CN116219279B - High-strength high-toughness steel for nuclear reactor containment vessel and manufacturing method thereof - Google Patents

High-strength high-toughness steel for nuclear reactor containment vessel and manufacturing method thereof Download PDF

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CN116219279B
CN116219279B CN202211665196.7A CN202211665196A CN116219279B CN 116219279 B CN116219279 B CN 116219279B CN 202211665196 A CN202211665196 A CN 202211665196A CN 116219279 B CN116219279 B CN 116219279B
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steel
percent
strength
temperature
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CN116219279A (en
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孙殿东
郑明光
王永东
王义栋
王勇
孟劲松
胡海洋
宁冬
王谊清
王爽
白玉璞
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Angang Steel Co Ltd
Shanghai Nuclear Engineering Research and Design Institute Co Ltd
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Angang Steel Co Ltd
Shanghai Nuclear Engineering Research and Design Institute Co Ltd
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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
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • G—PHYSICS
    • G21—NUCLEAR PHYSICS; NUCLEAR ENGINEERING
    • G21C—NUCLEAR REACTORS
    • G21C13/00—Pressure vessels; Containment vessels; Containment in general
    • G21C13/08—Vessels characterised by the material; Selection of materials for pressure vessels
    • G21C13/087—Metallic vessels
    • 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
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/30—Nuclear fission reactors

Abstract

The invention discloses a high-strength high-toughness steel for a nuclear reactor containment vessel and a manufacturing method thereof, wherein the steel comprises the following components: 0.12 to 0.17 percent; si:0.6 to 0.8 percent; mn:1.2 to 1.6 percent; p is less than or equal to 0.010 percent; s is less than or equal to 0.003%; ni:0.2 to 0.4 percent; cr:0.65 to 0.8 percent; mo:0.2 to 0.5 percent; v: 0.06-0.09%; al:0.05 to 0.08 percent; b:0.0005 to 0.0009 percent; zr: 0.005-0.009%. The content of [ O ] is less than or equal to 20ppm; [H] less than or equal to 1.5ppm. Adopting a high-permeability direct rolling, low-temperature quenching and high-temperature tempering heat treatment process, wherein the room-temperature tensile strength of the steel plate is more than 710MPa, the yield strength is more than or equal to 630MPa, and the elongation after breaking is more than or equal to 20%; high-temperature tensile strength at 200 ℃ is more than 670MPa, and yield strength is more than 580MPa; the impact energy at the temperature of minus 60 ℃ is more than or equal to 200J. The steel plate still maintains excellent mechanical properties after simulated post-welding heat treatment with the heat preservation temperature of 605 ℃ and the heat preservation time of 10 hours. The steel for the nuclear reactor containment vessel with the high-performance complex phase structure is obtained, and the production process is stable and concise, and is suitable for industrial mass production.

Description

High-strength high-toughness steel for nuclear reactor containment vessel and manufacturing method thereof
Technical Field
The invention belongs to the field of metal materials, and particularly relates to high-strength high-toughness steel for a nuclear reactor containment vessel and a manufacturing method thereof.
Background
The continuous development of the third generation nuclear power technology has continuously improved the toughness requirement of the steel for construction, and the ASME SA-738Gr B steel with the tensile strength grade of 585MPa, which is originally used for constructing the steel containment of the AP1000 nuclear power unit, cannot completely meet the application requirement.
According to the design requirement, the tensile strength level of the steel for the nuclear reactor containment of the novel pressurized water reactor nuclear power unit needs to be improved to more than 685MPa, and meanwhile, good plasticity and toughness are required to be maintained.
The prior domestic patents related to the steel have the problems of poor comprehensive performance, low strength and the like.
Example 1: the invention discloses a super-thick high-strength steel for a nuclear reactor containment and a manufacturing method thereof (CN 111394547A), which discloses a high-strength steel for a 110-150mm thick nuclear reactor containment and a manufacturing method thereof, wherein the composition design is C:0.15% -0.20%; si:0.15% -0.30%; mn:0.80% -1.30%; p is less than or equal to 0.010 percent; s is less than or equal to 0.005%; ni:0.65% -1.10%; cr:0.10% -0.30%; mo:0.15% -0.40%; cu:0.15% -0.20%; alt:0.02% -0.04%.
