CN118326262A - Thick steel plate for 1300MPa grade pressure equipment, manufacturing, forming and post-heat treatment method - Google Patents
Thick steel plate for 1300MPa grade pressure equipment, manufacturing, forming and post-heat treatment method Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
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- 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
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- 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
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- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- 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
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- C21D2211/00—Microstructure comprising significant phases
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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Abstract
The invention provides a thick steel plate for 1300 MPa-level pressure equipment, and a manufacturing, forming and post heat treatment method thereof, wherein the steel plate comprises the following ：C 0.19％～0.23％、Si 0.10％～0.40％、Mn 0.40％～0.70％、P≤0.010％、S≤0.003％、Cr 1.40％～2.0％、Mo 0.40％～0.60％、B 0.001％～0.005％、Alt 0.015％～0.045％, weight percent of Fe and unavoidable impurities as the rest. The manufacturing method comprises smelting, continuous casting, heating, rolling control, cooling control and tempering; the mechanical properties of the steel after molding and heat treatment at normal temperature are 950 MPa- p0.2 MPa-1100 MPa, 1300 MPa-1430 MPa and elongation A-19%; at 400 ℃,560 MPa- 0.2 MPa; impact power KV 2 is more than or equal to 120J at 0 ℃; the use requirement of high-strength pressure equipment is ensured.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a thick steel plate for 1300 MPa-level pressure equipment, a manufacturing method, a forming method and a post heat treatment method thereof.
Background
The pressure-bearing equipment is widely applied to the processing and preparation fields of large amounts of energy sources such as coal electricity, chemical industry and the like as important places for product storage, medium reaction or heat exchange, and plays an important role in the whole energy production link. For example, the violent medium reaction process in chemical plants generates huge internal pressure and the air pressure generated in the steam heat energy delivery process of coal power plants, the bearing equipment bears huge pressure in the process, the bearing pressure can reach more than 100MPa for high-power equipment, the special equipment industry defines the bearing pressure as extra-high pressure, and the tensile strength of steel for manufacturing the equipment needs to reach 1300MPa. In order to meet the high-speed development of the manufacturing industry of the pressure-bearing equipment in recent years, the pressure-bearing equipment with high efficiency, high parameters and high reliability design requirements is proposed by the design institutes, but the metal material for the pressure-bearing equipment with the existing strength level cannot meet the design requirements, and the ultra-high-toughness material is required to support the development of high-end equipment.
The disclosed invention patent refers to steel for nuclear power bearing equipment and a manufacturing method thereof (publication No. CN 103160732A), and the disclosed components, production method and beneficial effects are seen from the fact that the steel for the nuclear power bearing equipment is applied to the nuclear power field, the tensile strength of a steel plate is in the range of 560-625N/mm 2, the tensile strength of the steel plate in a simulated post-welding heat treatment state is reduced to 510-600N/mm 2, and when the steel is faced with a service environment with higher pressure, the steel cannot provide higher strength for supporting equipment, and particularly, the steel is not provided with a formed technical scheme and data support, and has enough strength to meet the service requirement of high-pressure clothing.
The disclosed invention patent refers to a steel plate for hot-rolled weldable pressure-bearing equipment and a production method thereof (publication No. CN 110983175A), and the patent product is used for automobile manufacture, relates to an ultrathin specification with the thickness of 2-4 mm, is not suitable for manufacturing the pressure-bearing equipment, and also relates to a technical scheme and data support after relevant molding for manufacturing the pressure-bearing equipment.
The disclosed invention patent "a steel sheet for hot-rolled weldable pressure-containing equipment and a method for producing the same" (publication No. CN 110983175A), which is a steel for pressure-containing equipment in view of the disclosed composition, production method and advantageous effects. The tensile strength of the product in the supply state and the simulated post-welding heat treatment state is in the range of 450-610 MPa, and the microstructure is ferrite and pearlite. The organization and performance of the product cannot meet the application requirements when facing service environments with higher pressure and higher temperature.
