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
  • 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
  • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
  • C21D1/22—Martempering
• • 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
  • 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
  • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
• • 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
  • 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
  • C21D9/085—Cooling or quenching
• • 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
  • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/44—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
  • 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
  • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
• • 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
  • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
• • 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
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/008—Martensite

Definitions

• the present invention relates to a martensitic stainless steel seamless steel pipe for oil well used for oil wells and gas wells of crude oil or natural gas (hereinafter simply referred to as oil wells) and a method for producing the same.
• the present invention relates to a seamless steel pipe for oil well pipe excellent in sulfide stress corrosion cracking resistance (SSC resistance) in an environment containing hydrogen sulfide (H 2 S) with a yield stress YS of 758 MPa or more, and a manufacturing method thereof.
• SSC resistance sulfide stress corrosion cracking resistance
• Patent Document 1 describes a component system 13% Cr-based martensitic stainless steel pipe containing a very low C amount of 0.015% or less and Ti of 0.03% or more, and has a high strength of yield stress 95 ksi class, It has low hardness of less than 27 in HRC, and has excellent SSC resistance.
• Patent Document 2 describes a martensitic stainless steel satisfying 6.0 ⁇ Ti / C ⁇ 10.1 because Ti / C has a correlation with a value obtained by subtracting a yield stress from a tensile stress. According to the described technology, the value obtained by subtracting the yield stress from the tensile stress is 20.7 MPa or more, and it is possible to suppress the variation in hardness which lowers the SSC resistance.
• the amount of Mo in the steel is defined as Mo0.82.3 ⁇ 0.89 Si + 32.2 C, and the metal structure is mainly tempered martensite, carbide precipitated during tempering, and Laves precipitated finely during tempering.
• a martensitic stainless steel composed of intermetallic compounds such as phase and ⁇ phase is described. According to the described technology, it is said that the 0.2% proof stress of the steel becomes high strength of 860 MPa or more, and can have excellent carbon dioxide gas corrosion resistance and sulfide stress corrosion cracking resistance.
• Patent Document 1 states that resistance to sulfide stress cracking can be maintained under a condition of applying a stress of 655 MPa in an atmosphere adjusted to a pH of 3.5 with a 5% NaCl aqueous solution (H 2 S: 0.10 bar). .
• H 2 S: 0.10 bar a 5% NaCl aqueous solution
• Patent Document 2 25% NaCl aqueous solution (H 2 S: 0.03) is used in the atmosphere in which 20% NaCl aqueous solution (H 2 S: 0.03 bar, CO 2 bal.) Is adjusted to pH: 4.5.
• the steel is considered to have resistance to sulfide stress cracking under an atmosphere adjusted to pH: 4.0 bar, CO 2 bal).
• sulfide stress corrosion cracking resistance under an atmosphere other than the above has not been studied, and it can not be said to have sulfide stress corrosion cracking resistance that can withstand the current severe corrosion environment.
• An object of the present invention is to provide a martensitic stainless steel seamless steel pipe for oil well pipes having a yield stress of 758 MPa (110 ksi) or more and having excellent sulfide stress corrosion cracking resistance and a method for producing the same. .
• excellent resistance to sulfide stress corrosion cracking refers to a test solution: 0.165 mass% NaCl aqueous solution (liquid temperature: 25 ° C., H 2 S: 1 bar, CO 2 bal), Na acetate acetic acid + hydrochloric acid Add 0.82 g / L acetic acid Na + acetic acid to an aqueous solution adjusted to pH: 3.5 and to a test solution: 20 mass% aqueous NaCl solution (liquid temperature: 25 ° C, H 2 S: 0.1 bar, CO 2 bal)
• the test piece is immersed in an aqueous solution adjusted to pH 5.0, the immersion time is 720 hours, 90% of the yield stress is applied as a load stress, and the test is conducted, and no crack occurs in the test piece after the test. Shall be said.
• the present inventors have resistance to sulfide stress corrosion cracking in a corrosive environment containing 13% Cr-based stainless steel pipe as a basic composition, CO 2 , Cl ⁇ and H 2 S.
• the effects of various alloying elements on SSC resistance) were studied intensively.
• each component is contained in a predetermined range, and C, Mn, Cr, Cu, Ni, Mo, W, Nb, N, and Ti are adjusted and contained so as to satisfy an appropriate relational expression and range.
