[go: up one dir, main page]

WO2024113654A1 - Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation - Google Patents

Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation Download PDF

Info

Publication number
WO2024113654A1
WO2024113654A1 PCT/CN2023/089649 CN2023089649W WO2024113654A1 WO 2024113654 A1 WO2024113654 A1 WO 2024113654A1 CN 2023089649 W CN2023089649 W CN 2023089649W WO 2024113654 A1 WO2024113654 A1 WO 2024113654A1
Authority
WO
WIPO (PCT)
Prior art keywords
weight percentage
corrosion
oil casing
casing
resistant
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
PCT/CN2023/089649
Other languages
English (en)
Chinese (zh)
Inventor
王奎
邓叙燕
冯莹
郭振
高辉
肖旭
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
DALIPAL PIPE Co
Original Assignee
DALIPAL PIPE Co
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by DALIPAL PIPE Co filed Critical DALIPAL PIPE Co
Priority to PCT/CN2023/089649 priority Critical patent/WO2024113654A1/fr
Priority to US18/671,752 priority patent/US20240352564A1/en
Publication of WO2024113654A1 publication Critical patent/WO2024113654A1/fr
Anticipated expiration legal-status Critical
Pending legal-status Critical Current

Links

Classifications

    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/06—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/54—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • E—FIXED CONSTRUCTIONS
    • E21—EARTH OR ROCK DRILLING; MINING
    • E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
    • E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings

