CN112126862A - Production method of steel for CAP passive nuclear power plant nuclear-grade mechanical module - Google Patents
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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- 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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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—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
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- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- 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
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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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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Abstract
The production method of the steel for the nuclear grade mechanical module of the CAP passive nuclear power plant comprises the following chemical components in percentage by mass: c = 0.12-0.20, and Si =0.10-0.35%, Mn = 0.40-0.65%, P ≤ 0.015%, S ≤ 0.005, V = 0.010-0.030, Ni = 0.10-0.35, Mo = 0.40-0.60, Ti = 0.010-0.080, Nb = 0.010-0.020, Cr = 1.40-2.00, B = 0.0010-0.0050%, Alt = 0.020-0.050%, and the balance of Fe and unavoidable impurities; the carbon equivalent Ceq is less than or equal to 0.65. The process comprises the steps of converter smelting, LF refining, vacuum degassing treatment, continuous casting, slab heating, rolling, quenching and tempering heat treatment. The grain size of the steel is above grade 9.0; the nonmetallic inclusions of A class, B class, C class and D class are all less than 1.5 grade; transverse impact AKV (alkyl ketene dimer) at-18 ℃ in delivery state and die welding state8Average value is more than or equal to 47J, and lateral expansion amount LENot less than 0.64mm, and can be applied to the manufacture of nuclear-grade mechanical modules of CAP passive nuclear power plants.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and relates to steel for a CAP passive nuclear power plant nuclear-grade mechanical module and a manufacturing method thereof.
Technical Field
The nuclear-grade mechanical module is composed of an equipment pipeline, a pipeline bracket, a frame steel structure and the like, the nuclear-grade mechanical module is generally installed in a loop of a nuclear island of a nuclear power plant and needs to be used in environments of high radiation, high humidity, high temperature, corrosion, earthquake resistance and the like, and the stability and the safety of the mechanical module directly influence the safe operation and the service life of the nuclear power plant, so that the technical requirements on the steel for the nuclear-grade mechanical module are very strict, and imported steel products such as SA517 strength level are generally adopted. The domestic nuclear power steel which replaces the import and has more excellent autonomous development performance and higher safety is necessary for promoting the development of the nuclear power industry in China and the export of the nuclear power technology.
SA517Gr.E normal temperature tensile property in ASME SA-517/SA-517M standard is matched with CAP1400 nuclear power technical requirement, but no specific requirement is provided for low temperature toughness and high temperature strength at 360 ℃, CAP1400 nuclear power technology has requirements for high temperature tensile at 360 ℃ and low temperature impact toughness at-18 ℃, and the requirements for conventional delivery state and simulated postweld heat treatment state (hereinafter referred to as 'die welding state') are consistent; the carbon equivalent Ceq of SA517Gr.E is not limited in the ASME SA-517/SA-517M standard, but the Ceq of the steel is less than or equal to 0.65, which is more beneficial to the performance after welding.
Disclosure of Invention
The invention aims to provide a production method of steel for a CAP passive nuclear power plant nuclear-grade mechanical module, the produced steel not only meets the requirement of consistent tensile strength at high temperature of 360 ℃ and normal temperature in a delivery state and a die welding state, but also has better impact toughness at low temperature of 18 ℃ below zero, and the normal temperature tensile strength and the 360 ℃ tensile strength of the steel in the delivery state and the die welding state can reach more than 725 Mpa.
The technical scheme of the invention is as follows:
the production method of the steel for the CAP passive nuclear power plant nuclear-grade mechanical module comprises the following chemical components, by mass, C = 0.12-0.20, Si = 0.10-0.35, Mn = 0.40-0.65, P is less than or equal to 0.015, S is less than or equal to 0.005, V = 0.010-0.030, Ni = 0.10-0.35, Mo = 0.40-0.60, Ti = 0.010-0.080, Nb = 0.010-0.020, Cr = 1.40-2.00, B = 0.0010-0.0050%, Alt = 0.020-0.050%, and the balance of Fe and inevitable impurities; the carbon equivalent Ceq is less than or equal to 0.65.
