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
• • 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
• • 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
  • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/10—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
  • 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
  • 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
  • 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
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • 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
  • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
• • 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
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
• • 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
  • C21D2211/001—Austenite
• • 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
  • C21D2211/005—Ferrite
• • 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 disclosure relates to a stainless steel seamless pipe suitable for use in oil wells and gas wells (hereafter simply referred to as oil wells).
• the present disclosure especially relates to a stainless steel seamless pipe with improved corrosion resistance in high-temperature severe corrosion environments containing carbon dioxide (CO 2 ) and chloride ions (Cl ⁇ ), environments containing hydrogen sulfide (H 2 S), and the like.
• Stainless steel seamless pipes are widely used for applications such as steel pipes for oil wells.
• Steel pipes for oil wells are required to have not only excellent yield stress but also excellent low-temperature toughness in view of recent oil field development in cold regions.
• 13Cr martensitic stainless steel pipes are commonly used as steel pipes for oil wells for mining in oil and gas fields in environments containing CO 2 , Cl ⁇ , etc. Recently, however, the development of oil wells of higher temperatures (up to 200° C.) is underway, and 13Cr martensitic stainless steel pipes sometimes lack corrosion resistance. There is thus a demand for a steel pipe for oil wells with higher corrosion resistance, which can be used even in such environments.
• WO 2013/146046 A1 proposes a stainless steel for oil wells having a composition containing, in mass %, C: 0.05% or less, Si: 1.0% or less, Mn: 0.01% to 1.0%, P: 0.05% or less, S: less than 0.002%, Cr: 16% to 18%, Mo: 1.8% to 3%, Cu: 1.0% to 3.5%, Ni: 3.0% to 5.5%, Co: 0.01% to 1.0%, Al: 0.001% to 0.1%, O: 0.05% or less, and N: 0.05% or less where Cr, Ni, Mo, and Cu satisfy a specific relationship.
• WO 2017/168874 A1 proposes a high-strength stainless steel seamless pipe for oil wells having a composition containing, in mass %, C: 0.005% to 0.05%, Si: 0.05% to 0.50%, Mn: 0.20% to 1.80%, P: 0.030% or less, S: 0.005% or less, Cr: 12.0% to 17.0%, Ni: 4.0% to 7.0%, Mo: 0.5% to 3.0%, Al: 0.005% to 0.10%, V: 0.005% to 0.20%, Co: 0.01% to 1.0%, N: 0.005% to 0.15%, and O: 0.010% or less where Cr, Ni, Mo, Cu, C, Si, Mn, and N satisfy a specific relationship.
• WO 2018/155041 A1 proposes a high-strength stainless steel seamless pipe for oil wells having: a composition containing, in mass %, C: 0.05% or less, Si: 0.5% or less, Mn: 0.15% to 1.0%, P: 0.030% or less, S: 0.005% or less, Cr: 14.5% to 17.5%, Ni: 3.0% to 6.0%, Mo: 2.7% to 5.0%, Cu: 0.3% to 4.0%, W: 0.1% to 2.5%, V: 0.02% to 0.20%, Al: 0.10% or less, N: 0.15% or less, and B: 0.0005% to 0.0100% where C, Si, Mn, Cr, Ni, Mo, Cu, N, and W satisfies a specific relationship; and a microstructure containing, in volume fraction, more than 45% martensite phase as a primary phase, 10% to 45% ferrite phase as a secondary phase, and 30% or less retained austenite phase.
• such a high-strength stainless steel seamless pipe for oil wells has a strength of 862 MPa or more in yield stress YS, and exhibits sufficient corrosion resistance even in high-temperature severe corrosion environments containing CO 2 , Cl ⁇ , and H 2 S.
• WO 2021/065263 A1 proposes a high-strength stainless steel seamless pipe for oil wells having: a composition containing, in mass %, C: 0.06% or less, Si: 1.0% or less, P: 0.05% or less, S: 0.005% or less, Cr: more than 15.7% and 18.0% or less, Mo: 1.8% or more and 3.5% or less, Cu: 1.5% or more and 3.5% or less, Ni: 2.5% or more and 6.0% or less, Al: 0.10% or less, N: 0.10% or less, O: 0.010% or less, W: 0.5% or more and 2.0% or less, and Co: 0.01% or more and 1.5% or less where C, Si, Mn, Cr, Ni, Mo, Cu, and N satisfy a specific relationship; and a microstructure containing, in volume fraction, 25% or more martensite phase, 65% or less ferrite phase, and 40% or less retained austenite phase.
