CN107287509A - A kind of 550MPa grades of nuclear power voltage-stablizer equipment steel and its manufacture method - Google Patents
A kind of 550MPa grades of nuclear power voltage-stablizer equipment steel and its manufacture method Download PDFInfo
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- CN107287509A CN107287509A CN201610203419.6A CN201610203419A CN107287509A CN 107287509 A CN107287509 A CN 107287509A CN 201610203419 A CN201610203419 A CN 201610203419A CN 107287509 A CN107287509 A CN 107287509A
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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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- 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
- C22C38/02—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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
Abstract
The present invention provides a kind of 550MPa grades of nuclear power voltage-stablizer equipment steel and its manufacture method, and the composition of the steel plate is as follows by weight percentage：C：0.10%~0.20%, Si：0.10%~0.40%, Mn：1.30%~1.60%, Mo：0.40~0.60%, Ni：0.60%~0.80%, Cr：0.25%~0.45%, V：0.02%~0.05%, surplus is Fe and inevitable impurity.Manufacture method includes smelting, forges, rolls, being heat-treated, and after invention steel plate is conditioned, preferable strength level is respectively provided with different conditions：After steel plate of the present invention is conditioned, 20 DEG C of impact absorbing energy under different conditions are equally maintained at higher level, not only meet the requirement of index, and with larger surplus.
Description
Technical field
The invention belongs to ferrous material field, more particularly to more particularly to 550MPa grades of core
Electric voltage-stablizer equipment steel and its manufacture method.
Background technology
Nuclear energy is as a kind of cleaning, the safe and stable energy, increasingly by countries in the world
Attention, safe utilization nuclear energy, greatly develop nuclear power turn into a kind of trend.China is current
Through as building the most country of nuclear power generating sets in the world, while as nuclear power technology exporting country,
Priority and the national signing related protocol such as South Africa, Pakistan, Turkey, are that it is built first
Enter nuclear power generating sets.Wherein in Nuclear island equipment voltage-stablizer belong to core one-level equipment, due to need with
Aqueous phase contact with radioactive high temperature, high pressure, therefore application site is extremely crucial.Simultaneously
To ensure safety, reducing weld seam, it is generally the case that voltage-stablizer cylinder is by upper, middle and lower three
Block steel plate is suppressed, is welded, and every piece of steel plate thickness is 119mm.End socket of voltage regulator by it is upper,
Low head is constituted, and each end socket is formed by a steel plate compacting, and steel plate thickness is 100mm,
Therefore above-mentioned steel plate not only super thick, but also ultra-wide (width is more than 4000mm), simultaneously
It is more strict in terms of combination property requirement, therefore from domestic and international existing iron and steel enterprise's equipment capability
From the point of view of, producing such steel plate has larger difficulty.
The enterprise for producing such steel plate in the world at present is mainly French Industeel, and steel grade is
16MND5 as defined in RCC-M M2126 standards, the mode of production is using large-scale steel ingot rolling
Form.The problem of being primarily present from the point of view of its condition of production in terms of two：One is by RCC-M
M2126 standards are produced, and the control of the constituent content such as C and Ni, Mo in steel is closed not to the utmost
Reason, modifier treatment (hereinafter referred to as QT) although tempered sorbite tissue can be obtained afterwards,
Again through long-time Simulated post-weld heat treatment (hereinafter referred to as SPWHT), a large amount of conjunctions can be separated out in steel
Golden carbide, so as to cause intensity and toughness to decline, it is difficult to meet and require.Under normal circumstances,
Such steel can only meet the SPWHT of 10 small left and right, and be difficult to meet in actual production and be up to
The SPWHT requirements of 16-16.5 hours；Two be the usual feelings into steel plate by steel ingot Direct Rolling
Due to the limitation of mill capacity under condition, steel plate centre can not fully participate in deformation, therefore one
A little center porosities, crackle can not obtain effective soldering, so as to cause flaw detection not conform to, this is for core
It is extremely fatal for first device steel.
