CN101892442A - Steel for nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement and making method thereof - Google Patents
Steel for nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement and making method thereof Download PDFInfo
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Abstract
The invention discloses a steel for nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement and a making method thereof. The steel comprises the following chemical compositions in percentage by weight: 0.08-0.15 percent of C, 0.20-0.35 percent of Si, 0.80-1.60 percent of Mn, P no more than 0.012 percent, S no more than 0.005, 0.01-0.05 percent of Alt, 0.08-0.015 percent of Ti, N no more than 0.010 and the balance of Fe and unavoidable impurities. The chemical compositions of the steel also satisfy that Ni+Cr+Mo+Cu is no more than 0.70, Alt/N is no less than 2.0, Cu+6Sn is no more than 0.30 and Sn+Sb+As+Pb no more than 0.020. In the invention, the making method in a controlled rolling state and a normalized state is designed according to the requirements of different delivery states of steel products and different steel thicknesses, has the advantages of simple rolling technology and high product qualified rate of steel plates and can towel meet the requirements of mass production. The steel can be widely used for making second generation nuclear power pressure equipment, second generation improved nuclear power pressure equipment and third generation nuclear power pressure equipment.
Description
Technical field
The invention belongs to the low-carbon micro steel-alloy technical field, relate to a kind of nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement steel and manufacture method thereof particularly.
Background technology
Steel for nuclear power pressure equipment is applicable to that the reactor housing of making nuclear reactor, pressurized vessel, pressure pipeline etc. support the material of reactor foundation structure; also playing the operation of protection nuclear power generating equipment simultaneously, prevent the effect that radioactive ray spreads, is last one safety curtain of reactor.Different according to the difference of type of reactor and foundation structure material effects, the security level required of steel for nuclear power pressure equipment also is different.In bearing devices such as nuclear power reactor housing, support, bracket, secondary pipeline, adopt at present as tensile strength 400～550MPa level steel such as A42, A52, P265GH, P295GH, P355GH more, but the toughness of these steel grades, ductility and intensity control level are not high, can only be applicable to 2, the 3 grades of bearing devices of Nuclear safety in the s-generation nuclear power engineering.Along with the development of third generation nuclear power technology, original bearing device can not satisfy nuclear power engineering to performance requriementss such as the intensity of steel plate, toughness, weldabilities fully with steel.In order to improve operating security of Nuclear power plants and reliability, bearing device needs further to improve its toughness, ductility, high temperature tensile properties, welding property with steel, reduce the radiation embrittlement effect, reduce the plate property fluctuation, thereby realize reducing the manufacturing cost and the difficulty of construction of nuclear power pressure equipment, improve engineering life-span and security.
Before the present invention, domestic technical literature and patent documentation about third generation nuclear power technology steel for nuclear power pressure equipment is less.As " heavy casting and forging " 2008, (1): " comparison and the analysis of SA508 Series Steel of a nuclear reactor pressure container forging " literary composition and " heavy casting and forging " 2002 among the 1-3, (1): " research of 1000MW nuclear power evaporator tube sheet process for making " literary composition is inquired into the technical problem of A508-3 and 18MND5 steel for nuclear power pressure equipment respectively among the 5-9.The advantage of these two kinds of steel is all to have high strength and high tenacity, but the responsive element Cu of radiation embrittlement, V have been added in its chemical ingredients, and the controlled levels to residual element in the steel plate such as P, S, Sn, Sb, As etc. is not high, has increased the weight of the radiation embrittlement effect of steel plate.Simultaneously, in order to improve the intensity of steel, added more alloying element in these steel constitutions, cause the purity of steel that to a certain degree reduction is arranged, the segregation degree also increases, thereby the too high ductility that causes of the intensity of steel descends, and is not suitable for making bearing devices such as nuclear power reactor housing that over-all propertieies such as intensity, ductility, toughness, weldability are had relatively high expectations, support, bracket, secondary pipeline.Thereby be not suitable for making s-generation modified version and third generation nuclear power pressure equipment.
