CN114959512B - Steel for high-strength welded sleeve for thickened oil thermal recovery well, production method of steel and high-strength welded sleeve heat treatment method for thickened oil thermal recovery well - Google Patents
Steel for high-strength welded sleeve for thickened oil thermal recovery well, production method of steel and high-strength welded sleeve heat treatment method for thickened oil thermal recovery well Download PDFInfo
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
- C21D2211/002—Bainite
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- 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
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- 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
- C21D2211/009—Pearlite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The application provides steel for a high-strength welding sleeve for a thickened oil thermal production well, a production method thereof and a heat treatment method for the high-strength welding sleeve for the thickened oil thermal production well, which comprise the following components: c:0.14% -0.20%, si: less than or equal to 0.30 percent, mn:0.80% -1.20%, P: less than or equal to 0.015 percent, S: less than or equal to 0.0050 percent, mo:0.10% -0.30%, V:0.03-0.06%, ti:0.01-0.03%, cr:0.80-1.20%; als:0.020-0.035%, N: less than or equal to 0.0040 percent; the balance of Fe and unavoidable impurities. The hot rolled coil is obtained through reasonable component design, smelting and rolling processes, and the heat treatment process enables the product to have good strong plasticity, higher high-temperature mechanical property and creep property.
Description
Technical Field
The application belongs to hot continuous rolling steel coils, and particularly relates to steel for a high-strength welding sleeve for a thickened oil thermal production well and a production method thereof, and a high-strength welding sleeve heat treatment method for the thickened oil thermal production well.
Background
The thick oil is oil reservoir with high viscosity, and is mainly distributed in Canada, america, russia and China, and has total weight of 4000-6000×10 8 m 3 The domestic thick oil resources are mainly distributed in Liaohe, victory, henan and Xinjiang, and the accumulated and ascertained thick oil reserves are about 20 multiplied by 10 8 t. At present, thermal oil recovery is the main method of heavy oil recovery, steam huff and puff is the most main method of thermal oil recovery, and steam is injected from a steam injection pipe at 300-350 ℃ to stay at the top of an oil reservoir and preheat the oil reservoir, so that the viscosity of the oil reservoir is reduced, and the oil reservoir is produced after being diffused.
In the steam huff and puff exploitation process, the steel pipe is subjected to great pressure when high-temperature and high-pressure steam is injected, and when oil extraction is stopped, the steel pipe is subjected to great tensile stress due to the fact that the temperature-reducing steel pipe is subjected to repeated tensile-compressive stress in the high-temperature environment, so that the steel pipe is extremely easy to damage. Steam injection is used as a main way for improving recovery efficiency of a thick oil well, and the average temperature of steam injection is about 320 ℃ and is higher than 350 ℃. Because of the injection of high-temperature steam, the sleeve is subjected to compression load caused by thermal stress and alternating load of compression and extension caused by reciprocating gas injection and stop injection besides being subjected to loads such as stretching, internal pressure and external extrusion. Therefore, there is a need to develop a new casing product for heavy oil well production that has high room temperature strength, good plasticity, less high temperature strength drop, and low high temperature creep rate.
The patent publication No. CN 103131947A discloses a high-performance low-carbon microalloy steel SEW expansion sleeve and a manufacturing method thereof, wherein the expansion sleeve comprises the following chemical components in percentage by mass: 0.10-0.25% of C, 0.12-0.30% of Si, 0.60-1.50% of Mn, less than or equal to 0.010% of P, less than or equal to 0.005% of S, 0.05-0.5% of Nb+V+Ti, and the balance of Fe and unavoidable impurities, wherein the low-carbon microalloyed steel TMCP hot rolled coil controlled by high dimensional accuracy is used as a raw material, and HFW welded pipes are subjected to pipe-integrating treatment by using thermomechanical rolling, thermal tension reducing and a whole pipe special heat treatment process, so that weld joint tissue optimization is realized, and the related requirements of expansion sleeves are met; however, the low-carbon microalloy is used as the sleeve material, so that the plastic toughness of the material is obviously reduced after a certain amount of cold plastic deformation, particularly the high-temperature strength is obviously reduced, and the severe environment of a thick oil thermal production well cannot be satisfied.
The patent with application number 00100635.5 published in 3/21/2001 discloses a high-strength petroleum casing pipe for a super heavy oil thermal production well and a production method thereof, which are mainly manufactured by adopting medium carbon Cr-Mo steel through tempering heat treatment, and the defect is that the product is only limited to be used at 300 ℃, and no corresponding description is made on working conditions which are frequently appeared and are more than 350 ℃.