Example 2: the invention discloses a high-strength steel plate for a containment head of a pressurized water reactor nuclear power plant and a manufacturing method thereof (CN 111020405A), which are disclosed by the invention, wherein the components of the steel are designed as C:0.10-0.17%; si:0.15-0.35%; mn:1.10-1.60%; p is less than or equal to 0.015 percent; s is less than or equal to 0.008 percent; ni:0.20-0.60%; cr:0.20-0.50%; mo:0.65-0.95%; al:0.015-0.035%; nb:0.032-0.045%; cu is less than or equal to 0.050%; v is less than or equal to 0.020%, and the balance is Fe and unavoidable impurities.
Example 3: the invention discloses a thick steel plate for a containment vessel of a nuclear power plant and a manufacturing method thereof (CN 102766805A), which comprises the following components in percentage by weight: 0.06-0.15%; si:0.1-0.4%; mn:1.0-1.5%; p is less than or equal to 0.012%; s is less than or equal to 0.003%; ni:0.2-0.5%; cr is less than or equal to 0.25%; mo:0.1-0.3%; v is less than or equal to 0.05%; nb is less than or equal to 0.03%; ti is less than or equal to 0.03%; al:0.015-0.05%; ca:0.0005-0.005%. The tensile yield strength of the steel plate obtained by the method is 468-649 MPa, the tensile strength is 585-705 MPa, and the strength is low.
Example 4: the invention relates to a high-strength steel plate for a nuclear reactor containment and a manufacturing method thereof (CN 102264936A), wherein the components of the steel are designed as follows: c:0.03-0.20%; si:0.15-0.55%; mn:0.9-1.5%; al:0.001-0.05%; p is less than or equal to 0.030%; s is less than or equal to 0.030%; cr is less than or equal to 0.30 percent; mo is less than or equal to 0.20 percent; ni is less than or equal to 0.60%; v is less than or equal to 0.07%; nb is less than or equal to 0.04 percent; 0.005-0.025% of Ti; n:0.0020 to 0.0060%; b:0.0005-0.0020%, ca:5ppm to 50ppm, the balance Fe and unavoidable impurities. The tensile yield strength of the steel plate is 621-648 MPa, the tensile strength is 670-700 MPa, and compared with the tensile strength, the tensile strength is lower, and the high-temperature tensile performance and the simulated post-welding heat treatment performance of the steel plate are not clear.
Disclosure of Invention
The invention provides a high-strength high-toughness steel for a nuclear reactor containment vessel and a manufacturing method thereof, and the produced steel plate has high strength (Rm is greater than 710MPa, rp0.2 is greater than or equal to 630 MPa), high toughness (-60 ℃ KV2 is greater than or equal to 200J), high temperature resistance and the like, and can meet the use requirements of the steel for the containment vessel of a novel pressurized water reactor nuclear motor unit.
The invention provides high-strength high-toughness steel for a nuclear reactor containment vessel, which comprises the following components in percentage by weight: c:0.12 to 0.17 percent; si:0.6 to 0.8 percent; mn:1.2 to 1.6 percent; p is less than or equal to 0.010 percent; s is less than or equal to 0.003%; ni:0.2 to 0.4 percent; cr:0.65 to 0.8 percent; mo:0.2 to 0.5 percent; v: 0.06-0.09%; al:0.05 to 0.08 percent; b:0.0005 to 0.0009 percent; zr: 0.005-0.009%. The content of [ O ] is less than or equal to 20ppm; [H] less than or equal to 1.5ppm, and the balance of Fe and unavoidable impurities.
The reason for adopting the components is as follows:
c: the most basic strengthening elements in the steel can effectively improve the strength of the steel plate; promoting the formation of bainite and martensite; when forming tiny dispersed carbide with Cr, V, zr and other alloy elements, the alloy can play a remarkable role in precipitation strengthening, thereby effectively improving the toughness of the steel plate. The excessive carbon content adversely affects the toughness and weldability of the steel, so that the C content in the steel of the present invention is designed to be 0.12 to 0.17%.
Si: the invention is used for improving the crack propagation resistance of bainite, thereby improving the low-temperature toughness of the steel plate, having a certain solid solution strengthening effect and effectively improving the strength of the steel plate. The silicon content is too high, inclusion is easy to form, and the purity of the steel is damaged. Therefore, the Si content of the invention is designed to be 0.6-0.8%.
Mn: the strength and hardenability of the steel plate are improved, and the steel plate is matched with Si, so that the toughness of a bainite structure is improved; the alloy is used together with Cr and Mo to inhibit the tempering brittleness of the steel plate, thereby improving the comprehensive performance of the steel plate after heat treatment. The Mn content of the invention is 1.2-1.6%.