In addition, in the actual production process, also adopted a lot of stainless steels such as Z2CN18-10 etc. in the nuclear power pressure equipment, these stainless steels have higher intensity and low yield tensile ratio, good anti-fatigue performance and fracture toughness property are arranged, have erosion resistance and low-temperature flexibility preferably simultaneously, but these stainless weak points are valuable alloying element Ni in their chemical ingredients, Mo, the Cr equal size is all higher, make the steel manufacturing cost higher, the production thickness of stainless-steel sheet is also restricted simultaneously, also very strict to later stage steel plate welding process requirement, thereby cause whole nuclear island construction project cost up.
Summary of the invention
The objective of the invention is to provide a kind of nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement steel and manufacture method thereof, this steel has good cold and hot working performance and excellent welding property, and this manufacture method can accurately be controlled at the strength range of different condition of delivery lower steel plates such as normalizing attitude or controlled rolling attitude.
For achieving the above object, the nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement steel that the present invention is designed, its chemical ingredients percentage ratio is by weight counted: 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 unavoidable impurities; The chemical ingredients of this steel also satisfies following relational expression:
(1)Ni+Cr+Mo+Cu≤0.70；
(2)Alt/N≥2.0；
(3)Cu+6Sn≤0.30；
(4)Sn+Sb+As+Pb≤0.020。
The preferred chemical ingredients of this steel percentage ratio is by weight counted: C:0.10～0.15, Si:0.20～0.35, Mn:0.90～1.50, P≤0.012, S≤0.003, Alt:0.02～0.04, Ti:0.008～0.015, N≤0.010, and all the other are Fe and unavoidable impurities;
It is that the manufacture method of 4～10mm controlled rolling attitude steel plate may further comprise the steps that nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement of the present invention is processed into thickness with steel: desulfurizing iron, converter smelting, vacuum-treat, continuous casting, slab heating, hot continuous rolling, cool off, batch, open equality, described slab heating temperature is made as 1100～1250 ℃, described hot continuous rolling start rolling temperature is controlled to be 1000～1150 ℃, finishing temperature is controlled to be 800～900 ℃, and coiling temperature is controlled to be 60～680 ℃.
Further, described slab heating temperature is controlled to be 1180～1250 ℃; Described hot continuous rolling start rolling temperature is controlled to be 1040～1100 ℃, and finishing temperature is controlled to be 840～860 ℃.
Further, to the product made from steel of CE≤0.30, described coiling temperature is controlled to be 620～650 ℃; The described coiling temperature of the product made from steel of CE＞0.30 is controlled to be 650～680; Wherein, described CE=C+Mn/6+ (Cu+Mo+V)/5+ (Ni+Cu)/15.
It is that 10～60mm normalizing attitude steel plate manufacture method may further comprise the steps: desulfurizing iron, converter smelting, vacuum-treat, continuous casting, slab heating, hot continuous rolling, cooling, normalizing treatment etc. that nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement of the present invention is processed into thickness with steel, wherein, start rolling temperature is controlled to be 1100～1280 during described hot continuous rolling, finishing temperature is controlled at 800～900 ℃, rolling total draft 〉=60%, described normalizing thermal treatment temp is 870～930 ℃; Air cooling is to room temperature after the normalizing.
Further, described start rolling temperature is controlled to be 1180～1240 ℃; Described finishing temperature is controlled to be 800～860 ℃; Described rolling total draft 〉=70%;
Further, to the product made from steel of CE≤0.36, described normalizing thermal treatment temp is controlled to be 870～900 ℃; The described normalizing thermal treatment temp of the product made from steel of CE＞0.36 is controlled to be 900～930 ℃; Wherein, described CE=C+Mn/6+ (Cu+Mo+V)/5+ (Ni+Cu)/15.
The setting of main alloy element and manufacture method principle are as follows in the composition of steel of the present invention:
During this steel grade of design invention, consider that this steel mainly is toughness, the levels of ductility that will guarantee steel plate and the strength range of controlling well.Therefore, low-carbon micro steel-alloy can reach design requirements.To control the purity of molten steel during steel-making, prevent that impurity element and residual element are to steel plate radiation embrittlement Effect on Performance.The design mix of C, Si, Mn, Alt will guarantee that the strength range of steel plate meets steel for nuclear power pressure equipment as the requirement of equipment such as nuclear power reactor housing, support, bracket, pipeline.The interpolation of trace Ti has improved the ductility and the toughness levels of steel plate, has guaranteed the safe in utilization of steel plate.