• such a high-strength stainless steel seamless pipe for oil wells has a strength of 758 MPa or more in yield stress YS, and exhibits sufficient corrosion resistance even in high-temperature severe corrosion environments containing CO 2 , Cl ⁇ , and H 2 S.
• WO 2021/187331 A1 proposes a high-strength stainless steel seamless pipe for oil wells having: a composition containing, in mass %, C: 0.06% or less, Si: 1.0% or less, Mn: 0.01% or more and 1.0% or less, P: 0.05% or less, S: 0.005% or less, Cr: 15.2% or more and 18.5% or less, Mo: 1.5% or more and 4.3% or less, Cu: 1.1% or more and 3.5% or less, Ni: 3.0% or more and 6.5% or less, Al: 0.10% or less, N: 0.10% or less, O: 0.010% or less, and Sb: 0.001% or more and 1.000% or less where C, Si, Mn, Cr, Ni, Mo, Cu, and N satisfy a specific relationship; and a microstructure containing, in volume fraction, 30% or more martensite phase, 65% or less ferrite phase, and 40% or less retained austenite phase.
• such a high-strength stainless steel seamless pipe for oil wells has a strength of 758 MPa or more in yield stress YS, and exhibits sufficient corrosion resistance even in high-temperature severe corrosion environments containing CO 2 , Cl ⁇ , and H 2 S.
• steel pipes for oil wells are required to have not only excellent yield stress and low-temperature toughness but also high corrosion resistance to withstand use in severe corrosion environments.
• steel pipes for oil wells are required to have excellent corrosion resistance in carbon dioxide environments (CO 2 corrosion resistance), and particularly required to have excellent CO 2 corrosion resistance even in high-temperature environments.
• CO 2 corrosion resistance carbon dioxide environments
• Steel pipes for oil wells are also required to have resistance (SSC resistance) to sulfide stress cracking (SSC) in hydrogen sulfide environments.
• SSC resistance resistance
• SSC sulfide stress cracking
• cold seawater has a high specific gravity and stays near the seabed, so that the pipes for oil wells are exposed to temperatures lower than the atmospheric temperature of the region. Accordingly, steel pipes for oil wells are required to have excellent SSC resistance even in low-temperature environments.
• the technique described in PTL 5 is supposed to provide high strength, high-temperature corrosion resistance, and corrosion resistance in acid environments, but the SSC resistance is not necessarily sufficient.
• the reason for this is considered as follows: If the phase fraction during steel pipe production is not appropriate, the hot workability is insufficient, and cracking occurs on the inner and outer surfaces of the steel pipe. In the case where such a steel pipe is used in an oil well, corrosive ions stay inside the cracks and further concentrate with the progress of corrosion. This causes insufficient SSC resistance.
• excellent corrosion resistance means excellent in all of high-temperature CO 2 corrosion resistance, low-temperature SSC resistance, and corrosion resistance in acid environments.
• excellent high-temperature CO 2 corrosion resistance means that the corrosion rate when a test piece is immersed in a test liquid: 20 mass % NaCl aqueous solution (liquid temperature: 200° C., 30 atm CO 2 gas atmosphere) held in an autoclave for an immersion time of 336 hours is 0.127 mm/y or less.
• excellent low-temperature SSC resistance means that, when a C-shaped test piece conforming to NACE TM0177 Method C is immersed in an aqueous solution obtained by adding acetic acid+sodium acetate to a 0.165 mass % NaCl aqueous solution (liquid temperature: 7° C., 0.995 atm CO 2 gas, 0.005 atm H 2 S atmosphere) to adjust the pH to 3.0 for an immersion time of 720 hours under load of 100% of yield stress as load stress, there is no cracking in the test piece after the test.
• excellent corrosion resistance in acid environments means that the corrosion rate when a test piece is immersed in a 15 mass % hydrochloric acid solution heated to 80° C. for an immersion time of 40 minutes is 600 mm/y or less.
• “excellent low-temperature toughness” means that the Charpy absorbed energy vE ⁇ 10 at ⁇ 10° C. is 40 J or more.
• the Charpy absorbed energy vE ⁇ 10 is measured by the following procedure. First, three V-notch test pieces (10 mm thick) whose longitudinal direction is perpendicular to the pipe axis and whose notch is on a plane perpendicular to the pipe axis are collected per one stainless steel seamless pipe in accordance with ASTM E23.
• test pieces are then subjected to a Charpy impact test at a test temperature of ⁇ 10° C., and the lowest value of the absorbed energies of the three test pieces is taken to be the Charpy absorbed energy vE ⁇ 10 at ⁇ 10° C.
