CN114737120A - Steel for large-diameter tube bundle outer bearing tube and preparation method thereof - Google Patents
Steel for large-diameter tube bundle outer bearing tube and preparation method thereof Download PDFInfo
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- CN114737120A CN114737120A CN202210351233.0A CN202210351233A CN114737120A CN 114737120 A CN114737120 A CN 114737120A CN 202210351233 A CN202210351233 A CN 202210351233A CN 114737120 A CN114737120 A CN 114737120A
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C21D2211/005—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
Abstract
The invention provides steel for a large-caliber tube bundle outer bearing tube and a preparation method thereof, wherein the steel comprises the following components in percentage by weight: c: 0.12% -0.16%, Si: 0.20-0.40%, Mn: 1.20% -1.40%, P: 0.015% or less, S: 0.01% or less, Al: 0.01% -0.055%, Nb: 0.005-0.025%, Ti: 0.005% -0.015%, V: 0.03% -0.05%, N: 0.0010-0.0040 percent, and Ca/S in the steel is more than or equal to 1.8; the balance of Fe and inevitable impurities; the preparation method comprises smelting, continuous casting, heating and rolling; the high-strength and high-toughness performance of the large-wall-thickness tube bundle outer bearing tube prepared by the method is well matched, tempering heat treatment is not needed after online controlled cooling, the production efficiency is improved, the production cost is saved, and industrial batch production is easy to realize.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to steel for a large-diameter tube bundle outer bearing tube and a production and preparation method thereof.
Background
With the improvement of environmental awareness, the demand for clean energy is increasing, and petroleum and natural gas are one of the cleanest energy sources, and the development and utilization of petroleum and natural gas are more and more paid attention by countries in the world. Because of the limited land resources, the exploitation amount of seabed oil and gas resources is increased year by year, and in oil fields developed offshore in China, crude oil mostly has the characteristics of high viscosity, high coagulation and high wax content, so a hot oil pipeline conveying process is mostly adopted. The tube bundle can provide economic and high-quality heat preservation performance and is suitable for the requirement of a conveying process. At present, in a plurality of shallow sea (the water depth is less than 200 meters) water areas of oil fields developed offshore in China, the oil fields are relatively close to the shore, a plurality of oil, gas and water submarine pipelines and cables are often required between platforms in the oil fields or between the platforms and single-point mooring, the method of adopting the pipe bundle is very advantageous, and the design of a plurality of pipes and offshore installation can be completed at one time. A tube bundle system refers to two or more tubes that are assembled together and prefabricated and installed as a single tube. Under the background, the steel for the large-caliber tube bundle outer bearing tube has high research value. Tube bundle systems have been used throughout the world for over 20 years, most commonly in the north sea and in the gulf of mexico. In 1980, the first tube bundle system was designed and installed in the north sea, and the offshore installation adopts the controlled depth pipe-pulling method (CDTM), and the outer diameter of the bearing tube is 12.75 inches, and the total length is only 800 meters. Many different scale tube bundle systems were subsequently designed and installed in the north sea and gulf of mexico and around the world, with rapid growth in complexity, overall length and number of internal pipelines and water depths, to date over 80. With the development of the application of the tube bundle, the tube bundle develops towards the direction of large wall thickness and large caliber, the outer diameter of the outer sleeve reaches 50 inches and the wall thickness reaches 35mm in the maximum-scale tube bundle designed and installed at present. The research and development work of the steel for the large-diameter pipe bundle outer bearing pipe is not carried out in China, and the steel for the pipe bundle outer bearing pipe is replaced by the steel for the oil casing pipe in the shallow sea seabed oil field in China. However, the oil casing is usually thin, is usually produced by hot rolled strip steel, and has the problems of poor matching of strength and toughness, thin thickness specification, high-temperature creep deformation and the like with a medium plate. In addition, the steel plate for the sleeve developed at present mainly comprises a hot rolled coil, and has a thickness of 12 to 23mm, and no report has been found on the steel plate for the sleeve having a thickness of 23mm or more.