The disclosed invention patent refers to a thick ultra-high strength steel plate with 1300 MPa-level tensile strength and a manufacturing method thereof (publication No. CN 105039866A), and the patent product is applicable to the field of engineering machinery and has the thickness specification of 50mm at maximum from the aspects of disclosed components, production methods and beneficial effects, and has no technological embodiment and performance index in the aspects of molding and manufacturing of pressure-bearing equipment.
The comprehensive performance and the forming performance of the high-strength steel plate for the pressure-bearing equipment cannot meet the development requirement of new energy equipment, so that the development requirement of the high-strength key material for the 1300 MPa-grade (40-80) mm thick pressure-bearing equipment with excellent normal-temperature strength, high-temperature strength, forming performance and post-welding heat treatment performance is urgently needed to be developed, and the development requirement of large new energy pressure-bearing equipment or equipment in China is supported.
Disclosure of Invention
The invention aims to solve the technical scheme problems that the strength of the invention is insufficient or the strength of the steel plate cannot be improved after the high-strength pressure-bearing equipment is formed, and provides a steel plate with the thickness specification (40-80 mm) and a steel product for the pressure-bearing equipment, which has 1300 MPa-level tensile strength after the steel plate is formed, and manufacturing, forming and post heat treatment processes thereof, so that the manufacturing of the ultra-high-strength pressure-bearing equipment is met.
The invention aims at realizing the following steps:
A thick steel plate for 1300MPa pressure equipment comprises the following ：C0.19％～0.23％、Si 0.10％～0.40％、Mn 0.40％～0.70％、P≤0.010％、S≤0.003％、Cr 1.40％～2.0％、Mo 0.40％～0.60％、B 0.001％～0.005％、Alt 0.015％～0.045％, weight percent of Fe and unavoidable impurities.
The thickness of the thick steel plate for the pressure-bearing equipment is 40-80 mm; the mechanical property of the thick steel plate for the pressure-bearing equipment is more than or equal to 930MPa and less than or equal to 1430MPa, wherein R p0.2≤1080MPa、1300MPa≤Rm; impact power KV 2 is more than or equal to 100J at 0 ℃.
The reason for designing the components of the invention is as follows:
C is the most important element for improving the strength of steel, and the hardenability of the steel is obviously improved by adding the C element, in addition, the combination of the C and the strong carbide alloy element in the steel plays a role in precipitation strengthening, so that a secondary hardening effect is obtained, and the high strength requirement of the steel is ensured. When the carbon content is lower than 0.13%, the hardenability is lower, and even sorbite structure is difficult to obtain in the subsequent tempering treatment, so that the strength of the steel cannot meet the use requirement. However, too high a carbon content affects the machinability of the steel, and therefore the present invention limits the C content to a range of 0.19% to 0.23%.
Si acts as a reducing agent and deoxidizing agent in the steelmaking process. Si has a certain influence on martensitic transformation in the tempering process, and when the silicon content is higher than 0.5%, the activity of C in martensite is hindered in the tempering process, so that epsilon carbide is generated in martensitic steel instead of M 3 C type carbide, the hardness and toughness of the steel are reduced, and the sensitivity of tempering brittleness is increased, and therefore, the Si content range is limited to be 0.10-0.40%.
Mn is an element for strongly stabilizing austenite, can effectively reduce the decomposition speed of austenite, improve the hardenability of steel, and can strongly increase the strength and hardness of steel, but the high Mn content can enhance the tempering brittleness of steel, so the invention limits the Mn content range to 0.40-0.70%.
S, P is used as a harmful element in steel, and the purity and the toughness of the steel are required to be strictly controlled, so that the invention is limited to S less than or equal to 0.003 percent and P less than or equal to 0.010 percent.
The addition of a certain amount of Cr in the Cr steel obviously improves the hardenability of the steel and ensures the matrix strength of the steel. In addition, cr is a strong carbide forming element, and forms stable carbide with C in steel, thereby improving the bearing capacity of the bearing equipment. When the Cr content is lower than 0.3%, the quenching degree is slightly improved, the generation of lath martensitic structure is not facilitated, and the high-strength performance requirement of the steel cannot be met, so that the Cr content range is limited to 1.40% -2.00%.