(1) carbon
Carbon belongs to the deleterious interstitial element of irradiation, and the quantity of irradiation hardening and steel intermediate gap element is closely related.Along with carbon content increases, the unit elongation of steel and impelling strength descend, and especially the low-temperature flexibility decline scope is bigger, and also the phenomenon of hardening can occur at the welded heat affecting zone of steel, causes the generation of welding cold cracking.Guaranteeing suitably to reduce the weight percentage of carbon under the proper strength prerequisite during steel design mix of the present invention.Therefore, the carbon weight percentage should be controlled at 0.08～0.15% scope among the present invention, and preferred 0.10～0.15% scope is so that obtain excellent comprehensive performances.
(3) silicon
Silicone content in the steel for nuclear power pressure equipment is not the alloying element that have a mind to add, but from steel scrap and pig iron raw material, bring when smelting.Silicon has the effect of constant illumination defective, makes recovery Effects not obvious.Silicone content is too high harmful to irradiation, answers the content of silicon in the strict control steel for nuclear power pressure equipment, and its weight percentage generally should be less than 0.35%.But silicon can reduce the greying tendency of carbon in the steel, and improves the intensity of steel with the solution strengthening form, so silicon is controlled at 0.20～0.35% among the present invention.
(4) manganese
Manganese is the effective element that enlarges γ phase, crystal grain thinning, spheroidized carbide and assurance over-all properties and improve hardening capacity, but experiment shows that it has the trend that increases radiation embrittlement.This is that the thermal spike quantity that makes steel plate satisfy austenitizing temperature in the steel under irradiation increases, and promptly is similar to the microcell that is quenched and increases because manganese causes the Ac3 temperature to reduce.Therefore, the weight percentage that will control manganese under the situation that guarantees the certain intensity of steel for nuclear power pressure equipment is 0.80～1.60%, and preferred 0.90～1.50% scope can guarantee the intensity and the low irradiation embrittlement performance of steel simultaneously.
(5) aluminium
Aluminium is the main deoxidant element in the steel, and aluminium is about 0.6% at the maxima solubility of γ in mutually, and it only faintly increases hardening capacity after dissolving in austenite, so think that full aluminium (Alt) not have to influence to the welding hydrogen induced cracking substantially.But, when the Alt too high levels, easily cause being mingled with in the steel and increase, unfavorable to the toughness of steel, so the present invention is controlled at 0.01～0.05% with the aluminium weight percentage, preferred 0.02～0.04% scope.
(6) nitrogen
What of solid solution nitrogen are to nitrogen and radiation defect and to influence other elements relevant with quantity, stability that exposure spots defective or defective group form complicated defective.As German power station alliance card prestige room company (KWU) regulation in the steel for nuclear power pressure equipment is contained N＜0.013%, require N weight percentage≤0.010% in the present invention.
In the steel for nuclear power pressure equipment of the present invention, relevant for the aluminium content that deoxidation is controlled with crystal grain thinning with N content, Alt/N there is requirement.If the Alt/N ratio is reasonable, can improve toughness, the minimizing radiation sensitivity of steel in the steel.The present invention defines Alt/N 〉=2.0% simultaneously at qualification Alt content range and helps improving steel plate toughness, reduces radiation sensitivity, reduces the steel plate strain aging sensitivity simultaneously.
(7) titanium
Titanium is a kind of intensive carbide and nitride forming element, and the TiN of formation, Ti particles such as (CN) is highly stable, and the pinning crystal boundary stops the γ grain growth effectively, thereby plays the effect of crystal grain thinning.Titanium can suppress the generation in irradiation cavity to a certain extent, but too much titanium can cause the precipitate of titanium to increase.Simultaneously, the titanium of trace can be put forward the hot strength and the toughness of kind steel, so the weight percentage of titanium is controlled at 0.008～0.015%.