• a stainless steel seamless pipe comprising: a chemical composition containing (consisting of), in mass %, C: 0.06% or less, Si: 1.0% or less, Mn: 0.01% or more and 1.0% or less, P: 0.05% or less, S: 0.005% or less, Cr: 15.2% or more and 18.0% or less, Mo: 1.5% or more and 4.3% or less, Cu: 1.2% or more and 3.5% or less, Ni: 3.5% or more and 5.2% or less, V: 0.5% or less, Al: 0.10% or less, N: 0.10% or less, O: 0.010% or less, Sb: 0.001% or more and 1.000% or less, Co: 0.01% or more and 1.00% or less, and Ca: 0.001% or more and 0.030% or less, with a balance consisting of Fe and inevitable impurities; 30% or more martensite phase, 50% or less ferrite phase, and 40% or less retained austenite phase in volume fraction; a yield stress of 758 MPa or more; and a Charpy
• the stainless steel seamless pipe according to 1. wherein the chemical composition further contains, in mass %, at least one selected from the group consisting of Nb: 0.07% or less, Ti: 0.2% or less, W: 0.9% or less, B: 0.01% or less, Ta: 0.3% or less, Zr: 0.3% or less, REM: 0.3% or less, Mg: 0.01% or less, and Sn: 1.0% or less.
• the stainless steel seamless pipe according to 1, or 2. comprising: 50% or more martensite phase, 50% or less ferrite phase, and 25% or less retained austenite phase in volume fraction; and a yield stress of 862 MPa or more.
• a production method for a stainless steel seamless pipe comprising: making a seamless steel pipe from a steel material having the chemical composition according to 1, or 2.; heating the seamless steel pipe to a quenching temperature of 850° C. to 1150° C.; cooling the seamless steel pipe after the heating to a cooling stop temperature of 50° C. or less at a cooling rate of 0.01° C./s or more; and heating the seamless steel pipe after the cooling to a tempering temperature of 500° C. to 650° C., to produce a stainless steel seamless pipe having: 30% or more martensite phase, 50% or less ferrite phase, and 40% or less retained austenite phase in volume fraction; a yield stress of 758 MPa or more; and a Charpy absorbed energy vE. 10 at ⁇ 10° C. of 40 J or more.
• a stainless steel seamless pipe according to the present disclosure has the foregoing chemical composition.
• mass % is simply written as “%” unless otherwise noted.
• the C content is an element inevitably contained in the steelmaking process. If the C content is more than 0.06%, the corrosion resistance decreases. The C content is therefore 0.06% or less.
• the C content is preferably 0.05% or less, more preferably 0.04% or less, and further preferably 0.03% or less. Since the C content is desirably as low as possible from the viewpoint of the corrosion resistance, no lower limit is placed on the C content. From the viewpoint of decarburization cost, however, the C content is preferably 0.002% or more, more preferably 0.003% or more, and further preferably 0.005% or more.
• Si is an element that acts as a deoxidizer. If the Si content is more than 1.0%, the hot workability and the corrosion resistance decrease. The Si content is therefore 1.0% or less, preferably 0.7% or less, more preferably 0.5% or less, and further preferably 0.4% or less. Although no lower limit is placed on the Si content, the Si content is preferably 0.03% or more, more preferably 0.05% or more, and further preferably 0.1% or more from the viewpoint of enhancing the deoxidizing effect.
• Mn is an element that acts as a deoxidizing material and a desulfurizing material and improves the hot workability.
• the Mn content is 0.01% or more, preferably 0.03% or more, more preferably 0.05% or more, and further preferably 0.1% or more. If the Mn content is more than 1.0%, the effect is saturated. The Mn content is therefore 1.0% or less, preferably 0.8% or less, more preferably 0.6% or less, and further preferably 0.4% or less.
• S is an element that significantly decreases the hot workability and hinders stable operation in the hot pipe making process. Moreover, S exists as sulfide-based inclusions in the steel, and decreases the corrosion resistance.
• the S content is therefore 0.005% or less, preferably 0.004% or less, more preferably 0.003% or less, and further preferably 0.002% or less. Since it is desirable to reduce the S content as much as possible, no lower limit is placed on the S content, and the S content may be 0%. Since excessive reduction causes an increase in cost, the S content is preferably 0.0003% or more and more preferably 0.0005% or more from the viewpoint of cost.
