WO2021227921A1 - 一种高强度抗挤毁石油套管及其制造方法 - Google Patents
一种高强度抗挤毁石油套管及其制造方法 Download PDFInfo
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- WO2021227921A1 WO2021227921A1 PCT/CN2021/091903 CN2021091903W WO2021227921A1 WO 2021227921 A1 WO2021227921 A1 WO 2021227921A1 CN 2021091903 W CN2021091903 W CN 2021091903W WO 2021227921 A1 WO2021227921 A1 WO 2021227921A1
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 40
- 238000001816 cooling Methods 0.000 claims abstract description 35
- 238000005496 tempering Methods 0.000 claims abstract description 17
- 238000005096 rolling process Methods 0.000 claims abstract description 15
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 12
- 238000009749 continuous casting Methods 0.000 claims abstract description 10
- 238000004513 sizing Methods 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 229910000831 Steel Inorganic materials 0.000 claims description 58
- 239000010959 steel Substances 0.000 claims description 58
- 239000003208 petroleum Substances 0.000 claims description 36
- 238000000034 method Methods 0.000 claims description 28
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- MKYBYDHXWVHEJW-UHFFFAOYSA-N N-[1-oxo-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propan-2-yl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(C(C)NC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 MKYBYDHXWVHEJW-UHFFFAOYSA-N 0.000 description 2
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- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B19/00—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work
- B21B19/02—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work the axes of the rollers being arranged essentially diagonally to the axis of the work, e.g. "cross" tube-rolling ; Diescher mills, Stiefel disc piercers or Stiefel rotary piercers
- B21B19/04—Rolling basic material of solid, i.e. non-hollow, structure; Piercing, e.g. rotary piercing mills
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B19/00—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work
- B21B19/02—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work the axes of the rollers being arranged essentially diagonally to the axis of the work, e.g. "cross" tube-rolling ; Diescher mills, Stiefel disc piercers or Stiefel rotary piercers
- B21B19/06—Rolling hollow basic material, e.g. Assel mills
- B21B19/10—Finishing, e.g. smoothing, sizing, reeling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D3/00—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D37/00—Tools as parts of machines covered by this subclass
- B21D37/16—Heating or cooling
-
- 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
- C21D1/06—Surface hardening
-
- 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
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D6/02—Hardening by precipitation
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
- C22C38/04—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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
-
- 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
Definitions
- the invention relates to a metal material and a manufacturing method thereof, in particular to a petroleum casing and a manufacturing method thereof.
- the publication number is JPH11-131189A
- the publication date is May 18, 1999
- the Japanese patent document titled "A method for manufacturing steel pipes” discloses a method for manufacturing steel pipes, which is proposed at 750-400°C Heating in the temperature range, and then rolling in the range of 20% or 60% deformation or more, to produce steel pipe products with a yield strength of 950Mpa or more and good toughness.
- rolling is more difficult; in addition, the low rolling temperature is prone to produce martensite structure, and this microstructure is a microstructure that is not allowed in petroleum casing products.
- the publication number is JP04059941A, and the publication date is February 26, 1992.
- the Japanese patent document entitled "A strong and tough high-strength TRIP steel” points out that the residual austenite (20%) in the steel matrix is controlled by a heat treatment process. -45%) and the ratio of upper bainite, the tensile strength can reach 120-160ksi.
- the design components mentioned in this patent are characterized by high carbon and high silicon. These two components can significantly increase the strength, but also reduce the toughness.
- the retained austenite will undergo structural transformation during the use of the oil pipe (deep well oil well pipe).
- the use temperature is above 120°C), which will reduce the toughness while increasing the strength.
- One of the objectives of the present invention is to provide a high-strength anti-collapsing petroleum casing.
- the high-strength anti-collapsing petroleum casing adds Cr and B instead of Mn in the chemical composition design to increase the hardenability of steel. Ti
- the embrittlement effect of N on the grain boundary is suppressed, so that the alloy addition cost of the petroleum casing is reduced, and quenching cracking is prevented.
- the high-strength anti-collapse oil casing has high strength, high toughness and high anti-extrusion performance.
- the present invention provides a high-strength anti-collapse oil casing, which contains the following chemical elements in the following mass percentages:
- the mass percentage of each chemical element is:
- the balance is Fe and other unavoidable impurities.
- C In the high-strength anti-collapse oil casing pipe of the present invention, C is a carbide forming element, which can effectively improve the strength of steel.
- the C mass percentage content is less than 0.08%, the hardenability of the steel will be reduced, thereby reducing the toughness of the steel.
- the C mass percentage content is higher than 0.18%, the segregation of the steel will be significantly worsened and easy to produce Quenching cracks. Therefore, in order to meet the high-strength requirement of the petroleum casing, the mass percentage content of the C element in the high-strength anti-collapsing petroleum casing of the present invention is controlled to be between 0.08-0.18%.
- the mass percentage of C can be controlled between 0.1-0.16% to improve the hardenability and inhibit quenching cracks.
- Si element can be dissolved in ferrite, which can increase the yield strength of steel, but the amount of Si element added in the steel should not be too high or too high The Si element will deteriorate the workability and toughness of the steel.
- the mass percentage of Si element in the steel is less than 0.1%, it will make the oil casing easy to oxidize. Therefore, the mass percentage of Si in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.1-0.4%.
- the mass percentage of Si can be controlled between 0.15-0.35% to improve the workability and toughness of the steel.
- Mn is an austenite-forming element, which can improve the hardenability of steel.
- Mn mass percentage content is less than 0.1%, the hardenability of the steel will be significantly reduced, and the proportion of martensite in the steel will be reduced, and thus This leads to a decrease in the toughness of steel.
