CN104561824A - Nuclear class equipment supporting steel and production method thereof - Google Patents
Nuclear class equipment supporting steel and production method thereof Download PDFInfo
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- CN104561824A CN104561824A CN201310470887.6A CN201310470887A CN104561824A CN 104561824 A CN104561824 A CN 104561824A CN 201310470887 A CN201310470887 A CN 201310470887A CN 104561824 A CN104561824 A CN 104561824A
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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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
- 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
-
- 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
-
- 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
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- Engineering & Computer Science (AREA)
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- Mechanical Engineering (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides a nuclear class equipment supporting steel and a production method thereof. The chemical components of the steel comprise 0.12-0.18wt% of C, 0.15-0.35wt% of Si, 1.20-1.65wt% of Mn, 0.015wt% or less of P, 0.010wt% or less of S, 0.50-0.85wt% of Ni, 0.05-0.15wt% of Cr, 0.020-0.050wt% of Al, 0.02wt% or less of V, 0.02wt% or less of Ti, 1.5ppm or less of [H], 30ppm or less of [O], and the balance of Fe and inevitable impurities; and the level of nonmetal inclusions in the steel is controlled. The method comprises the steps of converter smelting, external refining, vacuum degassing treatment, continuous casting, rolling, and hardening and tempering treatment, or comprises the steps of electric furnace smelting, external refining, vacuum degassing treatment, die casting, rolling, and hardening and tempering treatment. The steel maintains the high level of mechanical performances of steel plates made of the steel in a heat treatment, a simulated post weld heat treatment state and a 200DEG C high temperature state; and the 0DEG C impact absorption energy level is still high, so the matching of the strength and the toughness of the steel plate is very good.
Description
Technical field
The invention belongs to ferrous material field, particularly relate to core level device support steel and manufacture method thereof.
Background technology
Along with countries in the world rapid development of economy, nuclear energy, as a kind of clean, safe, stable energy, is more and more subject to the attention of various countries, safe utilization nuclear energy, greatly develops nuclear power and has become a kind of trend.And there has also been significant progress in nuclear power technology application aspect, from original " two generations " technology, develop into present " two generations added " and " three generations " technology, safety performance is had larger raising.But at present, China now runs also be at most the safest at present nuclear power generating sets is still " two generations added " technology (seat of honour nuclear power generating sets built of " three generations " AP1000 technology just can generate electricity by way of merging two or more grid systems before estimating the end of the year in 2013) substantially
In " two generations added " nuclear power generating sets, steel for nuclear power pressure equipment plays a part very important as the propping material of the important core level equipment such as nuclear reactor pressure container, potentiostat, various pipeline, case, groove, tank.The stable of its safety run, performance will directly have influence on by support vessels and whole unit safety work.
At present, more as core level device support material, as: A42, A52, P295GH, P355GH and S355J0 etc., above-mentioned steel grade is carbon steel or Hi-Stren steel substantially, tensile strength mostly controls between 400-550MPa, can effectively reduce adding due to alloying element, the radiation embrittlement effect caused.But as core level device support material, also need to stand long-time stress-removal process, also to check its high temperature tensile properties, and above-mentioned steel grade intensity after long-time stress-removal process or at high operating temperatures all has decline in various degree, be difficult to meet the demands, be only applicable to the pressure-bearing material manufacturing nuclear power support equipment, utility appliance, far can not meet the demand of existing " two generations added " and following " three generations " nuclear power generating sets core level key equipment support steel.As thickness of slab be the S355J0 steel plate of 60mm after normalizing treatment, yield strength (Rel) and tensile strength (Rm) are respectively 360N/mm
2and 525N/mm
2(index request Rel>=330N/mm
2, Rm>=510N/mm
2); After Simulated post-weld heat treatment, yield strength (Rel) and tensile strength (Rm) are respectively 340N/mm
2and 500N/mm
2(index request Rel>=330N/mm
2, Rm>=510N/mm
2); During 200 DEG C of drawing by high temperature, yield strength (Rel) and tensile strength (Rm) are respectively 255N/mm
2and 470N/mm
2.From three processes, steel plate is after normalizing treatment, and intensity can full up sufficient index request, and has certain surplus.But after Simulated post-weld heat treatment, armor plate strength declines obviously, and especially tensile strength can not meet index request; The intensity of steel plate when 200 DEG C, especially yield strength decline more obvious, show that this steel grade high-temperature resistance is relatively low, can not meet the demand that core level device support critical material manufactures.