• Cr is an element that forms a protective coating on the steel pipe surface and contributes to improved corrosion resistance. If the Cr content is less than 15.2%, the desired CO 2 corrosion resistance and SSC resistance cannot be ensured. The Cr content is therefore 15.2% or more, preferably 15.5% or more, more preferably 16.0% or more, and further preferably 16.30% or more. If the Cr content is more than 18.0%, the ferrite fraction is excessively high, and the desired strength cannot be ensured. The Cr content is therefore 18.0% or less, preferably 17.5% or less, more preferably 17.2% or less, and further preferably 17.0% or less.
• Mo stabilizes the protective coating on the steel pipe surface and increases the resistance to pitting corrosion caused by Cl ⁇ and low pH, thus enhancing the corrosion resistance.
• the Mo content is 1.5% or more, preferably 1.8% or more, more preferably 2.0% or more, and further preferably 2.3% or more. If the Mo content is more than 4.3%, the ferrite fraction is excessively high, and the desired strength cannot be ensured.
• the Mo content is therefore 4.3% or less, preferably 4.0% or less, more preferably 3.5% or less, and further preferably 3.0% or less.
• the Cu has the effect of enhancing the CO 2 corrosion resistance and the SSC resistance by strengthening the protective coating on the steel pipe surface.
• the Cu content is 1.2% or more, preferably 1.8% or more, more preferably 2.0% or more, and further preferably 2.3% or more. If the Cu content is excessively high, the hot workability of the steel decreases and outer surface flaws occur during pipe making, making it impossible to achieve the desired SSC resistance.
• the Cu content is therefore 3.5% or less, preferably 3.2% or less, more preferably 3.0% or less, and further preferably 2.7% or less.
• V is an element that forms carbonitrides to thus increase the strength without impairing the toughness. V also has the effect of improving the corrosion resistance. This is because, as a result of V preferentially forming carbonitrides, corrosion-resistant elements such as Cr are prevented from forming carbonitrides and consequently a decrease in the amount effective for the corrosion resistance is suppressed. If the V content is more than 0.5%, the effect is saturated. The V content is therefore 0.5% or less, preferably 0.2% or less, and further preferably 0.1% or less. Although no lower limit is placed on the V content, the V content is preferably 0.01% or more, and more preferably 0.03% or more.
• Al is an element that acts as a deoxidizer. If the Al content is more than 0.10%, the corrosion resistance decreases. The Al content is therefore 0.10% or less, preferably 0.07% or less, and more preferably 0.05% or less. Although no lower limit is placed on the Al content, the Al content is preferably 0.005% or more, more preferably 0.01% or more, and further preferably 0.015% or more from the viewpoint of enhancing the deoxidizing effect.
• N is an element that is inevitably contained in the steelmaking process but also enhances the strength of the steel. If the N content is more than 0.10%, the amount of nitride formed is excessive and the corrosion resistance decreases.
• the N content is therefore 0.10% or less, preferably 0.07% or less, more preferably 0.05% or less, and further preferably 0.03% or less. Although no lower limit is placed on the N content, excessive reduction of the N content causes an increase in steelmaking cost.
• the N content is therefore preferably 0.002% or more, more preferably 0.003% or more, and further preferably 0.005% or more.
• O oxygen
• the hot workability and the corrosion resistance decrease.
• the O content is therefore 0.010% or less. Since excessive reduction causes an increase in cost, the O content is preferably 0.00005% or more and more preferably 0.001% or more from the viewpoint of cost.
• the Sb content is 0.001% or more, preferably 0.003% or more, more preferably 0.005% or more, and further preferably 0.010% or more. If the Sb content is more than 1.000%, the effect is saturated. The Sb content is therefore 1.000% or less, preferably 0.500% or less, more preferably 0.100% or less, and further preferably 0.050% or less.
• Co is an element that improves the corrosion resistance.
• the Co content is 0.01% or more, preferably 0.03% or more, and more preferably 0.05% or more. If the Co content is more than 1.00%, the effect is saturated.
• the Co content is therefore 1.00% or less, preferably 0.50% or less, more preferably 0.30% or less, and further preferably 0.10% or less.
• Ca is an element that improves the hot workability through sulfide morphological control, and suppresses flaws during pipe making to thus contributes to improved SSC resistance of the steel pipe.
• the Ca content is 0.001% or more, preferably 0.003% or more, more preferably 0.005% or more, even more preferably more than 0.010%, further preferably 0.012% or more, and most preferably 0.014% or more. If the Ca content is more than 0.030%, the effect is saturated, and the effect commensurate with the amount cannot be expected.
• the Ca content is therefore 0.030% or less, preferably 0.025% or less, and more preferably 0.020% or less.
• a stainless steel seamless pipe has a chemical composition containing the foregoing components with the balance consisting of Fe and inevitable impurities.
