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
  • 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
  • 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
  • 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
  • C22C38/02—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
  • 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 an oil country tubular goods martensitic stainless steel pipe used for oil or gas wells (hereinafter simply referred to as oil wells) and a method for producing the same.
• oil wells oil country tubular goods martensitic stainless steel pipe used for oil or gas wells
• CO 2 chloride ion
• Cl ⁇ chloride ion
• SSC resistance sulfide stress corrosion cracking resistance
• 13% Cr martensitic stainless steel pipes are often used as oil country tubular goods for mining in oil fields and gas fields that contain carbon dioxide and chlorine ions. Recently, development of oil fields, etc. in extremely severe corrosive environments containing hydrogen sulfide has been carried out on a global scale, so the demand for SSC resistance is increasing, and components that have reduced C and increased Ni and Mo The use of improved 13% Cr martensitic stainless steel pipes is also expanding.
• 13% Cr-based steel is used as the basic composition, C is remarkably reduced as compared with the prior art, Ni, Mo and Cu are further included, Cr + 2Ni + 1.1Mo + 0.7Cu ⁇ 32.5 is satisfied, and Nb is further added.
• V 0.20% or less
• yield strength high strength of 965 MPa or more
• ⁇ It is said that it has high toughness with Charpy absorbed energy at 40 ° C of 50J or more, and can secure good corrosion resistance.
• Patent Document 2 describes a 13% Cr martensitic stainless steel pipe containing 0.01% or less of an extremely low C content and 0.03% or more of Ti, and has a yield stress of 95 ksi class (655 to 758 MPa). It has both high strength and low hardness of Rockwell hardness HRC of less than 27, and is said to have excellent SSC resistance.
• Patent Document 3 describes martensitic stainless steel in which Ti / C having a correlation with a value obtained by subtracting yield stress from tensile stress satisfies 6.0 ⁇ Ti / C ⁇ 10.1. According to the described technique, the value obtained by subtracting the yield stress from the tensile stress is 20.7 MPa or more, and it is possible to suppress variation in hardness that reduces the SSC resistance.
• the amount of Mo in steel is defined by Mo ⁇ 2.3 ⁇ 0.89Si + 32.2C, and the metal structure is mainly tempered martensite, carbides precipitated during tempering, and Laves phase precipitated finely during tempering. And martensitic stainless steel composed of intermetallic compounds such as ⁇ phase and the like. According to the described technology, 0.2% proof stress can achieve high strength of 860MPa or more, and it has excellent carbon-dioxide-corrosion-resistance and sulfide stress corrosion cracking resistance. .
• Patent Document 2 the resistance to sulfide stress corrosion cracking can be maintained under the condition that a stress of 655 MPa is applied in an atmosphere in which a 5% NaCl aqueous solution (H 2 S: 0.10 bar) is adjusted to pH 3.5.
• Patent Document 3 it is said that it has resistance to sulfide stress corrosion cracking in an atmosphere in which a 20% NaCl aqueous solution (H 2 S: 0.03 atm, CO 2 bal.) Is adjusted to pH: 4.5.
• Patent Document 4 it is said that it has sulfide stress corrosion cracking resistance in an atmosphere in which a 25% NaCl aqueous solution (H 2 S: 0.003 MPa, CO 2 bal.) Is adjusted to pH: 4.0.
• a 25% NaCl aqueous solution H 2 S: 0.003 MPa, CO 2 bal.
• the resistance to sulfide stress corrosion cracking in atmospheres other than those described above has not been studied, and it is difficult to say that it has the resistance to sulfide stress corrosion cracking that can withstand the more severe corrosion environments of recent years.
• An object of the present invention is to provide a martensitic stainless steel seamless pipe for oil well pipes having high strength and excellent sulfide stress corrosion cracking resistance, and a method for producing the same.
• “high strength” is assumed to be a yield stress of 758 MPa (110 ksi) or more.
• the yield stress is 896 MPa or less.
• “excellent sulfide stress corrosion cracking resistance” as used herein refers to test solution: 0.165% by mass NaCl aqueous solution (liquid temperature: 25 ° C., H 2 S: 1 bar, CO 2 bal), Na acetate and hydrochloric acid.
• test piece is immersed in an aqueous solution adjusted to pH: 3.5, the immersion time is set to 720 hours, 90% of the yield stress is applied as the load stress, and the test piece is cracked after the test. The case where it does not do shall be said.