Definitions

  • the present application belongs to the technical field of oil casing for oil and gas fields, and in particular relates to a corrosion-resistant and high-toughness oil casing and a preparation method thereof.
  • the oil casing used for development not only needs to have high strength and excellent corrosion resistance (excellent SCC resistance at high temperatures and excellent SSC resistance at room temperature), but also needs to have high toughness at low temperatures. Therefore, in order to improve the competitiveness of enterprises, it is urgent to develop an oil casing with high strength, excellent SCC resistance at high temperatures, excellent SSC resistance at room temperatures, and high toughness at low temperatures to adapt to the increasingly severe mining environment.
  • the purpose of this application is to provide a petroleum casing with high strength, excellent SCC resistance at high temperature and excellent SSC resistance at room temperature and high toughness at low temperature, so as to solve the problem that the corrosion resistance of the existing 13Cr petroleum casing drops sharply when the temperature changes and cannot meet the current market demand.
  • the present application provides a corrosion-resistant and high-toughness petroleum casing, wherein the weight percentage of the components is: 0.01% ⁇ C ⁇ 0.04%, 0.1% ⁇ Si ⁇ 0.8%, 0.05% ⁇ Mn ⁇ 0.25%, 11.0% ⁇ Cr ⁇ 14.0%, 1.5% ⁇ Mo ⁇ 2.8%, 0.5% ⁇ Cu ⁇ 1.8%, 3.7% ⁇ Ni ⁇ 5.0%, 0.03% ⁇ N ⁇ 0.05%, 0.001% ⁇ Al ⁇ 0.05%, 0.002% ⁇ B ⁇ 0.008%, 0.03% ⁇ Ti ⁇ 0.08%, 0.07% ⁇ La ⁇ 0.35%, 0.12% ⁇ Ce ⁇ 0.40%, P ⁇ 0.013%, S ⁇ 0.001%, and the balance is Fe and unavoidable impurities;
  • the weight percentage of the components satisfies the following relationship: [Ni]/[Cu] ⁇ 3.0, 4360 ⁇ ([Ni]+[Cr]+[Mo])/[B] ⁇ 16200, wherein [Ni] represents the weight percentage of the Ni element content in the oil casing, [Cu] represents the weight percentage of the Cu element content in the oil casing, [Cr] represents the weight percentage of the Cr element content in the oil casing, [Mo] represents the weight percentage of the Mo element content in the oil casing, and [B] represents the weight percentage of the B element content in the oil casing;
  • the metallographic structure of the oil casing consists of ferrite with a volume fraction of 10% to 20%, residual austenite with a volume fraction of 5.0% to 20%, and the rest being tempered martensite.
  • the inventor has conducted a lot of experiments and studies on the corrosion resistance of oil casing in severe corrosive environments containing CO 2 , H 2 S, etc.
  • the low-temperature toughness of stainless steel has been studied, and it is found that an appropriate amount of ferrite can improve the corrosion resistance of steel, but if the ferrite content is too high, the strength of the steel will be reduced.
  • retained austenite can improve the toughness of steel under low temperature conditions, but excessive retained austenite will also reduce the strength of steel. Therefore, the metallographic structure of the oil casing disclosed in the present application is composed of ferrite with a volume fraction of 10% to 20%, retained austenite with a volume fraction of 5.0% to 20%, and the rest is tempered martensite.
  • the steel can ensure that the steel has a sufficiently high strength, and on the other hand, it can also appropriately control and adjust the amount of ferrite and retained austenite to obtain an oil casing with high strength, excellent corrosion resistance and relatively high low-temperature toughness, which meets the current market demand.
  • the C content is set to 0.01% to 0.04%, preferably 0.02% to 0.04%.
  • Si acts as a deoxidizer. If the content is too low, it will not have a deoxidizing effect. However, if the content exceeds 0.8%, the corrosion resistance and hot workability of the oil casing will be significantly reduced. Therefore, the Si content is set to 0.1% to 0.8%, preferably 0.1% to 0.5%.
  • Mn can improve the toughness, strength and hot workability of steel. If the Mn content is too high, excessive austenite may remain after quenching and tempering, resulting in reduced strength; and if the Mn content is too high, the SSC and SCC resistance will be greatly reduced. Therefore, the Mn content is set to 0.05% to 0.25%, preferably 0.05% to 0.20%.
  • the Cr is an element that forms a protective film to improve corrosion resistance. If the content is too low, it will not play a corresponding role. On the other hand, if the content is too high, the ferrite content will exceed 20%, which is not good for the strength of the oil casing. Therefore, the Cr content is set to 11.0% to 14.0%, preferably 11.5% to 13.0%.
  • Mo can improve the SSC resistance, and containing Mo and Cr can better improve the SCC resistance of steel at high temperatures.
  • Mo content is set to 1.5% to 2.8%, preferably 1.5% to 2.6%.
  • Cu can stabilize the protective film formed by Cr to improve SSC resistance.
  • Cu precipitates as fine Cu particles during tempering to improve the strength of steel.
  • the Cu content is set to 0.5% to 1.8%, preferably 1.0% to 1.6%.
  • Ni can stabilize the protective film formed by Cr, thereby improving SSC resistance, and can also improve the strength of steel. In addition, during tempering, Ni can also promote the formation of retained austenite at room temperature to improve its low-temperature toughness. However, if the Ni content is too high, the stability of tempered martensite decreases and the strength of the steel decreases. Therefore, the Ni content is set to 3.7% to 5.0%, preferably 3.7% to 4.8%.
  • N can form carbonitrides with C, and refine the grains through the pinning effect of carbonitride precipitation, thereby improving strength and corrosion resistance.
  • N content exceeding 0.05% will reduce toughness and corrosion resistance. Therefore, the N content is set to 0.03% to 0.05%, preferably 0.03% to 0.04%.
  • Al is a good deoxidizer and grain refiner, which improves the toughness of oil casing at low temperatures and improves the oxidation resistance of oil casing; however, too high Al content will increase non-metallic inclusions in oil casing, which will have a negative impact on the toughness of steel. Therefore, the Al content is set to 0.001% to 0.05%, preferably 0.001% to 0.04%.
  • B can increase the hardenability of steel, reduce deformation and improve SSC resistance. Adding appropriate B can save other rare and precious metals, such as Ni, Cr, and Mo. 0.001% of B can replace 1.6% of Ni, 0.3% of Cr or 0.2% of Mo. However, excessive B tends to promote temper brittleness and reduce the low-temperature toughness of steel, so the B content is set to 0.001% to 0.005%, preferably 0.001% to 0.003%.