• the appropriate hardening and tempering treatment the stress near the yield stress is applied under the corrosive atmosphere having the desired strength and containing CO 2 , Cl ⁇ , and H 2 S. It has been found that the martensitic stainless steel seamless steel pipe for oil well pipes having excellent SSC resistance can be obtained under
• the present invention has been completed based on the above-mentioned findings, with further studies. That is, the gist of the present invention is as follows. [1] mass%, C: 0.010% or more, Si: 0.5% or less, Mn: 0.05 to 0.24%, P: 0.030% or less, S: 0.005% or less, Ni: 4.6 to 8.0%, Cr: 10.0 to 14.0%, Mo: 1.0 to 2.7%, Al: 0.1% or less, V: 0.005 to 0.2%, N: 0.1% or less Ti: 0.06 to 0.25%, Cu: 0.01 to 1.0%, Co: 0.01 to 1.0%
• Nb not more than 0.1% in mass%
• W The martensitic stainless steel seamless steel pipe for oil well tubes according to [1], which has a composition containing one or two or more selected from 1.0% or less.
• Ca 0.010% or less
• REM 0.010% or less
• Mg 0.010% or less
• B A martensitic stainless steel seamless steel pipe for oil well tubes according to [1] or [2], which has a composition containing one or more selected from 0.010% or less.
• the present invention has excellent sulfide stress corrosion cracking resistance (SSC resistance) in a corrosive environment containing CO 2 , Cl ⁇ and further H 2 S, and yield stress YS: 758 MPa (110 ksi)
• SSC resistance sulfide stress corrosion cracking resistance
• composition limitation reason of the steel pipe of the present invention will be described.
• mass% is simply described as% unless otherwise specified.
• C 0.010% or more C is an important element related to the strength of martensitic stainless steel, and is effective for improving the strength. In the present invention, C is limited to 0.010% or more in order to secure a desired strength. On the other hand, by containing excessively, hardness will become high and sulfide stress corrosion cracking sensitivity will increase. For this reason, it is desirable to contain 0.040% or less. Therefore, it is preferably 0.010% to 0.040%.
• Si 0.5% or less Since Si acts as a deoxidizer, it is desirable to contain 0.05% or more. On the other hand, the content exceeding 0.5% reduces carbon dioxide corrosion resistance and hot workability. For this reason, Si was limited to 0.5% or less. Preferably, it is 0.10 to 0.30% from the viewpoint of securing stable strength.
• Mn 0.05 to 0.24%
• Mn is an element that improves the hot workability and strength, and in order to secure the required strength, it is desirable to contain 0.05% or more.
• Mn is limited to 0.05 to 0.24%.
• P 0.030% or less
• P is an element that reduces both carbon dioxide gas corrosion resistance, pitting corrosion resistance, and sulfide stress corrosion cracking resistance, and in the present invention, it is desirable to reduce as much as possible.
• extreme reductions increase manufacturing costs. Therefore, P was limited to 0.030% or less as an industrially inexpensively practicable range within a range that does not cause an extreme decrease in the characteristics. In addition, Preferably it is 0.015% or less.
• S 0.005% or less Since S is an element that significantly reduces the hot workability, it is desirable to reduce it as much as possible. By reducing the amount to 0.005% or less, it is possible to manufacture a pipe in a normal process, so S in the present invention is limited to 0.005% or less. In addition, Preferably it is 0.002% or less.
• Ni 4.6 to 8.0%
• Ni is an element which strengthens the protective film to improve the corrosion resistance and further increases the strength of the steel by solid solution. In order to obtain such an effect, the content needs to be 4.6% or more. On the other hand, when the content exceeds 8.0%, the stability of the martensitic phase decreases and the strength decreases. Therefore, Ni was limited to 4.6 to 8.0%.
• Cr 10.0 to 14.0% Cr is an element which forms a protective film and improves corrosion resistance, and by containing 10.0% or more, the corrosion resistance necessary for oil well pipes can be secured. On the other hand, if the content exceeds 14.0%, the formation of ferrite becomes easy, so that the martensite phase can not be stably ensured. Therefore, Cr is limited to 10.0 to 14.0%. Preferably, it is 11.0 to 13.5%.
• Mo 1.0 to 2.7% Mo is an element that improves the resistance to pitting corrosion by Cl ⁇ , and needs to be 1.0% or more in order to obtain the corrosion resistance necessary for a severe corrosive environment.
