CN113930692A - High-homogenization super-thick steel plate for advanced pressurized water reactor nuclear power station and manufacturing method thereof - Google Patents
High-homogenization super-thick steel plate for advanced pressurized water reactor nuclear power station and manufacturing method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- 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
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/40—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
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/40—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
Abstract
The invention provides a high-homogenization super-thick steel plate for an advanced pressurized water reactor nuclear power station and a manufacturing method thereof, wherein the steel plate comprises the following components in percentage by weight: c: 0.1 to 0.35 percent; mn: 0.30% -1.50%; p is less than or equal to 0.010 percent; s is less than or equal to 0.005 percent; cr: 0.10 to 3.30 percent; 0.10 to 3.90 percent of Ni; 0.01 to 0.60 percent of Mo; v: 0.001% -0.020%; cu: 0.01 to 2.10 percent; ca is less than or equal to 0.030 percent; ti: 0.001 to 0.020 percent, and the balance of Fe and inevitable impurities. The manufacturing method comprises smelting, continuous casting, assembling, rolling and tempering; after the steel plate produced by the invention is subjected to quenching and tempering treatment and simulated postweld heat treatment, the-20 ℃ impact absorption energy is respectively kept above 122J and above 107J; the tensile strength of the steel plate at the positions of 1/2 and 1/4 is less than or equal to 25 MPa.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a high-homogenization super-thick steel plate for an advanced pressurized water reactor nuclear power station and a manufacturing method thereof.
Background
At present, nuclear power stations operated in China are mainly pressurized water reactor nuclear power stations, some extra-thick and super-thick steel plates in the nuclear power stations are generally produced by forging large steel ingots, but the process has the major problems that 'two-in-one' is often generated, the conditions of serious chemical composition segregation, coarse grain structure and standard exceeding of non-metallic inclusions exist in the large steel ingots, the performance of equipment materials is often unqualified due to the genetic effect of the nonuniformity of the materials, and the problem seriously influences the manufacturing period and the stability of the equipment.
The invention removes the phenomena of chemical composition segregation, coarse grain structure and excessive non-metallic inclusions in the material through the high-temperature heating of the original blank, the special high-temperature rolling process and the high steel rolling speed design, combines the design in the aspect of alloy elements, and is matched with the proper rolling and heat treatment process, thereby ensuring that the performance of the steel plate in different states meets the requirements.
The related patent documents of the nuclear power ultra-thick steel produced at present are as follows:
(1) the invention discloses a three-generation nuclear power station high-shear strength extra-thick composite steel plate and a manufacturing method thereof (patent number ZL201810890483.5), and the invention relates to a manufacturing method of a heterogeneous composite steel plate, wherein the composite effect of the composite plate is good, the thickness of a single composite plate can reach 110mm, the shear strength of an interface is more than 400MPa, and the I-grade standard bonding rate requirement of GB/T8165 stainless steel composite steel plate and steel strip can be met by flaw detection, namely 100% bonding. However, the steel plate of the invention is a composite plate of carbon steel and stainless steel, aims at corrosion resistance, and cannot meet the requirement of an extra-thick steel plate.
(2) "a method for conditioning thick steel plate for pressure vessel" (application No. 201010154420.7) is a method for hardening and tempering thick steel plate for pressure vessel invented by Shanxi Tai Steel stainless Steel Co., Ltd, which comprises the following steps in sequence: step I, heating the steel plate to 920-930 ℃ by quenching, keeping the temperature for 45-55 minutes, and then quenching; II, tempering, heating the quenched steel plate to 630-650 ℃, preserving heat for 40-50 minutes, taking out the steel plate and cooling to room temperature; III, secondary quenching, namely heating the heated steel plate to 920-930 ℃, preserving heat for 50-60 minutes, and quenching the steel plate; IV, secondary tempering, namely, putting the steel plate after secondary quenching in a chamber furnace, requiring the temperature control fluctuation to be not more than +/-5 ℃, heating to 615-625 ℃, preserving the heat for 40-50 minutes, taking out and naturally cooling to room temperature. In the invention, the tensile strength R of the steel plate is subjected to twice quenching and tempering treatmentsmThe elongation A is increased to 630MPa and 20-23%, and the strength of the product can be reached or even exceeded by adopting one-time quenching and tempering treatment, and the cost can be greatly reduced.