  • the weight percentages of Ni, Cr, Mo and B are set to satisfy the following relationship: 4360 ⁇ ([Ni]+[Cr]+[Mo])/[B] ⁇ 16200, where [Ni] represents the weight percentage of Ni in oil casing, [Cr] represents the weight percentage of Cr in oil casing, [Mo] represents the weight percentage of Mo in oil casing, and [B] represents the weight percentage of B in oil casing.
  • the generated Ti carbides can prevent grain growth, refine grains, and increase the toughness of oil casing at low temperatures.
  • an appropriate amount of Ti can improve the corrosion resistance of oil casing.
  • too high a Ti content will generate TiN, and the resistance to sulfide stress cracking will drop sharply. Therefore, the Ti content is set to 0.03% to 0.08%, preferably 0.04% to 0.06%.
  • Appropriate content of rare earth elements La and Ce can purify molten steel and also change the composition, morphology, distribution and properties of inclusions in steel, thereby improving the toughness and processing properties of steel.
  • rare earth elements are relatively expensive, so the rare earth element La content is set to 0.07% to 0.35%, and the Ce content is set to 0.12% to 0.40%.
  • P is an impurity element that reduces the toughness and SSC resistance of steel.
  • a higher phosphorus content will segregate at the grain boundary and reduce the bonding strength of the grain boundary, seriously weakening the low-temperature impact toughness of the steel.
  • the content exceeds 0.013%, its toughness and SSC resistance drop sharply. Therefore, the P content is set to 0.013% or less.
  • S is an impurity element that reduces the toughness and SSC resistance of steel.
  • the S content is set to 0.001% or less.
  • the present application also provides a corrosion-resistant and high-toughness petroleum casing, which, based on the above composition, further contains 0.01% ⁇ W ⁇ 1.3% and 0.06% ⁇ V ⁇ 0.1%.
  • W is an optional element.
  • W, Mo and Cr can better improve the SCC resistance of steel at high temperatures.
  • the special compound formed by W and C can significantly refine the grains and improve the strength and toughness of the steel.
  • the W content should not be too high. When it exceeds 1.3%, too much ferrite will be generated in the steel, which will significantly reduce the strength of the steel. Therefore, the W content is set to 0.01% to 1.3%.
  • V is an optional element.
  • V can precipitate as fine precipitates with N and C, and refine the grains through the pinning effect of the precipitates, thereby improving the strength. If the V content is too high, the SSC resistance and low temperature toughness of the steel will decrease. Therefore, the V content is set to 0.06% to 0.1%.
  • the present application also provides a corrosion-resistant and high-toughness petroleum casing, which, based on the above composition, further contains any one or two of 0.0001% ⁇ Ca ⁇ 0.005% and 0.0001% ⁇ Mg ⁇ 0.005%.
  • Ca and Mg are both optional elements.
  • the hot workability of steel can be improved; however, if the content is too high, larger oxides will be generated, reducing the SSC resistance. Therefore, the Ca content is set to 0.0001% to 0.005%, and the Mg content is set to 0.0001% to 0.005%.
  • the second aspect of the present application provides a method for preparing a corrosion-resistant and high-toughness petroleum casing, comprising the following steps:
  • Melting and casting process preparing raw materials according to the weight percentage of the components of the corrosion-resistant and high-toughness petroleum casing, and sequentially subjecting the raw materials to electric furnace smelting, ladle refining outside the furnace, vacuum degassing and arc continuous casting to obtain billets;
  • Pipe making process heating and keeping the billet to obtain a hot billet, performing conical perforation on the hot billet to obtain a rough pipe with an outer diameter of 300 mm to 302 mm, rolling the rough pipe in a continuous pipe rolling unit to obtain a rough pipe with an outer diameter of 264 mm to 266 mm, and reducing the rough pipe by micro-tension and cooling it on a walking cooling bed to obtain a rolled steel pipe;
  • Heat treatment process heating the rolled steel pipe to 980°C to 1030°C, maintaining it for 15min to 25min, and then air cooling or water cooling it to 80°C to 100°C for quenching treatment; then, heating the quenched steel pipe to 650°C to 700°C, maintaining it for 20min to 40min, and then air cooling it for tempering treatment.
  • the present application prepares raw materials according to the weight percentage of the components of the oil casing, and the raw materials are sequentially subjected to the smelting and casting process, the pipe making process and the heat treatment process to prepare the corrosion-resistant and high-toughness oil casing with excellent comprehensive performance.
  • the steel pipe is further heated to a temperature above the Ac3 phase transformation point (Ac3: the final temperature of transformation to austenite during heating), maintained for 15min to 25min, and then cooled to a cooling temperature below 100°C for quenching.
  • Ac3 the final temperature of transformation to austenite during heating
  • the quenching heating temperature is lower than the temperature of the Ac3 phase transformation point, it cannot be heated to the austenite single phase domain, and sufficient martensite structure cannot be obtained in the subsequent cooling, and a high-strength oil casing cannot be obtained. Therefore, the quenching heating temperature is limited to above the Ac3 phase transformation point, preferably 980°C to 1030°C. Then, the oil casing that has been quenched is tempered. During the tempering treatment, heat to below the Ac1 transformation point (Ac1: the temperature at which pearlite transforms to austenite during heating), keep it for at least 10 minutes, and then air cool it.
  • Ac1 the temperature at which pearlite transforms to austenite during heating
  • the tempering temperature is higher than the temperature of the Ac1 transformation point, the formation of the austenite phase cannot be ensured, and the low-temperature toughness cannot be guaranteed. Therefore, the tempering temperature is limited to below the Ac1 transformation point, preferably 650°C ⁇ 700°C. It can be understood that the above-mentioned Ac3 transformation point (°C) and Ac1 transformation point (°C) can be measured by the expansion method: the temperature history of the test piece after heating and cooling is detected according to the micro-displacement of expansion and contraction. The Formaster phase change dilatometer or Gleeble thermal simulation tester can be used for determination.
  • the rolled steel pipe is heated to 980°C to 1030°C and maintained for 15min to 25min.
  • the preferred quenching heating temperature and holding time reduce the dissolved residues of carbides and refine the grains of the structure.
  • the quenched steel pipe is heated to 650°C to 700°C and maintained for 20min to 40min.