Patent " high toughness, high ductility low irradiation catalysis steel for nuclear power pressure equipment and manufacture method thereof " (publication number: 101892442A), discloses a kind of nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement steel and manufacture method thereof.The chemical composition percentage of this steel is: C:0.08 ~ 0.15, Si:0.20 ~ 0.35, Mn:0.80 ~ 1.60, P≤0.012, S≤0.005, Alt:0.01 ~ 0.05, Ti:0.008 ~ 0.015, N≤0.010, and all the other are Fe and inevitable impurity.This invention devises the manufacture method of controlled rolling state and normalizing state according to the different requirement different with thickness of steel product of product made from steel condition of delivery, this invention steel can be widely used in the s-generation, two generation modified version and the manufacture of generation Ⅲ nuclear power bearing device.Its weak point is, the intensity rank that the steel plate that this invention is produced can reach is also very limited, and the steel plate specification limit of this invention is only 4-60mm.
" a kind of-50 DEG C of steel for nuclear power pressure equipment and production method thereof " " (publication number: CN102181807A), relate generally to high tenacity, low irradiation embrittlement steel for nuclear power pressure equipment and the manufacture method thereof under a kind of-50 DEG C of conditions.Be specially tensile strength and be greater than 585MPa, just requirement is proposed to normal temperature stretching and-50 DEG C of impelling strength, and the Simulated post-weld heat treatment needed nuclear power generating equipment and high-temperature behavior do not have requirement, simultaneously from Composition Control, the requirement of above-mentioned two aspects can not be met.
Summary of the invention
The object of the invention is to overcome the problems referred to above and not enough and a kind of core level device support steel and manufacture method thereof are provided, steel plate all keeps higher level in the mechanical property of as-heat-treated condition, Simulated post-weld heat treatment state and 200 DEG C of conditions of high temperature, and has the coupling of good armor plate strength and toughness.
The present invention seeks to realize like this:
A kind of core level device support steel, its chemical composition provides as follows the C of 0.12%-0.18% by weight percentage; The Si of 0.15%-0.35%; The Mn of 1.20%-1.65%; The P of≤0.015%; The S of≤0.010%; The Ni of 0.50%-0.85%; The Cr of 0.05%-0.15%; The Al of 0.020%-0.050%; The V of≤0.02%; The Ti of≤0.02%, [H]≤1.5ppm, [O]≤30ppm, all the other content are iron and inevitable impurity; Control nonmetallic inclusionsin steel simultaneously, by ASTM E45 method A test ensure A, B, C, D class be mingled with≤1.5 grades.
Present component design reason is as follows:
(1) C: in steel, C content is the principal element ensureing armor plate strength, C content is on the low side, intensity may can not meet requirement, especially run through long-time Simulated post-weld heat treatment and under 200 DEG C of high temperature, intensity all will obtain decline to a certain extent, therefore in application claims steel, C content should control in the upper limit, and therefore the preferred span of control of C content of the present invention is 0.13%-0.18%.
(2) Si:Si is effective strengthening element, also be cheap element simultaneously, therefore same collateral security steel plate different steps Strength Changes all can meet the consideration of index request angle, and controlled by Si content in the middle upper limit as well, therefore the preferred span of control of Si content of the present invention is 0.20%-0.35%.
(3) Mn: in steel, Mn element is except playing the effect of strengthening matrix, and effectively can also improve the hardening capacity of steel, therefore in actual production steel, Mn content controls equally in the upper limit, and the preferred span of control of C content of the present invention is 1.35%-1.65%.
(4) Ni:Ni obviously can improve the low-temperature flexibility of steel, improve the low-temperature flexibility (especially the steel plate of more than 100mm) of thick cross section steel plate simultaneously, make steel plate also can have higher toughness while having sufficient intensity, meet the requirement of index, therefore from actual needs, therefore the preferred span of control of Ni content of the present invention is 0.65%-0.85%.
(5) Cr:Cr significantly can improve the antioxygenation of steel in steel, increases resistance to corrosion.Reduce austenite phase field simultaneously, improve the through hardening performance of steel.But Cr also can significantly improve the brittle transition temperature of steel, promote temper brittleness, therefore the preferred span of control of Cr content of the present invention is 0.05%-0.15%.
(6) nitrogen agent is determined in the Al:Al deoxidation be mainly used in steel when making steel, and can crystal grain thinning, prevents the timeliness of soft steel, and improve steel in low-temperature flexibility, Al content is too much unsuitable simultaneously, is mingled with in order to avoid produce Al2O3.Therefore the preferred span of control of Al content of the present invention is 0.020%-0.035%.