Mo can improve the hardenability of the steel, effectively refine austenite grains, and strengthen the solid solution strengthening effect of ferrite. The tempering resistance of the steel can be improved by adding a certain amount of Mo, and the tempering embrittlement can be inhibited. Meanwhile, molybdenum is a strong carbide forming element, and carbide formed during tempering has a secondary hardening effect, so that the content range of Mo is limited to 0.40-0.60%.
B increases the hardenability of the steel, and utilizes high-hardness boride formed by boron to improve the strength of the steel, but the boron content exceeding 0.007% leads to the hot embrittlement phenomenon of the steel, and influences the forming processability of pressure-bearing equipment.
Alt is a commonly used deoxidizer in steel, and a small amount of aluminum is added, so that grains can be refined, and the strength and impact toughness of the steel are improved. When the content of Alt is too high, the hot workability, welding performance and cutting workability of the steel are affected, and the content range of Alt is limited to 0.015% -0.045%.
The second technical proposal of the invention is to provide a manufacturing method of the thick steel plate for 1300 MPa-level pressure equipment, which comprises smelting, continuous casting, heating, rolling control, cooling control and tempering;
Smelting: smelting molten steel in a converter, wherein high-quality scrap steel and molten iron are adopted as raw materials, the content of molten iron is controlled to be 75% -85%, meanwhile, the content of harmful element P is effectively reduced, dephosphorization and decarburization are separately smelted in the converter, wherein dephosphorization and oxygen blowing are controlled to be 7-10 min, decarburization and oxygen blowing are controlled to be 8-12 min, and the mass fraction of phosphorus is finally reduced to be within 0.006%; deep desulfurization treatment is carried out in an LF refining furnace, and the sulfur content is controlled below 0.002%; degassing is completed in a VD furnace, the net circulation time is 10-15 min, and the sedation time is 3-5 min before casting.
Continuous casting: and after vacuum breaking, casting by adopting a slab continuous casting machine, wherein the superheat degree is set to be 20-30 ℃, and the blank drawing speed during casting is 1.0-1.4 m/min. And feeding the casting blank into a stacking and slow cooling machine, wherein the stacking and slow cooling time is 24-36 h, and unstacking is performed at the temperature below 400 ℃, so that the defects of cracking and the like of the casting blank caused by quenching are prevented.
Heating: the heating temperature is controlled between 1180 and 1230 ℃, and the total heating time is 4.0 to 6.0 hours.
And (3) rolling control: the rolling adopts a two-stage control rolling method, the rolling end temperature of a recrystallization zone is more than or equal to 1000 ℃, and the total deformation rate is more than or equal to 50 percent in order to fully crush the core structure of the steel billet. The rolling temperature of the non-recrystallized region is 870-930 ℃, the finishing temperature is 830-870 ℃, and the total deformation rate is more than or equal to 55%. At this time, austenite grains are further flattened and elongated, and along with the increase of the grain boundary area, the ferrite nucleation rate is increased in the subsequent phase transformation process, the grains are fully refined, and the target thickness of the rolled piece is 40-80 mm.
And (3) cooling control: in order to further refine the internal structure of the thick steel plate, the rolling start of the steel plate adopts a controlled cooling process, the start cooling temperature is 780-820 ℃, the cooling rate is 30-55 ℃/s, and the reddening temperature is 450-500 ℃.
Tempering: as more C, mn, cr, mo and other solid solution strengthening elements are added into the steel, the lath martensitic structure with ultrahigh strength and hardness can be obtained after the steel plate is rolled. However, the grain size of the steel sheet is coarse, and there are structural stress and thermal stress concentration, and delay cracks are easily generated during flame cutting. Therefore, the heat treatment is adopted in time to soften and eliminate stress, and the tempering heat treatment is adopted to ensure that the strength of the pressure-bearing steel plate is not lost, and meanwhile, the steel plate has proper plasticity and toughness, thereby being beneficial to the forming processing of the steel plate. Therefore, the tempering heat treatment temperature of the steel is 650-700 ℃, and the heat preservation is 2.0-4.0 min/mm.