The method comprises the following process steps:
a. smelting in a converter: c is more than or equal to 0.06 and P is less than or equal to 0.012 during tapping;
b. LF refining: the white slag is kept for more than 15min, and the S discharged is less than or equal to 0.005 percent;
c. vacuum degassing treatment: the holding time is more than or equal to 12min under the condition that the vacuum degree is less than or equal to 0.5 tor; after the air is broken, Ca treatment is carried out, and a pure calcium line is fed to be more than or equal to 200 m; the soft argon blowing time is more than or equal to 15 min;
d. continuous casting: protecting and casting in the whole process; controlling the superheat degree of molten steel in the tundish at 8-18 ℃; adopting dynamic soft reduction technology, wherein the reduction is more than or equal to 6 mm;
e. heating the plate blank: the heating temperature of the plate blank before rolling is 1150-1200 ℃, and the heating speed is 7-12 min/cm.
f. Rolling: TMCP rolling is adopted, the initial rolling temperature of one stage is more than or equal to 1050 ℃, the final rolling temperature of one stage is more than 980 ℃, and the reduction rate of the last three passes is more than 15%; the initial rolling temperature of the second stage is 830-890 ℃, the final rolling temperature is 790-850 ℃, the red returning temperature is 600-650 ℃, and the accumulated reduction rate is more than 45%;
g. and (3) heat treatment: adopting a quenching and tempering heat treatment process, wherein the quenching temperature is 910-940 ℃, the heat preservation time is 20-40 min, and then cooling to room temperature with large water amount; tempering at 630-680 ℃, keeping the temperature for 30-60 min, and then air cooling.
The standard of the steel product for the CAP passive nuclear power plant nuclear-grade mechanical module refers to ASME SA-517/SA-517M and CAP1400 related nuclear power technical standards. The mechanical properties of the steel plate in delivery state and die welding state are both satisfied: the normal-temperature stretching Rp0.2 is more than or equal to 620MPa, Rm = 725-930 MPa, A50 is more than or equal to 14%, and Z is more than or equal to 45%; the high-temperature stretching at 360 ℃ is that Rp0.2 is more than or equal to 530Mpa, Rm is more than or equal to 725 Mpa; -18 ℃ transverse impact AKV8Average value is more than or equal to 47J, and lateral expansion amount LENot less than 0.64 mm. Meanwhile, the detection of the non-metallic inclusion in the delivery state meets the following requirements: the nonmetallic inclusions of A, B, C and D are all less than 1.5 grade.
The calculation formula of the carbon equivalent Ceq is as follows: ceq = C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15.
The steel for the CAP passive nuclear power plant nuclear-grade mechanical module and the manufacturing method thereof have the advantages that the carbon equivalent Ceq is less than or equal to 0.65% through reasonable chemical composition design; the cleanliness of the steel is ensured through an LF refining and vacuum degassing treatment process; the technology of TMCP, quenching and tempering is adopted, the structure of the tempered sorbite is finally obtained, and the grain size reaches 9.0-10.0 grade; the tensile strength of the steel in the delivery state, the die welding state at normal temperature and the high temperature of 360 ℃ reaches more than 725Mpa, and the steel has good low-temperature toughness and good welding performance and is 65-150 mm thick.
Drawings
FIG. 1 is a metallographic structure diagram of a sample of the steel of example 2.
Detailed Description
The following is further illustrated with reference to the examples.
Example 1
The implementation process of the steel-making process comprises the following steps: and (3) converter tapping C =0.08, and P = 0.011. Keeping the LF refining white slag for 18min, leaving S =0.0030, keeping the VD vacuum degree at 0.49tor for 14min, feeding a pure Ca wire for 250 m treatment after breaking the vacuum, and blowing argon for 16min in a soft blowing way. And continuously casting a casting blank with the thickness of 300mm, wherein the superheat degree of molten steel in a continuous casting tundish is 10-13 ℃, the dynamic soft reduction of continuous casting is 6.5mm, and the smelting chemical components of the steel are shown in Table 1.