P: the lower the content is, the better the composition is, but the invention requires controlling P in steel to be less than or equal to 0.010% in view of steelmaking conditions and cost.
S: sulfide inclusions are easy to form in steel, the impact toughness of the steel is reduced, and S is controlled to be less than or equal to 0.003 percent.
Ni: the invention is used for improving the low-temperature toughness of the steel plate, improving the structural stability of the steel plate and improving the toughness of the steel plate, and the Ni content is 0.2-0.4%.
Cr: the invention is used for improving the strength, especially the high temperature resistance of the steel, effectively improving the hardenability of the steel plate, promoting the generation of bainite and martensite, refining the structure in heat treatment and improving the toughness of the steel plate. The Cr content in the steel is designed to be 0.65-0.8%.
Mo: the steel plate tempering agent is used for improving the tempering stability of the steel plate, is used in combination with Cr and Mn, and improves the comprehensive performance of the steel plate after heat treatment. The Mo content of the invention is designed to be 0.2-0.5%.
V: fine VC can be formed in the steel, so that a strong precipitation strengthening effect is achieved; grain boundaries can be pinned in controlled rolling, and ferrite grains are refined; and the dislocation is prevented from being combined and disappeared by dispersion precipitation in heat treatment, so that the tempering resistance of the steel plate is improved. The V content of the invention is controlled to be 0.06-0.09%.
Al: the method is used for fixing the residual nitrogen and oxygen in the steel and improving the effectiveness of B; plays a certain solid solution strengthening role and improves the high-temperature strength of the steel plate. The Al content of the invention is controlled to be 0.05-0.08%.
B: the method is used for improving the hardenability of the steel plate and improving the uniformity of the thickness section tissue performance of the steel plate. The content of B in the invention is designed to be 0.0005 to 0.0009 percent
Zr: the fine dispersed carbonitride is formed in the steel, so that the cast structure of the steel can be effectively improved, the coarsening temperature of the reheated austenite can be increased, and the growth of the austenite can be restrained in high-temperature rolling. The Zr content in the steel of the invention is controlled to be 0.005 to 0.009 percent
H and O: hydrogen and oxygen are harmful elements in steel, and hydrogen dissolved in steel can cause defects such as hydrogen embrittlement, white spots and the like of steel. Oxygen is easy to form oxide inclusion in steel, and the strength and plasticity of the steel are reduced, so that the invention controls [ H ] to be less than or equal to 1.5ppm and [ O ] to be less than or equal to 20ppm.
The invention provides a method for manufacturing high-strength high-toughness steel for a nuclear reactor containment vessel, which comprises the following steps of converter smelting, continuous casting, heating, rolling and heat treatment:
heating the continuous casting blank in a step furnace at 1140-1180 ℃ for 4-6h;
the rolling start temperature is 1060-1110 ℃, the single-pass deformation of the first 3 passes is more than or equal to 40mm, the final rolling temperature is 860-920 ℃, and the thickness of the rolled steel plate is less than or equal to 80mm; stacking and slowly cooling rolled steel plates for more than 24 hours;
the steel plate is subjected to off-line quenching and tempering heat treatment, wherein the quenching and heat preservation temperature is 840-880 ℃, the heat preservation time is 60-160 min, and the quenching cooling rate is controlled at 5-10 ℃/s; tempering and heat preserving temperature is 600-640 ℃, heat preserving time is 3-7 min/mm, and air cooling is carried out after discharging.
Further, the converter smelting is controlled to be less than or equal to 0.010 percent of P, less than or equal to 0.003 percent of S, less than or equal to 1.5ppm of [ H ] and less than or equal to 20ppm of [ O ] through a converter and external refining process, and nonmetallic inclusion in steel is reduced to be less than or equal to 1.0 grade.
Further, in the continuous casting, the superheat degree of the tundish is controlled to be 15+/-5 ℃, and the blank drawing speed is controlled to be 1.1-1.3 m/min.
Further, a dynamic soft reduction mode is adopted at the tail end of continuous casting, and the total reduction is 6-10 mm.
Further, the thickness of the continuous casting billet is 200-300 mm, and the continuous casting billet is stacked and slowly cooled for more than 24 hours after being taken off line.
