CN112143976A - P265GH steel plate for nuclear power and manufacturing method thereof - Google Patents
P265GH steel plate for nuclear power 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C21D8/0205—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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- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
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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
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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
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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
- 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
Abstract
The invention relates to a P265GH steel plate for nuclear power and a manufacturing method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c: 0.10 to 0.20 percent; si: 0.15-0.30%; mn: 0.70-0.90%; p: less than or equal to 0.015 percent; s: less than or equal to 0.005 percent; al: more than or equal to 0.020%; ni: 0.10-0.30%; h is less than or equal to 1 ppm; as + Sb + Bi + Sn + Pb is less than or equal to 0.10 percent; CEV is less than or equal to 0.40, and the balance is Fe and inevitable impurities. By utilizing the continuous casting billet and through the synergistic process of steel rolling and normalizing heat treatment, the delivery state mechanical property and the process property of the obtained steel plate meet the following requirements: transverse and longitudinal tensile strength Rm of steel plate test sample: 410-530MPa, the yield strength Rel is more than or equal to 265MPa, and the elongation A is more than or equal to 22 percent; and at the temperature of minus 20 ℃, the impact absorption energy KV2 of the transverse impact test sample is more than or equal to 27J; ensuring that the mechanical property of the steel plate (615 +/-5) DEG C X24h after stress relief meets the mechanical property requirement of the steel plate in a delivery state.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a P265GH steel plate for nuclear power and a manufacturing method thereof.
Background
Nuclear power energy is one of the important clean energy at present, but the safe operation of nuclear power equipment is the focus of most attention otherwise; the evaporator is one of the cores of the whole nuclear power equipment; the performance reliability and the overall performance of the raw material steel plate for manufacturing the evaporator are rich, and the safe and stable operation of the whole evaporator is concerned.
The P265GH is a mature carbon steel plate material, has stable and reliable conventional performance and good weldability, is suitable for being used as a material for nuclear power evaporator equipment, and has the thickness of 5-50mm generally. However, the nuclear power evaporator equipment is a complex system, and welding repair, stress relief heat treatment of the whole equipment and the like are inevitable in the manufacturing process. Therefore, in addition to the requirement of qualified properties of the steel plate base material, sufficient stability and allowance of the properties of the steel plate material in the manufacturing process of the equipment need to be ensured.
Compared researches are carried out by a plurality of scholars aiming at the P265GH steel plate material for nuclear power. The researchers compared the influence of post-weld heat treatment of different specifications on the performance of the steel plate, (ancient times: the mechanical properties of nuclear power carbon steel subjected to post-weld heat treatment of different specifications are compared, pressure vessel, 2015, (32) 6: 35-39), aiming at the thickness specification of the steel plate of 85-100mm, the longest stress relief time is 10h, and the authors think that the cooling rate has a greater influence on the performance of the steel plate under the condition that the heat preservation time and the heat preservation temperature of the post-stress relief heat treatment are fixed. The researchers proposed "a steel sheet for nuclear power plant pressure vessel and a method for manufacturing the same" (application publication No. CN 103911559 a), which is similar to P265GH, is a C — Mn carbon steel sheet, and is not added with any alloy; the scholars demonstrate that the steel plate has certain reliability under the delivery condition, but do not mention the performance condition of the steel plate after stress relief.
The above literature data have made a great deal of research and practice on steel plates for nuclear power, and have achieved good results. However, it is noted that in these studies, no mention has been made of a steel sheet of thin gauge and stress relief for a long period of time and a method for producing the same; in nuclear power equipment, when a thin steel plate and the equipment are subjected to complex overall stress relief or repeated repair, the performance of the steel plate subjected to long-time stress relief heat treatment is particularly important in order to ensure the overall safety of nuclear power.
Disclosure of Invention
The invention aims to solve the technical problem of providing a P265GH steel plate for nuclear power and a manufacturing method thereof aiming at the prior art, so that the performance of the steel plate after long-time stress relief heat treatment is ensured, and the overall safety of the nuclear power is ensured.