(3) Among steel sheet components disclosed in Baoshan Steel Ltd entitled "Thick Steel sheet for Nuclear Power station Containment and method for producing the same" (application No. 201210269122.1): 0.06% -0.15%, Si: 0.10-0.40%, Mn: 1.0% -1.5%, Mo: 0.10-0.30%, P is less than or equal to 0.012%, S is less than or equal to 0.003%, Alt: 0.015% -0.050%, Ni: 0.20 to 0.50 percent; and V is less than or equal to 0.050%, Ti is less than or equal to 0.030%, Cr is less than or equal to 0.25%, Nb is less than or equal to 0.030%, Ca: 0.0005 to 0.0050% of at least one; the balance being Fe and unavoidable impurities. The thick steel plate for the nuclear power station containment vessel, provided by the invention, has high strength and high toughness, and the base metal and the heat affected zone have good impact toughness under the low temperature condition, so that the thick steel plate is suitable for being applied to the field of manufacturing of the nuclear power station containment vessel. However, the maximum thickness of the steel sheet in this invention is 60mm, while not providing the high temperature elongation index of 150 ℃ or 200 ℃.
Disclosure of Invention
The invention aims to overcome the problems and the defects and provide a high-homogenization super-thick steel plate for an advanced pressurized water reactor nuclear power station and a manufacturing method thereof.
The purpose of the invention is realized as follows:
a high-homogenization super-thick steel plate for an advanced pressurized water reactor nuclear power station comprises the following components in percentage by weight: c: 0.1 to 0.35 percent; mn: 0.30% -1.50%; p is less than or equal to 0.010 percent; s is less than or equal to 0.005 percent; cr: 0.10 to 3.30 percent; 0.10 to 3.90 percent of Ni; 0.01 to 0.60 percent of Mo; v: 0.001% -0.020%; cu: 0.01 to 2.10 percent; ca is less than or equal to 0.030 percent; ti: 0.001 to 0.020 percent, and the balance of Fe and inevitable impurities.
The steel plate is adjusted to have impact absorption energy of more than 122J at the temperature of minus 20 ℃; the impact absorption energy of the steel plate at the temperature of minus 20 ℃ after the simulated postweld heat treatment is more than 107J; the tensile strength of the steel plate is more than or equal to 615MPa at normal temperature; the tensile strength is more than or equal to 540MP at the high temperature of 350 ℃; the tensile strength is more than or equal to 500MPa at the high temperature of 400 ℃; the difference of the tensile strength of the steel plates at the positions of 1/2 and 1/4 is less than or equal to 25 MPa.
The invention has the following design reasons:
(1) c: c is the most effective element for strengthening structural steel, and directly influences the strength, plasticity, toughness, welding performance and the like of steel. Therefore, the steel of the present invention requires, in designing the composition, C: 0.1 to 0.35 percent.
(2) Mn: mn is a good deoxidizer and desulfurizer, a certain amount of manganese contained in the steel can eliminate or weaken the hot brittleness of the steel caused by sulfur, and meanwhile, Mn is the most main alloy element in the steel and has great influence on the comprehensive performance of the steel. Therefore, the Mn content in the actual production is controlled to be 0.30-1.50%.
(3) P: p is dissolved in ferrite, the tempering brittleness of steel is increased, the plasticity and the toughness of the steel are obviously reduced, and adverse effects are also caused on welding, so that the lower the content of phosphorus is, the better the phosphorus content is, but the P can improve the strength and the atmospheric corrosion resistance of the steel, and the P in the steel is required to be controlled to be less than or equal to 0.010 percent.
(4) S: sulfide inclusions are easily formed in steel, the impact toughness of the steel is reduced, the welding performance is damaged, the defects of center segregation, looseness and the like are aggravated, and irradiation embrittlement is increased, so that the S is required to be less than or equal to 0.005 percent.
(5) Cr: cr can remarkably improve the antioxidation of steel in steel, and because the steel for the nuclear power station belongs to steel for a nuclear power station safety shell module, the steel for the nuclear power station requires a steel plate with certain corrosion resistance, the chromium can increase the corrosion resistance, and a certain amount of chromium can also improve the hardness of the steel, the invention requires that the Cr: 0.10 to 3.30 percent.