Disclosure of Invention
The application aims to provide steel for a high-strength welding sleeve for a thickened oil thermal recovery well and a manufacturing method thereof, which have low cost of alloy elements and excellent initial welding performance.
The application also provides a heat treatment method for producing the high-strength welding sleeve for the heavy oil thermal recovery well by utilizing the steel for the high-strength welding sleeve for the heavy oil thermal recovery well, wherein the yield strength of the produced steel pipe is 800-850MPa, the tensile strength is 900-960MPa, the Charpy impact energy Akv at the transverse temperature of-10 ℃ is more than or equal to 100J, and the elongation A is more than or equal to 13%; under the condition of 350 ℃, the typical yield strength is 720-750MPa, the tensile strength is 820-850MPa, and the elongation A is 12-15%; under the condition of 400 ℃, the typical yield strength is 670-710MPa, the tensile strength is 750-800MPa, and the elongation A is9-12%. The strength of the exemplary embodiment is reduced by 15% or less at 350 c compared to normal temperature. Creep rate is less than or equal to 3.79×10 under the conditions of 400 ℃ and 0.8 stress coefficient (552 MPa) -6 ％·s -1 。
The specific technical scheme of the application is as follows:
the steel for the high-strength welding sleeve for the thick oil thermal production well comprises the following components in percentage by mass:
c:0.14% -0.20%, si: less than or equal to 0.30 percent, mn:0.80% -1.20%, P: less than or equal to 0.015 percent, S: less than or equal to 0.0050 percent, mo:0.10% -0.30%, V:0.03-0.06%, ti:0.01-0.03%, cr:0.80-1.20%; als:0.020-0.035%, N: less than or equal to 0.0040 percent; the balance of Fe and unavoidable impurities.
The steel composition for the high-strength welding sleeve for the thick oil thermal production well meets the following conditions: c/mo=0.5 to 2.0, C/cr=0.12 to 0.17; the main elements Cr and Mo for improving heat resistance should be kept in a certain proportion with the element C so as to ensure the high temperature performance of the steel.
The steel for the high-strength welding sleeve for the thick oil thermal production well comprises ferrite, pearlite and a small amount of bainitic structure, wherein the area of the ferrite is about 60-80%, the area of the pearlite is about 20-40%, the bainitic is less than or equal to 5%, the grain size grade is 8.0-10.0, and the higher ferrite is used for obtaining lower strength of an original coil so as to facilitate easy forming in the welding process.
The application provides a production method of steel for a high-strength welding sleeve for a thick oil thermal production well, which comprises the following steps: molten iron pretreatment, converter smelting, LF refining, RH refining, continuous casting, casting blank slow cooling, heating, rolling, laminar cooling and coiling to obtain hot rolled coils with the thickness of 8-12 mm.
The production process specifically comprises the following steps:
the molten iron pretreatment is specifically as follows: the front slag skimming and the rear slag skimming are required to be carried out, and the desulfurized molten iron [ S ] is controlled to be less than or equal to 0.0050%;
the converter smelting specifically comprises the following steps: less than or equal to 0.015 percent of [ P ], [ S ] < 0.0050 percent; adding most of alloy in the tapping process to enable the molten steel components to reach or approach the inner control lower limit; the slag blocking operation is performed, so that the phosphorous is prevented from being removed;
the LF furnace refining specifically comprises: fully reducing ladle top slag, and adjusting components to a target value or close to the target value;
the RH furnace refining specifically comprises the following steps: adjusting all components to target values; vacuum treatment is carried out for more than 12min, so that the [ H ] content of molten steel is less than or equal to 1.2ppm, and the [ Ca ] content of the end point is controlled to be 15-30ppm.
The continuous casting specifically comprises the following steps: baking the middle ladle for more than or equal to 24 hours; the target temperature of the tundish is controlled to be 10-25 ℃ above the liquidus temperature; finally casting into a casting blank with the thickness of 230 mm.
The casting blank slow cooling specifically comprises the following steps: stacking and slowly cooling the casting blank for more than 48 hours;
the heating is specifically as follows: the tapping temperature of the initial continuous casting slab is 1170-1210 ℃, and the main purpose is to ensure complete austenitization of the material and make the alloy elements fully solid-solved.