• the inventors of the present invention have a 13% Cr stainless steel pipe as a basic composition, and are resistant to sulfide stress corrosion cracking in a corrosive environment containing CO 2 , Cl ⁇ and H 2 S ( The effect of various alloying elements on SSC resistance was studied. As a result, proper quenching and tempering with a composition containing C, Mn, Cr, Cu, Ni, Mo, W, Nb, N, and Ti adjusted to satisfy the appropriate relational expression and range. An oil well having excellent SSC resistance in a corrosive atmosphere containing CO 2 , Cl ⁇ , and H 2 S, and in an environment where stress near the yield stress is applied by applying the treatment. It has been found that a martensitic stainless steel seamless pipe for pipes can be obtained.
• the present invention has been completed by further studies based on the above findings. That is, the gist of the present invention is as follows. [1] By mass%, C: 0.035% or less, Si: 0.5% or less, Mn: 0.05 to 0.5%, P: 0.03% or less, S: 0.005% or less, Cu: 2.6% or less, Ni: 5.3 to 7.3% , Cr: 11.8 to 14.5%, Al: 0.1% or less, Mo: 1.8 to 3.0%, V: 0.2% or less, N: 0.1% or less, and the following formulas (1), (2) and (3 ) Formula satisfies the following (4), has a composition consisting of the balance Fe and inevitable impurities, A martensitic stainless steel seamless pipe for oil well pipes characterized by having a yield stress of 758 MPa or more.
• SSC resistance sulfide stress corrosion cracking resistance
• the stainless steel seamless pipe of the present invention is in mass%, C: 0.035% or less, Si: 0.5% or less, Mn: 0.05 to 0.5%, P: 0.03% or less, S: 0.005% or less, Cu: 2.6% or less, Ni: 5.3-7.3%, Cr: 11.8-14.5%, Al: 0.1% or less, Mo: 1.8-3.0%, V: 0.2% or less, N: 0.1% or less, and the following formula (1), ( 2) and 3) satisfy the following (4), (5) or (6), have a composition consisting of the remaining Fe and inevitable impurities, and have a yield stress of 758 MPa or more.
• Stainless steel seamless steel pipe satisfy the following (4), (5) or (6), have a composition consisting of the remaining Fe and inevitable impurities, and have a yield stress of 758 MPa or more.
• C 0.035% or less C is an important element related to the strength of martensitic stainless steel and is effective in improving the strength. However, if the content exceeds 0.035%, the hardness becomes too high, so that the sensitivity to sulfide stress corrosion cracking increases. For this reason, in the present invention, the C content is limited to 0.035% or less. Preferably, the C content is 0.015% or less. More preferably, the C content is 0.0090% or less. More preferably, the content is 0.0075% or less. On the other hand, in order to ensure a desired strength, the C content is desirably 0.005% or more.
• Si 0.5% or less Since Si acts as a deoxidizer, it is desirable to contain 0.05% or more of Si. On the other hand, the Si content exceeding 0.5% reduces the carbon dioxide gas corrosion resistance and hot workability. For this reason, Si content is limited to 0.5% or less.
• the lower limit of the Si content is preferably 0.10% or more, and the upper limit is preferably 0.30% or less.
• Mn 0.05-0.5%
• Mn is an element that improves hot workability and contains 0.05% or more of Mn.
• the Mn content is limited to 0.05 to 0.5%. Preferably, it is 0.40% or less.
• P 0.03% or less
• P is an element that lowers the carbon dioxide corrosion resistance, pitting corrosion resistance, and sulfide stress corrosion cracking resistance, and is desirably reduced as much as possible in the present invention.
• extreme reduction increases manufacturing costs. Therefore, the P content is limited to 0.03% or less as a range that does not cause an extreme deterioration of the characteristics and can be industrially inexpensively implemented.
• the P content is 0.02% or less.
• S 0.005% or less Since S is an element that significantly reduces hot workability, it is desirable to reduce it as much as possible. By reducing the S content to 0.005% or less, pipe production in a normal process becomes possible, so the S content in the present invention is limited to 0.005% or less. Preferably, the S content is 0.003% or less.
• Cu 2.6% or less Cu enhances the resistance to sulfide stress corrosion cracking by strengthening the protective coating. However, if Cu content exceeds 2.6%, CuS is precipitated and hot workability is lowered. Therefore, the Cu content is limited to 2.6% or less.
