CN118326262B - Thick steel plate for 1300 MPa-level pressure-bearing equipment, manufacturing, forming and post heat treatment method thereof - Google Patents
Thick steel plate for 1300 MPa-level pressure-bearing equipment, manufacturing, forming and post heat treatment method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 125
- 239000010959 steel Substances 0.000 title claims abstract description 125
- 238000010438 heat treatment Methods 0.000 title claims abstract description 53
- 238000000034 method Methods 0.000 title claims abstract description 40
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 28
- 238000005496 tempering Methods 0.000 claims abstract description 27
- 238000005096 rolling process Methods 0.000 claims abstract description 21
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 229910052742 iron Inorganic materials 0.000 claims abstract description 13
- 238000003723 Smelting Methods 0.000 claims abstract description 10
- 238000009749 continuous casting Methods 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 229910052796 boron Inorganic materials 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 230000008569 process Effects 0.000 claims description 31
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 18
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical group OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 claims description 17
- 238000000465 moulding Methods 0.000 claims description 17
- 238000005266 casting Methods 0.000 claims description 12
- 238000004321 preservation Methods 0.000 claims description 12
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 6
- 238000007664 blowing Methods 0.000 claims description 6
- 238000005261 decarburization Methods 0.000 claims description 6
- 229910052760 oxygen Inorganic materials 0.000 claims description 6
- 239000001301 oxygen Substances 0.000 claims description 6
- 239000002245 particle Substances 0.000 claims description 6
- 238000001953 recrystallisation Methods 0.000 claims description 5
- 238000010583 slow cooling Methods 0.000 claims description 5
- 229910015417 Mo2 C Inorganic materials 0.000 claims description 4
- 239000012267 brine Substances 0.000 claims description 4
- HPALAKNZSZLMCH-UHFFFAOYSA-M sodium;chloride;hydrate Chemical compound O.[Na+].[Cl-] HPALAKNZSZLMCH-UHFFFAOYSA-M 0.000 claims description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 3
- 238000007872 degassing Methods 0.000 claims description 3
- 238000006477 desulfuration reaction Methods 0.000 claims description 3
- 230000023556 desulfurization Effects 0.000 claims description 3
- 239000011574 phosphorus Substances 0.000 claims description 3
- 239000002994 raw material Substances 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 3
- 239000011593 sulfur Substances 0.000 claims description 3
- 238000009740 moulding (composite fabrication) Methods 0.000 description 19
- 229910001566 austenite Inorganic materials 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 238000011161 development Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 238000013461 design Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 229910000521 B alloy Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 206010039897 Sedation Diseases 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 239000003245 coal Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000007599 discharging Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 230000036280 sedation Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 239000003638 chemical reducing agent Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
Classifications
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y40/00—Manufacture or treatment of nanostructures
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/064—Dephosphorising; Desulfurising
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- C21D8/0247—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
-
- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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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
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- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
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- Nanotechnology (AREA)
- Condensed Matter Physics & Semiconductors (AREA)
- General Physics & Mathematics (AREA)
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- Heat Treatment Of Steel (AREA)
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, wherein the mechanical properties of the formed and heat-treated steel at normal temperature are 950 MPa-or-less R p0.2 -or-less 1100MPa, 1300 MPa-or-less Rm-or-less 1430MPa, and elongation A-or-less 19%, at 400 ℃,560 MPa-or-less Rp 0.2 -or-less 630MPa, and at 0 ℃ impact power KV 2 -or-more 120J, and the use requirements of high-strength pressure-bearing equipment are 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 tensile strength of a steel plate of the steel for the bearing equipment applied to the nuclear power field 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 technical scheme after molding and data support, and has enough strength to meet the service requirement of high-pressure clothing.
The invention discloses a steel plate for hot-rolled weldable pressure-bearing equipment and a production method thereof (publication No. CN 110983175A), and the steel plate 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 forming to manufacture 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 within 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 existing pressure-bearing equipment cannot meet the development requirement of new energy equipment, so that development of high-strength key materials for 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 required, 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 steel plate is insufficient or the strength of the steel plate cannot be improved after the steel plate is molded, and provides a steel product for the pressure-bearing equipment, and the steel product, the manufacturing process, the molding process and the post heat treatment process for the pressure-bearing equipment are used for manufacturing the steel plate with the thickness specification (40-80) mm and the tensile strength of 1300MPa after the steel plate is molded, so that the steel product can meet the manufacturing requirement of the ultra-high-strength pressure-bearing equipment.
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 930MPa or less and R p0.2≤1080MPa、1300MPa≤Rm or less and 1430MPa or less, and the impact power KV 2 or more 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, so the invention limits the C content to 0.19% -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 the 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 0.10% -0.40%.
Mn is an element for strongly stabilizing austenite, can effectively reduce the decomposition speed of austenite, improves 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 Mn content range is limited 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%.
The hardenability of the steel is improved by B, and meanwhile, the strength of the steel is improved by utilizing high-hardness boride formed by boron, but the boron content exceeds 0.007% to cause the hot embrittlement phenomenon of the steel, so that the forming processability of pressure-bearing equipment is affected.