The rolling is specifically as follows: the method adopts two stages of rolling, wherein the rolling temperature is controlled to be 1000-1060 ℃ in a recrystallization area, austenite grains are obviously refined through repeated deformation and recrystallization, the rolling temperature is controlled to be 900-1000 ℃ in an unrecrystallized area, deformation and phase transformation are carried out simultaneously, the austenite grains are elongated in the stage, a slip zone is generated simultaneously, the increase of austenite grain boundaries and the occurrence of the slip zone provide favorable conditions for ferrite nucleation, and fine-grain ferrite is obtained. In order to ensure that the coil has excellent initial welding performance, the rolled coil is subjected to laminar cooling, the cooling end temperature is 650-750 ℃, and coiling is performed at the temperature.
The application provides a heat treatment method for producing a high-strength welded sleeve for a thickened oil thermal recovery well by utilizing the steel for the high-strength welded sleeve for the thickened oil thermal recovery well, which specifically comprises the following steps: quenching and tempering are carried out.
The quenching specifically comprises the following steps: the temperature is 920+/-20 ℃, the heat preservation time is 40+/-5 min, and the water quenching is carried out;
the tempering specifically comprises the following steps: the temperature is 550+/-20 ℃, the heat preservation time is 80+/-5 min, and the air cooling is carried out after the heat preservation.
The reasonable component design of the application is the primary basis for obtaining the product, and in the application:
c: the C element mainly improves the hardenability, the strength can be improved by carbide formed by the C element and other alloy elements in the steel, the C content is lower than 0.14%, the hardenability and strength of the steel are difficult to ensure, but the C element can damage the toughness of the steel, and the toughness is difficult to ensure when the C element is higher than 0.20%, so that the C content is controlled to be 0.14% -0.20%.
Si: silicon mainly plays a deoxidizing role here, but is largely detrimental to toughness, so that it is limited to 0.30% or less.
Mn: manganese can improve hardenability, is combined with S element in steel to form MnS, can avoid the generation of hot brittleness of steel, can expand austenitic region of steel, can refine crystal grains, plays a role in improving toughness of steel, has insignificant effect when the content is lower than 0.80%, and has significant effect when the content exceeds 1.20%, so that harmful elements are promoted to start to gather in grain boundaries, toughness of ultrahigh-strength oil well pipe steel is reduced, and meanwhile, hydrogen sulfide stress corrosion is easy to generate in steel, so that the Mn is controlled to be 0.80% -1.20%.
Cr: chromium improves hardenability, improves toughness of steel, has corrosion resistance, is a strong precipitate forming element, can expand a heat treatment process window in the subsequent heat treatment, forms precipitates, and obviously improves strength of steel. For the purpose of the present application, cr is more preferably in the range of 0.80% to 1.20%.
Mo: the stability of austenite is improved, and the stability of a heat treatment control process is improved (a heat treatment process window is enlarged) in the subsequent heat treatment process; the steel strength is improved by precipitation with V and Ti, the refining effect of Mo on the precipitated phase is obvious, and the curing and growth of the precipitated phase can be inhibited, but the cost of Mo alloy is higher, so the more preferable range of the application is 0.10-0.30%.
V: the vanadium forms C, N compound, has the functions of refining grains and improving strength, and can improve the toughness of steel. For the purposes of the present application, V is more preferably in the range of 0.03% to 0.06%.
Ti: titanium is a typical precipitation strengthening element, in this patent, tiN is mainly used to precipitate, inhibit the growth of grains in a heat affected zone in the subsequent welding process, and the remaining Ti is combined with C, so that the precipitation strengthening effect is achieved, and the strength of the steel is improved.
P, S is a harmful impurity element in steel, and it induces segregation and increases brittleness of the material, so that the lower the content is, the better the content is.
In order to ensure the high temperature performance of the steel, the components meet the following design conditions: c/mo=0.5 to 2.0, C/cr=0.12 to 0.17; the main elements Cr and Mo for improving heat resistance should be kept in a certain proportion with the element C.
Cr, mn and Mo in the steel of the present application form a precipitate phase of strong carbide after heat treatment under the conditions of the present application, and it can be found from an analysis chart of a transmission electron microscope that a large number of spherical precipitate phases with diameters of about 100 to 150nm and rod-like precipitate phases with lengths of about 200nm exist in a matrix, as shown in particular in FIG. 5 and FIG. 6. The strong carbide precipitated phases formed by Cr, mn and Mo in the application form staggered distribution, the dislocation slip is not easy to bypass and is started mainly by a cutting mode, the creep property of the test steel is certainly improved, and the method has remarkable effect on obtaining products with more excellent properties.