In future, a plurality of deep sea oil and gas fields are newly built in China, and the demand of steel for the large-diameter tube bundle outer bearing tube is estimated to be up to 30 ten thousand tons. The steel for the pipe bundle outer bearing pipe is developed abroad, the submarine oil gas production and transmission efficiency is obviously improved, the cost is low, but the steel is still blank in China and becomes a potential threat for autonomous guarantee of submarine oil gas. The steel for the large-wall-thickness large-caliber pipe bundle outer bearing pipe is produced by adopting a medium plate process and a longitudinal submerged arc welding process, and is required to have excellent low-temperature impact toughness, no high-temperature creep phenomenon, stable yield strength in a heat affected zone, no obvious softening and embrittlement phenomena and obvious difference from the steel for the sleeve.
At present, some researches on steel for the bearing pipe outside the pipe bundle are carried out at home and abroad, and partial patents and documents are found through search, but the contents recorded in the researches and the technical scheme of the invention have obvious defects in the aspects of stability of a heat affected zone, low-temperature toughness and the like of components, a production method, high-temperature creep and yield strength.
Related patent 1: a2250 mm production line for preparing H40 petroleum casing steel and a preparation method thereof (CN201911408022.0) only provide a hot rolled coil for a casing in oil and gas pipeline engineering with the caliber of less than 711mm and the thickness of 3-19mm and a preparation method thereof, have no high-temperature performance index and do not conform to the manufacturing process of medium plates.
Related patent 2: a steel for large thick wall high toughness resistance welding sleeve and a manufacturing method thereof (CN202010765824.3) provide a manufacturing method of the steel for large thick wall high toughness resistance welding sleeve with the steel wall thickness more than 13mm, the steel for resistance welding is also a hot rolling coiled plate, the caliber is less than 711mm, the thickness is less than 23mm, no high temperature performance index exists, and the steel does not conform to the manufacturing process of medium plate.
Related patent No. 3: a Cr microalloyed steel for petroleum casing pipe and its manufacturing method (CN201710990236.8) provide a high strength steel for petroleum casing pipe and its preparation method, through adding certain Cr content such as 0.40-0.50%, to meet the requirement for steel pipe strength, and increase the corrosion resistance of steel to a certain extent, the material used is the hot-rolled coil, there is no high-temperature performance index, do not accord with the manufacturing process of medium plate.
Related patent No. 4: needle ferrite type low temperature resistant N80 grade petroleum casing steel and a preparation method thereof (CN201811577443.1) disclose needle ferrite type low temperature resistant N80 grade petroleum casing steel and a preparation method thereof, and the needle ferrite type low temperature resistant N80 grade petroleum casing steel has good low temperature impact resistance and HIC corrosion resistance. The hot-rolled coil still has no high-temperature performance index and does not conform to the manufacturing process of medium plates.
In summary, in the prior art, for a medium plate with a wall thickness of more than 23mm and used for a large-diameter tube bundle outer bearing tube produced by a submerged arc welding process, the development of the performance of low temperature resistance, high toughness, high temperature creep resistance and stable yield strength in a heat affected zone is still insufficient, and the requirements of a seabed oil and gas field on the material performance cannot be met.
Disclosure of Invention
The invention aims to overcome the problems and the defects and provide the steel for the large-diameter tube bundle outer bearing tube, which meets the material requirements of a submarine oil-gas field, has low alloy cost, simple and feasible process, does not need tempering heat treatment and is easy to realize industrialized batch production, and the preparation method thereof.
Aiming at the defects of thin thickness specification, poor high-temperature creep, poor toughness performance matching and other key characteristic requirements of the steel for the tube bundle bearing tube in the oil gas production and transportation process of the seabed oil gas field, the invention provides the steel for the tube bundle outer bearing tube and the production and preparation method thereof from the aspects of material composition design, steel ladle metallurgy technology, microstructure state control and the like, solves the problems and meets the material requirements of the seabed oil gas field. The product is suitable for a thick-wall submerged arc welded pipe, the steel plate is a medium plate, and the structure of the steel plate is ferrite and a small amount of pearlite;
the purpose of the invention is realized as follows:
the steel for the large-caliber pipe bundle outer bearing pipe comprises the following components in percentage by weight: c: 0.12% -0.16%, Si: 0.20-0.40%, Mn: 1.20% -1.40%, P: 0.015% or less, S: 0.01% or less, Al: 0.01% -0.055%, Nb: 0.005-0.025%, Ti: 0.005% -0.015%, V: 0.03-0.05%, N: 0.0010-0.0040 percent, and Ca/S in the steel is more than or equal to 1.8; the balance being Fe and unavoidable impurities.
Further, in the steel, Ti: the proportion of N is 2.78-3.54.