• Mo is an expensive element, the content exceeding 2.7% causes a rise in manufacturing cost. Therefore, Mo was limited to 1.0 to 2.7%. Preferably, it is 1.5 to 2.5%.
• Al 0.1% or less Since Al acts as a deoxidizer, in order to obtain such an effect, it is necessary to contain 0.01% or more. However, since the content exceeding 0.1% adversely affects the toughness, Al in the present invention is limited to 0.1% or less. Preferably, it is 0.01 to 0.03%.
• V 0.005 to 0.2%
• V is required to be contained at 0.005% or more in order to improve the strength of the steel by precipitation strengthening and further improve the resistance to sulfide stress corrosion cracking.
• the V content in the present invention is limited to 0.005 to 0.2%, since the toughness is lowered when the content exceeds 0.2%.
• N 0.1% or less N improves the pitting resistance and has an effect of dissolving in steel and increasing the strength. However, if the content is more than 0.1%, many various nitride-based inclusions are generated, and the pitting resistance is lowered. Therefore, N in the present invention is limited to 0.1% or less. In addition, Preferably it is 0.010% or less.
• Ti 0.06 to 0.25%
• Ti can form carbides, reduce solid solution carbon, and reduce hardness.
• the content exceeds 0.25%, TiN is generated as inclusions to be a starting point of pitting corrosion, and the sulfide stress corrosion cracking resistance is deteriorated. Therefore, Ti was limited to 0.06 to 0.25%.
• the content is 0.08 to 0.15%.
• Cu 0.01 to 1.0%
• Cu is contained 0.01% or more in order to strengthen a protective film and to improve sulfide stress corrosion cracking resistance. However, if the content exceeds 1.0%, CuS precipitates to reduce the hot workability. Therefore, Cu was limited to 0.01 to 1.0%.
• Co 0.01 to 1.0%
• Co is an element that reduces the hardness and improves the pitting resistance by raising the Ms point and promoting the ⁇ transformation. In order to acquire such an effect, 0.01% or more needs to be contained. On the other hand, excessive content may lower the toughness and further increase the material cost. Therefore, Co in the present invention is limited to 0.01 to 1.0%. More preferably, it is 0.03 to 0.6%.
• the following value (1), value (2) and value (3) Each element is contained to be satisfied.
• the value (1) is an equation correlating to the amount of residual ⁇ , and by reducing the value of the value (1), retained austenite is reduced, the hardness is reduced, and the sulfide stress corrosion cracking resistance is improved.
• the value (2) is an equation correlating to the re-passivation potential, and C, Mn, Cr, Cu, Ni, Mo, W, Nb so that the value (1) satisfies the range of the equation (4).
• the value (3) is an equation correlating to the pitting potential, and C, Mn, Cr, Cu, Ni, Mo, W, Nb, and so that the value (1) satisfies the range of the equation (4).
• Nb can reduce solid solution carbon and reduce hardness by forming carbides.
• excessive content may lower toughness.
• W is an element improving the pitting resistance, but an excessive content may lower the toughness and further increase the material cost. Therefore, in the case of containing Nb: 0.1% or less, W: 1.0% or less.
• Ca 0.010% or less
• REM 0.010% or less
• Mg 0.010% or less
• B One or more selected from 0.010% or less can be contained.
• Ca, REM, Mg and B are all elements which improve corrosion resistance through shape control of inclusions. To get this effect, Ca: 0.0005% or more, REM: 0.0005% or more, Mg: 0.0005% or more, B: It is desirable to contain 0.0005% or more. on the other hand, Ca: 0.010%, REM: 0.010%, Mg: 0.010%, B: 0.010% If the content is more than the above, the toughness and the carbon dioxide corrosion resistance decrease. Therefore, when it contains, Ca: 0.010% or less, REM: 0.010% or less, Mg: 0.010% or less, B: Limited to 0.010% or less.
• the balance other than the above-mentioned component composition consists of Fe and unavoidable impurities.
• a steel pipe material having the above composition is used, but the method of manufacturing a stainless steel seamless steel pipe, which is a steel pipe material, is not particularly limited, and any known method of manufacturing a seamless pipe can be applied.
• the molten steel of the above composition is melted by a melting method such as a converter and made into a steel pipe material such as billet by a method such as continuous casting or ingot-slab rolling. Subsequently, these steel tube materials are heated, hot worked and piped in a pipe forming process of Mannesman-plug mill method or Mannesman-mandrel mill method which is a known pipe forming method, and a joint having the above composition No steel pipe.