The hot rolled coil is obtained through reasonable component design, smelting and rolling processes, and the heat treatment process enables the product to have good strong plasticity, higher high-temperature mechanical property and creep property. The smelting, hot rolling and cooling related by the application comprise the following heat treatment and other working procedures which are closely connected and are indistinct. In the smelting process, P, S and gas content in molten steel are strictly controlled, the content of alloy elements is ensured, and the purity of the molten steel is improved, so that the strength and plasticity of a product in subsequent heat treatment are ensured; in the hot rolling and cooling process, ferrite, pearlite and a small amount of bainite structure are obtained at a higher coiling temperature, and a higher ferrite structure ratio is maintained in order to obtain lower strength of the original coil, so that the forming is easy in the welding process; in the heat treatment process, the tempering temperature cannot be too low in order to obtain a final higher toughness index, and the final product can be ensured to reach a higher level (more than or equal to 100J) by selecting the tempering temperature to be 550+/-20 ℃.
Compared with the prior art, the steel structure for the high-strength and high-toughness welded sleeve, which is produced by adopting the method, is ferrite, pearlite and a small amount of bainite structure, the yield strength of the whole pipe after quenching and tempering is 800-850MPa, the tensile strength is 900-960MPa, the Charpy impact energy Akv at the transverse temperature of minus 10 ℃ is more than or equal to 100J, and the elongation A is more than or equal to 13%; under the condition of 350 ℃, the typical yield strength is 720-750MPa, the tensile strength is 820-850MPa, the elongation A is 12-15%, and under the condition of 400 ℃, the typical yield strength is 670-710MPa, the tensile strength is 750-800MPa, and the elongation A is 9-12%. The strength of the typical representative example is reduced by less than or equal to 15% at the temperature of 350 ℃. Creep rate is less than or equal to 3.79×10 under the conditions of 400 ℃ and 0.8 stress coefficient (552 MPa) -6 ％·s -1 。
Drawings
FIG. 1 is a drawing showing the metallographic structure of a typical hot rolled coil according to the application;
FIG. 2 is a typical metallurgical structure after thermal refining according to the present application;
FIG. 3 is a typical normal and high temperature stretch curve of the present application;
FIG. 4 is a graph showing creep curves at 400℃and a stress coefficient of 0.8 for an exemplary embodiment of the present application;
FIG. 5 is a TEM morphology of a precipitated phase according to an exemplary embodiment of the present application;
FIG. 6 is a particle energy spectrum of a precipitated phase;
FIG. 7 is a hot rolled structure chart of the comparative example.
Detailed Description
The application provides steel for a high-strength welding sleeve for a thickened oil thermal recovery well, which comprises the following components in percentage by mass:
c:0.14% -0.20%, si: less than or equal to 0.30 percent, mn:0.80% -1.20%, P: less than or equal to 0.015 percent, S: less than or equal to 0.0050 percent, mo:0.10% -0.30%, V:0.03-0.06%, ti:0.01-0.03%, cr:0.80-1.20%; als:0.020-0.035%, N: less than or equal to 0.0040 percent; the balance of Fe and unavoidable impurities.