The third technical proposal of the invention is to provide a forming process of the thick steel plate for 1300 MPa-level pressure equipment; the forming is the necessary procedure from the steel plate to the bearing equipment. Therefore, how the steel sheet meets the designed bearing pressure after the bearing equipment is manufactured, and the forming heat treatment process is important. The invention establishes the optimal forming heat treatment process of the steel. The parameters and reasons are set as follows: the molding process is to keep the temperature at 930-960 ℃ for 1.0-2.0 min/mm, and then cool the product to room temperature in a salt water bath after discharging. The chemical element and the B alloy element in the process C, mn, cr, mo enter an austenite region, the alloy element is in solid solution in an austenite matrix after a period of heat preservation, then enters a saline water bath at 0-10 ℃ to be rapidly cooled and transformed into a fine lath martensitic structure at 35-55 ℃ per second, and the steel has ultrahigh strength at the moment and meets the requirement of pressure-bearing equipment. But the toughness of the steel is poor and the structural stress is high, the quenching stress is timely eliminated through short-time tempering heat treatment at 370-400 ℃ for 0.5-1.0 h, the structure is softened, the toughness of the steel is improved, the steel forming process is completed, and the microstructure of the steel is sorbite.
The fourth technical scheme of the invention is to provide a post-forming heat treatment process of the thick steel plate for 1300 MPa-level pressure equipment; in order to ensure the ultra-high strength and excellent plastic toughness of the steel for pressure equipment, the steel is further obtained by further adjusting the size and the type of second phase particles in the steel, namely, secondary hardening heat treatment, wherein the process is heating temperature 400-430 ℃, net heat preservation and heat preservation are carried out for 2.0-4.0 h, at the moment, stable (Fe, mn, cr, mo) 23C6、Mo2 C second phase particles and boride with the size of 10-30 nm are separated out from the steel, the volume percentage of the second phase particles is 18-23%, the second phase particles interact with sorbite high-density dislocation, the strong plasticity of a matrix is improved, and the formed and heat treated steel has normal-temperature mechanical properties of 950 MPa- p0.2 MPa-1300 MPa-1430 MPa-A-19%; at 400 ℃,560 MPa- 0.2 MPa; impact power KV 2 is more than or equal to 120J at 0 ℃; the use requirement of high-strength pressure equipment is ensured.
The invention has the beneficial effects that:
(1) By compounding and adding Cr, mo, ni, B alloy elements on the basis of C, si and Mn strengthening elements and strictly controlling the content of harmful elements P, S, the steel plate of the invention obtains a high-density sorbite structure by combining a manufacturing process.
(2) The mechanical property of the steel plate for the pressure equipment, which is obtained by the special production process, is represented by that the normal temperature is 930MPa or less, R p0.2≤1080MPa、1300MPa≤Rm is or less, 1430MPa or less, and the impact power KV 2 is or more than 100J at 0 ℃.
(3) The steel plate of the invention obtains high-density sorbite structure after molding and secondary hardening heat treatment, and simultaneously, a large amount of (Fe, mn, cr, mo) 23C6、Mo2 C second phase particles and boride with the size of 10-30 nm are dispersed and separated out from the steel, the structure accounts for 18-23%, and the strength of 1300MPa and the better plasticity and toughness of the steel plate after molding are ensured.
(4) The mechanical property of the steel plate for the pressure equipment, which is obtained by the special production process, is represented by that the R p0.2≤1100MPa、1300MPa≤Rm MPa is not less than 950MPa and not more than 1430MPa at normal temperature; at 400 ℃,560MPa is less than or equal to R p0.2 and less than or equal to 630MPa; impact energy KV 2 is more than or equal to 120J at 0 ℃.
(5) The invention obtains the high-strength steel plate with the thickness of 40-80 mm for 1300 MPa-level pressure equipment.
Detailed Description
The invention is further illustrated by the following examples.
According to the component proportion of the technical scheme, smelting, continuous casting, rolling control, cooling control, tempering, forming and heat treatment are carried out.