• the lower limit of the Cu content is preferably 0.5% or more, and the upper limit is preferably 2.0% or less.
• Ni 5.3-7.3%
• Ni is contained in an amount of 5.3% or more to strengthen the protective film and improve the corrosion resistance, and further increase the strength of the steel by solid solution.
• the Ni content exceeds 7.3%, the stability of the martensite phase decreases and the strength decreases. Therefore, the Ni content is limited to 5.3-7.3%. Preferably, it is 5.7% or more, more preferably 6.0% or more.
• Cr 11.8 to 14.5% Cr is an element that improves the corrosion resistance by forming a protective film, and the content of 11.8% or more of Cr can ensure the necessary corrosion resistance for oil well pipes. On the other hand, if the Cr content exceeds 14.5%, the formation of ferrite becomes easy, and it becomes impossible to ensure the stability of the martensite phase. Therefore, the Cr content is limited to 11.8 to 14.5%.
• the lower limit of the Cr content is preferably 12.0% or more, and the upper limit is preferably 13.5% or less.
• Al 0.1% or less Since Al acts as a deoxidizer, it is effective to contain 0.01% or more of Al in order to obtain such an effect. However, since Al content exceeding 0.1% adversely affects toughness, the Al content in the present invention is limited to 0.1% or less. Preferably, the Al content is 0.01 to 0.03%.
• Mo 1.8-3.0%
• Mo is Cl - is an element which improves the resistance to pitting, in order to obtain the corrosion resistance necessary for severe corrosive environment, it is necessary to contain 1.8% or more of Mo.
• Mo is an expensive element, which causes an increase in manufacturing cost. Therefore, the Mo content is limited to 1.8 to 3.0%.
• the lower limit of the Mo content is preferably 2.4% or more, and the upper limit is preferably 2.9% or less.
• V 0.2% or less
• V is preferably contained in an amount of 0.01% or more because V improves the strength of the steel by precipitation strengthening and further improves the resistance to sulfide stress corrosion cracking.
• the V content in the present invention is limited to 0.2% or less.
• the lower limit of the V content is preferably 0.01% or more, and preferably the upper limit is 0.08% or less.
• N 0.1% or less
• N is an element that remarkably improves pitting corrosion resistance.
• various nitrides are formed to reduce toughness, so the N content in the present invention is limited to 0.1% or less.
• the N content is 0.003% or more.
• the lower limit of the N content is more preferably 0.004% or more, and further preferably 0.005% or more.
• the upper limit is more preferably 0.08% or less, still more preferably 0.05% or less.
• the present invention further contains C, Mn, Cr, Cu, Ni, Mo, W, Nb, N, and Ti within the above range, and the following formulas (1), (2), and (3 ) Each element is contained so that the following formula (4) or (5) or (6) is satisfied.
• Equation (1) correlates with the amount of residual ⁇ . By reducing the value calculated by equation (1), residual austenite is reduced, hardness is reduced, and resistance to sulfide stress corrosion cracking is reduced. improves.
• Equation (2) is an equation that correlates with the repassivation potential, and the values calculated in Equation (1) are C, Mn so that the range of (4), (5), or (6) is satisfied.
• equation (3) is an equation that correlates with the pitting potential, and the value calculated by equation (3) is C, Mn, so as to satisfy the range of (4) or (5) or (6).
• the value calculated by the formula (1) satisfies the range of (4)
• the value calculated by the formula (1) leads to an increase in hardness at 10 or more, but was calculated by the formula (2).
• the value and the value calculated by the expression (3) satisfy the range of (4), regeneration of the passive film and suppression of pitting corrosion appear remarkably, and resistance to sulfide stress corrosion cracking is improved.
• the value calculated by the expression (1) in the following (4) is 5 or more and 45 or less
• the value calculated by the expression (1) in the following (5) is -5 or more and 5 or less.
• the balance other than the above components is composed of Fe and inevitable impurities.
• Ti and Nb can reduce the solid solution carbon and reduce the hardness by forming carbides. On the other hand, since excessive inclusion may reduce toughness, when Ti and / or Nb is contained, Ti is limited to 0.19% or less, and Nb is limited to 0.25% or less.
• W and Co are both elements that improve pitting corrosion resistance. However, excessive inclusion may reduce toughness and further increase the material cost. Therefore, when W and / or Co is contained, W is limited to 1.1% or less, and Co is limited to 0.45% or less.