The production method of the steel for the high-strength welding sleeve for the thick oil thermal production well comprises the following steps: molten iron pretreatment, converter smelting, LF refining, RH refining, continuous casting, casting blank slow cooling, heating, rolling, laminar cooling and coiling to obtain a hot rolled coil with the thickness of 8-12 mm; in production, the molten iron pretreatment is specifically as follows: the front slag skimming and the rear slag skimming are required to be carried out, and the desulfurized molten iron [ S ] is controlled to be less than or equal to 0.0050%; the converter smelting specifically comprises the following steps: less than or equal to 0.015 percent of [ P ], [ S ] < 0.0050 percent; adding most of alloy in the tapping process to enable the molten steel components to reach or approach the inner control lower limit; the slag blocking operation is performed, so that the phosphorous is prevented from being removed; the LF furnace refining specifically comprises: fully reducing ladle top slag, and adjusting components to a target value or close to the target value; the RH furnace refining specifically comprises the following steps: adjusting all components to target values; vacuum treatment is carried out for more than 12min, so that the [ H ] content of molten steel is less than or equal to 1.2ppm, and the [ Ca ] content of the end point is controlled to be 15-30ppm. The continuous casting specifically comprises the following steps: baking the middle ladle for more than or equal to 24 hours; the target temperature of the tundish is controlled to be 10-25 ℃ above the liquidus temperature; finally casting into a casting blank with the thickness of 230 mm. The casting blank slow cooling specifically comprises the following steps: stacking and slowly cooling the casting blank for more than 48 hours; the tapping temperature of the initial continuous casting slab is 1170-1210 ℃, and the main purpose is to ensure complete austenitization of the material and make the alloy elements fully solid-solved. And then adopting two-stage rolling, wherein the rolling temperature is controlled to be 1000-1060 ℃ in a recrystallization area, austenite grains are obviously refined through repeated deformation and recrystallization, the rolling temperature is controlled to be 900-1000 ℃ in an unrecrystallized area, deformation and phase transformation are carried out simultaneously, the austenite grains are elongated in the stage, a sliding band is generated at the same time, and the increase of austenite grain boundaries and the occurrence of the sliding band provide favorable conditions for ferrite nucleation, so that fine-grain ferrite is obtained. In order to ensure that the coil has excellent initial welding performance, the rolled coil is air-cooled, the air-cooled ending temperature is 650-750 ℃, and the coil is coiled at the temperature. The steel structure is ferrite, pearlite and a small amount of bainite, the grain size grade is 8.0-10.0, and the steel structure is formed by cooling the steel for the high-strength welding sleeve for the thick oil thermal production well, as shown in figure 1.
After the hot rolled coil produced by the method is subjected to high-frequency resistance welding for pipe making, heating the whole pipe to 900-940 ℃, preserving heat for 35-45min, and carrying out water quenching; heating the whole tube to 530-570 ℃, preserving heat for 75-85min, and air cooling. A typical organization is shown in fig. 2. The yield strength of the whole pipe after quenching and tempering is 800-850MPa, the tensile strength is 900-960MPa, the Charpy impact energy Akv at the transverse temperature of-10 ℃ is more than or equal to 100J, and the elongation A is more than or equal to 13%; under the condition of 350 ℃, the typical yield strength is 720-750MPa, the tensile strength is 820-850MPa, the elongation A is 12-15%, and under the condition of 400 ℃, the typical yield strength is 670-710MPa, the tensile strength is 750-800MPa, and the elongation A is 9-12%. A typical representative tensile curve at a temperature of 350 ℃ is shown in FIG. 3, and the strength is reduced by 15%.
According to the method, the specific embodiment of the application is as follows:
examples 1 to 4
The production method of the steel for the high-strength welding sleeve for the thick oil thermal production well comprises the following process flows: molten iron pretreatment, converter steelmaking, alloy fine tuning station, LF external refining, RH external refining, continuous casting, casting blank slow cooling, heating, rolling, laminar cooling and coiling; the chemical components of the ladle molten steel meet the weight percentage (wt%): c:0.14% -0.20%, si: less than or equal to 0.30 percent, mn:0.80% -1.20%, P: less than or equal to 0.015 percent, S: less than or equal to 0.0050 percent, mo:0.10% -0.30%, V:0.03-0.06%, ti:0.01-0.03%, cr:0.80-1.20%; als:0.020-0.035%, N: less than or equal to 0.0040 percent; the balance of Fe and unavoidable impurities. And (5) performing protection casting in the whole continuous casting process.
The chemical compositions of the examples of the present application are shown in table 1, with the balance being Fe and unavoidable impurities not shown in table 1. The component detection is carried out according to GB/T4336 method for analyzing atomic emission spectra of spark sources of carbon steel and medium-low alloy steel (conventional method).
TABLE 1 chemical compositions of various embodiments of the application
The rolling process of each example produced according to the production process adopts slab heating to 1170-1210 ℃, high-pressure water descaling, 2 frame rough rolling, 7 frame finish rolling, laminar cooling and coiling, and the main rolling process parameters and the tensile mechanical properties of the test steel are shown in table 2.
TABLE 2 Main technological parameters and mechanical Properties of Rolling Process
Table 3 structure of test steel
The hot rolled coils produced in each example were produced according to the above heat treatment method, and specific heat treatment process parameters are shown in table 4.
The high-strength welding sleeve hardening and tempering process and mechanical properties of the thickened oil thermal recovery well produced by each embodiment of the application are shown in table 4.
TABLE 4 quenching and tempering process and mechanical properties of the tubes according to the examples of the present application
The high temperature tensile properties of the steel pipe of the present application of example 2 are shown in Table 5.