A manufacturing approach of thick steel plate for 1300 MPa-level pressure equipment, including smelting, continuous casting, heating, rolling, tempering;
heating: the heating temperature is controlled to 1180-1230 ℃, and the total heating time is 4.0-6.0 h;
And (3) rolling control: the rolling adopts a two-stage control rolling method, the rolling end temperature of a recrystallization zone is more than or equal to 1000 ℃, and the total deformation rate is more than or equal to 50%; the rolling temperature of the non-recrystallized region is 870-930 ℃, the finishing temperature is 830-870 ℃, and the total deformation rate is more than or equal to 55%;
And (3) cooling control: the cooling temperature is 780-820 ℃, the cooling rate is 30-55 ℃/S, and the reddening temperature is 450-500 ℃;
tempering: the tempering temperature is 650-700 ℃, and the heat preservation is 2.0-4.0 min/mm.
Further; smelting: smelting molten steel in a converter, wherein high-quality scrap steel and molten iron are adopted as raw materials, the content of molten iron is controlled to be 75% -85%, dephosphorization and decarburization are separately smelted by adopting the converter, wherein dephosphorization oxygen blowing is controlled to be 7-10 min, decarburization oxygen blowing is controlled to be 8-12 min, and finally the mass fraction of phosphorus is reduced to be within 0.006%; deep desulfurization treatment is carried out in an LF refining furnace, and the sulfur content is controlled below 0.002%; degassing is completed in a VD furnace, the net circulation time is 10-15 min, and the sedation time is 3-5 min before casting.
Further; continuous casting: the superheat degree is 20-30 ℃, and the blank pulling rate during casting is 1.0-1.4 m/min. And feeding the casting blank into a stacking and slow cooling machine, wherein the stacking and slow cooling time is 24-36 h, and unstacking is performed at the temperature below 400 ℃.
A process for shaping thick steel for 1300 MPa-level pressure-bearing equipment includes such steps as heating to 930-960 deg.C, maintaining the temp for 1.0-2.0 min/mm, discharging, cooling in saline-water bath, and cooling at 35-55 deg.C/S.
Further; and (3) carrying out short-time tempering heat treatment after the brine bath, wherein the short-time tempering heat treatment temperature is 370-400 ℃, the net heat preservation time is 0.5-1.0 h, and the microstructure of the steel after the short-time tempering heat treatment is sorbite.
A post-forming heat treatment process of thick steel for 1300 MPa-level pressure equipment, wherein the post-forming heat treatment is secondary hardening heat treatment, the matrix process is heating temperature 400-430 ℃, and the net heat preservation time is 2.0-4.0 h.
Further; the method is characterized in that: after the secondary hardening heat treatment, (Fe, mn, cr, mo) 23C6、Mo2 C second phase particles and boride with the size of (10-30) nm are precipitated in the steel, and the volume fraction is 18% -23%.
Further; after secondary hardening heat treatment, the mechanical property of the steel is 950 MPa- p0.2≤1100MPa、1300MPa≤Rm MPa; at 400 ℃,560MPa is less than or equal to R p0.2 and less than or equal to 630MPa, and at 0 ℃, the impact power KV 2 is more than or equal to 120J.
The composition of the steel of the example of the invention is shown in Table 1. The main process parameters of the steel of the example of the invention are shown in Table 2. The main technological parameters of the steel forming and heat treatment of the embodiment of the invention are shown in Table 3. The mechanical properties and microstructure of the steels of the examples of the present invention are shown in Table 4. The mechanical properties and microstructure of the formed and heat-treated steels of the examples of the present invention are shown in Table 5.