The present invention is improved by practice in terms of alloying element, introducing solution strengthening,
Precipitation strength and refined crystalline strengthening mechanism, then coordinate suitable rolling and Technology for Heating Processing, so as to protect
Demonstrate,prove performance of the steel plate under different conditions and meet requirement；Hydraulic press advantage is utilized simultaneously, by steel ingot
It is forged into suitable steel billet, it is ensured that the defect soldering of steel billet centre, dense structure, from basic
On solve above mentioned problem.
More patent and document have been formed to midium-carbon steel both at home and abroad at present《Nuclear power plant containment shell
With steel plate and its manufacture method》(application number：201210269122.1), disclose a seed nucleus
Power plant safety shell steel plate, its thickness is 10-60mm, and its chemical composition is:C:
0.06-0.15%；Si:0.10-0.40%；Mn:1.0-1.5%；Mo:0.10-0.30%；P≤
0.012%；S≤0.003%；Al:0.015-0.050；Ni:0.20-0.50%；And V≤0.05%,
Ti≤0.03%, Cr≤0.25, Nb≤0.03%, Ca:At least one of 0.0005-0.005%；
Surplus is Fe and other inevitable impurity.The nuclear power plant containment shell related generally to thickness steel
Plate has high intensity, a high tenacity, and at low temperatures mother metal and heat affected area all have it is good
Good impact flexibility, is suitably applied nuclear power plant containment shell manufacture field.
《A kind of generation Ⅲ nuclear power station containment vessel steel plate and its manufacture method》(application
Number：201210282831.3), relate generally to a kind of generation Ⅲ nuclear power station containment vessel use
Steel plate and its manufacture method, its composition range is：C:0.08-0.12%；Si:0.15-0.55%；
Mn:0.9-1.5%；P≤0.007%；S≤0.004%；Ni:0.1-0.5%；Cr:0.0-0.3%；
Mo:0.10-0.35%；V:0.010-0.050%；Nb:0.010-0.030%；Ti:0.008-0.035%；
Al:0.020-0.050%；N≤0.006%；Nb+V≤0.08%, surplus is iron and inevitable
Impurity.Steel plate produced by the present invention, tensile strength reaches more than 600MPa, resistance to 200 DEG C
High-temperature behavior, with low cost, welding performance is excellent.But examine nuclear reactor safety shell steel plate
An important technology index be steel plate after Simulated post-weld heat treatment mechanical property, in the patent
The performance of its Simulated post-weld heat treatment is not referred to.
Invent for above-mentioned two and all refer to the construction of nuclear reactor safety shell, and the invention mainly relates to
Core level equipment safety injection tank housing build.
《A kind of Clad steel plate for nuclear power engineering and manufacturing method of clad steel plate and preparation method thereof》(application number：
201210349026.8), relate generally to a kind of Clad steel plate for nuclear power engineering and manufacturing method of clad steel plate, comprising substrate and
Compound plate, substrate is killed steel steel plate, and compound plate is chromiumnickel austenite stainless steel steel plate.Substrate composition
For：C≤0.025%；Si:0.10-0.50%；Mn:1.00-1.80%；P≤0.015%；S≤
0.015%；Ni:0.30-0.80%；Cr≤0.25%；Mo:0.35-0.70%；Cu≤0.12%；
V≤0.06%；Nb≤0.02%；Ti≤0.03%；Co≤0.25%；Al >=0.02%, surplus
For iron and inevitable impurity.The patent is in addition to steel plate chemical composition is disclosed, and emphasis is disclosed
The preparation method of clad steel plate, although refer to the composition of substrate and compound plate, but for compound
The rolling mill practice and Technology for Heating Processing of steel plate are not proposed.