(6) Ni: the Ni element with a certain content can reduce dislocation motion resistance in steel, and stress in the steel can be relaxed along with the reduction of the dislocation motion resistance, so that the mode of matrix tissue dislocation and substructure is formally changed by the Ni element, the toughness of the steel is improved, and the Ni content in the steel is controlled to be 0.10-3.90%.
(7) Mo: the Cr-Mo alloy system is favorable for the production of modulation steel, and meanwhile, molybdenum is a strong carbide forming element, and when the content is lower, a composite cementite is formed, so that the heat resistance can be improved, and the temper brittleness can be reduced. Therefore, the invention requires 0.01 to 0.60 percent of Mo.
(8) V: in the quenched and tempered steel, the effects of improving the strength and yield ratio of the steel, refining grains and improving the strength and toughness are mainly achieved, but vanadium has strong affinity with carbon and oxygen and influences hardenability when existing in a carbide form, so that the range of adding V into the steel is 0.001-0.020%.
(9) Ti: the plasticity and toughness can be improved in common low alloy steel, and the strength of the steel is improved because the carbon fixes nitrogen and sulfur to form titanium carbide, so that the range of Ti is controlled to be 0.001-0.020%.
(10) Cu: cu can improve the strength and the toughness, and the matching of Ni and Cu can promote the precipitation of copper elements to strengthen the core strength and the toughness. And can avoid hot embrittlement, so the invention requires that the Cu content in the steel is controlled to be 0.01-2.10%.
(11) Ca: calcium plays a certain role in deoxidation in steel making and is beneficial to refining grains. Therefore, the Ca content of the Ca is required to be less than or equal to 0.030 percent.
The second technical scheme of the invention is to provide a manufacturing method of a high-homogenization super-thick steel plate for an advanced pressurized water reactor nuclear power station, which comprises smelting, continuous casting, assembling, rolling and tempering;
(1) assembling: two or more continuous casting billets are overlapped and then welded;
wherein, the roughness requirement after the surface treatment of the continuous casting billet is less than or equal to 5 μm, the vacuum degree of the continuous casting billet is as follows: 1000Pa at 500 plus and 500 ℃ at the continuous casting billet welding preheating temperature of 300 plus.
(2) Heating: feeding the casting blank into a chamber furnace for heating, and discharging the casting blank after passing through a preheating section, a heating section and a soaking section in sequence; wherein the temperature of the preheating section is 950-1150 ℃, the temperature of the heating section is 1150-1270 ℃, the temperature of the soaking section is 1200-1250 ℃, and the furnace time is 20-30 hours;
(3) rolling: before rolling, descaling the discharged casting blank for 30-60 s by using high-pressure water, wherein the pressure of a descaling machine is 32-39 MPa; rolling in two stages: the first stage is deformation recrystallization rolling, and the rolling temperature is as follows: rolling for less than or equal to 6 passes at 1100-1250 ℃; the second stage is low-temperature austenite deformation rolling, and the finishing temperature is as follows: 950 ℃ and 1200 ℃, the number of rolling passes is more than 5, and the rolling speed is 3-5 m/s.
(4) Tempering: the quenching temperature is 850-950 ℃, and the heat preservation time is 1-6 min/mm;
the tempering temperature is 620-680 ℃, and the heat preservation time is 1-10 min/mm. After the steel plate is rolled, a quenching and tempering treatment process is adopted to obtain a fine and uniform tempered sorbite structure, and the steel plate has good comprehensive mechanical properties.
The invention has the beneficial effects that:
(1) the steel plate produced by the process technology has excellent low-temperature toughness indexes through chemical component optimization and reasonable design of process parameters. The impact absorption energy of the steel plate in a quenched and tempered state at-20 ℃ is more than 122J; the impact absorption energy of the steel plate at the temperature of minus 20 ℃ after the simulated post-welding heat treatment is more than 107J.
(2) After quenching and tempering and simulated postweld heat treatment (the heat preservation temperature is 600 ℃, and the heat preservation time is as long as 15 hours), the steel grade has good strength and toughness in different states; the tensile strength of the steel plate after the quenching and tempering heat treatment and the simulated postweld heat treatment in normal temperature stretching is more than or equal to 615MPa, and the tensile strength in high temperature stretching at 350 ℃ is more than or equal to 540 MPa. The tensile strength is more than or equal to 500MPa at the high temperature of 400 ℃, and the difference of the tensile strength of 1/2 and 1/4 steel plates is less than or equal to 25 MPa.