The invention provides a high-strength high-toughness steel for a nuclear reactor containment vessel and a manufacturing method thereof, and compared with the prior art, the steel has the following beneficial effects:
the invention realizes the high-quality production of the high-Si low-alloy continuous casting billet through the effective control of smelting and continuous casting processes.
The invention obtains the steel for the nuclear reactor containment with the high-performance complex phase structure by the innovative design of chemical components and the combination of the high-permeability direct rolling, the low-temperature quenching and the high-temperature tempering heat treatment process, and the production process is stable and concise and is suitable for industrial batch production.
The steel plate for the nuclear reactor containment vessel, which is produced by adopting the technical scheme of the invention, has the room temperature tensile strength more than 710MPa, the yield strength more than or equal to 630MPa and the elongation after fracture more than or equal to 20 percent; high-temperature tensile strength at 200 ℃ is more than 670MPa, and yield strength is more than 580MPa; the impact energy at the temperature of minus 60 ℃ is more than or equal to 200J. The steel plate still maintains excellent mechanical properties after simulated post-welding heat treatment with the heat preservation temperature of 605 ℃ and the heat preservation time of 10 hours.
Drawings
FIG. 1 is a typical metallographic structure diagram (tempered sorbite 68% and tempered bainite 32%) of an example of the present invention.
Detailed Description
The invention provides a manufacturing method of high-strength high-toughness steel for a nuclear reactor containment vessel, which comprises the steps of converter smelting, continuous casting, rolling and heat treatment, and specifically comprises the following steps:
the steel plate is produced by adopting continuous casting billets. Through the converter and external refining process, P is controlled to be less than or equal to 0.010 percent, S is controlled to be less than or equal to 0.003 percent, H is controlled to be less than or equal to 1.5ppm, O is controlled to be less than or equal to 20ppm, and nonmetallic inclusion in steel is reduced to be less than or equal to 1.0 grade.
In continuous casting, the superheat degree of a tundish is controlled to be 15+/-5 ℃, a dynamic soft reduction mode is adopted at the tail end of continuous casting, the total reduction is 6-10 mm, and the blank drawing speed is controlled to be 1.1-1.3 m/min. Because the Si content is higher, si promotes the formation of columnar crystals in the steel, and in order to inhibit the formation of columnar crystals and promote the formation of equiaxial crystals, the invention effectively improves the as-cast structure of the continuous casting billet and reduces center segregation and looseness to be 1.0 level or below by adding a proper amount of Zr and combining a low superheat degree continuous casting process. The thickness of the continuous casting blank is preferably 200-300 mm, and after the continuous casting blank is off-line, stacking and slow cooling are carried out for more than 24 hours, so that the tissue homogenization and the precipitate dispersion distribution are further promoted, and the internal defects of the casting blank are eliminated or reduced.
Heating the continuous casting blank in a stepping furnace at 1140-1180 ℃ for 4-6h to promote the full solid solution and full and uniform heating of V. And (5) after the continuous casting billet is discharged from the furnace, performing high-pressure water descaling to remove surface iron scales. The initial rolling temperature is 1060-1110 ℃, the single-pass deformation of the first 3 passes is more than or equal to 40mm, and the final rolling temperature is 860-920 ℃. High-permeability rolling, fully refining the structure grains, promoting the dispersion and precipitation of the precipitates and improving the toughness of the steel plate.
The thickness of the rolled steel plate is less than or equal to 80mm. And after rolling, the steel plates are stacked and slowly cooled, the slow cooling time is more than 24 hours, the internal stress of the steel plates is fully released, good plate shape is ensured, meanwhile, the slow cooling is favorable for tissue homogenization and precipitate dispersion distribution, and the tissue property uniformity of the steel plates is improved.
The steel plate adopts off-line quenching and tempering heat treatment, wherein the quenching and heat preservation temperature is 840-880 ℃, the heat preservation time is 60-160 min, the quenching cooling rate is controlled at 5-10 ℃/s, the generation of martensite and bainite is promoted, and meanwhile, the structure is refined. Tempering and heat preserving temperature is 600-640 ℃, heat preserving time is 3-7 min/mm, and air cooling is carried out after discharging. And tempering to obtain tempered sorbite and tempered bainite complex phase structure (the tempered sorbite accounts for 65-70 percent and the tempered bainite accounts for 30-35 percent), and improving the toughness of the steel plate.
A high-strength high-toughness steel for a nuclear reactor containment vessel and a manufacturing method thereof, the specific embodiments are as follows: the chemical compositions of the examples are shown in Table 1, the process parameters of the steel of the examples are shown in Table 2, and the properties of the steel sheet of the examples are shown in tables 3 and 4.