- the Mn content in the steel should not be too high.
- the mass percentage of Mn in the high-strength anti-collapsing petroleum casing pipe of the present invention is controlled to be between 0.1-0.28%.
- the mass percentage of Mn can be controlled between 0.15-0.25% to improve hardenability and segregation.
- Cr In the high-strength collapse-resistant petroleum casing of the present invention, Cr is an element that strongly improves hardenability and a strong carbide forming element, which can precipitate carbides during tempering, thereby increasing the strength of steel.
- Cr element when the mass percentage of Cr element is higher than 0.8%, it is easy to precipitate coarse M 23 C 6 carbonization at the grain boundary It reduces the toughness of steel and is prone to quenching cracking; when the mass percentage of Cr element is less than 0.2%, the hardenability is insufficient. Therefore, the mass percentage of Cr in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.2-0.8%.
- the mass percentage of Cr can be controlled between 0.4-0.7% to further improve toughness and hardenability.
- Mo In the high-strength anti-collapsing petroleum casing pipe of the present invention, Mo mainly improves the strength and tempering stability of steel through carbides and solid solution strengthening forms. In the high-strength anti-collapsing oil casing steel system of the present invention, when the mass percentage of Mo element in the steel exceeds 0.6% or more, quenching cracks are prone to occur. However, it should be noted that once the Mo content is less than 0.2% by mass, the strength of the oil casing cannot meet the requirements of high strength. Therefore, the mass percentage of Mo in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.2-0.6%.
- the mass percentage of Mo can be controlled between 0.25-0.5% to further improve the strength and suppress quenching cracks.
- Nb is a fine-grained and precipitation-strengthening element in steel, which can make up for the decrease in strength caused by low carbon content.
- Nb element can form NbC precipitation It can effectively refine the austenite grains.
- the mass percentage of Nb in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.02-0.08%.
- the mass percentage of Nb can be controlled between 0.02-0.06% to further improve toughness and strength.
- V In the high-strength anti-collapse oil casing pipe of the present invention, V is a typical precipitation strengthening element, which can compensate for the decrease in strength caused by the decrease in carbon. It should be noted that when the V content in the steel is less than 0.01%, the strengthening effect of the V element is not obvious. When the V content in the steel is higher than 0.15%, it is easy to form coarse V(CN), thereby reducing the toughness of the steel. Therefore, the mass percentage of V in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.01-0.15%.
- the mass percentage of V can be controlled between 0.05-0.12% to further improve toughness and strength.
- Ti is a strong carbonitride forming element, which can significantly refine the austenite grains in the steel, and can compensate for the reduction in carbon content. The intensity of the decline.
- the Ti content in the steel is greater than 0.05%, coarse TiN is easily formed, thereby reducing the toughness of the steel. If the Ti content in the steel is less than 0.02% , The Ti element cannot fully react with N to form TiN, and the B in the steel will react with N to form the brittle phase of BN, resulting in a decrease in the toughness of the steel. Therefore, the mass percentage of Ti in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.02-0.05%.
- the mass percentage of Ti can be controlled between 0.02-0.04% to further improve toughness.
- B In the high-strength anti-collapse oil casing pipe of the present invention, B is also an element that can significantly improve the hardenability of steel. In steel grades with low C content, B element can solve the problem of reducing C content. The problem of poor hardenability comes.
- the high-strength anti-collapsing oil casing steel system of the present invention when the B content in the steel is less than 0.0015%, the effect of B in improving the hardenability of the steel is not significant.
- the mass percentage of B in the high-strength anti-collapse oil casing pipe of the present invention is controlled to be between 0.0015 and 0.005%.
- the mass percentage of B can be controlled between 0.0015 and 0.003% to further improve toughness and hardenability.
- Al In the high-strength collapse-resistant petroleum casing of the present invention, Al is a good deoxidizing and nitrogen-fixing element, which can effectively refine the crystal grains. In the high-strength collapse-resistant petroleum casing of the present invention, Al is controlled The mass percentage is between 0.01-0.05%.
- the mass percentage of Al can be controlled between 0.015 and 0.035% to further improve the deoxidation effect and suppress inclusions.
- other unavoidable impurities include S, P and N, and their content meets at least one of the following items: P ⁇ 0.015%, N ⁇ 0.008%, S ⁇ 0.003%.
- P, N and S are unavoidable impurity elements in steel, and the lower the content in the steel, the better.
- the mass percentage of each chemical element meets at least one of the following items:
- the microstructure is tempered sorbite.
- the economical low-yield ratio high-strength steel of the present invention its performance satisfies at least one of the following items: the yield strength is 758-965MPa, the tensile strength is ⁇ 862MPa, and the elongation is ⁇ 18. %, residual stress ⁇ 120MPa, 0 degree transverse Charpy impact energy ⁇ 80J, ⁇ 244.48*11.99mm specification collapse strength above 55MPa, exceeding the required value of API standard by more than 40%.
- another object of the present invention is to provide a method for manufacturing the above-mentioned high-strength anti-collapsing petroleum casing, which is specifically aimed at the manufacturing method of petroleum casing having the above-mentioned chemical element composition percentage.
- the manufacturing method has low production process cost, and the mass percentage of the chemical elements of the present invention is selected, combined with the manufacturing method, so that the high-strength anti-collapsing petroleum casing can meet the following properties at the same time: the yield strength is 758-965MPa, Tensile strength ⁇ 862MPa, elongation ⁇ 18%, residual stress ⁇ 120MPa, 0 degree transverse Charpy impact energy ⁇ 80J, ⁇ 244.48*11.99mm specification collapse strength above 55MPa, exceeding the required value of API standard by more than 40% , which can effectively meet the strength and collapse resistance requirements of deep wells and oil and gas fields for oil well pipes. That is, with the chemical composition ratio of the present invention combined with the petroleum casing manufacturing method of the present invention, the high-strength anti-collapsing petroleum casing can achieve the best performance.