The technical scheme adopted by the invention for solving the problems is as follows: a P265GH steel plate for nuclear power comprises the following chemical components in percentage by mass: c: 0.10 to 0.20 percent; si: 0.15-0.30%; mn: 0.70-0.90%; p: less than or equal to 0.015 percent; s: less than or equal to 0.005 percent; al: more than or equal to 0.020%; ni: 0.10-0.30%; h is less than or equal to 1 ppm; as + Sb + Bi + Sn + Pb is less than or equal to 0.10 percent; CEV is less than or equal to 0.40, and the balance is Fe and inevitable impurities.
The steel plate has the following chemical composition design principle:
carbon: carbon is a main reinforcing element in steel, and in this patent, when the carbon content is less than 0.10%, the strength of the steel sheet is low because the steel sheet cannot obtain a sufficient pearlite structure. And when the carbon content in the steel is more than 0.20%, the shape of the steel sheet may be deteriorated while the weldability of the steel sheet is deteriorated. Therefore, the carbon content of the present invention is controlled to be in the range of 0.10 to 0.20%.
Silicon: silicon is one of the main deoxidizing elements in steel, and has a certain solid solution strengthening effect, but too high silicon content deteriorates coatability of the steel sheet surface, and based on this, the range of the silicon content of the present invention is controlled to 0.15 to 0.30%.
Manganese: manganese is a main strengthening element in steel, and when the content of Mn is too high, the carbon equivalent of the Mn is increased, so that the welding performance is damaged; and Mn and S and other elements easy to segregate are combined, segregation is easily generated in the center of the slab to form lamellar MnS inclusions, and the impact toughness of the steel plate is unstable. Therefore, the Mn content of the invention is controlled to be 0.70-0.90%.
Nickel: the nickel can effectively reduce the ductile-brittle transition temperature of the steel plate, and the nickel does not form carbide with carbon in the steel, so the content of the nickel is controlled to be 0.10-0.30%.
Aluminum: mainly has the functions of deoxidation and grain refinement. Al and [ O ] in molten steel]、[N]Formed by bonding (Al)2O3) And (AlN) enters the slag to realize the purposes of deoxidation and nitrogen; very little residual Al in the steel2O3The grains act as second phase particles in the steel to refine the grains. Therefore, the content (Alt) of the compound is controlled to be more than 0.020.
H: is one of the most harmful elements in steel, and two H atoms form H in steel2Molecule, H2The molecules are gathered together to generate larger pressure, microcracks are formed in weak links in the steel plate, and the microcracks are macroscopically expressed as white spots, so that the steel plate is embrittled. Therefore, the content thereof is controlled to be not more than 1ppm by the present invention.
S, P and other harmful elements: are harmful impurity elements in steel, and are liable to form defects such as segregation and inclusion, and therefore, the lower the content, the better.
The smelting process adopts a converter, LF external refining, RH vacuum treatment, CC continuous casting blank forming and blank stack slow cooling.
The rolling process adopts a controlled rolling process for production; the heat treatment adopts continuous furnace normalizing heat treatment.
Preparing smelting raw materials according to the chemical composition, sequentially carrying out KR molten iron pretreatment, converter smelting, LF refining, RH refining and continuous casting to produce high-purity molten steel, and using an optimized continuous casting process (low casting superheat degree, low blank drawing speed and reasonable soft reduction parameters) to produce a continuous casting slab with low center segregation, looseness and 150mm thickness. After the continuous casting is finished, the continuous casting billet is subjected to covering and slow cooling to carry out H expansion treatment, so that the core quality of the continuous casting billet is further improved, and the uniformity and stability of the performance of a steel plate are ensured.
And (5) cleaning the surface of the continuous casting billet with temperature after slow cooling.
Heating the continuous casting slab to 1180-1280 ℃, preserving heat for 1-2 hours, fully dissolving alloy elements in steel in a solid manner to ensure the uniformity of the components and the performance of a final product, descaling the continuous casting slab after leaving a furnace by using high-pressure water, then carrying out two-stage rolling, wherein the first-stage rolling is rough rolling, the final three-pass single-pass reduction rate is more than or equal to 30%, and accumulating more than 60%, so as to ensure that the core defects of the continuous casting slab are fully closed, thereby ensuring the performance of a steel plate; the second stage rolling is finish rolling, the initial rolling temperature is 850-950 ℃, and for the specification below 8mm, a curling furnace is adopted to heat the intermediate blank, so that the temperature of the steel plate is not lower than 850 ℃ in the rolling process. After the rolling is finished, the cooling bed is cooled in air and then is taken off the line.