  • the preferred tempering heating temperature and holding time can remove the internal stress of the martensite, ensure the generation of the corresponding volume fraction of the austenite phase, and obtain an oil casing with higher low-temperature toughness.
  • the preferred quenching and tempering parameters can obtain an oil casing with high strength and small deviation, excellent corrosion resistance, and high low-temperature toughness.
  • borax is sprayed into the rough tube and then nitrogen is blown, the nitrogen blowing pressure is 3 bar to 8 bar, and the blowing time of the borax is 5 s to 12 s.
  • the hot billet When the hot billet is subjected to conical perforation to produce a rough tube in the pipe making process, an oxide layer is generated due to the contact between the hot billet surface and oxygen. Excessive and thick oxide layers affect the product qualification rate in the subsequent pipe rolling process, and affect the life of the internal deformation tools during rolling, such as the plug or the mandrel. Therefore, the oxide layer needs to be removed during rolling.
  • the present application continuously sprays borax into the rough tube to remove the oxide layer, and then blows nitrogen to blow away the oxide with high-speed nitrogen. At the same time, a part of the oxide forms an antioxidant film, which can prevent the rough tube from reoxidation, improve product quality, extend the service life of the internal deformation tools during rolling, and reduce rolling pressure and energy consumption.
  • the preferred nitrogen blowing pressure and borax blowing time can improve the efficiency of oxide layer removal and save the amount of borax and nitrogen.
  • the cooling rate when the quenching treatment is air-cooled, the cooling rate is 5°C/min to 20°C/min; when the quenching treatment is water-cooled, the cooling rate is 10°C/s to 65°C/s.
  • the cooling method is not specifically limited, and conventional air cooling or water cooling is acceptable.
  • the cooling rate is also not particularly limited. The use of the above preferred cooling rate can reduce the precipitation of coarse carbides, ensure the performance of the steel pipe, and is conducive to obtaining a petroleum casing with high strength and small deviation, excellent corrosion resistance, and high low-temperature toughness.
  • lime, fluorite and calcium carbide are added to the ladle for slag making, and the refining is carried out by gradually increasing the temperature, and the refining time is 60 minutes to 70 minutes.
  • Adding lime, fluorite and calcium carbide to the ladle for slagging is beneficial to further desulfurization and adsorption of inclusions, thereby improving the sulfide stress cracking resistance of the oil casing.
  • the casting speed is 2.8 m/min to 3.2 m/min
  • the vibration frequency of the crystallizer is 163 min -1 to 178 min -1
  • the amplitude is 10.0 mm to 10.3 mm
  • the negative slip rate is 30% to 32%.
  • the preferred vibration parameters of the crystallizer in the present application allow slag inclusions and bubbles in the molten steel to float up, reducing slag inclusions, pores, and cracks on the billet surface.
  • the vibration frequency and amplitude By controlling the vibration frequency and amplitude, the billet shell and the inner wall of the crystallizer can be separated more stably, avoiding adhesion between the billet shell and the crystallizer during the vibration process, causing cracks on the billet surface, and affecting the quality of the final finished petroleum casing.
  • the blank in the pipe making process, is heated to 1220°C to 1260°C and kept warm for 90min to 110min to obtain a hot blank; the temperature of the tapered perforation is not lower than 1150°C.
  • the blank is heated, and the internal structure of the heated blank is more uniform.
  • Hot perforation is performed at a temperature not lower than 1150° C. and the perforation process parameters are controlled to obtain a rough pipe with uniform diameter and uniform mechanical properties, thereby ensuring the quality of the rough pipe for subsequent rolling.
  • the raw tube feed amount of the continuous tube rolling mill is 62 mm to 113 mm
  • the roller speed is 20 rpm to 40 rpm
  • the wind pressure is 5.2 bar to 6.3 bar.
  • the present application utilizes a continuous tube rolling mill for rolling.
  • the preferred parameters of the continuous tube rolling mill can significantly suppress the generation of internal cracks and fully break the grains, thereby providing hot-rolled rough tubes with fine grains and dense structure for subsequent finished steel pipes.
  • the inventors of the present application have conducted in-depth research on the effects of various alloying elements and microstructures on the resistance to sulfide stress cracking and stress corrosion cracking, as well as low-temperature toughness in corrosive environments containing CO 2 and H 2 S, based on 13Cr series oil casing.
  • the Ni element can increase the amount of retained austenite after quenching and tempering, especially the amount of retained austenite after tempering. Therefore, the Ni element can improve the low-temperature toughness.
  • the Cu element precipitates as fine Cu particles during tempering to improve the strength of the steel. Therefore, by adjusting the Ni content and the Cu content, an oil casing with both high strength and excellent low-temperature toughness can be obtained.
  • the oil casing provided by the present application has a high strength of more than 862MPa of yield stress and more than 920MPa of tensile strength. Under high temperature conditions of more than 150°C, the maximum corrosion rate is 0.0442mm/a, and no cracks are observed in the SSC resistance evaluation test.
  • the oil casing provided by the present application has good high-temperature SCC resistance and room-temperature SSC resistance in severe corrosive environments containing CO 2 , H 2 S, etc., and still has an absorption energy of more than 100J under low temperature conditions of less than -50°C, and has very good toughness, which can meet the needs of oil fields in harsh corrosive environments such as extreme cold and high temperature, and has broad market prospects.
  • the embodiment of the present application provides a corrosion-resistant and high-toughness petroleum casing, the chemical composition of which is: C 0.01%, Si 0.5%, Mn 0.05%, Cr 11.0%, Mo 2.6%, Cu 0.7%, Ni 3.7%, N 0.03%, Al 0.001%, B 0.002%, Ti 0.03%, La 0.07%, Ce 0.12%, P 0.013%, S 0.001%, and the rest is Fe and unavoidable impurities.
  • melt and casting process alloy and scrap steel are used as raw materials, and the raw materials are sequentially subjected to electric furnace smelting, ladle refining outside the furnace, vacuum degassing and arc continuous casting to obtain billets;
  • the refining time is 60 minutes.
  • the billet drawing speed is 2.8m/min