(7) V, Ti: it is fine grained steel that midium-carbon steel requires, fine grained steel is less than coarse-grained steel irradiation fragility, add V, Ti in steel to have crystal grain thinning, improve grain coarsening temperature effect, therefore the preferred span of control of V, Ti content of the present invention is 0.005%-0.02%.
(8) P: irradiation test shows, P is also very responsive to radiation embrittlement, and P content is higher simultaneously, is also easy to the generation aggravating center segregation and center porosity in steel, therefore require that the P content in steel is more low better, therefore the preferred span of control of P content of the present invention is lower than 0.010%.
(9) S:S forms S compound and is mingled with in steel, reduces the impelling strength of steel, affects welding property, and aggravate the generation of center segregation, the defect such as loose, therefore the preferred span of control of S content of the present invention is less than 0.003% simultaneously.
(10) gas [H], [O]: generally speaking, they are all harmful to the performance of steel, also can increase radiation embrittlement effect simultaneously, therefore wishes their content to be reduced to minimum level.The present invention [H], the preferred span of control of [O] content are [H]≤1.5ppm, [O]≤30ppm.
A kind of manufacture method of core level device support steel, converter smelting-external refining-Fruit storage-continuous casting-rolling-thermal treatment process is adopted to produce, continuously cast bloom adopts recrystallization zone and the rolling of Unhydrated cement two-stage control, billet heating temperature is at 1150 DEG C ~ 1200 DEG C, rolling finishing temperature >=1000 DEG C, recrystallization zone, Unhydrated cement rolling temperature controls at 850 DEG C ± 20 DEG C, and cumulative deformation is greater than 50%, rolls rear naturally cooling; Thermal treatment adopts modifier treatment technique: quenching temperature 940 DEG C ± 10 DEG C, soaking time 2-3min/mm; Tempering temperature 590 DEG C ± 10 DEG C, soaking time 2-4min/mm.
A kind of manufacture method of core level device support steel, adopt electrosmelting-external refining-Fruit storage-die casting-rolling-thermal treatment, it is characterized in that, static ingot adopts ingot stocking mode to produce, Heating Steel Ingots temperature is at 1150 DEG C ~ 1200 DEG C, adopt high temperature to roll soon in the operation of rolling, roll rear naturally cooling; Thermal treatment adopts modifier treatment technique: quenching temperature 940 DEG C ± 10 DEG C, soaking time 2-3min/mm; Tempering temperature 590 DEG C ± 10 DEG C, soaking time 2-4min/mm.
Beneficial effect of the present invention is:
The present invention is by optimizing gas and nonmetal inclusion level in chemical composition, thermal treatment process, reduction steel further, make steel plate all keep higher level in the mechanical property of as-heat-treated condition, Simulated post-weld heat treatment state and 200 DEG C of conditions of high temperature, meet the requirement of technical indicator completely; 0 DEG C of shock absorption energy still remains on higher level simultaneously, embodies the coupling of good armor plate strength and toughness, is applicable to the demand of the key equipment support steel plates such as nuclear reactor pressure container completely.
Embodiment
Below by embodiment, the present invention is further illustrated.
For the steel plate of finished product thickness 80mm and following thickness, preferred employing converter smelting-external refining-Fruit storage-continuous casting-rolling-thermal treatment process, for the steel plate of finished product thickness > 80mm, preferably adopt electrosmelting-external refining-Fruit storage-die casting-rolling-thermal treatment process.
Embodiment 1
Molten steel is through converter smelting, external refining (LF, VD) process, and be cast into continuously cast bloom, mill product steel plate specification is 20mm.The composition of embodiment 1 is in table 1.The main technologic parameters of embodiment 1 is in table 2.The mechanical property of the embodiment of the present invention 1 is in table 3.
The composition of table 1 embodiment 1
The main technologic parameters of table 2 embodiment 1
The mechanical property of table 3 embodiment 1
Check nonmetallic inclusionsin steel: category-A 0.5 grade, category-B 0.5 grade, C class 0.5 grade, D class 1.0 grades simultaneously.
By to different states mechanical properties test after the thermal treatment of 20mm plate, its result all meets the requirement of index, and has certain affluence amount, meets the requirement of core level device support steel completely.
Embodiment two
Molten steel is through converter smelting, external refining (LF, VD) process, and be cast into continuously cast bloom, mill product steel plate specification is 40mm.The composition of embodiment 2 is in table 4.The main technologic parameters of embodiment 2 is in table 5.The mechanical property of the embodiment of the present invention 2 is in table 6.
The composition of table 4 embodiment 2
The main technologic parameters of table 5 embodiment 2
The mechanical property of table 6 embodiment 2
Check nonmetallic inclusionsin steel: category-A 0.5 grade, category-B 1.0 grades, C class 0.5 grade, D class 1.0 grades simultaneously.