When the content to individual element limited, steel of the present invention had also limited the residual quantity of the weight percentage of elements such as Ni, Cr, Mo, Cu with relational expression Ni+Cr+Mo+Cu≤0.70%.Because nickel can form unsettled small quench zone under radiation parameter, increased the inner embrittlement tendency of steel plate, and the free copper that the is settled out microvoid hole that collision produces to tandem there is stabilization, has increased the crisp effect of steel plate irradiation under irradiation.Make above-mentioned restriction and not only guaranteed the strength range of steel plate and the purity of molten steel, reduced the embrittlement effect of nuclear level equipment under irradiation again.
In addition, vestige element and impurity element all are naturally occurring elements in the ore deposit, ground, are difficult in the steelmaking feed avoid.The vestige element of steel of the present invention mainly is As, Pb, Sn, Sb, and is bigger to the irradiation behaviour influence although content is very few in steel, and strict its content of control can obviously reduce irradiation effect.But these vestige elements are only influential to high temperature irradiation, and when being lower than 149 ℃ of irradiation, influence is little.This influence of organizing in matrix during with low temperature irradiation greater than composition influence during high temperature irradiation the influence of composition relevant greater than organizing.Therefore the present invention defines the requirement of Sn+Sb+As+Pb≤0.020% and Cu+6Sn≤0.30% to the weight percentage of above-mentioned each vestige element.
Impurity element such as p and s has the tendency of quickening radiation embrittlement in composition of steel of the present invention.Sulphur can reduce sample maximum impact merit behind the irradiation test, and this is with to form low-melting FeS, MnS relevant.Phosphorus is relevant at grain boundary segregation with phosphorus to radiation sensitive.Because of being diffused into crystal boundary, phosphorus atom causes that segregation reduces the crystal boundary surface energy, so cause nil-ductility temperature (NDTT) to increase.In addition, phosphorus content is also relevant with copper content to the influence of radiation embrittlement.Increase with copper content, the irradiation effect of phosphorus reduces.Because when copper content is low in the steel, the phosphorus atom group and the phosphide precipitation that are gathered into youngster's nanometer size are many; Along with the copper amount increases, phosphorus is bonded in the rich copper precipitation, produces the copper phosphide, i.e. the independent influence of phosphorus increases and reduces along with copper.Consider actual metallurgical level, the weight percentage with P and S in the steel of the present invention is defined as P≤0.012%, S≤0.005%.
Nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement of the present invention is as follows with the principle of steel making method institute foundation:
In the steel controlled rolling attitude steel plate manufacture method of the present invention: finishing temperature (RT7) is arranged on 800～900 ℃ of scopes, preferred 840～860 ℃ of scopes.This temperature can cause the cooling intensity deficiency as being provided with to hang down, and armor plate strength is on the low side; As too high meeting is set makes the automatic cooling system water yield excessive, cause armor plate strength higher.(CT) is arranged on 620～680 ℃ with coiling temperature, is to guarantee that coil of strip is in the coiling temperature scope that equipment allows.Formulate suitable coiling temperature according to different carbon equivalents and accurately control strength range, preferred version is the product made from steel to CE≤0.30, and described coiling temperature is controlled to be 620～650 ℃; Product made from steel coiling temperature to CE＞0.30 is controlled to be 650～680 ℃; Wherein: CE=C+Mn/6+ (Cu+Mo+V)/5+ (Ni+Cu)/15.
Controlled rolling attitude steel plate manufacture method of the present invention preferably is applicable to produces thickness 4～10mm steel plate, so thickness limited is because controlled rolling attitude steel plate adopts the hot continuous rolling production technique, as produce thickness＜4mm, the plate shape control difficulty of steel plate is bigger, and be not easy to transportation, as thickness requirement＞10mm, can realize that then the whole mechanical property of steel plate is better than the controlled rolling attitude in normalizing attitude technology.