- the present invention proposes a method for manufacturing a high-strength anti-collapse oil casing suitable for the above-mentioned chemical element ratio, which includes the following steps:
- the opening cooling temperature is between Ar3+30°C and Ar3+70°C (including Ar3+30°C and Ar3+70°C), where Ar3 refers to the starting temperature of ferrite transformation during cooling, further opening
- the cooling temperature is controlled at Ar3+50°C; the final cooling temperature is ⁇ 80°C; during the cooling process, only the outer surface of the casing is cooled, not the inner wall of the casing.
- the outer surface of the casing can be cooled by spraying water ; Control the cooling rate to 30-70°C/s;
- the existing manufacturing method usually adopts an off-line quenching + tempering process. Specifically, the hot-rolled tube is cooled to room temperature, and then reheated to the austenitizing temperature in the furnace, and water cooled to room temperature and then tempered.
- the method of producing high-strength anti-collapsing petroleum casing pipes according to the present invention uses hot rolling The residual heat of the steel pipe is quenched, that is, the residual heat of the steel pipe after hot rolling is used for quenching to room temperature and then tempering, eliminating the need for reheating.
- the manufacturing method of the present invention removes the offline quenching process, and by adopting a controlled cooling process, it can play a role equivalent to online quenching, and then cooperates with tempering heat treatment production, thereby significantly improving production efficiency, reducing production costs, reducing energy consumption, and realizing green production .
- the difference between the controlled cooling process and the conventional off-line quenching is that the controlled cooling process of the present invention only cools the outer surface of the sleeve during the cooling process, and does not cool the inner wall of the sleeve.
- This cooling method can significantly reduce the tube body Residual stress is conducive to the improvement of anti-collapse performance.
- it is usually necessary to add more alloying elements to improve the strengthening effect.
- the casing is directly controlled and cooled after hot rolling due to grain distortion. High energy is stored, and cracks are prone to occur during the controlled cooling process.
- the manufacturing method of the present invention needs to optimize the alloy type and content to prevent cracks and stress concentration in the high-strength anti-collapsing casing and ensure production The safety and the stability of quality.
- the Mn element in the high-strength anti-collapsing casing is prone to dendrite segregation, which leads to high hardness of the local alloy enrichment and easy to produce quenching cracks. Therefore, in order to solve the problem of insufficient hardenability of low-carbon steel, the addition of B element improves Hardenability, increase the martensite content after quenching, and form a more uniform tempered sorbite structure after tempering heat treatment to ensure the strength and toughness of the high-strength anti-collapse oil casing.
- the purpose of the present invention is to make the microstructure formed after tempering be tempered sorbite, of course, it will inevitably contain some other impurity microstructures.
- the goal of the present invention is to form tempered sorbite with a volume fraction close to 100%, and the volume fraction can reach 95% (including 95%) or more, and further control it to 98% (including 98%) or more.
- Other inevitable microstructures are, for example, retained austenite or ferrite, or a combination of retained austenite and ferrite.
- the volume fraction of these inevitable microstructure components is controlled within 5% (including 5%). , And further control within 2% (including 2%).
- the structure after quenching is mainly martensite and a small amount of retained austenite and/or ferrite, wherein the volume fraction of martensite is 95% and above, and the remaining retained austenite and/or iron The volume fraction of elemental tissue is 5% and below.
- the microstructure of tempered sorbite is more conducive to the high strength and good toughness of oil casing.
- the superheat of molten steel is controlled to be lower than 30° C., and the continuous casting drawing speed is 1.6-2.0 m/min to further improve segregation.
- step (2) the round billet is soaked in a furnace at 1260 to 1290°C, the piercing temperature is controlled to be 1180-1260°C, and the finishing rolling temperature is controlled to 900-980°C. °C, the sizing temperature after finishing rolling is 850-920°C, which further improves the stability of the microstructure after rolling.
- the tempering temperature is 500-600° C.
- the holding time is 50-80 min, which further improves the stability of performance.
- the hot straightening temperature is 400-500° C. to improve the straightness of the steel pipe.
- the high-strength anti-collapsing petroleum casing pipe and the manufacturing method thereof have the following advantages and beneficial effects:
- the yield strength of this high-strength anti-collapsing petroleum casing is 758-965MPa, tensile strength ⁇ 862MPa, elongation ⁇ 18%, residual stress ⁇ 120MPa, 0 degree transverse Charpy impact energy ⁇ 80J, at ⁇ 244.48*11.99
- its collapse resistance is above 55MPa, which exceeds the API standard requirement by more than 40%, which can meet the strength and collapse resistance requirements of deep wells and oil and gas fields for oil well pipes.
- the manufacturing method of the high-strength anti-collapse oil casing pipe of the present invention uses TMCP technology to make the steel material obtain higher strength and better toughness, its operation process is simple, the production cost is low, and it is easy to realize large-scale production. Manufacturing has good economic benefits.
- Table 1 lists the mass percentages of the chemical elements in the high-strength anti-collapsing petroleum casing pipes of Examples 1-6 and the casing pipes of Comparative Examples 1-4.
- Controlled cooling the opening cooling temperature is Ar3+30°C to Ar3+70°C, and the final cooling temperature is ⁇ 80°C; during the cooling process, only the outer surface of the casing is cooled, and the inner wall of the casing is not cooled, and the cooling is controlled.
- the speed is 30-70°C/s.