By to different states mechanical properties test after the thermal treatment of 40mm plate, its result all meets the requirement of index, and has certain affluence amount, meets the requirement of core level device support steel completely.
Embodiment 3
Molten steel is through converter smelting, external refining (LF, VD) process, and be cast into continuously cast bloom, mill product steel plate specification is 60mm.The composition of embodiment 3 is in table 7.The main technologic parameters of embodiment 3 is in table 8.The mechanical property of the embodiment of the present invention 3 is in table 9.
The composition of table 7 embodiment 3
The main technologic parameters of example 3 executed by table 8
The mechanical property of table 9 embodiment 3
Check nonmetallic inclusionsin steel: category-A 0.5 grade, category-B 1.5 grades, C class 0.5 grade, D class 1.0 grades simultaneously.
After the modifier treatment of 60mm plate, yield strength (Rel) and tensile strength (Rm) are respectively 445N/mm
2and 605N/mm
2(index request Rel>=330N/mm
2, Rm:510-650N/mm
2); After Simulated post-weld heat treatment, yield strength (Rel) and tensile strength (Rm) are respectively 420N/mm
2and 580N/mm
2(index request Rel>=330N/mm
2, Rm>=510N/mm
2); During 200 DEG C of drawing by high temperature, yield strength (Rel) and tensile strength (Rm) are respectively 400N/mm
2and 530N/mm
2(index request Rel>=330N/mm
2, Rm>=510N/mm
2).From three states, armor plate strength fall is all less, and different states all can meet index request.Have compared with other steel grades and improved significantly.
Shock absorption energy after the modifier treatment of 60mm plate and Simulated post-weld heat treatment is respectively about 220J, not only meets the requirement of index, and has larger surplus.
By to different states mechanical properties test after the thermal treatment of 60mm plate, its result all meets the requirement of index, and has certain affluence amount, meets the requirement of core level device support steel completely.
Embodiment 4
Molten steel is through converter smelting, external refining (LF, VD) process, and be cast into continuously cast bloom, mill product steel plate specification is 80mm.The composition of embodiment 4 is in table 10.The main technologic parameters of embodiment 4 is in table 11.The mechanical property of the embodiment of the present invention 4 is in table 12.
The composition of table 10 embodiment 4
The main technologic parameters of table 11 embodiment 4
The mechanical property of table 12 embodiment 4
Check nonmetallic inclusionsin steel: category-A 1.0 grades, category-B 1.0 grades, C class 0.5 grade, D class 0.5 grade simultaneously.
By to different states mechanical properties test after the thermal treatment of 80mm plate, its result all meets the requirement of index, and has certain affluence amount, meets the requirement of core level device support steel completely.
Embodiment 5
Molten steel, through electrosmelting, external refining (LF, VD) process, be cast into steel ingot, and Direct Rolling finished steel plate specification is 100mm.The composition of embodiment 5 is in table 13.The main technologic parameters of embodiment 5 is in table 14.The mechanical property of the embodiment of the present invention 5 is in table 15.
The composition of table 13 embodiment 5
The main technologic parameters of table 14 embodiment 5
The mechanical property of table 15 embodiment of the present invention 5
Check nonmetallic inclusionsin steel: category-A 0.5 grade, category-B 1.0 grades, C class 0.5 grade, D class 1.0 grades simultaneously.
By to different states mechanical properties test after the thermal treatment of 100mm plate, its result all meets the requirement of index, and has certain affluence amount, meets the requirement of core level device support steel completely.
Embodiment six
Molten steel, through electrosmelting, external refining (LF, VD) process, be cast into steel ingot, and Direct Rolling finished steel plate specification is 120mm.The composition of embodiment 6 is in table 16.The main technologic parameters of embodiment 6 is in table 17.The mechanical property of the embodiment of the present invention 6 is in table 18.
The composition of table 16 embodiment 6
The main technologic parameters of table 17 embodiment 6
The mechanical property of table 18 embodiment 6
Check nonmetallic inclusionsin steel: category-A 0.5 grade, category-B 1.5 grades, C class 0.5 grade, D class 1.5 grades simultaneously.
By to different states mechanical properties test after the thermal treatment of 120mm plate, its result all meets the requirement of index, and has certain affluence amount, meets the requirement of core level device support steel completely.
The present invention is by optimizing gas and nonmetal inclusion level in chemical composition, thermal treatment process, reduction steel further, make steel plate all keep higher level in the mechanical property of as-heat-treated condition, Simulated post-weld heat treatment state and 200 DEG C of conditions of high temperature, meet the requirement of technical indicator completely; 0 DEG C of shock absorption energy still remains on higher level simultaneously, embodies the coupling of good armor plate strength and toughness, is applicable to the demand of the key equipment support steel plates such as nuclear reactor pressure container completely.