In the steel normalizing attitude steel plate manufacture method of the present invention: the hot continuous rolling start rolling temperature is arranged on 1100～1280 ℃, preferred 1180～1240 ℃, be provided with as this temperature and low can cause rolling stress excessive, crackle may appear when rolling, even disconnected base and become waste product.Simultaneously, start rolling temperature is crossed the low fragmentation that also is unfavorable for coarse grain in the steel, makes in the steel crystal grain thick, has reduced the mechanical property of steel plate, has also increased mill load, has reduced the work-ing life of milling train.Be provided with as start rolling temperature and too highly easily cause mixed crystal when rolling, the steel plate homogeneity of structure is reduced, toughness descends.Finishing temperature is controlled at 800～900 ℃, preferred 800～860 ℃ of comprehensive mechanical properties that also can better guarantee steel.Normalizing temperature is arranged on 860～950 ℃, mainly is to make the steel complete austenitizing, forms uniform austenite structure.In order accurately to control the strength range of steel plate, preferred fabrication scheme is according to different carbon equivalents the normalizing temperature scope to be set, and to the product made from steel of CE≤0.36, described normalizing thermal treatment temp is controlled to be 870～900 ℃; The described normalizing thermal treatment temp of the product made from steel of CE＞0.36 is controlled to be 900～930 ℃; Wherein, described CE=C+Mn/6+ (Cu+Mo+V)/5+ (Ni+Cu)/15.
Normalizing attitude steel plate manufacture method of the present invention is applicable to produces thickness 10～60mm steel plate, because as thickness＞60mm, the thickness of slab effect strengthens, and strength range difference increases between the different thickness steel plate, and for also becoming big than Plate Steel different sites intensity, ductility and toughness difference.As thickness＜10mm, steel plate template after rolling, thermal treatment is difficult to reach design requirements.
The present invention is by strictness control steel following chemical components in percentage by weight and take reasonably rolling and thermal treatment process, can accurately control the strength range of steel plate under different condition of delivery.Last yield strength (the R of product made from steel of the present invention
EH) between 300～345MPa, under this strength range, steel plate has best matching when combining with material such as concrete, be not easy to occur crackle and gap under cold and hot condition.Steel plate of the present invention has high tenacity, high ductility, low irradiation embrittlement simultaneously, good cold and hot working performance and excellent welding property, can shorten the technological process of production and production cycle, lower the production cost of steel greatly, realize the production domesticization of steel grade, finish the present situation of third generation significant points steel for nuclear power pressure equipment material dependence on import.
Embodiment
Below in conjunction with specific embodiment nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement of the present invention is elaborated with steel and manufacture method thereof.
Table 1 has been listed the chemical component weight per-cent (surplus is Fe and unavoidable impurities) of specific examples steel 1～8 of the present invention, and 9～12 steel are the domestic and international steel grades of the same type of existing 4 stoves in the table 1, select steel as a comparison.
Table 1 embodiment of the invention and contrast steel grade chemical ingredients (wt%)
| Numbering | C | Si | Mn | P | S | Alt | Ti | N | Ni+Cr+ Mo+Cu | Alt/ N | Cu+6Sn | Sn+Sb+ As+Pb |
| 1 | 0.08 | 0.20 | 1.03 | 0.008 | 0.004 | 0.028 | 0.009 | 0.0025 | ＜0.10 | 11.2 | ＜0.10 | ＜0.020 |
| 2 | 0.10 | 0.35 | 0.80 | 0.010 | 0.003 | 0.050 | 0.008 | 0.0026 | ＜0.30 | 2.0 | ＜0.10 | ＜0.020 |
| 3 | 0.12 | 0.21 | 1.60 | 0.009 | 0.004 | 0.022 | 0.011 | 0.0025 | ＜0.10 | 8.8 | 0.30 | 0.020 |
| 4 | 0.13 | 0.20 | 0.90 | 0.011 | 0.003 | 0.040 | 0.012 | 0.010 | 0.70 | 10.9 | 0.30 | ＜0.018 |
| 5 | 0.13 | 0.32 | 1.25 | 0.012 | 0.004 | 0.010 | 0.012 | 0.0025 | ＜0.10 | 10.4 | ＜0.20 | ＜0.010 |
| 6 | 0.15 | 0.31 | 1.50 | 0.010 | 0.004 | 0.030 | 0.013 | 0.0027 | 0.50 | 11.1 | ＜0.10 | ＜0.020 |
| 7 | 0.14 | 0.34 | 1.35 | 0.012 | 0.005 | 0.020 | 0.015 | 0.0024 | ＜0.10 | 12.9 | ＜0.10 | ＜0.015 |
| 8 | 0.15 | 0.32 | 1.40 | 0.011 | 0.004 | 0.029 | 0.013 | 0.0020 | ＜0.10 | 14.5 | ＜0.10 | ＜0.020 |