《A kind of nuclear plant pressure vessels and equipment gate steel plate and its manufacture method》(application
Number：201310076884.4), relate generally to a kind of nuclear plant pressure vessels and equipment gate is used
Steel plate, steel plate includes：C:0.10-0.20%；Si:0.15-0.35%；Mn:1.00-1.65%；P
≤ 0.015%；S≤0.005%；Ni:0.50-0.85%；Cr≤0.15%；Cu≤0.06%；
Mo≤0.05%；V≤0.020%；Nb≤0.040%；Ti≤0.020%；Al:0.020-0.050%；
N≤0.015%；As≤0.015%；Sn≤0.010%, surplus is iron and inevitable impurity.
The patent is essentially disclosed uses converter smelting under the conditions of existing equipment, realizes clean steel
Production.Plate Production cost is low simultaneously, with stable structure property, low-temperature flexibility and high temperature
Performance, welding performance, cold and hot working function admirable, its ductile-brittle transition temperature TNDT≤- 28
℃.But compared with the present invention, one side purposes is different, and (the invention mainly relates to Nuclear island equipment
--- safety injection tank casing substrate steel), contrast patent is organized as ferrite+pearlite, and
It is normalizing that condition of heat treatment is proposed in the invention.
《A kind of Steel plate with super-large thickness for nuclear power engineering equipment》
(201210309621.9), relate generally to a kind of Steel plate with super-large thickness for nuclear power engineering equipment and
Production method, belongs to technical field of steel production.Chemical composition includes：C≤0.020%；
Si:0.10-0.30%；Mn:1.15-1.60%；P≤0.012%；S≤0.010%；
Ni:0.50-0.80%；Cr≤0.20%；Mo:0.45-0.55%；Cu≤0.18%；V≤0.01%；
Nb≤0.02%；Ti≤0.03%；Al is always >=0.020%；Cu+6Sn≤0.33%, surplus is
Iron and inevitable impurity.The patent be mainly used in nuclear power plant evaporator, high pressure cover end and
The manufacture of the key equipments such as pressure vessel.Though also belong to special heavy plate with steel plate of the present invention
(thickness >=100mm), but exist substantially not in composition design, production technology and aspect of performance
Together.
《A kind of nuclear power station mechanical module support member high strength steel plate and its manufacture method》(Shen
Please number：201310083274.7), a kind of nuclear power station module support member steel plate is related generally to,
Composition includes：C:0.08-0.22%；Si:0.15-0.45%；Mn:0.60-1.10%；P≤0.020%；
S≤0.015%；Ni:0.60-1.00%；Cr:0.40-0.70%；Cu:0.15-0.55%；
Mo:0.40-0.60%；V:0.020-0.080%；Ti:0.008-0.030%；B:0.0005-0.005%；
Al:0.020-0.050%, surplus is iron and impurity.The patent is fitted in low carbon content design basis
When addition alloying element, the tensile strength of steel is set to reach more than 800MPa.It is disadvantageous in that,
Thickness specification is only limitted to 6-65mm, ballistic work average value for 160Mpa, is unsuitable for safety injection tank
The manufacture of substrate.
Document " nuclear pressure container steel plate SA533B tissue and mechanical property,《Material
Material heat treatment journal》, volume 2012,33, the 8th phase " and report a kind of 620MPa grades of core
Voltage force Vessel Steels, it has the precipitation of molybdenum after Simulated post-weld heat treatment, made in sheet material tissue
The toughness reduction of sheet material；Document " nuclear power pressure vessel forging 16MND5 Heat-Treatments of Steel
Technique,《Steel research journal》, volume 2012,21, the 1st phase " report using forging
The method of technique productions 16MND5 steel, is given birth to the present invention using forging, rolling bonding technique
There is production cost height, cycle in production, while the two is in Composition Control, other productions
There is larger difference in process aspect；" the advanced heap-type of nuclear power and China's nuclear power developing,《Chinese engineering
Science》, volume 2005,7, o. 11th " mainly introduce be nuclear power generating sets heap-type and I
The development of state's nuclear power technology, specific equipment and steel grade are not related to, has larger difference with the present invention
Not.