• the preferable manufacturing method of the martensitic stainless steel seamless pipe for oil country tubular goods of this invention is demonstrated.
• a steel pipe material having the above composition is used.
• the manufacturing method of the stainless steel seamless steel pipe which is a steel pipe raw material does not need to be specifically limited, All the manufacturing methods of a well-known seamless steel pipe are applicable.
• the molten steel having the above composition is preferably melted by a melting method such as a converter and used as a steel pipe material such as a billet by a continuous casting method, an ingot-bundling rolling method, or the like.
• the processing after forming the steel pipe material into a steel pipe is not particularly limited.
• the steel pipe is heated to the Ac 3 transformation point or higher, followed by quenching to air-cool at a cooling rate of 0.1 ° C./s to a cooling stop temperature of 100 ° C. or lower, and then tempered at a temperature below the Ac 1 transformation point. And tempering.
• the steel pipe is further reheated to a temperature above the Ac 3 transformation point, preferably kept for 5 min or more, and then subjected to a quenching treatment for air cooling to a cooling stop temperature of 100 ° C. or less.
• a quenching treatment for air cooling to a cooling stop temperature of 100 ° C. or less.
• the quenching heating temperature is less than the Ac 3 transformation point, heating cannot be performed in the austenite single phase region, and thus sufficient martensite structure cannot be obtained by subsequent cooling, and a desired high strength cannot be achieved. Therefore, the quenching heating temperature is limited to the Ac 3 transformation point or higher.
• said air cooling refers to the cooling rate of 0.1 degree-C / s or more.
• the tempering process is a process of heating below the Ac 1 transformation point, preferably holding for 10 min or more, and air cooling.
• the tempering temperature is higher than the Ac 1 transformation point, the martensite phase precipitates after tempering, and the desired high toughness and excellent corrosion resistance cannot be ensured. Therefore, the tempering temperature is limited to the Ac 1 transformation point or lower.
• a four-master test that gives a temperature history of heating and cooling to the test piece and detects the transformation point from minute displacements of expansion and contraction. Can be measured.
• molten steel having the components shown in Table 1 is melted in a converter, it is cast into a billet (steel pipe material) by a continuous casting method, further piped by hot working using a model seamless rolling mill, and air-cooled (cooling rate 0.5) C./s) After that, a seamless steel pipe having an outer diameter of 83.8 mm and a wall thickness of 12.7 mm was obtained.
• a test material was cut out from the obtained seamless steel pipe and subjected to quenching and tempering treatment under the conditions shown in Table 2.
• a specimen for microstructure observation was collected from the test material subjected to quenching and tempering treatment, polished, and then the amount of retained austenite ( ⁇ ) was measured by an X-ray diffraction method.
• I ⁇ ⁇ integral strength
• I ⁇ ⁇ integral strength
• R ⁇ ⁇ crystallographic theoretical calculated value
• API specimen specimens by API standard 5CT are collected from specimens that have been quenched and tempered, and subjected to a tensile test in accordance with the API regulations to obtain tensile properties (yield stress YS). , Tensile stress TS).
• yield stress YS yield stress
• Tensile stress TS Tensile stress TS
• Table 2 for Ac 3 point (° C.) and Ac 1 point (° C.), a test piece of 4 mm ⁇ ⁇ 10 mm was taken from the test material subjected to quenching treatment and measured by a formaster test. Specifically, the test piece was heated to 500 ° C. at 5 ° C./s, further heated to 920 ° C. at 0.25 ° C./s and held for 10 minutes, and then cooled to room temperature at 2 ° C./s. The Ac 3 point (° C.) and Ac 1 point (° C.) were obtained by detecting the expansion and contraction of the test piece accompanying this temperature history.
• the SSC test was performed according to NACE TM0177 Method A.
• the test environment is 0.165% NaCl by adding 0.41 g / L CH 3 COONa + HCl to pH 3.5 and the hydrogen sulfide partial pressure is 0.1 MPa, and 90% of the yield stress is loaded. The test was carried out as stress.
• All of the examples of the present invention have a high strength of yield stress of 758 MPa or more and martensite stainless steel seamless steel pipe having excellent SSC resistance without cracking even when stress is applied in an environment containing H 2 S. It has become.
• the desired high strength is obtained, but excellent SSC resistance cannot be ensured.

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