Drawings
FIG. 1 is a gold phase diagram of a microstructure according to example 1 of the present invention.
Detailed Description
The present invention is further illustrated by the following examples.
According to the embodiment of the invention, smelting, continuous casting, assembling, rolling and tempering are carried out according to the component ratio of the technical scheme.
(1) Assembling: two or more continuous casting billets are overlapped and then welded;
(2) heating: feeding the casting blank into a chamber furnace for heating, and discharging the casting blank after passing through a preheating section, a heating section and a soaking section in sequence; wherein the temperature of the preheating section is 950-1150 ℃, the temperature of the heating section is 1150-1270 ℃, the temperature of the soaking section is 1200-1250 ℃, and the furnace time is 20-30 hours;
(3) rolling: rolling in two stages: the first stage is deformation recrystallization rolling, and the rolling temperature is as follows: rolling for less than or equal to 6 passes at 1100-1250 ℃; the second stage is low-temperature austenite deformation rolling, and the finishing temperature is as follows: 950-1200 ℃, the number of rolling passes is more than 5, and the rolling speed is 3-5 m/s;
(4) tempering: the quenching temperature is 850-950 ℃, and the heat preservation time is 1-6 min/mm;
the tempering temperature is 620-680 ℃, and the heat preservation time is 1-10 min/mm.
Further, the method comprises the following steps of; in the casting blank process, the roughness requirement of the surface of the continuous casting blank after treatment is less than or equal to 5 microns, and the vacuum degree of the continuous casting blank is as follows: 500-1000Pa, and the welding preheating temperature of the continuous casting billet is 300-500 ℃.
Further, the method comprises the following steps of; and (4) before rolling in the step (3), descaling the discharged casting blank for 30-60 s by using high-pressure water, wherein the pressure of a descaling machine is 32-39 MPa.
The compositions of the steels of the examples of the invention are shown in table 1. The main process parameters of the steel assembly of the embodiment of the invention are shown in Table 2. The process parameters of heating and dephosphorization of the steel of the embodiment of the invention are shown in Table 3. The rolling process parameters of the steels of the examples of the invention are shown in Table 4. The heat treatment process parameters of the steels of the examples of the invention are shown in Table 5. The properties of the steels of the examples of the invention are shown in Table 6.
TABLE 1 composition (wt%) of steels of examples of the present invention
| Examples | C | Mn | P | S | Cr | Ni | Mo | V | Ti | Cu | Ga |
| 1 | 0.10 | 0.30 | 0.002 | 0.001 | 1.51 | 2.57 | 0.01 | 0.018 | 0.017 | 1.51 | 0.010 |
| 2 | 0.13 | 1.45 | 0.007 | 0.002 | 2.51 | 1.56 | 0.52 | 0.016 | 0.013 | 0.72 | 0.015 |
| 3 | 0.16 | 0.55 | 0.004 | 0.003 | 1.91 | 1.88 | 0.27 | 0.015 | 0.012 | 1.32 | 0.013 |
| 4 | 0.19 | 0.71 | 0.005 | 0.004 | 1.25 | 2.81 | 0.39 | 0.011 | 0.007 | 0.35 | 0.029 |
| 5 | 0.21 | 1.12 | 0.008 | 0.005 | 2.91 | 1.31 | 0.15 | 0.007 | 0.011 | 1.62 | 0.001 |
| 6 | 0.25 | 0.95 | 0.005 | 0.004 | 2.25 | 1.25 | 0.09 | 0.002 | 0.013 | 0.07 | 0.021 |
| 7 | 0.23 | 1.45 | 0.008 | 0.005 | 0.19 | 0.97 | 0.56 | 0.019 | 0.019 | 0.03 | 0.025 |
| 8 | 0.28 | 0.85 | 0.005 | 0.002 | 0.59 | 0.59 | 0.42 | 0.014 | 0.002 | 2.08 | 0.006 |
| 9 | 0.31 | 1.25 | 0.002 | 0.001 | 3.29 | 0.25 | 0.35 | 0.008 | 0.013 | 1.95 | 0.002 |
| 10 | 0.35 | 0.43 | 0.003 | 0.003 | 0.11 | 3.84 | 0.22 | 0.001 | 0.001 | 0.19 | 0.027 |
TABLE 2 Main Process parameters for the assembly of steels of the examples of the invention
TABLE 3 Process parameters for heating and phosphorus removal of steels of examples of the invention
TABLE 4 Rolling Process parameters of steels of examples of the invention
TABLE 5 Heat treatment Process parameters of steels of examples of the invention
| Examples | Quenching temperature/. degree.C | Holding time/min/mm | Tempering temperature/. degree.C | Holding time/min/mm |
| 1 | 894 | 1.8 | 652 | 5.2 |
| 2 | 916 | 2.2 | 643 | 5.3 |
| 3 | 901 | 2.7 | 645 | 5.7 |
| 4 | 915 | 2.5 | 634 | 4.5 |
| 5 | 932 | 3.0 | 679 | 4.0 |
| 6 | 920 | 4.5 | 637 | 5.2 |
| 7 | 910 | 6.0 | 670 | 7.2 |
| 8 | 944 | 5.0 | 679 | 8.2 |
| 9 | 852 | 3.5 | 623 | 7.2 |
| 10 | 870 | 4.0 | 679 | 9.5 |
TABLE 6 Properties of steels of examples of the invention
Remarking: simulating the postweld heat treatment process with the temperature of 605 ℃, the heat preservation time of 16h, and the temperature rise and fall rate of more than 400 ℃ of less than or equal to 55 ℃/h; the delta value is the difference in tensile strength at steel sheet thicknesses 1/2 and 1/4.