TABLE 1 composition of inventive example steels
| Examples | C | Si | Mn | P | S | Cr | Mo | B | Alt |
| 1 | 0.22 | 0.12 | 0.60 | 0.006 | 0.001 | 1.45 | 0.43 | 0.003 | 0.039 |
| 2 | 0.20 | 0.18 | 0.64 | 0.006 | 0.002 | 1.87 | 0.50 | 0.002 | 0.022 |
| 3 | 0.19 | 0.30 | 0.70 | 0.008 | 0.003 | 1.68 | 0.58 | 0.004 | 0.033 |
| 4 | 0.19 | 0.18 | 0.52 | 0.010 | 0.001 | 2.00 | 0.40 | 0.001 | 0.028 |
| 5 | 0.20 | 0.25 | 0.45 | 0.005 | 0.002 | 1.65 | 0.49 | 0.005 | 0.045 |
| 6 | 0.20 | 0.35 | 0.70 | 0.009 | 0.001 | 1.40 | 0.60 | 0.003 | 0.031 |
| 7 | 0.23 | 0.40 | 0.50 | 0.006 | 0.001 | 1.80 | 0.56 | 0.002 | 0.028 |
| 8 | 0.21 | 0.24 | 0.40 | 0.007 | 0.002 | 1.95 | 0.57 | 0.004 | 0.020 |
| 9 | 0.23 | 0.15 | 0.57 | 0.009 | 0.003 | 1.75 | 0.44 | 0.001 | 0.023 |
| 10 | 0.22 | 0.10 | 0.65 | 0.006 | 0.001 | 1.50 | 0.47 | 0.005 | 0.040 |
TABLE 2 Main Process parameters for Rolling Steel according to the inventive example
TABLE 3 main process parameters for forming and heat treatment of the inventive example steel
TABLE 4 mechanical Properties and microstructure of the inventive example steels
| Examples | Sampling position | Rp0.2/MPa | Rm/MPa | A/％ | (0℃)KV2/J | Microstructure structure |
| 1 | T/4 | 986 | 1325 | 19.0 | 118 | Sorbite (Sod) |
| 2 | T/4 | 1023 | 1340 | 19.0 | 100 | Sorbite (Sod) |
| 3 | T/4 | 1050 | 1352 | 19.5 | 110 | Sorbite (Sod) |
| 4 | T/4 | 1000 | 1300 | 21.0 | 122 | Sorbite (Sod) |
| 5 | T/4 | 995 | 1385 | 19.5 | 100 | Sorbite (Sod) |
| 6 | T/4 | 1017 | 1408 | 19.0 | 109 | Sorbite (Sod) |
| 7 | T/4 | 1060 | 1420 | 19.0 | 106 | Sorbite (Sod) |
| 8 | T/4 | 991 | 1361 | 19.0 | 115 | Sorbite (Sod) |
| 9 | T/4 | 933 | 1302 | 20.5 | 122 | Sorbite (Sod) |
| 10 | T/4 | 1012 | 1374 | 19.0 | 101 | Sorbite (Sod) |
TABLE 5 mechanical Properties and microstructure after Forming and Heat treatment of Steel sheets according to examples of the invention
According to the results, the steel plate for 1300 MPa-level pressure-bearing equipment, which is produced by the invention, has extremely low control of the content of P, S harmful elements, and the mechanical properties of the steel plate are that the R p0.2≤930MPa、1100MPa≤Rm MPa is less than or equal to 1200MPa at normal temperature and the elongation A is more than or equal to 19 percent; impact energy KV 2 is more than or equal to 100J at 0 ℃. The mechanical properties of the formed and heat-treated steel at normal temperature are 950 MPa- p0.2 MPa-1100 MPa, 1300 MPa-1430 MPa and elongation A-19%; at 400 ℃,560 MPa- 0.2 MPa; impact power KV 2 is more than or equal to 120J at 0 ℃.
The present invention has been properly and fully described in the foregoing embodiments by way of example only, and not by way of limitation, and various changes and modifications may be made by one skilled in the art without departing from the spirit and scope of the invention, any modification, equivalent substitution, improvement, etc. should be included in the scope of the invention, and the scope of the invention is defined by the claims.
Claims (10)
1. A thick steel plate for 1300 MPa-level pressure equipment is characterized in that the steel plate comprises the following ：C 0.19％～0.23％、Si 0.10％～0.40％、Mn 0.40％～0.70％、P≤0.010％、S≤0.003％、Cr 1.40％～2.0％、Mo 0.40％～0.60％、B 0.001％～0.005％、Alt0.015％～0.045％, weight percent of Fe and unavoidable impurities as the rest.