- the cooling device is a cooling water ring with controllable water volume and pressure, which sprays water on the outer surface of the tube.
- the initial cooling temperature is Ar3+50°C, and water cooling to ⁇ 80°C. This process is online quenching.
- the tempering temperature is 500-600°C, and the holding time is 50-80min.
- Hot straightening The temperature of hot straightening is 400-500°C.
- Table 2-1 and Table 2-2 list the specific process parameters of the manufacturing method of the high-strength anti-collapsing oil casing pipe of Example 1-6 and the casing pipe of Comparative Example 1-4.
- Table 3 lists the mechanical performance test results of the high-strength anti-collapse oil casing pipes of Examples 1-6 and the casing pipes of Comparative Examples 1-4. Among them, the yield strength, tensile strength, elongation, and transverse impact energy are in accordance with API SPEC5CT, and the collapse resistance and residual stress are in accordance with ISO/TR10400.
- Example 6 is within the preferred composition range, and its performance indicators are better.
- the C content in the chemical composition design of Comparative Example 1 exceeds the range defined by the technical solution of the present invention, and the open cooling temperature also exceeds the range defined by the technical solution of the present invention;
- Comparative Example 2 is in the chemical composition design. No B and Ti were added; Comparative Example 3 did not add V and Nb, and did not use the controlled cooling process after rolling.
- the off-line quenching + tempering process was adopted. The quenching temperature was 900°C, and the holding time was 40min.
- the tempering process parameters are in accordance with Table 2. -2 shows that the residual stress of the tube is relatively high; the Mn and Cr in the chemical composition design of Comparative Example 4 are beyond the scope of the technical solution of the present invention, and the final cooling temperature is beyond the technology of the present invention. The scope defined by the plan. At least one mechanical property of the casing in Comparative Examples 1-4 failed to meet the standards of high strength, high toughness and high collapse resistance petroleum casing.
- the yield strength of each embodiment of the present invention is ⁇ 758Mpa
- the tensile strength is ⁇ 862Mpa
- the transverse impact energy at 0°C is ⁇ 80J
- the elongation is ⁇ 18%
- the residual stress is ⁇ 120MPa