Normalizing the rolled steel plate, carrying out heat treatment in a continuous furnace, wherein the normalizing heating temperature is 860-930 ℃, the furnace time is 2.5-6min/mm, and air cooling after discharging. Compared with the normalizing in-furnace time of the common steel plate, the heat treatment process of the steel plate obviously prolongs, and aims to ensure the full solid solution of the microalloy elements and improve the performance stability of the steel plate.
Aiming at the urgent need of a nuclear power construction evaporator, the invention uses reasonable chemical component design; producing a continuous cast slab with low center segregation and porosity in combination with a continuous casting process; matching with a large reduction rolling process; optimizing the heat treatment process, and manufacturing the P265GH steel plate with the thickness specification of 5-50mm and ensured mechanical property and process property. Steel plate normalization delivery, steel plate sample transverse and longitudinal tensile strength Rm: 410-530MPa, the yield strength Rel is more than or equal to 265MPa, and the elongation A is more than or equal to 22 percent; and at the temperature of minus 20 ℃, the impact absorption energy KV2 of the transverse impact test sample is more than or equal to 27J; the mechanical property of the steel plate (615 +/-5) DEG C X24h after stress relief meets the requirement of the mechanical property of the steel plate in a delivery state, the temperature rise and fall rate of a sample above 300 ℃ is less than or equal to 55 ℃/h, and the heat preservation time is 24 h.
Compared with the prior art, the invention has the advantages that:
(1) the invention stipulates the transverse and longitudinal mechanical properties, the process performance and the like of the steel plate with the thickness specification of P265GH of 5-50mm, and meets the requirements of the nuclear power field on high-requirement steel plates.
(2) The invention stipulates the mechanical property of the P265GH steel plate with the thickness specification of 5-50mm after stress relief for 24 hours, and is beneficial to ensuring the long-time stable service of the steel plate.
(3) The invention adopts continuous casting billet production, and adopts a covering and slow cooling mode to expand H for the continuous casting billet, thereby solving the difficult problem of H expansion of thin steel plates.
(4) The invention adopts long-time normalizing heat treatment, the microalloy elements are fully dissolved in solution, and the performance stability of the steel plate is improved.
Drawings
FIG. 1 is a photograph showing the delivered state of 1/4T, a 14mm gauge steel plate according to an example of the present invention.
FIG. 2 is a photograph showing the stress-relieved microstructure of 1/4T, a 14mm gauge steel sheet according to an example of the present invention.
Detailed Description
The present invention will be described in further detail with reference to examples.
Example 1
The steel sheet of example 1 had a thickness of 6 mm.
The production process of the steel plate with the thickness of 6mm comprises the following steps:
preparing smelting raw materials according to the chemical composition of the steel plate, and sequentially carrying out KR molten iron pretreatment, converter smelting, LF refining, RH refining, 150mm continuous casting, covering and slow cooling of a continuous casting billet, cleaning of the continuous casting billet, heating of the continuous casting billet, heat preservation treatment, high-pressure water descaling, controlled rolling, straightening and heat treatment.
And (3) covering and stacking the high-temperature slab out of the continuous casting machine for slow cooling, wherein the covering inlet temperature is not lower than 800 ℃, the slow cooling time is not lower than 72H, the covering outlet temperature is not higher than 400 ℃, and the slow cooling step aims at reducing the H content in the steel.
Further, the specific process of the heating, controlled rolling and cooling stages for rolling the plate blank into the steel plate comprises the following steps: heating the blank to 1180-1280 ℃, preserving heat for 1-2 hours, removing scale by high-pressure water after discharging, and then carrying out two-stage rolling. The initial rolling temperature of the first stage rolling (namely rough rolling) is 1070 ℃, the rolling is carried out for 5 passes, and the thickness of the intermediate billet is 20 mm; the second stage rolling is finish rolling, the initial rolling temperature is 920-950 ℃, and the final plate thickness is 6 mm. Straightening, inserting the wire, wherein the offline temperature is higher than 300 ℃; and (4) piling for slow cooling in a mode of upper paving and lower covering so as to be beneficial to further H expansion.