From the point of view of above-mentioned patent and document contrast, the 550MPa level nuclear powers mentioned with the present invention
There is larger difference in voltage-stablizer equipment steel, cannot be used for manufacture nuclear power end socket of voltage regulator,
The equipment such as cylinder.
The content of the invention
What this practicality was invented aims to overcome that above mentioned problem and deficiency and provides a kind of 550MPa
Level nuclear power voltage-stablizer equipment steel and its manufacture method, steel plate is in quenched and tempered state (QT), simulation weldering
The mechanical property of heat treatment state (SPWHT) two states keeps higher level, steel plate afterwards
Intensity and toughness matching at thickness 1/4, at 1/2 are good, tissue stabilization, fully meet core
The demand that the equipment such as group of motors end socket of voltage regulator, cylinder are built.
The object of the present invention is achieved like this：
A kind of 550MPa grades of nuclear power voltage-stablizer equipment steel, the composition by weight hundred of the steel plate
Divide as follows than counting：C：0.10%~0.20%, Si：0.10%~0.40%, Mn：1.30%~
1.60%th, Mo：0.40~0.60%, Ni：0.60%~0.80%, Cr：0.25%~0.45%,
V：0.02%~0.05%, surplus is Fe and inevitable impurity.Impurity element in steel
Control：P≤0.012%, S≤0.008%, [H]≤2.0ppm, [O]≤30ppm.
Composition design reason is as follows：
C：C is the essential element for ensureing armor plate strength in steel, and in the technical program, C contains
Amount is less than 0.10%, and tensile strength would generally can not meet requirement, particularly through 16 small durations
Intensity can further decline after time SPWHT.It is mainly shown as thick steel plates thickness 1/2
And be difficult to obtain preferable tempered sorbite tissue at 1/4, matrix solution strengthening effect is not enough；
On the contrary, C content is more than 0.20%, it can directly cause the decline of toughness plasticity.Therefore the present invention will
It is 0.10%~0.20% to seek C content scope in steel, and preferably control range is 0.10%-0.16%.
Si：Si is effective intensified element, plays deoxidation, is required in the technical program
Si contents are not less than 0.10%；But content is higher to bring toughness plasticity to decline, and deteriorates weldability
Can, therefore control Si upper content limits to be 0.40%.And collateral security steel plate different conditions obdurability
From the aspect of energy, the control of Si contents is limited in, i.e., preferred control range is
0.20%-0.30%.
Mn：Mn elements are in addition to playing reinforcing matrix in steel, moreover it is possible to effectively improve steel
Quenching degree, similarly help to improve intensity but reduce tough, plasticity, therefore the technical program
The control of Mn contents is 1.30%~1.60%.Mn contents are preferably controlled in actual production steel
The upper limit, i.e., preferred control range is 1.40%-1.60%.
Mo：Mo effect be improve quenching degree, heat resistance, and with Cr, Mn collective effect
Reduce or suppress temper brittleness.When the control of Mo contents is 0.5% or so in steel, Ji Huke
So that temper brittleness is completely eliminated；But when Mo contents are less than 0.20% or more than 0.80%, then
It is little to the action effect of the Low-Temperature Temper Brittleness of steel, it is thus determined that being in Mo composition ranges
0.40~0.60%, it is 0.45%-0.55% preferably to control Mo contents.
Ni：Ni can be obviously improved the low-temperature flexibility of steel, while improving the low of thick section steel plate
Warm toughness, makes steel plate also have higher toughness while with sufficient intensity, meets index
Requirement.In view of steel plate thickness >=100mm of the present invention, for ensure intensity and it is tough,
Plasticity reaches preferable matching, therefore Ni contents of the present invention are defined as：0.60%~0.80%.
Cr：Cr can significantly improve the antioxidation of steel in steel, increase resistance to corrosion.