- the destruction strength is more than or equal to 55MPa, which exceeds the API standard by more than 50% (API standard value 36.5MPa), that is, the high-strength anti-collapse oil casing in Examples 1-6 has high strength, high toughness and high collapse resistance. It can be suitable for making oil pipes for deep well opening.
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Abstract
一种高强度抗挤毁石油套管及其制造方法,其含有质量百分比如下的化学元素:C:0.08-0.18%;Si:0.1-0.4%;Mn:0.1-0.28%;Cr:0.2-0.8%;Mo:0.2-0.6%;Nb:0.02-0.08%;V:0.01-0.15%;Ti:0.02-0.05%;B:0.0015-0.005%;Al:0.01-0.05%。其制造方法包括步骤:(1)冶炼和连铸;(2)穿孔、轧制和定径;(3)控制冷却:开冷温度为Ar3+50℃,终冷温度为≤80℃;冷却过程中仅对套管外表面进行冷却,而不对套管内壁进行冷却,控制冷却速度为30-70℃/s;(4)回火;(5)热矫直。
Description
本发明涉及一种金属材料及其制造方法,尤其涉及一种石油套管及其制造方法。
随着目前国内外油气资源开采深度和难度的增加,地层的流体场、压力场等都将发生很大的变化。油、水井套管的技术状况和受力状况也越来越复杂。我国现今约20%的油水井发生了套管损坏,有的地区甚至达到了50%以上。套管挤毁后,轻则影响原油正常生产,重则会使整口油井报废,由此会带来巨大的经济损失。因此为充分开发现有资源,提高采收率,减少不必要的损失,需要有效解决套管挤毁的问题。
目前,国内外在套管挤毁机理、影响因素、检测手段和高抗挤毁性能套管的研制与开发等方面做了大量的研究工作,开发出一系列不同钢级不同规格的高抗挤套管产品,目前已用于油田开发和生产,但是油田服役的工矿条件极其复杂,不同油田间差异也较大,因此对抗挤毁套管提出了更多的差异化需求。
公开号为JPH11-131189A,公开日为1999年5月18日,名称为“一种钢管的制造方法”的日本专利文献,公开了一种钢管的制造方法,该制造方法提出在750-400℃温度范围内加热,然后在20%或60%变形量以上的范围内进行轧制,生产获得屈服强度950Mpa以上、具有良好韧性的钢管产品。不过,由于此工艺技术的加热温度较低,轧制难度较大;此外,轧制温度较低容易产生马氏体组织,而这一微观组织是石油套管产品所不允许出现的微观组织。
公开号为JP04059941A,公开日为1992年2月26日,名称为“一种强韧的高强度TRIP钢”的日本专利文献,其指出通过热处理工艺来控制钢基体中残余奥氏体(20%-45%)和上贝氏体的比例,抗拉强度可以达到120-160ksi。此专利提到的设计成分特点是高碳和高硅,此两种成分可以显著提高强度,但也会降低韧性,同时残余奥氏体会在石油管使用过程中发生组织发生转变(深 井油井管使用温度120℃以上),提高强度的同时会降低韧性。
发明内容
本发明的目的之一在于提供一种高强度抗挤毁石油套管,该高强度抗挤毁石油套管在化学成分设计中添加了Cr、B替代Mn来增加钢的淬透性,采用Ti抑制了N对晶界的脆化作用,使得石油套管的合金添加成本降低,防止淬火开裂。该高强度抗挤毁石油套管具有高强度、高韧性和高抗挤性能,其屈服强度为758-965MPa,抗拉强度≥862MPa,延伸率≥18%,残余应力≤120MPa,0度横向夏比冲击功≥80J,在φ244.48*11.99mm典型规格下,抗挤毁强度在55MPa以上,超出API标准要求值40%以上,可以满足深井、油气田对油井管提出的强度和抗挤毁性能的要求。
为了实现上述目的,本发明提供了一种高强度抗挤毁石油套管,其含有质量百分比如下的下述化学元素:
C:0.08-0.18%;
Si:0.1-0.4%;
Mn:0.1-0.28%;
Cr:0.2-0.8%;
Mo:0.2-0.6%;
Nb:0.02-0.08%;
V:0.01-0.15%;
Ti:0.02-0.05%;
B:0.0015-0.005%;
Al:0.01-0.05%。
进一步地,在本发明所述的高强度抗挤毁石油套管中,其各化学元素质量百分比为:
C:0.08-0.18%;
Si:0.1-0.4%;
Mn:0.1-0.28%;
Cr:0.2-0.8%;
Mo:0.2-0.6%;
Nb:0.02-0.08%;
V:0.01-0.15%;
Ti:0.02-0.05%;
B:0.0015-0.005%;
Al:0.01-0.05%;
余量为Fe和其他不可避免的杂质。
在本发明所述的高强度抗挤毁石油套管中,各化学元素的设计原理如下所述:
C:在本发明所述的高强度抗挤毁石油套管中,C为碳化物形成元素,其可以有效提高钢的强度。当C质量百分比含量低于0.08%时,会使得钢的淬透性降低,从而降低钢的韧性,然而,当C质量百分比含量高于0.18%时,则会显著地恶化钢的偏析,易产生淬火裂纹。因此,为了达到石油套管的高强度的要求,在本发明所述的高强度抗挤毁石油套管中将C元素的质量百分比含量控制在0.08-0.18%之间。
在一些优选的实施方式中,C的质量百分比可以控制在0.1-0.16%之间,改善淬透性并抑制淬火裂纹。
Si:在本发明所述的高强度抗挤毁石油套管中,Si元素可以固溶于铁素体,其可以提高钢的屈服强度,但是钢中Si元素的添加量不宜过高,太高的Si元素会恶化钢的加工性和韧性,但是,需要注意的是,钢中Si元素质量百分含量低于0.1%时,会使得石油套管容易氧化。因此,在本发明所述的高强度抗挤毁石油套管中控制Si的质量百分比在0.1-0.4%之间。
在一些优选的实施方式中,Si的质量百分比可以控制在0.15-0.35%之间,改善钢的加工性和韧性。
Mn:在本发明所述的高强度抗挤毁石油套管中,Mn为奥氏体的形成元素,其可以提高钢的淬透性。在本发明所述的高强度抗挤毁石油套管的钢种体系中,当Mn质量百分比含量小于0.1%时,钢的淬透性会显著降低,钢中马氏体的比例会降低,进而导致钢的韧性降低。然而,需要说明的是,钢中Mn元素含量也不宜过高,当Mn质量百分比含量大于0.28%时,易产生成分偏析,产生淬火裂纹。因此,在本发明所述的高强度抗挤毁石油套管中控制Mn的质量百分比在0.1-0.28%之间。