Further, Si: 0.25-0.35%, P: 0.012% or less, Al: 0.01 to 0.05 percent.
Further, the ratio of Ti/N is 2.78 to 3.54.
The thickness of the steel plate for the outer bearing pipe is more than or equal to 23mm, and the steel structure is ferrite and pearlite.
The yield strength of the steel for the outer bearing pipe is 375-425 MPa, the tensile strength is 515-530 MPa, and the elongation is 28-32%; the impact absorption work at the temperature of minus 20 ℃ is 203-298J; the yield strength at a high temperature of 650 ℃ is 355-375 MPa, the tensile strength is 500-515 MPa, and the elongation is 29-35%.
The design reason of the components of the invention is as follows:
c: is an essential element for securing the strength of steel, and the content is 0.12% or more, but when the content exceeds a certain amount, the weldability deteriorates. Therefore, the upper limit is 0.16%. From the viewpoint of economy and product performance, the C content is preferably controlled to 0.12 to 0.16%.
Si: is a main deoxidation component in the steel making process, and must be contained by 0.10% or more in order to obtain a sufficient deoxidation effect. However, if the content exceeds the upper limit, the toughness of the base material and the weld zone is lowered, and Si in the form of solid solution increases the toughness and the brittle transition temperature, so that the content of Si is 0.20 to 0.40%, preferably 0.25 to 0.35%.
Mn: the Mn and S are combined to form MnS, thereby avoiding hot cracks caused by FeS formed at the grain boundary, and the Mn is also a good deoxidizer. Manganese is used as a low-cost toughening element, the content of manganese is too low, the strength of the material cannot be ensured, but when the content of Mn is higher than 1.40%, the segregation of a casting blank is increased, and the low-temperature toughness of a Coarse Grain Heat Affected Zone (CGHAZ) is deteriorated, so that the content of Mn should be controlled to be 1.20-1.40%.
P: are inevitable impurity elements in steel and deteriorate toughness and weldability of steel. Studies have shown that when the P content is higher than 0.015%, its corrosivity under the conditions of the acid gas phase medium of the upper deck is significantly reduced, so that the upper limit is 0.015%, preferably 0.012% or less.
S: if the content exceeds 0.01%, a large amount of MnS inclusions are formed in the steel, and the MnS inclusions are sites of origin of pitting corrosion to lower the corrosion resistance of the steel, so that measures are taken to reduce the S content in the steel as much as possible. Therefore, in the present invention, the upper limit of the S content is determined to be 0.01%, and the preferable upper limit is 0.006%.
Al: the content of the deoxidation and grain refinement elements is generally 0.01% or more, but if it exceeds 0.06%, the ingot is likely to be thermally cracked, a large amount of inclusions are formed, and the toughness of the steel is lowered, so the upper limit of the Al content is 0.055%, and the preferable content range is 0.01 to 0.05%.
Nb: the element is added to improve the strength and toughness of the steel, and can effectively reduce the grain size of the steel. When the Nb content is less than 0.005%, the effect on the strength and toughness of the steel is small, and when the Nb content exceeds 0.025%, MA brittle components are easily generated during high-heat input welding, so that the welding performance and low-temperature toughness of the steel are reduced, and therefore, the Nb content ranges from 0.005% to 0.025%.
V: vanadium has strong affinity with carbon, nitrogen and oxygen, and forms corresponding stable compounds with the vanadium. Vanadium is mainly present in steel in the form of carbides. The main function of the steel is to refine the structure and the crystal grains of the steel and reduce the strength and the toughness of the steel. When the solid solution is dissolved at high temperature, the hardenability is increased; conversely, if present in the carbide form, the hardenability is reduced. Vanadium increases the temper stability of the quenched steel and produces a secondary hardening effect. The content of the invention is controlled to be 0.03-0.05%.
Ti: the TiN-based composite material is added as a component for improving the toughness of steel and a welding part, is used as a strong N-fixing element, is easy to form TiN to improve the N-pore resistance of a welding seam metal, has little effect when the content is less than 0.005 percent, and is easy to form large-particle TiN when the content exceeds 0.055 percent to lose the effect. Steel plate to obtain low temperature toughness at high heat input, it is necessary to control Ti: the proportion of N is 2.78-3.54, so the content of Ti added is 0.005-0.015%.