TABLE 5 high temperature tensile Property of typical example 2 Steel pipes
The creep properties and comparison of the steel pipe of the present application of the exemplary embodiment 2 are shown in Table 6.
TABLE 6 creep properties and comparative examples of typical example 2 steel pipes
The creep property of the steel pipe according to the exemplary embodiment 2 of the present application is shown in FIG. 4, and the creep rate is 3.79×10 under the conditions of 400℃and 0.8 stress coefficient (552 MPa) -6 ％·s -1 . The creep rate of the product in the petroleum casing pipe for the thick oil thermal recovery well disclosed in patent 00100635.5, CN 103131947A and the like is not clearly shown, the creep performance of the product is equivalent to that of a seamless pipe of the same grade, and the index is obviously higher than the national standard requirement.
Claims (7)
1. The steel for the high-strength welding sleeve for the thickened oil thermal recovery well is characterized by comprising the following components in percentage by mass:
c:0.14% -0.20%, si: less than or equal to 0.30 percent, mn:0.80% -1.20%, P: less than or equal to 0.015 percent, S: less than or equal to 0.0050 percent, mo:0.10% -0.30%, V:0.03-0.06%, ti:0.01-0.03%, cr:0.80-1.20%; als:0.020-0.035%, N: less than or equal to 0.0040 percent; the balance of Fe and unavoidable impurities;
the components of the steel for the high-strength welding sleeve for the thick oil thermal production well are as follows: c/mo=0.5 to 2.0, C/cr=0.12 to 0.17;
the steel for the high-strength welding sleeve of the thick oil thermal production well comprises ferrite, pearlite and a small amount of bainitic structures, wherein the area of the ferrite is 60-80%, the area of the pearlite is 20-40%, the area of the bainitic structure is less than or equal to 5%, and the grain size grade is 8.0-10.0;
the yield strength of the high-strength welding sleeve for the thick oil thermal production well is 800-850MPa, the tensile strength is 900-960MPa, the Charpy impact energy Akv of the transverse-10 ℃ is more than or equal to 100J, and the elongation A is more than or equal to 13%; under the condition of 350 ℃, the typical yield strength is 720-750MPa, the tensile strength is 820-850MPa, and the elongation A is 12-15%; under 400 ℃, the typical yield strength is 670-710MPa, the tensile strength is 750-800MPa, and the elongation A is 9-12%; the strength of the exemplary embodiment is reduced at 350℃compared to normal temperatureThe lower is less than or equal to 15 percent; under the condition of 400 ℃ and 0.8 stress coefficient, the creep rate is less than or equal to 3.79 multiplied by 10 -6 %·s -1 。
2. A method of producing a steel for a high strength welded casing for a heavy oil thermal recovery well according to claim 1, wherein the method comprises heating: the tapping temperature of the initial continuous casting slab is 1170-1210 ℃.
3. The production method according to claim 2, wherein the production method comprises rolling, wherein the rolling is performed in two stages, the first stage is a recrystallization region rolling, the rolling temperature is controlled to be 1000-1060 ℃, the second stage is a non-recrystallization region rolling, and the rolling temperature is controlled to be 900-1000 ℃.
4. The production method according to claim 3, wherein the air cooling is performed after rolling, and the coiling is performed at a temperature of 650-750 ℃.
5. A heat treatment method for producing a high-strength welded casing for a heavy oil thermal recovery well by using the steel for the high-strength welded casing for a heavy oil thermal recovery well according to claim 1, characterized in that the heat treatment method comprises the following steps: quenching and tempering are carried out.
6. The heat treatment method according to claim 5, wherein the quenching is specifically: the temperature is 920+/-20 ℃, the heat preservation time is 40+/-5 min, and the water quenching is carried out.
7. The heat treatment method according to claim 5 or 6, wherein the tempering is specifically: the temperature is 550+/-20 ℃, and the heat preservation time is 80+/-5 min.
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| CN109722611B (en) * | 2017-10-27 | 2020-08-25 | 宝山钢铁股份有限公司 | Steel for low-yield-ratio ultrahigh-strength continuous oil pipe and manufacturing method thereof |
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| CN101864542A (en) * | 2009-04-16 | 2010-10-20 | 上海梅山钢铁股份有限公司 | Steel for high-frequency resistance straight weld oil well pipe and production method thereof |
| CN102212751A (en) * | 2011-06-03 | 2011-10-12 | 首钢总公司 | Steel for high-strength petroleum casing pipe used in heavy oil thermal recovery well and manufacturing method thereof |
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