• the treatment after forming the steel pipe material into the steel pipe is not particularly limited, but preferably, the steel pipe is heated to a temperature above the Ac 3 transformation point and then quenched to a cooling stop temperature of 100 ° C. or less And a tempering treatment which tempers at a temperature below the Ac 1 transformation point.
• the steel pipe is further reheated to a temperature above the Ac 3 transformation point, preferably held for 5 minutes or more, and then subjected to quenching treatment for cooling to a cooling stop temperature of 100 ° C. or less.
• a cooling stop temperature 100 ° C. or less.
• cooling is performed by air cooling (cooling rate 0.05 ° C./s or more and 20 ° C./s or less) or water cooling (cooling rate 5 ° C./s or more and 100 ° C./s or less). It is not limited.
• tempering treatment is applied to the steel pipe subjected to the quenching treatment.
• the tempering treatment is a treatment in which the steel pipe is heated to a temperature below the Ac 1 transformation point, preferably held for 10 minutes or more, and air-cooled.
• the tempering temperature becomes higher than the Ac 1 transformation point, a martensitic phase precipitates after tempering, and desired high toughness and excellent corrosion resistance can not be secured. Therefore, the tempering temperature is limited to the Ac 1 transformation point or less.
• the above-mentioned Ac 3 transformation point (° C.) and Ac 1 transformation point (° C.) give a temperature history of heating and cooling to the test piece and detect the transformation point from minute displacement of expansion and contraction by the Fourmaster test It can be measured.
• this billet After melting the molten steel of the component shown in Table 1 with a converter, it casts into a billet (steel pipe material) by a continuous casting method. Further, this billet was formed by hot working using a model seamless rolling mill and then cooled by air cooling or water cooling to obtain a seamless steel pipe having an outer diameter of 83.8 mm and a thickness of 12.7 mm.
• test material was cut out from the obtained seamless steel pipe, and the test material was subjected to quenching and tempering treatment under the conditions shown in Table 2. After a test piece for observation of structure was collected from a test material subjected to quenching and tempering treatment and polished, the amount of retained austenite ( ⁇ ) was measured by X-ray diffraction method.
• API arc-shaped tensile test specimens are collected from the test material subjected to quenching and tempering treatment, and a tensile test is performed according to the specification of API to determine tensile properties (yield stress YS, tensile stress TS).
• yield stress YS yield stress YS
• tensile stress TS tensile stress TS.
• the In Table 2 for Ac 3 point (° C.) and Ac 1 point (° C.), test pieces of 4 mm ⁇ ⁇ 10 mm were collected from the test material subjected to quenching treatment and measured by Fourmaster test. Specifically, the test piece was heated to 500 ° C. at 5 ° C./s, further heated to 920 ° C. at 0.25 ° C./s, held for 10 minutes, and then cooled to room temperature at 2 ° C./s. Ac 3 point (° C.) and Ac 1 point (° C.) were obtained by detecting the expansion and contraction of the test piece accompanying the temperature history
• the SSC test was performed according to NACE TM0177 Method A.
• the test environment is an aqueous solution prepared by adding Na acetate / acetic acid to a test environment 1: 0.165 mass% NaCl aqueous solution (liquid temperature: 25 ° C., H 2 S: 1 bar, CO 2 bal) to adjust pH to 3.5, and a test environment 2 : Using an aqueous solution adjusted to pH: 5.0 by adding 0.82 g / L acetic acid Na + acetic acid to 20 mass% NaCl aqueous solution (liquid temperature: 25 ° C., H 2 S: 0.1 bar, CO 2 bal), soaking time 720 The test was carried out with 90% of the yield stress as the applied stress. The case where a crack did not generate
• the martensitic stainless steel seamless steel pipe having excellent SSC resistance all of which have high strength of yield stress of 758 MPa or more and no generation of cracking even when stressed in an environment containing H 2 S according to the present invention. It has become.
• the comparative example out of the range of the present invention although the desired high strength is obtained, the excellent SSC resistance can not be secured.

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• 2018
  • 2018-09-04 JP JP2018564431A patent/JP6540920B1/ja active Active
  • 2018-09-04 BR BR112020004808-9A patent/BR112020004808B1/pt active IP Right Grant
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