  • the vibration frequency of the crystallizer is 163min -1
  • the amplitude is 10.0mm
  • the negative slip rate is 30%.
  • Pipe making process heat the billet to 1220°C and keep it warm for 90min to obtain a hot billet, perform conical perforation on the hot billet at a temperature not lower than 1150°C to obtain a rough pipe with an outer diameter of 300mm, and roll the rough pipe on a continuous pipe rolling unit to make a rough pipe with an outer diameter of 264mm. After the rough pipe is slightly tension reduced and cooled on a walking cooling bed, a ⁇ 244.48mm ⁇ 11.99mm rolled steel pipe is obtained.
  • borax is sprayed into the rough tube and then nitrogen is blown.
  • the nitrogen blowing pressure is 3 bar and the borax blowing time is 5 seconds.
  • the feed volume of the continuous tube rolling unit is 62mm, the roller speed is 20rpm, and the air pressure is 5.2bar.
  • Heat treatment process heat the rolled steel pipe to 980°C, keep it for 15 minutes, air cool it to 80°C for quenching, and the cooling rate is 5°C/min; then heat it to 650°C, keep it for 20 minutes, air cool it for tempering, and obtain corrosion-resistant and high-toughness petroleum casing.
  • the microstructure of the obtained oil casing consists of 10% ferrite, 5.0% retained austenite and 85% tempered martensite with a volume fraction of 10%.
  • test piece for observing its microstructure was cut out from the prepared petroleum casing, and a cross section (i.e., observation surface) was ground on the surface of the test piece.
  • the ground observation surface was etched using a mixture of aqua regia and glycerol, and the ferrite volume fraction (vol.%) was measured in accordance with the non-metallic inclusion inspection standard JIS G 0555:2003.
  • a specimen for observing the microstructure of the prepared oil casing was cut out and ground, and the amount of retained austenite ( ⁇ phase) was measured by X-ray diffraction.
  • the X-ray integrated intensity of the (200) and (211) planes of the ferrite ( ⁇ phase) and the X-ray integrated intensity of the (200) plane, (220) plane and (311) plane of the retained austenite ( ⁇ phase) were measured, and the retained austenite volume fraction V ⁇ of each plane (6 in total) was calculated using the following formula:
  • V ⁇ 100/(1+(I ⁇ ⁇ R ⁇ )/(I ⁇ ⁇ R ⁇ ))
  • I ⁇ in the formula is the integrated intensity of the ⁇ phase
  • I ⁇ is the integrated intensity of the ⁇ phase
  • R ⁇ is the crystallographically calculated value of the ⁇ phase
  • R ⁇ is the crystallographically calculated value of the ⁇ phase.
  • the average value of the volume fraction V ⁇ of each surface is defined as the retained austenite volume fraction (vol.%).
  • volume fraction of tempered martensite 100% - (volume fraction of ferrite + volume fraction of retained austenite).
  • the tensile test was carried out according to the provisions of API-5CT, and samples were taken from the petroleum casing prepared in Example 1 by random sampling, and the yield strength and tensile strength thereof were analyzed.
  • the Charpy impact test was carried out at -60°C according to ASTM E23, and the absorbed energy (J) was measured.
  • the statistical results of the measured yield strength, tensile strength and absorbed energy are shown in Table 1.
  • the petroleum casing specimen prepared in Example 1 was placed in an autoclave for corrosion test.
  • the components of the corrosion solution were: Na + +K + 11350mg/L, Cl - 17495mg/L, HCO 3 - 1312mg/L, SO 4 2- 1663mg/L, the flow rate was 1.5m/s, the test temperature was 150°C, the test time was 168h, the total pressure of the gas was 30MPa, the partial pressure of CO 2 was 1MPa, and the measured corrosion rate was 0.0432mm/a.
  • the petroleum casing prepared in Example 1 was subjected to a sulfide stress cracking performance evaluation test.
  • the sulfide stress cracking corrosion test was conducted using the A method (standard tensile method).
  • the pH value of the test solution was 4.0
  • the partial pressure of H2S was 3 kPa
  • the immersion time was 720 h
  • the loading stress was 706.4 MPa
  • the tensile surface of the sample was observed using a microscope with a magnification of ⁇ 10, and no cracks were found.
  • the embodiment of the present application provides a corrosion-resistant and high-toughness petroleum casing, whose chemical composition is: C 0.03%, Si 0.1%, Mn 0.15%, Cr 13.0%, Mo 1.5%, Cu 1.6%, Ni 5.0%, N 0.04%, Al 0.04%, B 0.003%, Ti 0.05%, La 0.12%, Ce 0.24%, P 0.011%, S 0.0009%, W 0.7%, V 0.06%, and the rest is Fe and unavoidable impurities.
  • melt and casting process alloy and scrap steel are used as raw materials, and the raw materials are sequentially subjected to electric furnace smelting, ladle refining outside the furnace, vacuum degassing and arc continuous casting to obtain billets;
  • the ladle refining process outside the furnace, lime, fluorite and calcium carbide are added to the ladle for slag making, and the refining time is 65 minutes.
  • the billet drawing speed is 3.0m/min
  • the vibration frequency of the crystallizer is 170min -1
  • the amplitude is 10.2mm
  • the negative slip rate is 31%.
  • Pipe making process heat the billet to 1242°C and keep it warm for 100min to obtain a hot billet, perform conical perforation on the hot billet at not less than 1150°C to obtain a rough pipe with an outer diameter of 301mm, and roll the rough pipe on a continuous pipe rolling unit to make a rough pipe with an outer diameter of 265mm. After the rough pipe is slightly tension reduced and cooled on a walking cooling bed, a ⁇ 244.48mm ⁇ 11.99mm rolled steel pipe is obtained.
  • borax is sprayed into the rough tube and then nitrogen is blown.
  • the nitrogen blowing pressure is 5 bar and the borax blowing time is 8 seconds.
  • the feed volume of the continuous tube rolling unit is 83mm, the roller speed is 30rpm, and the air pressure is 5.8bar.
  • Heat treatment process heat the rolled steel pipe to 1000°C, keep it for 20min, air cool it to 90°C for quenching, and the cooling rate is 12°C/min; then heat it to 680°C, keep it for 30min, air cool it for tempering, and obtain corrosion-resistant and high-toughness petroleum casing.
  • the microstructure of the obtained oil casing consists of 15% ferrite, 20% retained austenite and 65% tempered martensite with a volume fraction of 15%.
  • the method for determining the volume fractions of ferrite, retained austenite and tempered martensite is the same as that in Example 1.
  • the tensile test was carried out according to the provisions of API-5CT, and samples were taken from the petroleum casing prepared in Example 2 by random sampling, and the yield strength and tensile strength thereof were analyzed.
  • the Charpy impact test was carried out at -50°C according to ASTM E23, and the absorbed energy (J) was measured.
  • the statistical results of the measured yield strength, tensile strength and absorbed energy are shown in Table 2.