From the above, the steel plate with the specification of 130-200 mm is subjected to quenching and tempering treatment and simulated postweld heat treatment, all performance indexes completely meet the requirements, and the steel plate has good comprehensive mechanical properties.
In order to express the present invention, the above embodiments are properly and fully described by way of examples, and the above embodiments are only used for illustrating the present invention and not for limiting the present invention, and those skilled in the relevant art can make various changes and modifications without departing from the spirit and scope of the present invention, and any modifications, equivalent substitutions, improvements, etc. made by the persons skilled in the relevant art should be included in the protection scope of the present invention, and the protection scope of the present invention should be defined by the claims.
Claims (5)
1. The high-homogenization super-thick steel plate for the advanced pressurized water reactor nuclear power station is characterized by comprising the following components in percentage by weight: c: 0.1 to 0.35 percent; mn: 0.30% -1.50%; p is less than or equal to 0.010 percent; s is less than or equal to 0.005 percent; cr: 0.10 to 3.30 percent; 0.10 to 3.90 percent of Ni; 0.01 to 0.60 percent of Mo; v: 0.001% -0.020%; cu: 0.01 to 2.10 percent; ca is less than or equal to 0.030 percent; ti: 0.001 to 0.020 percent, and the balance of Fe and inevitable impurities.
2. The high-homogenization ultra-thick steel plate for the advanced pressurized water reactor nuclear power station as claimed in claim 1, wherein the impact absorption energy of the steel plate at-20 ℃ is 122J or more; the impact absorption energy of the steel plate at the temperature of minus 20 ℃ after the simulated postweld heat treatment is more than 107J; the tensile strength of the steel plate is more than or equal to 615MPa at normal temperature; the tensile strength is more than or equal to 540MPa at the high temperature of 350 ℃; the tensile strength is more than or equal to 500MPa at the high temperature of 400 ℃; the difference of the tensile strength of the steel plates at the positions of 1/2 and 1/4 is less than or equal to 25 MPa.
3. A method for manufacturing the high-homogenization super-thick steel plate for the advanced pressurized water reactor nuclear power station as claimed in claim 1 or 2, which comprises the steps of smelting, continuous casting, assembling, heating, rolling and tempering; the method is characterized in that:
(1) assembling: two or more continuous casting billets are overlapped and then welded;
(2) heating: feeding the combined casting blank into a chamber furnace for heating, and discharging the casting blank after passing through a preheating section, a heating section and a soaking section in sequence; wherein the temperature of the preheating section is 950-1150 ℃, the temperature of the heating section is 1150-1270 ℃, the temperature of the soaking section is 1200-1250 ℃, and the furnace time is 20-30 hours;
(3) rolling: rolling in two stages: the first stage is deformation recrystallization rolling, and the rolling temperature is as follows: rolling for less than or equal to 6 passes at 1100-1250 ℃; the second stage is low-temperature austenite deformation rolling, and the finishing temperature is as follows: 950-1200 ℃, the number of rolling passes is more than 5, and the rolling speed is 3-5 m/s;
(4) tempering: the quenching temperature is 850-950 ℃, and the heat preservation time is 1-6 min/mm;
the tempering temperature is 620-680 ℃, and the heat preservation time is 1-10 min/mm.