在一些优选的实施方式中,Mn的质量百分比可以控制在0.15-0.25%之间,以提高淬透性和改善偏析。
Cr:在本发明所述的高强度抗挤毁石油套管中,Cr作为强烈提高淬透性元素和强碳化物形成元素,其可以在回火时析出碳化物,进而提高钢的强度。但需要说明的是,在本发明所述的高强度抗挤毁石油套管的钢种体系中,当Cr元素质量百分含量高于0.8%时,容易在晶界析出粗大M
23C
6碳化物,降低钢的韧性,并且容易产生淬火开裂;当Cr元素质量百分含量低于0.2%时,淬透性不足。因此,在本发明所述的高强度抗挤毁石油套管中控制Cr的质量百分比在0.2-0.8%之间。
在一些优选的实施方式中,Cr的质量百分比可以控制在0.4-0.7%之间,进一步改善韧性和淬透性。
Mo:在本发明所述的高强度抗挤毁石油套管中,Mo主要是通过碳化物及固溶强化形式来提高钢的强度及回火稳定性。在本发明所述的高强度抗挤毁石油套管的钢种体系中,当钢中添加Mo元素的质量百分比超过0.6%以上时,容易产生淬火裂纹。但是,需要说明的是,一旦Mo元素的质量百分比含量低于0.2%时,则石油套管的强度就无法达到高强度的要求。因此,在本发明所述的高强度抗挤毁石油套管中控制Mo的质量百分比在0.2-0.6%之间。
在一些优选的实施方式中,Mo的质量百分比可以控制在0.25-0.5%之间,进一步改善强度和抑制淬火裂纹。
Nb:在本发明所述的高强度抗挤毁石油套管中,Nb是钢中细晶和析出强化的元素,其可弥补因碳含量低而引起的强度下降,另外Nb元素可以形成NbC析出物,可以有效细化奥氏体晶粒。但需要注意的是,在本发明所述的高强度抗挤毁石油套管的钢种体系中,当钢中Nb含量小于0.02%时,其添加产生的作用并不明显,而当Nb含量大于0.08%时,则容易形成粗大的Nb(CN),从而降低钢的韧性。因此,在本发明所述的高强度抗挤毁石油套管中控制Nb的质量百分比在0.02-0.08%之间。
在一些优选的实施方式中,Nb的质量百分比可以控制在0.02-0.06%之间,进一步改善韧性和提高强度。
V:在本发明所述的高强度抗挤毁石油套管中,V是典型的析出强化元素,可弥补因碳降低而引起的强度的下降。需要注意的是,当钢中V含量小于0.01% 时,V元素的强化效果不明显,当钢中V含量高于0.15%时,则容易形成粗大的V(CN),从而降低钢的韧性。因此,在本发明所述的高强度抗挤毁石油套管中控制V的质量百分比在0.01-0.15%之间。
在一些优选的实施方式中,V的质量百分比可以控制在0.05-0.12%之间,进一步改善韧性和提高强度。
Ti:在本发明所述的高强度抗挤毁石油套管中,Ti是强碳氮化物的形成元素,其能够显著地细化钢中奥氏体晶粒,可以弥补因碳含量降低而引起的强度下降。在本发明所述的高强度抗挤毁石油套管的钢种体系中,若钢中Ti含量大于0.05%,容易形成粗大的TiN,从而降低钢的韧性,若钢中Ti含量小于0.02%时,则Ti元素不能充分地与N反应形成TiN,钢中的B就会与N反应形成BN的脆性相,从而导致钢的韧性降低。因此,在本发明所述的高强度抗挤毁石油套管中控制Ti的质量百分比在0.02-0.05%之间。
在一些优选的实施方式中,Ti的质量百分比可以控制在0.02-0.04%之间,进一步改善韧性。
B:在本发明所述的高强度抗挤毁石油套管中,B也是可以显著提高钢的淬透性的元素,在C含量低的钢种中,B元素可以解决因C含量降低而带来的淬透性差的问题。然而,在本发明所述的高强度抗挤毁石油套管的钢种体系中,当钢中B含量低于0.0015%时,B提高钢的淬透性的作用并不显著,而若钢中B含量过高,高于0.005%时,则易于形成BN脆性相,从而降低钢的韧性。因此,在本发明所述的高强度抗挤毁石油套管中控制B的质量百分比在0.0015-0.005%之间。
在一些优选的实施方式中,B的质量百分比可以控制为0.0015-0.003%之间,进一步改善韧性和淬透性。
Al:在本发明所述的高强度抗挤毁石油套管中,Al是良好的脱氧固氮元素,可以有效细化晶粒,在本发明所述的高强度抗挤毁石油套管中控制Al的质量百分比在0.01-0.05%之间。
在一些优选的实施方式中,Al的质量百分比可以控制为0.015-0.035%之间,进一步改善脱氧效果和抑制夹杂物。
进一步地,在本发明所述的高强度抗挤毁石油套管中,其他不可避免的杂质包括S、P和N,其含量满足下列各项的至少其中之一:P≤0.015%,N≤ 0.008%,S≤0.003%。
上述技术方案中,在本发明所述的高强度抗挤毁石油套管中,P、N和S均是钢中不可避免的杂质元素,其在钢中的含量越低越好。
进一步地,在本发明所述的高强度抗挤毁石油套管中,其各化学元素质量百分含量满足下述各项的至少其中之一:
C:0.1-0.16%;
Si:0.15-0.35%;
Mn:0.15-0.25%;
Cr:0.4-0.7%;
Mo:0.25-0.5%;
Nb:0.02-0.06%;
V:0.05-0.12%
Ti:0.02-0.04%;
B:0.0015-0.003%;
Al:0.015-0.035%。
进一步地,在本发明所述的高强度抗挤毁石油套管中,其微观组织的回火索氏体。
进一步地,在本发明所述的经济型低屈强比高强度钢中,其性能满足下述各项的至少其中之一:屈服强度为758-965MPa,抗拉强度≥862MPa,延伸率≥18%,残余应力≤120MPa,0度横向夏比冲击功≥80J,φ244.48*11.99mm规格抗挤毁强度在55MPa以上,超出API标准要求值40%以上。
相应地,本发明的另一目的在于提供一种上述的高强度抗挤毁石油套管的制造方法,该制造方法是专门针对具有上述化学元素成分百分含量的石油套管的制造方法。该制造方法生产工艺成本较低,选用本发明的化学元素的质量百分比,再结合该制造方法,从而制得的高强度抗挤毁石油套管能够同时满足以下性能:屈服强度为758-965MPa,抗拉强度≥862MPa,延伸率≥18%,残余应力≤120MPa,0度横向夏比冲击功≥80J,φ244.48*11.99mm规格抗挤毁强度在55MPa以上,超出API标准要求值40%以上,可以有效满足深井、油气田对油井管提出的强度和抗挤毁性能的要求。即含有本发明的化学成分配比结合本发明的石油套管的制造方法,制得的高强度抗挤毁石油套管能够达到最佳 的性能。