  • the petroleum casing specimen prepared in Example 2 was placed in an autoclave for corrosion test.
  • the components of the corrosion solution were: Na + +K + 11350mg/L, Cl - 17495mg/L, HCO 3 - 1312mg/L, SO 4 2- 1663mg/L, the flow rate was 1.5m/s, the test temperature was 160°C, the test time was 168h, the total pressure of the gas was 30MPa, the partial pressure of CO 2 was 2MPa, and the measured corrosion rate was 0.0442mm/a.
  • the petroleum casing prepared in Example 2 was subjected to a sulfide stress cracking performance evaluation test.
  • the sulfide stress cracking corrosion test was conducted using the A method (standard tensile method).
  • the pH value of the test solution was 4.0
  • the partial pressure of H2S was 3 kPa
  • the immersion time was 720 h
  • the loading stress was 714.5 MPa.
  • the tensile surface of the sample was observed using a microscope with a magnification of ⁇ 10, and no cracks were found.
  • the embodiment of the present application provides a corrosion-resistant and high-toughness petroleum casing, whose chemical composition is: C 0.04%, Si 0.5%, Mn 0.25%, Cr 14.0%, Mo 2.6%, Cu 1.2%, Ni 4.8%, N 0.05%, Al 0.015%, B 0.004%, Ti 0.08%, La 0.34%, Ce 0.40%, P 0.01%, S 0.001%, Ca 0.0001%, Mg 0.0001%, and the rest is Fe and unavoidable impurities.
  • melt and casting process alloy and scrap steel are used as raw materials, and the raw materials are sequentially subjected to electric furnace smelting, ladle refining outside the furnace, vacuum degassing and arc continuous casting to obtain billets;
  • the refining time is 70 minutes.
  • the billet drawing speed is 3.2m/min
  • the vibration frequency of the crystallizer is 178min -1
  • the amplitude is 10.3mm
  • the negative slip rate is 32%.
  • Pipe making process heat the billet to 1260°C and keep it warm for 110min to obtain a hot billet, perform conical perforation on the hot billet at a temperature not lower than 1150°C to obtain a rough pipe with an outer diameter of 302mm, and roll the rough pipe on a continuous pipe rolling unit to make a rough pipe with an outer diameter of 266mm. After the rough pipe is slightly tension reduced and cooled on a walking cooling bed, a ⁇ 244.48mm ⁇ 11.99mm rolled steel pipe is obtained.
  • borax is sprayed into the rough tube and then nitrogen is blown.
  • the nitrogen blowing pressure is 8 bar and the borax blowing time is 12 seconds.
  • the feed volume of the continuous tube rolling unit is 113mm, the roller speed is 40rpm, and the air pressure is 6.3bar.
  • Heat treatment process heat the rolled steel pipe to 1030°C, keep it for 25min, water cool it to 90°C for quenching, and the cooling rate is 30°C/s; then heat it to 700°C, keep it for 40min, air cool it for tempering, and obtain corrosion-resistant and high-toughness petroleum casing.
  • the microstructure of the obtained oil casing consists of 15% ferrite, 10% retained austenite and 75% tempered martensite.
  • the method for determining the volume fractions of ferrite, retained austenite and tempered martensite is the same as that in Example 1.
  • the tensile test was carried out according to the provisions of API-5CT, and samples were taken from the petroleum casing prepared in Example 3 by random sampling, and the yield strength and tensile strength thereof were analyzed.
  • the Charpy impact test was carried out at -50°C according to ASTM E23, and the absorbed energy (J) was measured.
  • the statistical results of the measured yield strength, tensile strength and absorbed energy are shown in Table 3.
  • the petroleum casing specimen prepared in Example 3 was placed in an autoclave for corrosion test.
  • the components of the corrosion solution were: Na + +K + 11350mg/L, Cl - 17495mg/L, HCO 3 - 1312mg/L, SO 4 2- 1663mg/L, the flow rate was 1.5m/s, the test temperature was 160°C, the test time was 170h, the total pressure of the gas was 30MPa, the partial pressure of CO 2 was 2MPa, and the measured corrosion rate was 0.0412mm/a.
  • the petroleum casing prepared in Example 3 was subjected to a sulfide stress cracking performance evaluation test.
  • the sulfide stress cracking corrosion test was conducted using the A method (standard tensile method).
  • the pH value of the test solution was 3.0
  • the partial pressure of H2S was 4 kPa
  • the immersion time was 720 h
  • the loading stress was 810 MPa.
  • the tensile surface of the sample was observed using a microscope with a magnification of ⁇ 10, and no cracks were found.
  • Examples 1 to 3 the chemical composition ratio of the oil casing is appropriate, [Ni]/[Cu] is above 3.0, and 4360 ⁇ ([Ni]+[Cr]+[Mo])/[B] ⁇ 16200. Therefore, the microstructure of Examples 1 to 3 is composed of ferrite, retained austenite and tempered martensite, the volume fraction of ferrite is 10% to 20%, and the volume fraction of retained austenite is 5.0% to 20%.
  • the oil casing prepared by the present application through reasonable chemical composition and preparation process has a yield strength of more than 862MPa and a tensile strength of more than 920MPa.
  • the absorbed energy under low temperature environment is more than 100J, and the low temperature toughness is high.
  • the maximum corrosion rate is 0.0442mm/a, and the SCC resistance at high temperature is high; and no cracks are observed in the SSC resistance evaluation test, and the SSC resistance is high.
  • the comparative example provides a petroleum casing, the chemical composition of which is: C 0.01%, Si 0.5%, Mn 0.05%, Cr 11.0%, Mo 2.6%, Cu 1.6%, Ni 3.7%, N 0.03%, Al 0.001%, B 0.004%, Ti 0.03%, La 0.07%, Ce 0.012%, P 0.013%, S 0.001%, and the rest is Fe and inevitable impurities.
  • the microstructure of the petroleum casing obtained in Comparative Example 1 consists of 16% by volume of ferrite, 3% by volume of retained austenite, and 81% by volume of tempered martensite.
  • This comparative example provides a petroleum casing, whose chemical composition is the same as that of Example 1, and the smelting and casting steps and the pipe making steps in the preparation process are the same as those of Example 1, and only the heat treatment step is different from that of Example 1.
  • the heat treatment process in Comparative Example 2 is as follows: heating the rolled steel pipe to 750°C, maintaining it for 25 minutes, water cooling it to 90°C for quenching treatment, and the cooling rate is 30°C/s; then heating it to 630°C, maintaining it for 40 minutes, and air cooling it for tempering treatment to obtain the oil casing.
  • the microstructure of the petroleum casing obtained in Comparative Example 2 consists of 42% by volume of ferrite, 3% by volume of retained austenite, and 55% by volume of tempered martensite.
  • Comparative Example 2 has poor SCC resistance at high temperature; and cracks were observed in the SSC resistance evaluation test, and the SSC resistance is poor.