• the chemical composition may optionally further contain at least one selected from the group consisting of Nb, Ti, W, B, Ta, Zr, REM, Mg, and Sn.
• Nb, Ti, W, B, Ta, Zr, REM, Mg, and Sn are optional steel components, and the contents of these components may be 0%.
• Nb is an element that forms carbonitrides and further improves the strength and the corrosion resistance, and may be optionally added. Since Nb carbonitrides tend to decrease the low-temperature toughness, in the case of adding Nb, the Nb content is 0.07% or less, preferably 0.03% or less, and more preferably 0.01% or less. Regarding the lower limit, the Nb content may be 0%, but is preferably 0.001% or more from the viewpoint of enhancing the effect of the addition of Nb.
• Ti is an element that further improves the strength and the corrosion resistance, and may be optionally contained. If the Ti content is more than 0.2%, the low-temperature toughness decreases. Accordingly, in the case of adding Ti, the Ti content is 0.2% or less, preferably 0.05% or less, and more preferably 0.01% or less. Regarding the lower limit, the Ti content may be 0%, but is preferably 0.001% or more from the viewpoint of enhancing the effect of the addition of Ti.
• W is an element that contributes to improved strength of the steel and stabilizes the protective coating on the steel pipe surface to further enhance the corrosion resistance. If the W content is more than 0.9%, the low-temperature toughness decreases. Accordingly, in the case of adding W, the W content is 0.9% or less, preferably 0.5% or less, and more preferably 0.3% or less. No lower limit is placed on the W content and the W content may be 0%, but the W content is preferably 0.05% or more and more preferably 0.1% or more.
• B is an element that contributes to improved hot workability and also has the effect of suppressing cracking in the pipe making process. If the B content is more than 0.01%, the low-temperature toughness decreases. Accordingly, in the case of adding B, the B content is 0.01% or less, preferably 0.007% or less, and more preferably 0.005% or less. No lower limit is placed on the B content and the B content may be 0%, but the B content is preferably 0.0005% or more and more preferably 0.001% or more.
• Ta is an element that has the effect of further improving the strength and further improving the corrosion resistance, and may be optionally contained. If the Ta content is more than 0.3%, the effect is saturated. Accordingly, in the case of adding Ta, the Ta content is 0.3% or less. No lower limit is placed on the Ta content and the Ta content may be 0%, but the Ta content is preferably 0.001% or more.
• Zr is an element that further improves the strength, and may be optionally contained. Zr also has the effect of further improving the SSC resistance. If the Zr content is more than 0.3%, the effect is saturated. Accordingly, in the case of adding Zr, the Zr content is 0.3% or less. No lower limit is placed on the Zr content and the Zr content may be 0%, but the Zr content is preferably 0.0005% or more.
• REM rare earth metal
• the REM content is an element that contributes to further improved SSC resistance through sulfide morphological control, and may be optionally contained. If the REM content is more than 0.3%, the effect is saturated, and the effect commensurate with the amount cannot be expected. Accordingly, in the case of adding REM, the REM content is 0.3% or less. No lower limit is placed on the REM content and the REM content may be 0%, but the REM content is preferably 0.0005% or more.
• “REM” includes scandium (Sc) with atomic number 21, yttrium (Y) with atomic number 39, and lanthanoids from lanthanum (La) with atomic number 57 to lutetium (Lu) with atomic number 71.
• the chemical composition of the stainless steel seamless pipe according to the present disclosure may optionally contain at least one of these REMs.
• the “REM content” is the total content of these elements.
• Mg is an element that further improves the corrosion resistance, and may be optionally contained. If the Mg content is more than 0.01%, the effect is saturated, and the effect commensurate with the amount cannot be expected. Accordingly, in the case of adding Mg, the Mg content is 0.01% or less. No lower limit is placed on the Mg content and the Mg content may be 0%, but the Mg content is preferably 0.0005% or more.
• Sn is an element that further improves the corrosion resistance, and may be optionally contained. If the Sn content is more than 1.0%, the effect is saturated, and the effect commensurate with the amount cannot be expected. Accordingly, in the case of adding Sn, the Sn content is 1.0% or less. No lower limit is placed on the Sn content and the Sn content may be 0%, but the Sn content is preferably 0.001% or more.
• the stainless steel seamless pipe according to an embodiment of the present disclosure contains 30% or more martensite phase, 50% or less ferrite phase, and 40% or less retained austenite phase in volume fraction.
• volume fraction of martensite phase is less than 30%, the desired strength cannot be ensured.
• the volume fraction of martensite phase is therefore 30% or more, preferably 40% or more, more preferably 45% or more, and further preferably 50% or more.