The steel rolling process comprises the following implementation processes: the heating speed of a casting blank is 9.1min/cm, the tapping temperature is 1180 ℃, the initial rolling temperature of the first stage is 1070 ℃, the reduction rates of the last three passes are respectively 18 percent, 19 percent and 18 percent, the final rolling temperature is 1000 ℃, and the thickness of the rolled intermediate blank is 140 mm. The second stage is at the initial rolling temperature of 860 ℃, the accumulated reduction rate of 48 percent, the final rolling temperature of 820 ℃, the re-reddening temperature of 630 ℃ and the thickness of a rolled product of 70 mm.
The implementation process of the heat treatment process comprises the following steps: heating the steel plate from room temperature to 915 ℃, preserving heat for 20 ℃, and then cooling to room temperature by water; tempering at 650 deg.C, maintaining the temperature for 40 deg.C, and air cooling. The results of the non-metallic inclusion test of the steel sheets obtained are shown in Table 2, and the properties thereof are shown in Table 3.
Example 2:
the implementation process of the steel-making process comprises the following steps: converter tapping C =0.07%, and P = 0.010%. Keeping the LF refining white slag for 16min, leaving S =0.0027%, keeping the VD vacuum degree at 0.50tor, keeping the vacuum degree for 13min, feeding a pure Ca wire for 250 m treatment after breaking the vacuum, and blowing argon for 16min in a soft blowing way. And continuously casting a casting blank with the thickness of 300mm, wherein the superheat degree of molten steel in a continuous casting tundish is 12-15 ℃, the continuous casting dynamic soft reduction is 6.7mm, and the smelting chemical components of the steel are shown in table 1.
The steel rolling process comprises the following implementation processes: the heating speed of the casting blank is 8.9min/cm, the tapping temperature is 1175 ℃, the starting rolling temperature of the first stage is 1090 ℃, the reduction rates of the last three passes are respectively 20%, 19% and 20%, the final rolling temperature is 1010 ℃, and the thickness of the rolled intermediate blank is 170 mm. The second stage is at the initial rolling temperature of 865 ℃, the accumulated reduction rate of 46 percent, the final rolling temperature of 815 ℃, the re-reddening of 620 ℃ and the thickness of the rolled finished product of 100 mm.
The implementation process of the heat treatment process comprises the following steps: heating the steel plate from room temperature to 935 ℃, preserving the heat for 20 ℃, and then cooling the steel plate to room temperature by water; the tempering temperature is 635 ℃, the temperature is kept for 40 ℃, and then air cooling is carried out. Finally, the detection result of the non-metallic inclusions of the steel plate is shown in table 2; the properties are shown in Table 3; the metallographic structure is shown in figure 1, and the structure is tempered sorbite with grain size of 9-10 grade.
Table 1 chemical composition (wt.%) of the steels of the examples
TABLE 2 results of non-metallic inclusion test of steels of examples
TABLE 3 test results of properties of steels of examples
The room temperature tensile and Charpy V-notch impact tests in Table 3 were conducted in accordance with ASME SA370, and the high temperature tensile was conducted in accordance with ASME E21. All samples were perpendicular to the direction of rolling of the steel sheet, with the longitudinal axis of the sample being greater than the sheet thickness 1/4. The simulated postweld heat treatment process of the mode-welded test sample in the table 2 comprises the following steps: the temperature of the sample in the furnace is less than or equal to 425 ℃, and the heating rate is less than or equal to 55 ℃/h; the temperature is maintained at 610 +/-10 ℃, the temperature maintaining time is 15-15.5 h, and then the temperature is cooled to below 425 ℃ at the cooling rate of less than or equal to 55 ℃/h.
As shown in Table 1, the carbon equivalent Ceq of each example was less than 0.65%.
As shown in FIG. 1, the steel of the present invention has a stable tempered sorbite structure and a grain size of 9 or more.
As shown in Table 2, the nonmetallic inclusions of A-, B-, C-and D-types in the examples were all less than 1.5.