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 Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

La présente demande concerne un carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation. Le carter d'huile comprend les composants suivants en pourcentages en poids : 0,01 % ≤ C ≤ 0,04 %, 0,1 % ≤ Si ≤ 0,8 %, 0,05 % ≤ Mn ≤ 0,25 %, 11,0 % ≤ Cr ≤ 14,0 %, 1,5 % ≤ Mo ≤ 2,8 %, 0,5 % ≤ Cu ≤ 1,8 %, 3,7 % ≤ Ni ≤ 5,0 %, 0,03 % ≤ N ≤ 0,05 %, 0,001 % ≤ Al ≤ 0,05 %, 0,001 % ≤ B ≤ 0,005 %, 0,03 % ≤ Ti ≤ 0,08 %, 0,07 % ≤ La ≤ 0,35 %, 0,12 % ≤ Ce ≤ 0,40 %, P ≤ 0,013 %, S ≤ 0,001 %, le reste étant Fe et des impuretés inévitables ; les pourcentages en poids des composants satisfaisant aux expressions relationnelles suivantes : [Ni]/[Cu] ≥ 3,0, et 4 360 ≤ ([Ni] + [Cr] + [Mo])/[B] ≤ 16 200, [Ni] représentant le pourcentage en poids de la teneur en Ni dans le carter d'huile, [Cu] représentant le pourcentage en poids de la teneur en Cu dans le carter d'huile, [Cr] représentant le pourcentage en poids de la teneur en Cr dans le carter d'huile, [Mo] représentant le pourcentage en poids de la teneur en Mo dans le carter d'huile, et [B] représentant le pourcentage en poids de la teneur en B dans le carter d'huile ; et la structure métallographique du carter d'huile est composée d'un pourcentage en volume de 10 à 20 % de ferrite, d'un pourcentage en volume de 5,0 à 20 % d'austénite résiduelle, et du reste de martensite revenue. Le carter d'huile préparé dans la présente demande au moyen de composants chimiques rationnels et un processus de préparation présente une force élevée, une bonne résistance à la corrosion et une ténacité à basse température relativement élevée, et satisfait aux exigences du marché actuel.
PCT/CN2023/089649 2023-04-21 2023-04-21 Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation Pending WO2024113654A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PCT/CN2023/089649 WO2024113654A1 (fr) 2023-04-21 2023-04-21 Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation
US18/671,752 US20240352564A1 (en) 2023-04-21 2024-05-22 Corrosion-resistant and high toughness oil casing and method for manufacturing same