Ca: the Ca and the S are combined to form CaS which can coat inclusions such as alumina and the like, so that the denaturation and spheroidization of the inclusions are realized, and the corrosion resistance, the toughness and the fatigue resistance are improved; meanwhile, the early formed finely dispersed CaS can reduce the formation ratio of MnS, and the CaS and H2By the action of O, basic OH is dissociated-The ions can reduce the acidification degree of the corrosion pit, the pitting corrosion sensitivity is small, and Ca/S is more than or equal to 1.8 in the invention.
N can form fine precipitates with Nb, Ti and V to play a role of strengthening and fine grains and improve the toughness, but the toughness is deteriorated due to the excessively high content, and the content is preferably controlled to be 0.0010-0.0040%.
H. O is an inevitable harmful impurity element in the invention; the content of the additive is increased, so that the hydrogen induced cracking tendency is increased, the inclusion content is increased, and the corrosion resistance and the fatigue resistance are reduced, therefore, the invention controls H to be less than or equal to 0.00015 percent and O to be less than or equal to 0.0020 percent.
The second technical scheme of the invention provides a preparation method of the steel for the large-caliber pipe bundle outer bearing pipe, which comprises smelting, continuous casting, heating and rolling;
(1) smelting: the method is characterized in that deep desulfurization molten iron with the sulfur content less than or equal to 0.002 percent is adopted, after the molten iron reaches a converter, smelting is carried out by adopting a process combining double-slag dephosphorization with slag skimming of molten steel after the converter, the final slag alkalinity is controlled to be 3.1-4.3, a large amount of slag is completely eradicated through effective slag blocking operation, and the steel tapping time is not less than 5 min.
The smelting process adopts a high-carbon-drawing one-time point blowing mode for production, main elements of steel are adjusted in a converter to be within the range of the invention, and other alloy components are added according to requirements for smelting.
The molten steel carried out of the converter is subjected to secondary refining to further reduce the content of harmful impurities such as O, S and nonmetallic inclusions. In the LF refining process, aluminum particles, silicon carbide and calcium carbide are adopted for slag adjustment, and the alkalinity of final slag is controlled to be more than 2.3. And (4) performing Ca treatment after LF is finished, wherein the molten steel feeding line of each furnace is 300-500 m.
(2) Continuous casting: the degree of superheat is less than or equal to 20 ℃, weak cooling is adopted for secondary cooling, the casting process is operated according to temperature and drawing speed matching, the drawing speed of a continuous casting billet is 1.0-1.6 m/min, and the thickness of a cast slab is 200-360 mm.
(3) Heating: heating the steel plate blank to 1150-1250 ℃. This is because the temperature below 1150 c is not sufficient to completely dissolve the alloying elements into the austenite, and the finish rolling temperature required for hot rolling cannot be secured. And above 1250 ℃, coarsening of original austenite grains is remarkable, and low-temperature toughness of the steel plate is reduced.
(4) Rolling: in view of meeting the requirement of mechanical property of the tube bundle steel, the temperature of an austenite recrystallization zone and a non-recrystallization zone is preferably 1130-970 ℃ for two-stage controlled rolling, and the accumulated reduction of the two-stage rolling is ensured to be not less than 60%.
Different rolling temperatures and cooling rates of the unrecrystallized regions can be selected according to the mechanical property requirements of the steel plate. For example, a yield strength requirement of 355N/mm2When the impact toughness temperature of the high-strength steel is required to be-20 ℃, the rolling temperature of a hot rolling non-recrystallization zone is preferably less than 900 ℃, the finishing rolling temperature is more than 810 ℃, the cooling mode is laminar cooling, the cooling rate is controlled to be 5-8 ℃/s, and the steel plate is cooled to 680-700 ℃.
Preferably, after rolling, the controlled cooling is carried out for more than 20s, the starting water cooling temperature is more than 670, and the water cooling time is more than 10 s;
the invention has the beneficial effects that:
(1) the strength and toughness of the large-wall-thickness tube bundle outer bearing tube prepared by the invention are well matched: the yield strength is 375-425 MPa, the tensile strength is 515-530 MPa, the elongation is 28-32%, the impact absorption work at the temperature of minus 20 ℃ is 203-298J, the high-temperature performance at the temperature of 650 ℃, the yield strength is 355-375 MPa, the tensile strength is 500-515 MPa, and the elongation is 29-35%.
(2) The method is simple to operate, does not need tempering heat treatment after online controlled cooling, improves the production efficiency, saves the production cost and is easy to realize industrial batch production.