为了实现上述目的,本发明提出了适用于上述化学元素配比的高强度抗挤毁石油套管的制造方法,包括步骤:
(1)冶炼和连铸;
(2)穿孔、轧制和定径;
(3)控制冷却:开冷温度为Ar3+30℃到Ar3+70℃之间(包含Ar3+30℃和Ar3+70℃),其中Ar3是指冷却时铁素体转变的开始温度,进一步开冷温度控制在Ar3+50℃;终冷温度为≤80℃;冷却过程中仅对套管外表面进行冷却,而不对套管内壁进行冷却,例如可对套管的外表面进行喷水冷却处理;控制冷却速度为30-70℃/s;
(4)回火;
(5)热矫直。
现有的制造方法通常采用离线淬火+回火的工艺。具体来说,就是将热轧管冷却到室温,然后在炉子里重新加热到奥氏体化温度,水冷至室温再回火。在本发明所述的制造方法中,不同于常规高强度抗挤毁套管采用的离线淬火+回火的热处理工艺,本发明所述高强度抗挤毁石油套管的制造方法利用热轧后钢管余热进行淬火,即利用热轧后钢管余热进行淬火至室温,然后进行回火,省去了重新加热工序。本发明的制造方法去除离线淬火工序,通过采用控制冷却过程,可以起到等同于在线淬火的作用,再配合回火热处理生产,从而可以显著提高生产效率降低生产成本,降低能耗,实现绿色生产。
需要说明的是,控制冷却工艺与常规离线淬火区别在于:本发明控制冷却工艺在冷却过程中仅对套管外表面进行冷却,而不对套管内壁进行冷却,这样的冷却方式可以显著降低管体残余应力,有利于抗挤毁性能的提升。但是,需要注意的是,为保证获得的高强度抗挤毁套管具有较高的强度,通常需要加入较多的合金元素提高强化效果,套管在热轧后直接控制冷却时因晶粒畸变储存了较高的能量,在控制冷却过程中易发生开裂,因此本发明所述的制造方法需要对合金种类及含量进行优化设计,防止高强度抗挤毁套管产生裂纹和应力集中,保证生产的安全和质量的稳定。高强度抗挤毁套管中的Mn元素易产生枝晶偏析,导致局部合金富集硬度偏高,易产生淬火裂纹,因此为解决低碳钢种 的淬透性不足的问题,加入B元素提高淬透性,提高淬火后马氏体含量,回火热处理后形成较均匀的回火索氏体组织,保证高强度抗挤毁石油套管的强度和韧性。本发明的目的在于让回火后形成的微观组织为回火索氏体,当然其中不可避免的会含有一些其它杂质微观组织。本发明的目标希望能形成体积分数接近100%的回火索氏体,进一步体积分数能够达到95%(包含95%)以上即可,更进一步控制在98%(包含98%)以上。其中不可避免的其它微观组织例如是残余奥氏体或铁素体,或者残余奥氏体和铁素体的组合,这些不可避免的微观组织成分的体积分数控制在5%(包含5%)以内,进一步控制在2%(包含2%)以内。相应地,淬火后组织主要是马氏体和少量的残余奥氏体和/或铁素体组织,其中马氏体组织的体积分数在95%及以上,剩余的残余奥氏体和/或铁素体组织的体积分数在5%及以下。回火索氏体的微观组织更有利于石油套管既具有高的强度也能保证好的韧性。
进一步地,在本发明所述的制造方法中,在步骤(1)的连铸步骤中,控制钢水过热度低于30℃,连铸拉速为1.6-2.0m/min,进一步改善偏析。
进一步地,在本发明所述的制造方法中,在步骤(2)中,圆坯在1260-1290℃的炉内均热,控制穿孔温度为1180-1260℃,控制终轧温度为900-980℃,终轧后的定径温度为850-920℃,进一步提高轧制后微观组织的稳定性。
进一步地,在本发明所述的制造方法中,在步骤(4)中,回火温度为500-600℃,保温时间50-80min,进一步提高性能的稳定性。
进一步地,在本发明所述的制造方法中,在步骤(4)中,热矫直温度为400-500℃,提高钢管的直度。
本发明所述的高强度抗挤毁石油套管及其制造方法相较于现有技术具有如下所述的优点以及有益效果:
本发明所述的高强度抗挤毁石油套管,在化学成分设计中添加了Cr、B替代Mn来增加钢的淬透性,采用Ti抑制了N对晶界的脆化作用,使得石油套管的合金添加成本降低,有效防止淬火开裂。该高强度抗挤毁石油套管的屈服强度为758-965MPa,抗拉强度≥862MPa,延伸率≥18%,残余应力≤120MPa,0度横向夏比冲击功≥80J,在φ244.48*11.99mm的规格下,其抗挤毁强度在55MPa以上,超出API标准要求值40%以上,可以满足深井、油气田对油井管提出的强度和抗挤毁性能的要求。
此外,本发明所述的高强度抗挤毁石油套管的制造方法通过采用TMCP技术使得钢材获得较高的强度和较好的韧性,其操作过程简单,生产成本低,易于实现大规模的生产制造,具有良好的经济效益。
下面将结合具体的实施例对本发明所述的高强度抗挤毁石油套管及其制造方法做进一步的解释和说明,然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-6和对比例1-4
表1列出了实施例1-6的高强度抗挤毁石油套管和对比例1-4的套管中各化学元素质量百分比。
表1.(wt%,余量为Fe和其他除了P、S、N以外的不可避免的杂质)
本发明所述实施例1-6的高强度抗挤毁石油套管和对比例1-4的套管均采用以下步骤制得:
(1)冶炼和连铸:其中在连铸步骤中,控制钢水过热度低于30℃,连铸 拉速为1.6-2.0m/min。
(2)穿孔、轧制和定径:圆坯在1260-1290℃的炉内均热,控制穿孔温度为1180-1260℃,控制终轧温度为900-980℃,终轧后的定径温度为850-920℃。
(3)控制冷却:开冷温度为Ar3+30℃到Ar3+70℃,终冷温度为≤80℃;冷却过程中仅对套管外表面进行冷却,而不对套管内壁进行冷却,控制冷却速度为30-70℃/s。具体为:热轧管定径后保持高温状态进入控制冷却工序,冷却设备为可控水量和压力的冷却水环,对管体外表进行喷水冷却。起始冷却温度是Ar3+50℃,水冷至≤80℃,此过程为在线淬火。
(4)回火:回火温度为500-600℃,保温时间50-80min。
(5)热矫直:热矫直温度为400-500℃。
表2-1和表2-2列出了实施例1-6的高强度抗挤毁石油套管和对比例1-4的套管的制造方法的具体工艺参数。
表2-1.