And (3) putting the completely cooled steel plate into a continuous furnace for normalizing heat treatment, heating at 900 ℃, keeping the temperature in the furnace for 30min, and cooling in static air.
The finished steel sheets formed via the above manufacturing process had excellent overall properties, as detailed in tables 1, 2 and 3.
Example 2
Example 2 relates to a steel sheet having a thickness of 14 mm.
The production process of the steel plate with the thickness of 14mm comprises the following steps:
steel plate slab making and slab stacking slow cooling were identical to those of example 1.
Further, the specific process of the heating, controlled rolling and cooling stages for rolling the plate blank into the steel plate comprises the following steps: heating the blank to 1180-1280 ℃, preserving heat for 1-2 hours, removing scale by high-pressure water after discharging, and then carrying out two-stage rolling. The initial rolling temperature of the first stage rolling (namely rough rolling) is 1030 ℃, the rolling is carried out for 7 passes, and the thickness of the intermediate billet is 42 mm; the second stage rolling is finish rolling, the initial rolling temperature is 900-930 ℃, the initial rolling plate thickness is 42mm, and the final finished plate thickness is 14 mm. Straightening, inserting the wire, wherein the offline temperature is higher than 300 ℃; and (4) piling for slow cooling in a mode of upper paving and lower covering so as to be beneficial to further H expansion.
And (3) putting the completely cooled steel plate into a continuous furnace for normalizing heat treatment, heating at 900 ℃, keeping the temperature in the furnace for 42min, and cooling in static air.
The finished steel sheets formed via the above manufacturing process had excellent overall properties, as detailed in tables 1, 2 and 3.
Example 3
Example 3 relates to a steel sheet having a thickness of 45 mm.
The production process of the steel plate with the thickness of 45mm comprises the following steps:
steel plate slab making and slab stacking slow cooling were identical to those of example 1.
Further, the specific process of the heating, controlled rolling and cooling stages for rolling the plate blank into the steel plate comprises the following steps: heating the blank to 1180-1280 ℃, preserving heat for 1-2 hours, removing scale by high-pressure water after discharging, and then carrying out two-stage rolling. The initial rolling temperature of the first stage rolling (namely rough rolling) is 1030 ℃, the rolling is carried out for 7 passes, and the thickness of the intermediate billet is 36 mm; the second stage rolling is finish rolling, the initial rolling temperature is 870-900 ℃, the initial rolling plate thickness is 72mm, and the final finished plate thickness is 45 mm. Straightening, inserting the wire, wherein the offline temperature is higher than 300 ℃; and (4) piling for slow cooling in a mode of upper paving and lower covering so as to be beneficial to further H expansion.
And (4) putting the completely cooled steel plate into a continuous furnace for normalizing heat treatment, heating at 870 ℃, keeping the temperature in the furnace for 135min, and cooling in static air.
The finished steel sheets formed via the above manufacturing process had excellent overall properties, as detailed in tables 1, 2 and 3.
TABLE 1 examples Final product chemistry (% by weight)
| C | Si | Mn | P | S | Ni | Al | H | Nb | Ceq | |
| Example 1 | 0.14 | 0.229 | 0.86 | 0.009 | 0.0013 | 0.134 | 0.0366 | 0.00008 | 0.016 | 0.3092 |
| Example 2 | 0.16 | 0.242 | 0.88 | 0.010 | 0.0013 | 0.138 | 0.0296 | 0.00008 | 0.018 | 0.3259 |
| Example 3 | 0.16 | 0.248 | 0.88 | 0.013 | 0.0019 | 0.139 | 0.0322 | 0.00008 | 0.015 | 0.3305 |
TABLE 2 mechanical Properties (delivery state) of the steel sheets produced in the examples
Note 1: sample specification 5mm 10mm 55mm
TABLE 3 mechanical Properties of the steel sheets produced in the examples (specimen stress relief State Note 2)
Note 1: sample specification 5mm 10mm 55mm
Note 2: stress relief treatment is carried out on the sample, the sample is charged at 300 ℃, the heating rate is less than or equal to 55 ℃/h, and the heat preservation time is 615 ℃ for 24 h; the cooling rate is less than or equal to 55 ℃/h above 300 ℃.