Austenite phase field is reduced simultaneously, improves the through hardening performance of steel.But Cr can also significantly improve steel
Brittle transition temperature, promotes temper brittleness.Intensity during to be further ensured that steel plate different conditions
Stability, Cr contents control range of the present invention is：0.25%~0.45%, preferred scope is
0.30%-0.40%.
V：Midium-carbon steel requirement is fine-grained steel, smaller than coarse-grained steel irradiation fragility.Add in steel
Entering V has crystal grain thinning, improves grain coarsening temperature effect.Simultaneously more importantly in steel
Plus after V, separating out second phase particles can play effectively brilliant during long-time SPWHT
Boundary's " anchoring " is acted on, and delays the decline of intensity.Therefore V content scope of the present invention is
0.02%-0.05%, preferably control range are 0.02%-0.04%.
P：Irradiation test shows that P is very sensitive to radiation embrittlement, while P content is higher,
Be also easy to aggravate the generation of center segregation and center porosity, therefore it is required that in steel P content it is more low more
Good, P content control range of the present invention is≤0.012%.
S：S easily forms S compounds in steel and is mingled with, and reduces impact flexibility, influences welding performance,
Aggravate the generation of the defect such as center segregation, loose, therefore S contents control range of the present invention simultaneously
For≤0.008% ,≤0.002% is preferably controlled to.
Gas [H], [O]：Generally speaking, their performances to steel are harmful to, while can also increase
Plus radiation embrittlement effect, it is desirable to their content will be reduced to floor level.The present invention
[H], [O] content control range are [H]≤2.0ppm, [O]≤30ppm.
A kind of manufacture method of 550MPa grades of nuclear power voltage-stablizer equipment steel, including smelt, forge
Make, roll, be heat-treated,
Smelt：Produced using electric furnace, die casting process, using outside LF stoves in smelting process
Refining and VD applications of vacuum, qualified molten steel are cast into polygonal steel ingot；
Forging：The polygonal excessive fire time Stew of steel ingot warp is thick, pull out, the steel billet thickness that final production goes out
330-450mm, whole process initial forging temperature >=1180 DEG C, final forging temperature >=800 DEG C, forging
Than >=6.0；
Rolling：Under billet heating temperature >=1100 DEG C, rolled plate thickness >=100mm, stagnation pressure
Than >=2.5, average rolling pass deflection >=10%；
Heat treatment：Steel plate needs to carry out modifier treatment after rolling, it is ensured that even tissue, crystal grain is tiny,
Performance is stable.
Hardening and tempering process is：
Quenching：900 DEG C ± 15 DEG C, soaking time：2-4min/mm, fully is incubated to ensure
Uniform austenite structure is formed, water quenching is carried out immediately after until surface of steel plate temperature is down to
Less than 100 DEG C.
Tempering：645 DEG C ± 15 DEG C, soaking time：1-3min/mm, fully is incubated to ensure
Carbide Precipitation in steel, and form stable tempered sorbite tissue.
The beneficial effects of the present invention are：
Steel plate thickness >=100mm, width and length can be produced according to the actual requirements.With
Prior art is compared, and is had the beneficial effect that (by taking 119mm plates as an example)：
(1) steel plate of the present invention is respectively provided with preferable strength level after QT under different conditions：
It is strong at steel plate thickness 1/4 and at 1/2 from the point of view of QT and SPWHT two states
Spend fall smaller and controllable, index request can be met completely.
(2) steel plate of the present invention is after QT, and -20 DEG C of impact absorbing energy under different conditions are same
Higher level is maintained at, the requirement of index is not only met, and with larger surplus：
Brief description of the drawings
Fig. 1 is micro-organization chart at the quenched and tempered state thickness 1/4 of the embodiment of the present invention 1.
Fig. 2 is micro-organization chart at the Simulated post-weld heat treatment thickness 1/4 of the embodiment of the present invention 1.