表2-2.
将上述得到的实施例1-6的高强度抗挤毁石油套管和对比例1-4的套管制成φ244.48*11.99mm规格,并进行各项性能测试,所得测试结果列于表3中。
表3列出了实施例1-6的高强度抗挤毁石油套管和对比例1-4的套管的力学性能测试结果。其中,屈服强度、抗拉强度、延伸率、横向冲击功按API SPEC5CT,抗挤毁强度、残余应力按ISO/TR10400。
表3.
结合表1和表3,实施例1-6的高强度抗挤毁石油套管的化学成分和相关工艺参数均满足本发明设计规范控制要求。实施例6的成分在优选成分范围内,其性能指标较好。对比例1在化学成分设计中的C含量超出了本发明的技术方案所限定的范围,并且开冷温度也超出了本发明的技术方案所限定的范围;对比例2在化学成分设计中的中未添加B和Ti;对比例3未加V和Nb,在轧制后未采用控制冷却工艺,采用离线淬火+回火工艺,淬火温度900℃,保温时间为40min,回火工艺参数按表2-2所示,其制得的管体的残余应力较高;对比例4在化学成分设计中的Mn和Cr超出了本发明的技术方案所限定的范围,终冷温度超出了本发明的技术方案所限定的范围。对比例1-4中的套管的至少一项力学性能未能达到高强度、高韧性和高抗挤性能石油套管的标准。
由表3可看出,本发明各实施例的屈服强度均≥758Mpa,抗拉强度均 ≥862Mpa,并且0℃横向冲击功均≥80J,延伸率均≥18%,残余应力≤120MPa,抗挤毁强度≥55MPa,超出API标准50%以上(API标准值36.5MPa),即实施例1-6中的高强度抗挤毁石油套管均具有高强度、高韧性和高抗挤毁性能,其能够适合制成深井开采用的石油管。
需要注意的是,以上所列举实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例,随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的,均应属于本发明的保护范围。
Claims (11)
- 一种高强度抗挤毁石油套管,其特征在于,其含有质量百分比如下的下述化学元素:C:0.08-0.18%;Si:0.1-0.4%;Mn:0.1-0.28%;Cr:0.2-0.8%;Mo:0.2-0.6%;Nb:0.02-0.08%;V:0.01-0.15%;Ti:0.02-0.05%;B:0.0015-0.005%;Al:0.01-0.05%。
- 如权利要求1所述的高强度抗挤毁石油套管,其特征在于,其各化学元素质量百分比为:C:0.08-0.18%;Si:0.1-0.4%;Mn:0.1-0.28%;Cr:0.2-0.8%;Mo:0.2-0.6%;Nb:0.02-0.08%;V:0.01-0.15%;Ti:0.02-0.05%;B:0.0015-0.005%;Al:0.01-0.05%;余量为Fe和其他不可避免的杂质。
- 如权利要求2所述的高强度抗挤毁石油套管,其特征在于,其他不可避免的杂质包括P、S和N,其含量满足下列各项的至少其中之一:P≤0.015%,0<N≤0.008%,S≤0.003%。
- 如权利要求1或2所述的高强度抗挤毁石油套管,其特征在于,其各化学元素质量百分含量满足下述各项的至少其中之一:C:0.1-0.16%;Si:0.15-0.35%;Mn:0.15-0.25%;Cr:0.4-0.7%;Mo:0.25-0.5%;Nb:0.02-0.06%;V:0.05-0.12%Ti:0.02-0.04%;B:0.0015-0.003%;Al:0.015-0.035%。
- 如权利要求1或2所述的高强度抗挤毁石油套管,其特征在于,其微观组织为回火索氏体。
- 如权利要求1或2所述的高强度抗挤毁石油套管,其特征在于,其性能满足下述各项的至少其中之一:屈服强度为758-965MPa,抗拉强度≥862MPa,延伸率≥18%,残余应力≤120MPa,0度横向夏比冲击功≥80J,φ244.48*11.99mm规格抗挤毁强度在55MPa以上,超出API标准要求值40%以上。
- 一种如权利要求1-6中任意一项所述的高强度抗挤毁石油套管的制造方法,其特征在于,包括步骤:(1)冶炼和连铸;(2)穿孔、轧制和定径;(3)控制冷却:开冷温度为Ar3+30℃到Ar3+70℃,终冷温度为≤80℃;冷却过程中仅对套管外表面进行冷却,而不对套管内壁进行冷却,控制冷却速度为30-70℃/s;(4)回火;(5)热矫直。
- 如权利要求7所述的制造方法,其特征在于,在步骤(1)的连铸步骤中,控制钢水过热度低于30℃,连铸拉速为1.6-2.0m/min。
- 如权利要求7所述的制造方法,其特征在于,在步骤(2)中,圆坯在1260-1290℃的炉内均热,控制穿孔温度为1180-1260℃,控制终轧温度为900-980℃,终轧后的定径温度为850-920℃。
- 如权利要求7所述的制造方法,其特征在于,在步骤(4)中,回火温度为500-600℃,保温时间50-80min。
- 如权利要求7所述的制造方法,其特征在于,在步骤(4)中,热矫直温度为400-500℃。
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- 2021-05-06 US US17/922,548 patent/US20230211396A1/en active Pending
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CN113637892A (zh) | 2021-11-12 |
US20230211396A1 (en) | 2023-07-06 |
JP7458685B2 (ja) | 2024-04-01 |
EP4130327A4 (en) | 2023-09-20 |
EP4130327A1 (en) | 2023-02-08 |
JP2023523623A (ja) | 2023-06-06 |
CN113637892B (zh) | 2022-12-16 |
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