phase in each of the steel plates.
  • the “NO SCC” indicates that there was no SCC generated at the four-point bending test specimen, and the “SCC PRESENT” indicates that there was SCC.
  • the “ ⁇ 0.1” indicates that the corrosion rate was less than 0.1 g/(m 2 ⁇ hr), while the “ ⁇ 0.1” indicates that the corrosion rate was not less than 0.1 g/(m 2 ⁇ hr).
  • the steels with Nos. 1 to 12 did not have any SCC and their corrosion rates were all less than 0.1 g/(m 2 ⁇ hr). Their yield stress values were all 654 MPa or more.
  • the steels with Nos. 13, 15 and 17 had SCC because their Mo, Cu, and Ni contents were small.
  • the steel with No. 14 had SCC because it contained only a small amount of Cr, and its corrosion rate was not less than 0.1 g/(m 2 ⁇ hr).
  • the steel with No. 16 had SCC because it did not contain REM.
  • the stainless steel according to the invention can be applied as oil country tubular goods and particularly suitably applied to an oil country tubular good for use in a carbon dioxide gas contained, high temperature chloride aqueous solution environment at 150°C or higher.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Rigid Pipes And Flexible Pipes (AREA)

Claims (2)

  1. Acier inoxydable utilisé pour les fournitures tubulaires destinées aux produits pétroliers, constitué de, en pourcentage en masse, de 0,001 % à 0,05 % de C, de 0,05 % à 1 % de Si, au plus 2 % de Mn, au plus 0,03 % de P, moins de 0,002 % de S, de 16 % à 18 % de Cr, de 3,5 % à 7 % de Ni, plus de 2 % et au plus 4 % de Mo, de 1,5 % à 4 % de Cu, de 0,001 % à 0,3 % de métal des terres rares, de 0,001% à 0,1% d'Al sol., de 0,0001 % à 0,01 % de Ca, au plus 0,05 % de O et au plus 0,05 % de N, et au moins un élément choisi dans le groupe constitué de, au plus 0,5 % de Ti, au plus 0,5 % de Zr, au plus 0,5 % de Hf, au plus 0,5 % de V et au plus 0,5 % de Nb, le reste étant constitué de Fe et d'impuretés, l'acier présentant une structure comprenant, en pourcentage en volume, de 10 % à 60 % de phase ferritique et de 2 % à 10 % de phase d'austénite résiduelle et présentant une limite d'élasticité d'au moins 654 MPa.
  2. Acier inoxydable selon la revendication 1, comprenant en outre, au moins un élément choisi dans le groupe constitué de 0,005 % à 0,5 % de Ti, de 0,005 % à 0,5 % de Zr, de 0,005 % à 0,5 % de Hf, de 0,005 % à 0,5 % de V et de 0,005 % à 0,5 % de Nb.
EP09726339.6A 2008-03-28 2009-03-19 Acier inoxydable destiné à être utilisé dans un tuyau de puits de pétrole Active EP2256225B1 (fr)

Applications Claiming Priority (2)

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JP2008087643 2008-03-28
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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EP2256225A4 EP2256225A4 (fr) 2017-01-04
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Publication number Publication date
AU2009230545A1 (en) 2009-10-01
EP2256225A1 (fr) 2010-12-01
BRPI0909042A2 (pt) 2016-06-07
JPWO2009119048A1 (ja) 2011-07-21
RU2449046C1 (ru) 2012-04-27
JP4577457B2 (ja) 2010-11-10
CN101981215A (zh) 2011-02-23
ES2674255T3 (es) 2018-06-28
EP2256225A4 (fr) 2017-01-04
MX2010010435A (es) 2010-11-05
AR070745A1 (es) 2010-05-05
WO2009119048A1 (fr) 2009-10-01
BRPI0909042B1 (pt) 2020-03-24
CA2717104A1 (fr) 2009-10-01
CA2717104C (fr) 2014-01-07
AU2009230545B2 (en) 2011-12-15
US20110014083A1 (en) 2011-01-20
BRPI0909042B8 (pt) 2020-05-05

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