4. The method for manufacturing the high-homogenization ultra-thick steel plate for the advanced pressurized water reactor nuclear power plant as claimed in claim 3, wherein the method comprises the following steps: in the assembly process, the roughness requirement of the surface of the continuous casting billet is less than or equal to 5 microns, and the vacuum degree of the continuous casting billet is as follows: 500-1000Pa, and the welding preheating temperature of the continuous casting billet is 300-500 ℃.
5. The method for manufacturing the high-homogenization ultra-thick steel plate for the advanced pressurized water reactor nuclear power plant as claimed in claim 3, wherein the method comprises the following steps: and (4) before rolling in the step (3), descaling the discharged casting blank for 30-60 s by using high-pressure water, wherein the pressure of a descaling machine is 32-39 MPa.
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| CN114892085A (en) * | 2022-05-06 | 2022-08-12 | 鞍钢股份有限公司 | Wide and thick steel plate for advanced nuclear power unit positioning and manufacturing method thereof |
| WO2023212971A1 (en) * | 2022-05-06 | 2023-11-09 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit evaporator, and manufacturing method for steel plate |
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| CN107988550A (en) * | 2016-10-27 | 2018-05-04 | 鞍钢股份有限公司 | A kind of pressurized-water reactor nuclear power plant pressure vessel supporting steel and its manufacture method |
| CN111020405A (en) * | 2019-11-25 | 2020-04-17 | 鞍钢股份有限公司 | High-strength steel plate for pressurized water reactor nuclear power station containment shell head and manufacturing method thereof |
| CN111270145A (en) * | 2020-03-19 | 2020-06-12 | 鞍钢股份有限公司 | Ultra-thick high-strength steel plate for nuclear power station containment penetration piece and production method thereof |
| CN111270144A (en) * | 2020-03-19 | 2020-06-12 | 鞍钢股份有限公司 | High-strength steel plate for pressurized water reactor nuclear power station safety shell barrel and manufacturing method thereof |
| CN111270143A (en) * | 2020-03-19 | 2020-06-12 | 鞍钢股份有限公司 | Thick steel plate for nuclear power station containment equipment module and production method thereof |
| CN111363985A (en) * | 2020-03-19 | 2020-07-03 | 鞍钢股份有限公司 | Steel for supporting nuclear power station containment vessel and manufacturing method thereof |
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2021
- 2021-10-13 CN CN202111194019.0A patent/CN113930692B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN107988550A (en) * | 2016-10-27 | 2018-05-04 | 鞍钢股份有限公司 | A kind of pressurized-water reactor nuclear power plant pressure vessel supporting steel and its manufacture method |
| CN111020405A (en) * | 2019-11-25 | 2020-04-17 | 鞍钢股份有限公司 | High-strength steel plate for pressurized water reactor nuclear power station containment shell head and manufacturing method thereof |
| CN111270145A (en) * | 2020-03-19 | 2020-06-12 | 鞍钢股份有限公司 | Ultra-thick high-strength steel plate for nuclear power station containment penetration piece and production method thereof |
| CN111270144A (en) * | 2020-03-19 | 2020-06-12 | 鞍钢股份有限公司 | High-strength steel plate for pressurized water reactor nuclear power station safety shell barrel and manufacturing method thereof |
| CN111270143A (en) * | 2020-03-19 | 2020-06-12 | 鞍钢股份有限公司 | Thick steel plate for nuclear power station containment equipment module and production method thereof |
| CN111363985A (en) * | 2020-03-19 | 2020-07-03 | 鞍钢股份有限公司 | Steel for supporting nuclear power station containment vessel and manufacturing method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114892085A (en) * | 2022-05-06 | 2022-08-12 | 鞍钢股份有限公司 | Wide and thick steel plate for advanced nuclear power unit positioning and manufacturing method thereof |
| CN114892085B (en) * | 2022-05-06 | 2023-03-03 | 鞍钢股份有限公司 | Wide and thick steel plate for advanced nuclear power unit positioning and manufacturing method thereof |
| WO2023212971A1 (en) * | 2022-05-06 | 2023-11-09 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit evaporator, and manufacturing method for steel plate |
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| CN113930692B (en) | 2023-01-17 |
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