In addition to the above embodiments, the present invention also includes other embodiments, and any technical solutions formed by equivalent transformation or equivalent replacement should fall within the scope of the claims of the present invention.
Claims (7)
1. A P265GH steel plate for nuclear power is characterized in that: the steel plate comprises the following chemical components in percentage by mass: c: 0.10 to 0.20 percent; si: 0.15-0.30%; mn: 0.70-0.90%; p: less than or equal to 0.015 percent; s: less than or equal to 0.005 percent; al: more than or equal to 0.020%; ni: 0.10-0.30%; h is less than or equal to 1 ppm; as + Sb + Bi + Sn + Pb is less than or equal to 0.10 percent; CEV is less than or equal to 0.40, and the balance is Fe and inevitable impurities.
2. The P265GH steel plate for a nuclear power plant according to claim 1, wherein: the tensile strength Rm of the steel plate in the transverse direction and the longitudinal direction is as follows: 410-530MPa, the yield strength Rel is more than or equal to 265MPa, and the elongation A is more than or equal to 22 percent; and at the temperature of minus 20 ℃, the impact absorption energy KV2 of the transverse impact test sample is more than or equal to 27J; ensuring that the mechanical property of the steel plate (615 +/-5) DEG C X24h after stress relief meets the mechanical property requirement of the steel plate in a delivery state.
3. The nuclear power P265GH steel plate of claim 1, wherein: the thickness specification of the steel plate is 5-50mm, and the steel plate is delivered by normalizing.
4. A method for manufacturing the P265GH steel plate for nuclear power as claimed in claims 1-3, characterized in that; the method comprises the following steps:
1) preparing smelting raw materials according to the chemical composition, sequentially carrying out KR molten iron pretreatment, converter smelting, LF refining and RH refining to produce high-purity molten steel, and producing a continuous casting plate blank through a continuous casting process;
2) after the continuous casting is finished, covering the continuous casting billet with a cover and slowly cooling to carry out H expansion treatment, so that the core quality of the continuous casting billet is improved; cleaning the surface of the continuous casting billet with temperature after slow cooling;
3) heating the continuous casting slab to 1180-1280 ℃, preserving heat for 1-2 hours, and descaling the continuous casting slab by using high-pressure water after the continuous casting slab is discharged;
4) the continuous casting billet subjected to high-pressure water descaling is rolled in two stages, wherein the first stage is rough rolling, the last three-time single-pass reduction rate is more than or equal to 30 percent, and is accumulated by more than 60 percent, the second stage is finish rolling, the initial rolling temperature is 850-950 ℃, after the rolling is finished, a cooling bed is subjected to air cooling, and the coil is discharged, and the coil discharging temperature is higher than 300 ℃;
5) normalizing the rolled steel plate, carrying out heat treatment in a continuous furnace, wherein the normalizing heating temperature is 860-930 ℃, the furnace time is 2.5-6min/mm, and air cooling after discharging.
5. The manufacturing method of the nuclear power P265GH steel plate according to claim 4, wherein the method comprises the following steps: and (3) covering and stacking the high-temperature slab out of the continuous casting machine for slow cooling, wherein the cover inlet temperature is not lower than 800 ℃, the slow cooling time is not lower than 72h, and the cover outlet temperature is not higher than 400 ℃.
6. The manufacturing method of the nuclear power P265GH steel plate according to claim 4, wherein the method comprises the following steps: and piling and slowly cooling the rolled steel plate which is off-line by adopting a mode of upper laying and lower covering.
7. The manufacturing method of the nuclear power P265GH steel plate according to claim 4, wherein the method comprises the following steps: and in the finish rolling stage, for the specification below 8mm, a curling furnace is adopted to heat the intermediate blank, and the temperature of the steel plate is not lower than 850 ℃ in the rolling process.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114134401A (en) * | 2021-05-11 | 2022-03-04 | 江阴兴澄特种钢铁有限公司 | P355GH steel plate for papermaking drying cylinder and manufacturing method thereof |
| CN114410935A (en) * | 2021-12-30 | 2022-04-29 | 舞阳钢铁有限责任公司 | Production method of P265GH steel plate with good low-temperature impact toughness |
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