(3) The invention adopts two-stage controlled rolling, controls the structure of the steel for the tube bundle outer bearing tube through the finishing temperature of the steel plate for the tube bundle outer bearing tube, maintains ideal performance, has no high-temperature creep phenomenon and greatly reduces the production cost.
(4) The steel plate suitable for the large-wall-thickness tube bundle outer bearing tube has the maximum thickness of 35mm, has good low-temperature toughness and high-temperature thermal stability, and meets the technical requirements of materials required by manufacturing the large-wall-thickness tube bundle outer bearing tube.
Drawings
FIG. 1 is a microstructure of example 1 of the present invention.
FIG. 2 is a microstructure of example 1 of the present invention after air-cooling to room temperature at a high temperature of 650 ℃.
Detailed Description
The present invention is further illustrated by the following examples.
According to the embodiment of the invention, smelting, continuous casting, heating and rolling are carried out according to the component proportion of the technical scheme.
Heating: heating to 1150-1250 ℃;
rolling: and (3) rolling in two stages of an austenite recrystallization zone and a non-recrystallization zone, wherein the rolling temperature of the austenite recrystallization zone is 970-1130 ℃, and the rolling accumulated reduction rate of the non-recrystallization zone is not lower than 60%.
Further, the method comprises the following steps of; the rolling temperature of the unrecrystallized area is below 900 ℃, and the finishing temperature is above 810 ℃; the cooling mode is laminar cooling, the cooling rate is controlled to be 5-8 ℃/s, and the steel plate is cooled to 680-700 ℃.
After rolling, controlled cooling is carried out for more than 20s, the water cooling temperature is more than 670, and the water cooling time is more than 10 s;
further, the method comprises the following steps of; smelting: the method is characterized in that deep desulfurization molten iron with the sulfur content less than or equal to 0.002 percent is adopted, after the molten iron is transferred to a converter, smelting is carried out by adopting a process of combining 'double-slag' dephosphorization with 'slagging-off' of molten steel after the converter, the alkalinity of final slag is controlled to be 3.1-4.3, and the steel placing time is not less than 5min through effective slag stopping operation;
in the LF refining process, aluminum particles, silicon carbide and calcium carbide are adopted for slag adjustment, and the alkalinity of final slag is controlled to be more than 2.3; and (4) performing Ca treatment after LF is finished, wherein the molten steel feeding line of each furnace is 300-500 m.
The compositions of the steels of the examples of the invention are shown in table 1. The main process parameters of the steel of the embodiment of the invention are shown in Table 2. The properties of the steels of the examples of the invention are shown in Table 3. The mechanical properties of the steel of the embodiment of the invention after high temperature of 900 ℃ are shown in Table 4. The properties of the weld heat affected zone of the steel of the present invention are shown in Table 5.
TABLE 1 composition (wt%) of steels of examples of the present invention
TABLE 2 Main Process parameters of the steels of the examples of the invention
Note: t-thickness of finished product
TABLE 3 Properties of steels of examples of the invention
TABLE 4 mechanical properties of steels of the examples of the invention after exposure to 650 deg.C
TABLE 5 weld heat affected zone Properties of inventive steels
From the above, the high-strength and toughness performance of the large-wall-thickness tube bundle outer bearing tube prepared by the invention is well matched: the yield strength is 375-425 MPa, the tensile strength is 515-530 MPa, the elongation is 28-32%, the impact absorption work at-20 ℃ is 203-298J, the high-temperature performance at 650 ℃, the yield strength is 355-375 MPa, the tensile strength is 500-515 MPa, and the elongation is 29-35%. The steel plate has high performance after being welded, and the hardness is 170-220 Hv in a heat affected zone at the temperature of 600-1300 ℃.
In order to express the present invention, the above embodiments are properly and fully described by way of examples, and the above embodiments are only used for illustrating the present invention and not for limiting the present invention, and those skilled in the relevant art can make various changes and modifications without departing from the spirit and scope of the present invention, and any modifications, equivalent substitutions, improvements, etc. made by the persons skilled in the relevant art should be included in the protection scope of the present invention, and the protection scope of the present invention should be defined by the claims.