Table 1 chemical composition (%)
Table 2 process parameters of the steels of the examples
TABLE 3 quenched and tempered properties of Steel plates
Samples were taken from each example for a simulated post-weld heat treatment test, the process being: the temperature is kept at 605 ℃, the temperature keeping time is 10 hours, and the temperature rising and falling rate above 420 ℃ is not more than 80 ℃/h. The test performance is shown in Table 4.
Table 4 properties of steel sheet after simulated post-weld heat treatment

Claims (9)

1. The high-strength high-toughness steel for the nuclear reactor containment vessel is characterized by comprising the following components in percentage by weight: 0.12 to 0.17 percent; si:0.6 to 0.8 percent; mn:1.2 to 1.6 percent; p is less than or equal to 0.010 percent; s is less than or equal to 0.003%; ni:0.2 to 0.4 percent; cr:0.65 to 0.8 percent; mo:0.2 to 0.5 percent; v: 0.06-0.09%; al:0.05 to 0.08 percent; b:0.0005 to 0.0009 percent; zr: 0.005-0.009%; the content of [ O ] is less than or equal to 20ppm; [H] less than or equal to 1.5ppm, and the balance of Fe and unavoidable impurities; the manufacturing method of the steel comprises converter smelting, continuous casting, heating, rolling and heat treatment, wherein,
heating the continuous casting blank in a step furnace at 1140-1180 ℃ for 4-6h;
the rolling start temperature is 1060-1110 ℃, the single-pass deformation of the first 3 passes is more than or equal to 40mm, the final rolling temperature is 860-920 ℃, and the thickness of the rolled steel plate is less than or equal to 80mm; stacking and slowly cooling rolled steel plates for more than 24 hours;
the steel plate is subjected to off-line quenching and tempering heat treatment, wherein the quenching and heat preservation temperature is 840-880 ℃, the heat preservation time is 60-160 min, and the quenching cooling rate is controlled at 5-10 ℃/s; tempering and heat preserving temperature is 600-640 ℃, heat preserving time is 3-7 min/mm, and air cooling is carried out after discharging.
2. The high strength, high toughness steel for nuclear reactor containment according to claim 1, wherein the steel sheet has a thickness of 80mm or less.
3. The high strength, high toughness steel for nuclear reactor containment according to claim 1, wherein tempered sorbite is 65-70% and tempered bainite is 30-35%.
4. The high-strength high-toughness steel for nuclear reactor containment according to claim 1, wherein the tensile strength at room temperature is more than 710MPa, the yield strength is more than or equal to 630MPa, and the elongation after break is more than or equal to 21%; high-temperature tensile strength at 200 ℃ is more than 670MPa, and yield strength is more than 580MPa; impact energy at 60 ℃ below zero is more than 200J.
5. The high-strength high-toughness steel for a nuclear reactor containment vessel according to claim 1, wherein after the steel plate is subjected to simulated post-weld heat treatment at a temperature of 605 ℃ for 10 hours at a temperature rise and fall rate of not more than 80 ℃/h at 420 ℃, the room-temperature tensile strength of the steel plate is more than 690MPa, the yield strength is more than or equal to 600MPa, and the elongation after break is more than or equal to 22%; high-temperature tensile strength at 200 ℃ is more than 635MPa, and yield strength is more than 545MPa; impact energy at 60 ℃ below zero is more than 200J.
6. The steel for a high-strength and high-toughness nuclear reactor containment vessel according to claim 1, wherein the converter smelting is controlled by a process of converter+external refining to control P to 0.010%, S to 0.003%, H to 1.5ppm, O to 20ppm, and nonmetallic inclusion to 1.0 level.
7. The high-strength and high-toughness steel for nuclear reactor containment according to claim 1, wherein in the continuous casting, the superheat degree of the tundish is controlled to 15±5 ℃ and the withdrawal speed is controlled to 1.1 to 1.3m/min.
8. The high-strength high-toughness steel for nuclear reactor containment vessel according to claim 1, wherein a dynamic soft reduction mode is adopted at the end of continuous casting, and the total reduction is 6-10 mm.
9. The high-strength high-toughness steel for nuclear reactor containment vessel according to claim 1, wherein the thickness of the continuous casting billet is 200-300 mm, and the steel is stacked and slowly cooled for more than 24 hours after the steel is taken off line.
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