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 molten steel, namely smelting the molten steel in a converter, wherein high-quality scrap steel and molten iron are adopted as raw materials, the content of the 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 oxygen blowing is controlled to be 7-10 min, decarburization oxygen blowing is controlled to be 8-12 min, the phosphorus mass fraction is finally reduced to be less than 0.006%, deep desulfurization treatment is carried out in an LF refining furnace, the sulfur content is controlled to be less than 0.002%, degassing is completed in a VD furnace, the net circulation time is 10-15 min, and the sedation time before casting is 3-5 min.
And (3) continuous casting, namely casting by adopting a slab continuous casting machine after vacuum breaking, 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, and unstacking the casting blank at the temperature of 400 ℃ for 24-36 hours after the stacking and slow cooling machine so as to prevent the defects of cracks and the like of the casting blank caused by quenching.
Heating, namely controlling the heating temperature to 1180-1230 ℃ and the total heating time to 4.0-6.0 hours.
The rolling adopts a two-stage controlled 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 the moment, austenite grains are further flattened and elongated, along with the increase of the area of grain boundaries, 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) controlling cooling, namely controlling cooling process is adopted for rolling and starting the steel plate to further refine the internal structure of the thick steel plate, the cooling temperature is 780-820 ℃, the cooling rate is 30-55 ℃ per second, and the reddening temperature is 450-500 ℃.
Tempering, namely, adding more C, mn, cr, mo solid solution strengthening elements into the steel, and obtaining the lath martensitic structure with ultrahigh strength and hardness after rolling the steel plate. 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 molding process of the thick steel plate for 1300 MPa-grade pressure equipment, wherein the molding is a necessary procedure from the steel plate to the pressure 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 that the molding process is to keep the temperature at 930-960 ℃ for 1.0-2.0 min/mm, and the molding process is cooled to room temperature in a salt water bath after discharging. The chemical element and the B alloy element enter an austenite region in the process C, mn, cr, mo, after a period of heat preservation, the alloy element is dissolved in an austenite matrix in a solid mode, then enters a saline water bath at 0-10 ℃ to be rapidly cooled and transformed into a fine lath martensite structure at 35-55 ℃ per second, and the steel has ultrahigh strength 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 of heat preservation for 0.5-1.0 h at 370-400 ℃, 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 a thick steel plate for 1300 MPa-level pressure equipment, which is obtained by further adjusting the size and the type of second phase particles in steel in order to ensure the ultra-high strength and the excellent ductility and toughness of the steel for pressure equipment, namely, the post-hardening heat treatment process is that the heating temperature is 400-430 ℃, the net heat preservation is carried out for 2.0-4.0 h, stable (Fe, mn, cr, mo) 23C6、Mo2 C second phase particles and boride with the size of 10-30 nm are separated out in the steel, the volume percentage is 18-23%, the interaction with sorbite high-density dislocation is carried out, the strong plasticity of a matrix is improved, the mechanical properties of the formed and heat treated steel at normal temperature are 950MPa or less than or equal to 1100MPa, 1300MPa or less than or equal to 1430MPa, elongation A or equal to 19%, 560MPa or less than 32630 MPa at 400 ℃, KV power is 2 or equal to 120J, and the use requirement of the 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 shown as 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 obtains a 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 steel plate is ensured to have 1300MPa strength and better plasticity and toughness after molding.
(4) The mechanical properties of the steel plate for the pressure equipment obtained through the special production process are that the R p0.2≤1100MPa、1300MPa≤Rm MPa is less than or equal to 950MPa at normal temperature, the R p0.2 MPa is less than or equal to 560MPa at 400 ℃, and the impact power KV 2 is more than or equal to 120J at 0 ℃.
(5) The invention obtains the 1300 MPa-grade high-strength steel plate for the pressure-bearing equipment with the thickness specification of (40-80) mm.
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, namely controlling the heating temperature to 1180-1230 ℃ and the total heating time to 4.0-6.0 h;
The rolling is controlled by adopting a two-stage controlled rolling method, the rolling end temperature of a recrystallization zone is more than or equal to 1000 ℃, the total deformation rate is more than or equal to 50%, the rolling start temperature of a non-recrystallization zone is 870-930 ℃, the final rolling temperature is 830-870 ℃, and the total deformation rate is more than or equal to 55%;
controlling cooling, namely controlling the cooling temperature to 780-820 ℃, the cooling rate to 30-55 ℃ per second and the reddening temperature to 450-500 ℃;
Tempering, namely, the tempering temperature is 650-700 ℃, and the heat preservation is 2.0-4.0 min/mm.
Smelting, namely smelting molten steel in a converter, wherein high-quality scrap steel and molten iron are adopted as raw materials, the content of the molten iron is controlled to be 75% -85%, dephosphorization and decarburization are separately smelted in the converter, dephosphorization oxygen blowing is controlled to be 7% -10 min, decarburization oxygen blowing is controlled to be 8% -12 min, the phosphorus mass fraction is finally reduced to be less than 0.006%, deep desulfurization treatment is carried out in an LF refining furnace, the sulfur content is controlled to be less than 0.002%, degassing is completed in a VD furnace, the net circulation time is 10% -15 min, and the sedation time before casting is 3% -5 min.