| 9 | 0.10 | 0.08 | 1.08 | 0.014 | 0.008 | 0.005 | 0.005 | 0.0057 | ＜0.10 | 0.9 | ＜0.10 | ＜0.040 |
| 10 | 0.14 | 0.12 | 1.12 | 0.015 | 0.008 | 0.005 | 0.005 | 0.0056 | ＜0.10 | 0.9 | ＜0.10 | ＜0.040 |
| 11 | 0.16 | 0.24 | 1.16 | 0.015 | 0.006 | 0.015 | 0.005 | 0.0045 | ＜0.10 | 3.3 | ＜0.10 | ＜0.040 |
| 12 | 0.16 | 0.28 | 1.25 | 0.016 | 0.007 | 0.018 | 0.005 | 0.0051 | ＜0.10 | 3.5 | ＜0.10 | ＜0.040 |
Table 2 has been listed the embodiment steel plate of table 1 correspondence and the main process for making of manufacturing of contrast steel plate, and wherein embodiment steel 1,2,3,4 and compared steel 9,10 are controlled rolling attitude steel, and embodiment steel 5,6,7,8 and compared steel 11,12 are normalizing attitude steel.
Table 2 embodiment of the invention and the main process for making that contrasts steel grade:
Table 3 has been listed present embodiment 1～8 steel plate and has been contrasted firm 9～12 steel plate mechanical properties.
Table 3 embodiment of the invention and the mechanics assay that contrasts steel grade:
Compare with selected compared steel by table 3 steel of the present invention as can be seen, its mechanical property has following advantage:
Steel of the present invention-20 ℃ the summer is compared all with compared steel and improves a lot than v-notch ballistic work (20 ℃ of KV2) numerical value, controlled rolling attitude embodiment steel all is higher than 86J (impact specimen is 5*10*55mm), normalizing attitude embodiment steel has all surpassed 210J, some in addition up to 235J; Normalizing attitude embodiment steel nil-ductility temperature NDTT all is lower than-25 ℃, proves that steel of the present invention has high tenacity.Steel unit elongation A of the present invention has all surpassed 35%, thickness direction relative reduction in area Z
ZAll above 75%, compare with compared steel, steel of the present invention has high ductility.Simultaneously, table three data presentation steel of the present invention steel of the present invention has accurate strength range, the last yield strength R of embodiment steel
EHAll between 300～345Mpa, has good obdurability coupling.Normalizing attitude embodiment steel when 350 ℃ of tension tests, R
P0.2(disproportional extends 0.2% o'clock yield strength) all reaches more than the 230Mpa, has the excellent high-temperature tensile property.Simultaneously, steel grade of the present invention and manufacture method have guaranteed that product made from steel has extremely low residual element level, have guaranteed the welding property and the low irradiation embrittlement effect of steel plate, can simplify the weldprocedure when using greatly, improve welding efficiency.Steel of the present invention can be as required with controlled rolling attitude or the delivery of normalizing attitude, and steel product cost is relatively low, steel plate qualification rate height, and, adapt to batch production requirements.Steel of the present invention can be widely used in the s-generation, two generation modified version and the manufacturing of third generation nuclear power pressure equipment (reactor housing, support, bracket, secondary pipeline etc.).
Claims (8)
1. nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement steel, its chemical ingredients percentage ratio is by weight counted: 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 unavoidable impurities;
The chemical ingredients of this steel also satisfies following relational expression:
(1)Ni+Cr+Mo+Cu≤0.70；
(2)Alt/N≥2.0；
(3)Cu+6Sn≤0.30；
(4)Sn+Sb+As+Pb≤0.020。
2. nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement steel according to claim 1, it is characterized in that: the chemical ingredients of this steel percentage ratio is by weight counted: C:0.10～0.15, Si:0.20～0.35, Mn:0.90～1.50, P≤0.012, S≤0.005, Alt:0.02～0.04, Ti:0.008～0.015, N≤0.010, and all the other are Fe and unavoidable impurities;
3. method that the described nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement of claim 1 is processed into 4～10mm Plate Steel with steel, may further comprise the steps: desulfurizing iron, converter smelting, vacuum-treat, continuous casting, slab heating, hot continuous rolling, cool off, batch, open flat, it is characterized in that: described slab heating temperature is controlled to be 1100～1250 ℃, described hot continuous rolling start rolling temperature is controlled to be 1000～1150, finishing temperature is controlled to be 800～900 ℃, and coiling temperature is controlled to be 620～680 ℃.