2. The thick steel plate for 1300MPa grade pressure equipment of claim 1, wherein the thickness of the thick steel plate for pressure equipment is 40-80 mm; the mechanical property of the thick steel plate for the pressure-bearing equipment is more than or equal to 930MPa and less than or equal to 1430MPa, wherein R p0.2≤1080MPa、1300MPa≤Rm; impact power KV 2 is more than or equal to 100J at 0 ℃.
3. A method for manufacturing a thick steel plate for 1300 MPa-level pressure equipment according to claim 1 or 2, comprising smelting, continuous casting, heating, controlled rolling, controlled cooling and tempering; the method is characterized in that:
heating: the heating temperature is controlled to 1180-1230 ℃, and the total heating time is 4.0-6.0 h;
And (3) rolling control: the rolling adopts a two-stage control rolling method, the rolling end temperature of a recrystallization zone is more than or equal to 1000 ℃, and the total deformation rate is more than or equal to 50%; the rolling temperature of the non-recrystallized region is 870-930 ℃, the finishing temperature is 830-870 ℃, and the total deformation rate is more than or equal to 55%;
and (3) cooling control: the cooling temperature is 780-820 ℃, the cooling rate is 30-55 ℃/s, and the reddening temperature is 450-500 ℃;
tempering: the tempering temperature is 650-700 ℃, and the net heat preservation time is 2.0-4.0 min/mm.
4. A method for manufacturing a thick steel plate for 1300 MPa-level pressure equipment according to claim 3; the method is characterized in that: smelting: smelting molten steel in a converter, wherein high-quality scrap steel and molten iron are adopted as raw materials, the content of molten iron is controlled to be 75% -85%, dephosphorization and decarburization are separately smelted by adopting the converter, wherein dephosphorization oxygen blowing is controlled to be 7-10 min, decarburization oxygen blowing is controlled to be 8-12 min, and finally the mass fraction of phosphorus is reduced to be within 0.006%; deep desulfurization treatment is carried out in an LF refining furnace, and the sulfur content is controlled below 0.002%; degassing is completed in a VD furnace, the net circulation time is 10-15 min, and the sedation time is 3-5 min before casting.
5. A method for manufacturing a thick steel plate for 1300 MPa-level pressure equipment according to claim 3; the method is characterized in that: continuous casting: the superheat degree is 20-30 ℃, and the blank pulling rate during casting is 1.0-1.4 m/min; and feeding the casting blank into a stacking and slow cooling machine, wherein the stacking and slow cooling time is 24-36 h, and unstacking is performed at the temperature below 400 ℃.
6. A process for forming thick steel for 1300 MPa-level pressure equipment according to claims 1-5, characterized in that: in the forming process, the heating temperature is 930-960 ℃, the net heat preservation time is 1.0-2.0 min/mm, and the product is discharged and then enters into a brine bath to be rapidly cooled to the room temperature at the cooling rate of 35-55 ℃/s.
7. The process for forming thick steel for 1300 MPa-level pressure equipment of claim 6, wherein: and (3) carrying out short-time tempering heat treatment after the brine bath, wherein the short-time tempering heat treatment temperature is 370-400 ℃, the net heat preservation time is 0.5-1.0 h, and the microstructure of the steel after the short-time tempering heat treatment is sorbite.
8. A post-forming heat treatment process for thick steel for 1300 MPa-level pressure equipment according to any one of claims 1 to 7, characterized in that: the post-forming heat treatment is secondary hardening heat treatment, and the specific process is that the heating temperature is 400-430 ℃ and the net heat preservation time is 2.0-4.0 h.
9. The post-forming heat treatment process for thick steel for 1300 MPa-level pressure equipment of claim 8, wherein: after the secondary hardening heat treatment, the (Fe, mn, cr, mo) 23C6、Mo2 C second phase particles and boride with the volume fraction of 18-23% are precipitated in the steel.