Fig. 3 is micro-organization chart at the quenched and tempered state thickness 1/2 of the embodiment of the present invention 2.
Fig. 4 is micro-organization chart at the Simulated post-weld heat treatment state thickness 1/2 of the embodiment of the present invention 2.
Embodiment
Below by embodiment, the present invention is further illustrated.
The embodiment of the present invention according to the component proportion of technical scheme, smelted, forged, being rolled,
Heat treatment.The composition of steel of the embodiment of the present invention is shown in Table 1.The forging technology of steel of the embodiment of the present invention
Parameter is shown in Table 2.The rolling and heat treatment of steel of the embodiment of the present invention are shown in Table 3.The embodiment of the present invention
Steel Properties are shown in Table 4.
The composition of the steel of the embodiment of the present invention of table 1 is shown in
The smithing technological parameter of the steel of the embodiment of the present invention of table 2
| Embodiment | Initial forging temperature/DEG C | Final forging temperature/DEG C | Finish-forging size (thickness)/mm | Forging ratio |
| 1 | 1200 | 840 | 350 | 9.44 |
| 2 | 1220 | 850 | 350 | 9.44 |
| 3 | 1250 | 910 | 400 | 8.26 |
| 4 | 1260 | 920 | 400 | 8.26 |
| 5 | 1230 | 920 | 420 | 7.86 |
| 6 | 1200 | 890 | 420 | 7.86 |
| 7 | 1250 | 930 | 450 | 6.86 |
| 8 | 1260 | 940 | 450 | 6.86 |
The rolling and heat treatment of the steel of the embodiment of the present invention of table 3
The Steel Properties of the embodiment of the present invention of table 4
Claims (2)
1. a kind of 550MPa grades of nuclear power voltage-stablizer equipment steel, it is characterised in that the steel plate into
Divide as follows by weight percentage：C：0.10%~0.20%, Si：0.10%~0.40%,
Mn：1.30%~1.60%, Mo：0.40~0.60%, Ni：0.60%~0.80%, Cr：
0.25%~0.45%, V：0.02%~0.05%, surplus is Fe and inevitable impurity.
Impurity element control in steel：P≤0.012%, S≤0.008%, [H]≤2.0ppm, [O]
≤30ppm。
2. a kind of manufacturer of the 550MPa level nuclear power voltage-stablizer equipment steel described in claim 1
Method, including smelt, forge, roll, be heat-treated, it is characterised in that：
(1) smelt：Produced using electric furnace, die casting process, LF is used in smelting process
External refining and VD applications of vacuum, are cast into polygonal steel ingot；
(2) forge：The polygonal excessive fire time Stew of steel ingot warp is thick, pull out, and the steel billet produced is thick
Spend 330-450mm, forging process initial forging temperature >=1180 DEG C, final forging temperature >=800 DEG C, forging
Make ratio >=6.0；
(3) roll：Billet heating temperature >=1100 DEG C, rolled plate thickness >=100mm,
Ratio >=2.5 under stagnation pressure, average rolling pass deflection >=10%；
(4) it is heat-treated：Quenching：900 DEG C ± 15 DEG C, soaking time：2-4min/mm,
Water quenching is carried out immediately after until surface of steel plate temperature is down to less than 100 DEG C, is tempered afterwards：645
DEG C ± 15 DEG C, soaking time：1-3min/mm.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| 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 |
| CN117226218A (en) * | 2023-09-22 | 2023-12-15 | 东方法马通核泵有限责任公司 | Build-up welding process of pressurized water reactor nuclear power coolant main pump |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| 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 |
| 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 |
| CN117226218A (en) * | 2023-09-22 | 2023-12-15 | 东方法马通核泵有限责任公司 | Build-up welding process of pressurized water reactor nuclear power coolant main pump |
| CN117226218B (en) * | 2023-09-22 | 2024-04-23 | 东方法马通核泵有限责任公司 | Build-up welding process of pressurized water reactor nuclear power coolant main pump |
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