And further, continuous casting, wherein the superheat degree is 20-30 ℃, and the blank pulling rate during casting is 1.0-1.4 m/min. The casting blank is put down into a stack for slow cooling, stacking and slowly cooling for 24-36 h, and unstacking at the temperature below 400 ℃.
A molding process of thick steel for 1300 MPa-level pressure equipment comprises the steps of heating to 930-960 ℃ in the molding process, enabling the net heat preservation time to be 1.0-2.0 min/mm, discharging, and rapidly cooling to room temperature in a brine bath at a cooling rate of 35-55 ℃.
And further, 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 at a heating temperature of 400-430 ℃ and the net heat preservation time is 2.0-4.0 h.
Further, after the secondary hardening heat treatment, the (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 of the second phase particles and boride 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 ℃,560 MPa- p0.2 MPa, at 0 ℃ and impact energy KV 2 -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°C)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 over 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 800MPa and less than or equal to 1200MPa at normal temperature, the elongation A is more than or equal to 19%, and the 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-or-less R p0.2 -or-less 1100MPa, 1300 MPa-or-less Rm-or-less 1430MPa, elongation A-or-more 19%, 560 MPa-or-less Rp 0.2 -or-less 630MPa at 400 ℃ and impact energy KV 2 -or-more 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 (8)
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%、Alt 0.015%~0.045%, weight percent of Fe and unavoidable impurities as the rest;
The manufacturing method of the thick steel plate for 1300 MPa-level pressure equipment comprises smelting, continuous casting, heating, rolling control, cooling control and tempering;
Heating, namely controlling the heating temperature to 1180-1230 ℃ and the total heating time to 4.0-6.0 h;
The rolling is controlled by adopting a two-stage controlled rolling method, the rolling end temperature of a recrystallization zone is more than or equal to 1000 ℃, the total deformation rate is more than or equal to 50%, the rolling start temperature of a non-recrystallization zone is 870-930 ℃, the final rolling temperature is 830-870 ℃, and the total deformation rate is more than or equal to 55%;
controlling cooling, namely, the cooling temperature is 780-820 ℃, the cooling rate is 30-55 ℃ per second, and the redback temperature is 450-500 ℃;
Tempering, namely tempering temperature is 650-700 ℃, and the net heat preservation time is 2.0-4.0 min/mm.
2. The thick steel plate for 1300 MPa-level pressure equipment, which is disclosed in claim 1, is characterized in that the thickness of the thick steel plate for the pressure equipment is 40-80 mm, the mechanical property of the thick steel plate for the pressure equipment is 930 MPa- p0.2≤1080MPa、1300MPa≤Rm MPa-1430 MPa, and the impact power KV 2 -100J at 0 ℃.
3. A thick steel plate for 1300MPa grade pressure-bearing equipment according to claim 1 is characterized in that smelting is carried out in a converter, high-quality scrap steel and molten iron are adopted as raw materials, the molten iron content is controlled to be 75% -85%, dephosphorization and decarburization are separately smelted in the converter, dephosphorization oxygen blowing is controlled to be 7-10 min, decarburization oxygen blowing is controlled to be 8-12 min, the phosphorus mass fraction is finally reduced to be less than 0.006%, deep desulfurization treatment is carried out in an LF refining furnace, the sulfur content is controlled to be less than 0.002%, degassing is completed in a VD furnace, the net circulation time is 10-15 min, and the calm time before casting is started is 3-5 min.
4. The thick steel plate for 1300 MPa-level pressure equipment, which is characterized by continuous casting, wherein the superheat degree is 20-30 ℃, the blank pulling rate during casting is 1.0-1.4 m/min, the casting blank is fed into a stack for slow cooling, the stack slow cooling time is 24-36 h, and the unstacking is lower than 400 ℃.
5. A molding process of a thick steel plate for 1300 MPa-grade pressure equipment according to any one of claims 1-4 is characterized in that in the molding process, heating temperature is 930-960 ℃, net heat preservation time is 1.0-2.0 min/mm, the thick steel plate is discharged and then enters a brine bath to be cooled to room temperature at a cooling rate of 35-55 ℃ per second, short tempering heat treatment is carried out after the brine bath, the short tempering heat treatment temperature is 370-400 ℃, net heat preservation time is 0.5-1.0 h, and microstructure of steel after the short tempering heat treatment is sorbite.
6. The molding process according to claim 5, wherein the molding process is further followed by a secondary hardening heat treatment, the specific process is heating at 400-430 ℃ for a net heat preservation time of 2.0-4.0 h.
7. The molding process according to claim 6, wherein the secondary hardening heat treatment is performed to precipitate (Fe, mn, cr, mo) 23C6、Mo2 C second phase particles and boride of 10-30 nm grade in the steel, and the volume fraction thereof is 18% -23%.
8. The molding process according to claim 6, wherein the mechanical properties of the steel after the secondary hardening heat treatment are 950 MPa- p0.2≤1100MPa、1300MPa≤Rm MPa, 560 MPa- p0.2 MPa, and impact energy KV 2 -120J at 400 ℃.
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