As shown in Table 3, in each example, the room-temperature elongation Rp0.2 is not less than 620MPa, Rm = 725-930 MPa, A50 is not less than 14%, and Z% is not less than 45%; the high-temperature stretching at 360 ℃ is that Rp0.2 is more than or equal to 530Mpa, Rm is more than or equal to 725 Mpa; the average value of the transverse impact AKV8 at the temperature of minus 18 ℃ is more than or equal to 47J, and the lateral expansion LE is more than or equal to 0.64 mm. The steel has good high-temperature strength and low-temperature toughness, meets various mechanical property requirements of delivery states and die welding states, has good internal and surface quality, is qualified through direct-wave, oblique-wave and magnetic powder inspection of CAP1400 related technical requirements, and can be used for manufacturing nuclear-grade mechanical modules of CAP passive nuclear power plants.
Claims (1)
- A production method of steel for a CAP passive nuclear power plant nuclear-grade mechanical module is characterized by comprising the following steps: the steel comprises the following chemical components, by mass, 0.12-0.20% of C =0.12, 0.10-0.35% of Si = 0.40-0.65% of Mn, 0.015% or less of P, 0.005% or less of S, 0.010-0.030% of V =0.010, 0.10-0.35% of Ni, 0.40-0.60% of Mo, 0.010-0.080% of Ti, 0.010-0.020% of Nb, 1.40-2.00% of Cr, 0.0010-0.0050% of B, 0.020-0.050% of Alt, and the balance of Fe and inevitable impurities; the carbon equivalent Ceq is less than or equal to 0.65;the method comprises the following process steps:a. smelting in a converter: c is more than or equal to 0.06 and P is less than or equal to 0.012 during tapping;b. LF refining: the white slag is kept for more than 15min, and the S discharged is less than or equal to 0.005 percent;c. vacuum degassing treatment: the holding time is more than or equal to 12min under the condition that the vacuum degree is less than or equal to 0.5 tor; after the air is broken, Ca treatment is carried out, and a pure calcium line is fed to be more than or equal to 200 m; the soft argon blowing time is more than or equal to 15 min;d. continuous casting: protecting and casting in the whole process; controlling the superheat degree of molten steel in the tundish at 8-18 ℃; adopting dynamic soft reduction technology, wherein the reduction is more than or equal to 6 mm;e. heating the plate blank: the heating temperature of the plate blank before rolling is 1150-1200 ℃, and the heating speed is 7-12 min/cm; f. rolling: TMCP rolling is adopted, the initial rolling temperature of one stage is more than or equal to 1050 ℃, the final rolling temperature of one stage is more than 980 ℃, and the reduction rate of the last three passes is more than 15%; the initial rolling temperature of the second stage is 830-890 ℃, the final rolling temperature is 790-850 ℃, the red returning temperature is 600-650 ℃, and the accumulated reduction rate is more than 45%;g. and (3) heat treatment: adopting a quenching and tempering heat treatment process, wherein the quenching temperature is 910-940 ℃, the heat preservation time is 20-40 min, and then cooling to room temperature with large water amount; tempering at 630-680 ℃, keeping the temperature for 30-60 min, and then air cooling.
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| CN113186453A (en) * | 2021-03-30 | 2021-07-30 | 湖南华菱湘潭钢铁有限公司 | Production method of steel for low-temperature movable container |
| CN113186455A (en) * | 2021-03-30 | 2021-07-30 | 湖南华菱湘潭钢铁有限公司 | Production method of high-strength steel plate for nuclear energy safety container |
| CN114959459A (en) * | 2022-05-06 | 2022-08-30 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit reactor core shell barrel and manufacturing method thereof |
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| CN113186453A (en) * | 2021-03-30 | 2021-07-30 | 湖南华菱湘潭钢铁有限公司 | Production method of steel for low-temperature movable container |
| CN113186455A (en) * | 2021-03-30 | 2021-07-30 | 湖南华菱湘潭钢铁有限公司 | Production method of high-strength steel plate for nuclear energy safety container |
| CN114959459A (en) * | 2022-05-06 | 2022-08-30 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit reactor core shell barrel and manufacturing method thereof |
| CN114959459B (en) * | 2022-05-06 | 2023-06-16 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit reactor core shell cylinder and manufacturing method thereof |
| WO2023212970A1 (en) * | 2022-05-06 | 2023-11-09 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit reactor core shell cylinder and manufacturing method for steel plate |
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