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/CN2023/089649 WO2024113654A1 (fr) 2023-04-21 2023-04-21 Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US18/671,752 Continuation US20240352564A1 (en) 2023-04-21 2024-05-22 Corrosion-resistant and high toughness oil casing and method for manufacturing same

Publications (1)

Publication Number Publication Date
WO2024113654A1 true WO2024113654A1 (fr) 2024-06-06

Family

ID=91322913

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2023/089649 Pending WO2024113654A1 (fr) 2023-04-21 2023-04-21 Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation

Country Status (2)

Country Link
US (1) US20240352564A1 (fr)
WO (1) WO2024113654A1 (fr)

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07150251A (ja) * 1993-11-26 1995-06-13 Nippon Steel Corp 熱間加工性および耐食性に優れた高靭性マルテンサイト系ステンレス鋼継目無鋼管の製造法
JP2017014543A (ja) * 2015-06-29 2017-01-19 新日鐵住金株式会社 油井用ステンレス鋼及び油井用ステンレス鋼管
US20170029912A1 (en) * 2014-02-28 2017-02-02 Vallourec Tubos Do Brasil S.A. Martensitic-ferritic stainless steel, manufactured product and process using the s
US20190376157A1 (en) * 2017-02-24 2019-12-12 Jfe Steel Corporation High-strength stainless steel seamless pipe for oil country tubular goods, and method for producing same
CN112176241A (zh) * 2020-09-23 2021-01-05 达力普石油专用管有限公司 一种低合金耐腐蚀油套管材料及其制备方法
WO2022181164A1 (fr) * 2021-02-26 2022-09-01 Ｊｆｅスチール株式会社 Tube sans soudure en acier inoxydable à haute résistance pour puits de pétrole et son procédé de production
CN115369313A (zh) * 2021-05-17 2022-11-22 宝山钢铁股份有限公司 一种高韧性抗腐蚀马氏体不锈钢油套管及其制造方法
US20230033540A1 (en) * 2019-12-24 2023-02-02 Jfe Steel Corporation High-strength seamless stainless steel pipe for oil well

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07150251A (ja) * 1993-11-26 1995-06-13 Nippon Steel Corp 熱間加工性および耐食性に優れた高靭性マルテンサイト系ステンレス鋼継目無鋼管の製造法
US20170029912A1 (en) * 2014-02-28 2017-02-02 Vallourec Tubos Do Brasil S.A. Martensitic-ferritic stainless steel, manufactured product and process using the s
JP2017014543A (ja) * 2015-06-29 2017-01-19 新日鐵住金株式会社 油井用ステンレス鋼及び油井用ステンレス鋼管
US20190376157A1 (en) * 2017-02-24 2019-12-12 Jfe Steel Corporation High-strength stainless steel seamless pipe for oil country tubular goods, and method for producing same
US20230033540A1 (en) * 2019-12-24 2023-02-02 Jfe Steel Corporation High-strength seamless stainless steel pipe for oil well
CN112176241A (zh) * 2020-09-23 2021-01-05 达力普石油专用管有限公司 一种低合金耐腐蚀油套管材料及其制备方法
WO2022181164A1 (fr) * 2021-02-26 2022-09-01 Ｊｆｅスチール株式会社 Tube sans soudure en acier inoxydable à haute résistance pour puits de pétrole et son procédé de production
CN115369313A (zh) * 2021-05-17 2022-11-22 宝山钢铁股份有限公司 一种高韧性抗腐蚀马氏体不锈钢油套管及其制造方法

Also Published As

Publication number Publication date
US20240352564A1 (en) 2024-10-24

Similar Documents

Publication Publication Date Title
WO2021179443A1 (fr) Tôle d'acier de récipient ultra-épaisse présentant une bonne ténacité au choc à basse température dans le noyau et procédé de fabrication associé
WO2023173803A1 (fr) Rail en acier résistant à la fatigue au contact de roulement pour chemin de fer voyageurs et fret mixte, et son procédé de production
CN115386808B (zh) 一种耐腐蚀油套管及其制备方法与应用
CN106435368A (zh) 一种抗延迟断裂超高强度钢板的生产方法
CN115305409B (zh) 一种5～60mm厚850MPa级高强度高韧性易焊接纳米钢及其制备方法
CN114107816A (zh) 一种低成本、高强韧性x65ms级抗酸管线钢热轧卷板及制备方法
CN112226676B (zh) 一种低成本l320ms/x46ms抗硫化氢腐蚀焊管用热轧钢带及其制造方法
CN111979492A (zh) 一种高强韧抗疲劳含钒铌高铁车轴钢及其热处理方法
CN117431467B (zh) 一种轴用非调质钢的生产方法
CN115992332A (zh) 一种抗酸管线钢及其制造方法
CN112063926A (zh) 一种高耐蚀抗疲劳含铌时速400公里高铁车轴用钢及其热处理方法
EP4394074A1 (fr) Plaque d'acier pour évaporateur d'unité d'énergie nucléaire avancée, et procédé de fabrication de plaque d'acier
CN116949365A (zh) 一种1000MPa级抗大线能量焊接水电站压力钢管用钢板及其生产方法
CN114875321B (zh) 一种先进核电机组蒸发器支承用钢板及其制造方法
CN116377349A (zh) 一种屈服强度800MPa级含Cu低合金高强钢及其制造方法
CN114164315B (zh) 一种60～120mm厚1000MPa级高强度高韧性易焊接纳米钢及其制备方法
CN119265487B (zh) 一种125KSi级高强耐腐蚀无缝钢管及其生产方法
CN116875886B (zh) 一种590MPa级抗H2S应力腐蚀油套管用卷板及其制造方法
CN114959459B (zh) 一种先进核电机组堆芯壳筒体用钢板及其制造方法
CN114058960B (zh) 一种25～60mm厚1000MPa级高强度高韧性易焊接纳米钢及其制备方法
WO2024113654A1 (fr) Carter d'huile à haute ténacité résistant à la corrosion et son procédé de préparation
CN118028705A (zh) 一种火车电缆槽道用450MPa级低成本高强度钢及其制备方法
CN117305704A (zh) 高强韧高裂纹尖端张开位移lng接收站用厚壁无缝钢管用钢及生产无缝钢管的方法
CN116479344A (zh) 一种屈服强度600MPa级含Cu低合金高强钢及其制造方法
CN114737109A (zh) 厚壁抗hic油气管道用x52直缝焊管用钢及制造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 23895820

Country of ref document: EP

Kind code of ref document: A1