10. The post-forming heat treatment process for thick steel for 1300 MPa-level pressure equipment of claim 8, wherein: after secondary hardening heat treatment, the mechanical property of the steel is 950 MPa- p0.2≤1100MPa、1300MPa≤Rm MPa; at 400 ℃,560MPa is less than or equal to R p0.2 and less than or equal to 630MPa; impact power KV 2 is more than or equal to 120J at 0 ℃.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN118326260A (en) * | 2024-03-28 | 2024-07-12 | 鞍钢股份有限公司 | Thick steel plate for 1100MPa grade pressure equipment, manufacturing, forming and post-heat treatment method |
Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010121191A (en) * | 2008-11-21 | 2010-06-03 | Nippon Steel Corp | High-strength thick steel plate having superior delayed fracture resistance and weldability, and method for manufacturing the same |
| JP2010180446A (en) * | 2009-02-04 | 2010-08-19 | Jfe Steel Corp | High-strength hot-rolled steel plate and method for manufacturing the same |
| KR20110061260A (en) * | 2009-12-01 | 2011-06-09 | 주식회사 포스코 | High strength steel sheet and manufacturing method |
| CN103146997A (en) * | 2013-03-28 | 2013-06-12 | 宝山钢铁股份有限公司 | Low-alloy high-toughness wear resistant steel plate and manufacturing method thereof |
| CN104480406A (en) * | 2014-11-28 | 2015-04-01 | 宝山钢铁股份有限公司 | Low-alloy high-strength high-toughness steel plate and manufacturing method thereof |
| JP2015193874A (en) * | 2014-03-31 | 2015-11-05 | Ｊｆｅスチール株式会社 | Thick steel plate excellent in abrasion resistance and manufacturing method therefor |
| CN109023119A (en) * | 2018-10-08 | 2018-12-18 | 鞍钢股份有限公司 | Wear-resistant steel with excellent ductility and toughness and manufacturing method thereof |
| CN116145024A (en) * | 2022-11-25 | 2023-05-23 | 江阴兴澄特种钢铁有限公司 | A kind of high-toughness CrMo alloy steel plate and its manufacturing method |
| WO2023087833A1 (en) * | 2021-11-22 | 2023-05-25 | 宝山钢铁股份有限公司 | High-strength steel with good weather resistance and manufacturing method therefor |
-
2024
- 2024-03-28 CN CN202410363636.6A patent/CN118326262B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010121191A (en) * | 2008-11-21 | 2010-06-03 | Nippon Steel Corp | High-strength thick steel plate having superior delayed fracture resistance and weldability, and method for manufacturing the same |
| JP2010180446A (en) * | 2009-02-04 | 2010-08-19 | Jfe Steel Corp | High-strength hot-rolled steel plate and method for manufacturing the same |
| KR20110061260A (en) * | 2009-12-01 | 2011-06-09 | 주식회사 포스코 | High strength steel sheet and manufacturing method |
| CN103146997A (en) * | 2013-03-28 | 2013-06-12 | 宝山钢铁股份有限公司 | Low-alloy high-toughness wear resistant steel plate and manufacturing method thereof |
| JP2015193874A (en) * | 2014-03-31 | 2015-11-05 | Ｊｆｅスチール株式会社 | Thick steel plate excellent in abrasion resistance and manufacturing method therefor |
| CN104480406A (en) * | 2014-11-28 | 2015-04-01 | 宝山钢铁股份有限公司 | Low-alloy high-strength high-toughness steel plate and manufacturing method thereof |
| CN109023119A (en) * | 2018-10-08 | 2018-12-18 | 鞍钢股份有限公司 | Wear-resistant steel with excellent ductility and toughness and manufacturing method thereof |
| WO2023087833A1 (en) * | 2021-11-22 | 2023-05-25 | 宝山钢铁股份有限公司 | High-strength steel with good weather resistance and manufacturing method therefor |
| CN116145024A (en) * | 2022-11-25 | 2023-05-23 | 江阴兴澄特种钢铁有限公司 | A kind of high-toughness CrMo alloy steel plate and its manufacturing method |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN118326260A (en) * | 2024-03-28 | 2024-07-12 | 鞍钢股份有限公司 | Thick steel plate for 1100MPa grade pressure equipment, manufacturing, forming and post-heat treatment method |
| CN118326260B (en) * | 2024-03-28 | 2025-06-03 | 鞍钢股份有限公司 | Thick steel plate for 1100 MPa-level pressure-bearing equipment, manufacturing, forming and post heat treatment method thereof |
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