Claims (7)
1. The steel for the large-caliber tube bundle outer bearing tube is characterized by comprising the following components in percentage by weight: c: 0.12% -0.16%, Si: 0.20-0.40%, Mn: 1.20% -1.40%, P: 0.015% or less, S: 0.01% or less, Al: 0.01% -0.05%, Nb: 0.005-0.025%, Ti: 0.005% -0.015%, V: 0.03-0.05%, Ca: 0.002% -0.005%, N: 0.0010-0.0040 percent, and Ca/S in the steel is more than or equal to 1.8; the balance being Fe and unavoidable impurities.
2. The steel for the large-caliber tube bundle outer bearing tube according to claim 1, wherein the ratio of Ti/N in the steel is 2.78-3.54.
3. The steel for a large-caliber tube bundle outer bearing tube according to claim 1, wherein the ratio of Si: 0.25-0.35%, P: 0.012% or less, Al: 0.01 to 0.05 percent.
4. The steel for the large-caliber pipe bundle outer bearing pipe according to claim 1, wherein the thickness of the steel plate is more than or equal to 23mm, and the steel structure is ferrite and pearlite.
5. The steel for the large-caliber pipe bundle outer bearing pipe according to claim 1, wherein the steel has a yield strength of 375-425 MPa, a tensile strength of 515-530 MPa, an elongation of 28-32%, an impact absorption energy at-20 ℃ of 203-298J, a yield strength at 650 ℃ of 355-375 MPa, a tensile strength of 500-515 MPa, and an elongation of 29-35%.
6. A method for preparing the steel for the large-caliber pipe bundle outer bearing pipe according to the claims 1 to 5, which comprises the steps of smelting, continuous casting, heating and rolling; the method is characterized in that:
heating: heating the continuous casting slab to 1150-1250 ℃;
rolling: and (3) rolling in two stages of an austenite recrystallization zone and a non-recrystallization zone, wherein the rolling temperature of the austenite recrystallization zone is 970-1130 ℃, and the rolling accumulated reduction of the non-recrystallization zone is not lower than 60%.
7. The method for preparing the steel for the large-caliber tube bundle outer bearing tube according to the claim 6, wherein the rolling temperature of a non-recrystallization zone is less than 900 ℃, and the finishing rolling temperature is more than 810 ℃; the cooling mode is laminar cooling, the cooling rate is controlled to be 5-8 ℃/s, and the steel plate is cooled to 680-700 ℃.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101845596A (en) * | 2009-03-24 | 2010-09-29 | 宝山钢铁股份有限公司 | Wide thick plate for X80 pipe line steel and manufacturing method thereof |
| WO2011043287A1 (en) * | 2009-10-05 | 2011-04-14 | 新日本製鐵株式会社 | Steel for linepipe having good strength and malleability, and method for producing the same |
| CN102912228A (en) * | 2012-10-23 | 2013-02-06 | 鞍钢股份有限公司 | Economic-type pipe fitting steel with high strength and low yield ratio and production method thereof |
| US20180312937A1 (en) * | 2017-04-27 | 2018-11-01 | China University Of Petroleum-Beijing | Seamless Line Pipe Resistant to Corrosion by CO2/H2S and Sulfate-Reducing Bacteria and Manufacturing Method Thereof |
| JP2019116657A (en) * | 2017-12-27 | 2019-07-18 | Ｊｆｅスチール株式会社 | Thick walled large diameter electroseamed steel pipe excellent in fatigue strength, and manufacturing method therefor |
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2022
- 2022-04-02 CN CN202210351233.0A patent/CN114737120B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101845596A (en) * | 2009-03-24 | 2010-09-29 | 宝山钢铁股份有限公司 | Wide thick plate for X80 pipe line steel and manufacturing method thereof |
| WO2011043287A1 (en) * | 2009-10-05 | 2011-04-14 | 新日本製鐵株式会社 | Steel for linepipe having good strength and malleability, and method for producing the same |
| CN102912228A (en) * | 2012-10-23 | 2013-02-06 | 鞍钢股份有限公司 | Economic-type pipe fitting steel with high strength and low yield ratio and production method thereof |
| US20180312937A1 (en) * | 2017-04-27 | 2018-11-01 | China University Of Petroleum-Beijing | Seamless Line Pipe Resistant to Corrosion by CO2/H2S and Sulfate-Reducing Bacteria and Manufacturing Method Thereof |
| JP2019116657A (en) * | 2017-12-27 | 2019-07-18 | Ｊｆｅスチール株式会社 | Thick walled large diameter electroseamed steel pipe excellent in fatigue strength, and manufacturing method therefor |
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