• the volume fraction of martensite phase is preferably 90% or less, and more preferably 85% or less.
• the volume fraction of ferrite phase is more than 50%, the desired strength cannot be ensured.
• the volume fraction of ferrite phase is therefore 50% or less, preferably 40% or less, and more preferably 35% or less.
• the volume fraction of ferrite phase is preferably 10% or more, more preferably 15% or more, and further preferably 20% or more.
• the presence of retained austenite phase improves the ductility and the low-temperature toughness. However, if a large amount of austenite phase with a volume fraction exceeding 40% precipitates, the desired strength cannot be ensured.
• the volume fraction of retained austenite phase is therefore 40% or less, preferably 30% or less, and more preferably 25% or less. Although no lower limit is placed on the volume fraction of retained austenite phase, the volume fraction of retained austenite phase is preferably 3% or more, and more preferably 5% or more.
• the volume fraction of each phase can be measured by the following method: First, a test piece for microstructure observation collected from a stainless steel seamless pipe is etched with Vilella's reagent (a reagent obtained by mixing picric acid, hydrochloric acid, and ethanol in proportions of 2 g, 10 ml, and 100 ml respectively). Following this, the microstructure of the test piece for microstructure observation is imaged using a scanning electron microscope (SEM) with 1000 magnification to obtain a SEM image. The obtained SEM image is analyzed using image analysis software (ImageJ 1.52p, National Institute of Health), and the microstructure proportion (area ratio (%)) of ferrite phase is calculated. In the analysis, the SEM image is binarized, and each region with low brightness is regarded as ferrite phase. The area ratio obtained by this procedure is defined as the volume fraction (%) of ferrite phase.
• a test piece for microstructure observation collected from a stainless steel seamless pipe is etched with Vilella's reagent (a reagent obtained by mixing pic
• a test piece for X-ray diffraction collected from the stainless steel seamless pipe is ground and polished so that a cross section (C section) orthogonal to the pipe axis direction will be the measurement plane, and the microstructure proportion of retained austenite (Y) phase is measured using an X-ray diffraction method.
• the volume fraction of retained austenite phase is calculated from the integrated intensity of each of (220) plane of austenite and (211) plane of ferrite using the following formula:
• V ⁇ (%) 100/(1+( I ⁇ R ⁇ /I ⁇ R ⁇ ))
• the balance other than ferrite phase and retained y phase calculated by the foregoing measurement method is the fraction of martensite phase.
• the method of observing each microstructure will be described in detail in the EXAMPLES section below.
• the microstructure of the stainless steel seamless pipe according to the present disclosure substantially consists of martensite phase, ferrite phase, and retained austenite phase. That is, the microstructure may contain other microstructures as long as the effects according to the present disclosure are not impaired. Examples of the other microstructures include intermetallic compounds and inclusions.
• a stainless steel seamless pipe may comprise a microstructure containing, in volume fraction, 50% or less ferrite phase and 40% or less retained austenite phase with the balance substantially consisting of martensite phase, wherein the volume fraction of martensite phase is 30% or more.
• a stainless steel seamless pipe may comprise a microstructure consisting of, in volume fraction, 30% or more martensite phase, 50% or less ferrite phase, and 40% or less retained austenite phase.
• the microstructure In either case, it is permissible for the microstructure to contain inevitable impurity phase.
• the stainless steel seamless pipe according to the present disclosure has a yield stress of 758 MPa or more. Although no upper limit is placed on the yield stress, the yield stress is preferably 1034 MPa or less.
• the yield stress can be measured by a tensile test. More specifically, the yield stress can be measured by the method described in the EXAMPLES section.
• the stainless steel seamless pipe according to the present disclosure has a Charpy absorbed energy vE ⁇ 10 at ⁇ 10° C. of 40 J or more. Since the Charpy absorbed energy vE ⁇ 10 is desirably as high as possible, no upper limit is placed on the Charpy absorbed energy vE ⁇ 10 .
• the Charpy absorbed energy vE ⁇ 10 may be 300 J or less, and may be 250 J or less.
• the Charpy absorbed energy can be measured by a Charpy impact test. More specifically, the Charpy absorbed energy can be measured by the method described in the EXAMPLES section.
• the stainless steel seamless pipe according to the present disclosure may be used for any purpose without limitation.
• the stainless steel seamless pipe according to the present disclosure is particularly suitable for use in oil wells. That is, the stainless steel seamless pipe according to an embodiment of the present disclosure is a stainless steel seamless pipe for oil wells (high-strength stainless steel seamless pipe for oil wells).