Claims (3)
1. a core level device support steel, is characterized in that, its chemical composition provides as follows by weight percentage, the C of 0.12%-0.18%; The Si of 0.15%-0.35%; The Mn of 1.20%-1.65%; The P of≤0.015%; The S of≤0.010%; The Ni of 0.50%-0.85%; The Cr of≤0.15%; The Al of 0.020%-0.050%; The V of≤0.02%; The Ti of≤0.02%, [H]≤1.5ppm, all the other content of [O]≤30ppm are Fe and inevitable impurity; Controlling nonmetallic inclusionsin steel simultaneously, A, B, C, D class is mingled with≤and 1.5 grades.
2. the manufacture method of core level device support steel described in a claim 1, it is characterized in that, adopt converter smelting-external refining-Fruit storage-continuous casting-rolling-thermal treatment process, continuously cast bloom adopts recrystallization zone and the rolling of Unhydrated cement two-stage control, billet heating temperature at 1150 DEG C ~ 1200 DEG C, rolling finishing temperature >=1000 DEG C, recrystallization zone, Unhydrated cement rolling temperature controls at 850 DEG C ± 20 DEG C, cumulative deformation is greater than 50%, rolls rear naturally cooling; Thermal treatment adopts modifier treatment technique: quenching temperature 940 DEG C ± 10 DEG C, soaking time 2-3min/mm; Tempering temperature 590 DEG C ± 10 DEG C, soaking time 2-4min/mm.
3. the manufacture method of core level device support steel described in a claim 1, adopt electrosmelting-external refining-Fruit storage-die casting-rolling-thermal treatment, it is characterized in that, static ingot adopts ingot stocking mode to produce, Heating Steel Ingots temperature is at 1150 DEG C ~ 1200 DEG C, adopt high temperature to roll soon in the operation of rolling, roll rear naturally cooling; Thermal treatment adopts modifier treatment technique: quenching temperature 940 DEG C ± 10 DEG C, soaking time 2-3min/mm; Tempering temperature 590 DEG C ± 10 DEG C, soaking time 2-4min/mm.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107287500A (en) * | 2016-03-31 | 2017-10-24 | 鞍钢股份有限公司 | A kind of pressurized-water reactor nuclear power plant safety injection tank substrate steel and its manufacture method |
| CN107287509A (en) * | 2016-03-31 | 2017-10-24 | 鞍钢股份有限公司 | A kind of 550MPa grades of nuclear power voltage-stablizer equipment steel and its manufacture method |
| CN107746937A (en) * | 2017-11-22 | 2018-03-02 | 武汉钢铁有限公司 | High-strength high-toughness steel plate and its manufacture method for nuclear power pressure equipment |
| CN108385023A (en) * | 2018-03-30 | 2018-08-10 | 鞍钢股份有限公司 | A kind of high-strength and high ductility nuclear power voltage-stablizer steel and its manufacturing method |
| CN109694988A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | A kind of three generations's pressurized-water reactor nuclear power plant suspension and support steel and its manufacturing method |
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| CN112126861A (en) * | 2020-09-25 | 2020-12-25 | 湖南华菱湘潭钢铁有限公司 | Production method of high-strength and high-toughness steel for CAP nuclear power plant nuclear-grade mechanical module |
| CN112126862A (en) * | 2020-09-25 | 2020-12-25 | 湖南华菱湘潭钢铁有限公司 | Production method of steel for CAP passive nuclear power plant nuclear-grade mechanical module |
| CN115094303A (en) * | 2022-05-06 | 2022-09-23 | 鞍钢股份有限公司 | Steel plate for advanced nuclear power unit superheater and manufacturing method thereof |
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| CN103160732A (en) * | 2011-12-14 | 2013-06-19 | 鞍钢股份有限公司 | Steel for nuclear power pressure-bearing equipment and manufacturing method thereof |
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107287500A (en) * | 2016-03-31 | 2017-10-24 | 鞍钢股份有限公司 | A kind of pressurized-water reactor nuclear power plant safety injection tank substrate steel and its manufacture method |
| CN107287509A (en) * | 2016-03-31 | 2017-10-24 | 鞍钢股份有限公司 | A kind of 550MPa grades of nuclear power voltage-stablizer equipment steel and its manufacture method |
| CN109694988A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | A kind of three generations's pressurized-water reactor nuclear power plant suspension and support steel and its manufacturing method |
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