• the stainless steel seamless pipe according to the present disclosure can be produced by making a seamless steel pipe from a steel material and subjecting the seamless steel pipe to quenching-tempering treatment under specific conditions.
• the steel material is not limited, and may be any material.
• a billet is typically used as the steel material.
• As the steel material a material having the foregoing chemical composition can be used.
• the production method for the steel material is not limited, and the steel material can be produced by any method.
• molten steel having the foregoing chemical composition is obtained by conventional steelmaking using a converter or the like, and then a steel material such as a billet is produced by a method such as continuous casting or ingot casting and blooming.
• the obtained seamless steel pipe is then subjected to heat treatment (quenching-tempering treatment) composed of quenching treatment and tempering treatment under specific conditions.
• quenching-tempering treatment composed of quenching treatment and tempering treatment under specific conditions. The conditions in the quenching-tempering treatment will be described below.
• the seamless steel pipe is heated to a quenching temperature of 850° C. to 1150° C., and the heated seamless steel pipe is cooled to a cooling stop temperature of 50° C. or less at a cooling rate of 0.01° C./s or more.
• the heating temperature (quenching temperature) in the quenching treatment is less than 850° C., reverse transformation from martensite to austenite does not occur, and transformation from austenite to martensite does not occur during cooling, so that the desired strength cannot be ensured.
• the quenching temperature is therefore 850° C. or more, and preferably 900° C. or more. If the quenching temperature is more than 1150° C., crystal grains coarsen, as a result of which the low-temperature toughness degrades.
• the quenching temperature is therefore 1150° C. or less, and preferably 1100° C. or less.
• soaking treatment of holding the seamless steel pipe at the quenching temperature may be performed.
• the soaking treatment can make the temperature in the thickness direction of the seamless steel pipe uniform, and reduce variation in material property.
• the time (soaking time) for holding at the quenching temperature is not limited, but is preferably 5 minutes to 30 minutes.
• Cooling Rate 0.01° C./s or More
• the cooling rate in the quenching treatment is less than 0.01° C./s, the desired microstructure cannot be obtained.
• the cooling rate is therefore 0.01° C./s or more, preferably 1.0° C./s or more, more preferably 5.0° C./s or more, and further preferably 10.0° C./s or more.
• the cooling rate is preferably 100° C./s or less, more preferably 50° C./s or less, and further preferably 30° C./s or less.
• the cooling is not limited, and may be performed by any method.
• the cooling is preferably performed by at least one of air cooling and water cooling, and more preferably performed by water cooling.
• Cooling Stop Temperature 50° C. Or Less
• the cooling stop temperature is more than 50° C., the desired microstructure cannot be obtained.
• the cooling stop temperature in the quenching treatment is therefore 50° C. or less. No lower limit is placed on the cooling stop temperature, and the cooling stop temperature may be, for example, 0° C. or more.
• the cooling stop temperature herein is the surface temperature of the seamless steel pipe.
• the seamless steel pipe after the quenching treatment is then subjected to tempering treatment of heating to a tempering temperature of 500° C. to 650° C.
• Tempering Temperature 500° C. To 650° C.
• the tempering temperature is less than 500° C., the tempering effect is insufficient, as a result of which the low-temperature toughness degrades.
• the tempering temperature is therefore 500° C. or more, and preferably 520° C. or more. If the tempering temperature is more than 650° C., a large amount of intermetallic compounds precipitates, and excellent low-temperature toughness cannot be obtained.
• the tempering temperature is therefore 650° C. or less, and preferably 630° C. or less.
• the seamless steel pipe may be held at the tempering temperature.
• the time (holding time) for holding at the tempering temperature is not limited, but is preferably 5 minutes or more from the viewpoint of making the temperature in the thickness direction uniform and preventing variation in material property. No upper limit is placed on the holding time, but the holding time is preferably 90 minutes or less.
• the seamless steel pipe After the tempering treatment, the seamless steel pipe can be allowed to naturally cool.
• Each steel material was cast using molten steel having the chemical composition shown in Tables 1 to 3.
• the steel material was then heated, and hot worked using a model seamless mill into a seamless steel pipe of 177.8 mm in outer diameter and 16.0 mm in thickness, followed by air cooling.
• the heating temperature of the steel material before the hot working was 1250° C.
• the obtained seamless steel pipe was then subjected to quenching-tempering treatment under the following conditions to obtain a stainless steel seamless pipe.
• a corrosion test piece of 3 mm in thickness, 30 mm in width, and 40 mm in length was machined from the obtained stainless steel seamless pipe.
• a corrosion test was conducted using the corrosion test piece, and the corrosion rate was measured as an index of the CO 2 corrosion resistance.
• the corrosion test piece was immersed in a test liquid: 20 mass % NaCl aqueous solution (liquid temperature: 200° C., 30 atm CO 2 gas atmosphere) held in an autoclave for an immersion time of 14 days (336 hours). The weight of the corrosion test piece after the corrosion test was measured, and the pre-measured weight of the test piece before the corrosion test was subtracted from the measured weight to yield the weight loss by the corrosion test.
• the weight loss was then divided by the surface area of the test piece used and the immersion time to obtain the weight loss per unit time and per unit area.
• the weight loss per unit time and per unit area was divided by the density of the steel to convert it into the corrosion thickness per unit time and per unit area.
• the corrosion thickness per unit time and per unit area (mm/y) thus obtained was taken to be the corrosion rate in carbon dioxide.
• the stainless steel seamless pipe was rated pass in the case where the corrosion rate was 0.127 mm/y or less, and rated fail in the case where the corrosion rate was more than 0.127 mm/y.
• a C-shaped test piece was machined from the obtained stainless steel seamless pipe in accordance with NACE TM0177 Method C, and an SSC resistance test was conducted.
• the curved surfaces corresponding to the inner and outer surfaces of the steel pipe were not ground or polished.
• the C-shaped test piece conforming to NACE TM0177 Method C was immersed in an aqueous solution obtained by adding acetic acid+sodium acetate to a 0.165 mass % NaCl aqueous solution (liquid temperature: 7° C., 0.995 atm CO 2 gas, 0.005 atm H 2 S atmosphere) to adjust the pH to 3.0 for an immersion time of 720 hours under load of 100% of yield stress as load stress.
• the stainless steel seamless pipe was rated pass in the case where there was no cracking, and rated fail in the case where there was cracking.
• “1” denotes pass and “2” denotes fail.
• a rectangular parallelepiped test piece was machined from the obtained stainless steel seamless pipe.
• the test piece was 50 mm in length in the longitudinal direction of the steel pipe, 3 mm in thickness in the thickness direction of the steel pipe, and 25 mm in width.
• a corrosion test was conducted by immersing, for 40 minutes, the test piece in a 15 mass % hydrochloric acid solution heated to 80° C. The weight of the test piece after the corrosion test was measured, and the weight of the test piece before the corrosion test was subtracted from the measured weight to yield the weight loss by the corrosion test. The weight loss was then divided by the surface area of the test piece used and the immersion time in the corrosion test to obtain the weight loss per unit time and per unit area.
• the weight loss per unit time and per unit area was divided by the density of the steel to convert it into the corrosion thickness per unit time and per unit area.
• the corrosion thickness per unit time and per unit area (mm/y) thus obtained was taken to be the corrosion rate in acid environments.
• the stainless steel seamless pipe was rated pass in the case where the corrosion rate was 600 mm/y or less, and rated fail in the case where the corrosion rate was more than 600 mm/y.
• the following evaluation was conducted to evaluate the hot workability of the obtained stainless steel seamless pipe.
• the flaw depth on the surface of the test piece in the SSC resistance test corresponding to the outer surface of the steel pipe was measured by ultrasonic testing. Based on the maximum value of the flaw depth measured, the hot workability was evaluated in the following three levels:
• each stainless steel seamless pipe satisfying the conditions according to the present disclosure had high strength of 758 MPa (110 ksi) or more in yield stress and excellent low-temperature toughness and corrosion resistance.
• the corrosion resistance in particular, all of the high-temperature CO 2 corrosion resistance, the low-temperature SSC resistance, and the corrosion resistance in acid environments were excellent.
• Such a stainless steel seamless pipe according to the present disclosure is very suitable for various applications such as steel pipes for oil wells.

Landscapes

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

Applications Claiming Priority (3)

Publications (1)

Family

ID=89451910

Family Applications (1)

Country Status (5)

Families Citing this family (1)

Family Cites Families (5)

• 2023
  • 2023-03-08 JP JP2023537602A patent/JP7409569B1/ja active Active
  • 2023-03-08 US US18/865,416 patent/US20250320592A1/en active Pending
  • 2023-03-08 CN CN202380042711.2A patent/CN119256106A/zh active Pending
  • 2023-03-08 EP EP23835105.0A patent/EP4509629A4/en active Pending
• 2025
  • 2025-01-06 MX MX2025000005A patent/MX2025000005A/es unknown

Also Published As

Similar Documents

Legal Events