4. method according to claim 3 is characterized in that: described slab heating temperature is controlled to be 1180～1250 ℃, and described hot continuous rolling start rolling temperature is controlled to be 1040～1100 ℃, and finishing temperature is controlled to be 840～860.
5. according to claim 3 or 4 described methods, it is characterized in that: at the product made from steel of CE≤0.30, described coiling temperature is controlled to be 620～650 ℃, is controlled to be 650～680 ℃ at the described coiling temperature of the product made from steel of CE＞0.30;
Wherein, described CE=C+Mn/6+ (Cu+Mo+V)/5+ (Ni+Cu)/15.
6. method that the described nuclear power pressure equipment with high toughness, high ductility and low irradiation embrittlement of claim 1 is processed into 10～60mm Plate Steel with steel, may further comprise the steps: desulfurizing iron, converter smelting, vacuum-treat, continuous casting, slab heating, hot continuous rolling, cooling, normalizing treatment, it is characterized in that: start rolling temperature is controlled to be 1100～1280 ℃ during described hot continuous rolling, finishing temperature is controlled at 800～900 ℃, rolling total draft 〉=60%, described normalizing thermal treatment temp is 870～930 ℃; Air cooling is to room temperature after the normalizing.
7. method according to claim 6 is characterized in that: described start rolling temperature is controlled to be 1180～1240 ℃; Described finishing temperature is controlled to be 800～860 ℃; Described rolling total draft 〉=70%.
8. according to claim 6 or 7 described methods, it is characterized in that: at the product made from steel of CE≤0.36, described normalizing thermal treatment temp is controlled to be 870～900, is controlled to be 900～930 ℃ at the described normalizing thermal treatment temp of the product made from steel of CE＞0.36;
Wherein, described CE=C+Mn/6+ (Cu+Mo+V)/5+ (Ni+Cu)/15.
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102912222A (en) * | 2012-10-14 | 2013-02-06 | 浙江大隆合金钢有限公司 | 18MND5 low-alloy structural steel for nuclear power and technical control method for 18MND5 low-alloy structural steel |
| CN103509994A (en) * | 2012-06-21 | 2014-01-15 | 内蒙古包钢钢联股份有限公司 | Low carbon steel plate for pressure-bearing equipment and normalizing process thereof |
| CN103805919A (en) * | 2014-01-16 | 2014-05-21 | 安徽省杨氏恒泰钢管扣件加工有限公司 | Corrosion-resistant high-strength seamless steel tube material and preparation method thereof |
| CN104962812A (en) * | 2015-07-16 | 2015-10-07 | 武汉钢铁(集团)公司 | Hot-continuous-rolled axle housing steel with favorable plate shape and manufacturing method thereof |
| CN106702274A (en) * | 2016-12-01 | 2017-05-24 | 武汉钢铁股份有限公司 | 14.5mm-thickness dedicated automobile spoke steel uniform in property and manufacturing method and application of spoke steel |
| CN107475622A (en) * | 2017-09-05 | 2017-12-15 | 武汉钢铁有限公司 | Steel plate and its manufacture method with good thermal processability energy |
| CN108277435A (en) * | 2018-03-21 | 2018-07-13 | 包头钢铁（集团）有限责任公司 | A kind of anti-corrosion pressure-bearing seamless steel pipe and its production method |
| CN108660382A (en) * | 2017-03-29 | 2018-10-16 | 鞍钢股份有限公司 | A kind of nuclear power station Leak-tight liner steel that anti-radiation performance is excellent and its manufacturing method |
| CN111270153A (en) * | 2020-03-30 | 2020-06-12 | 南京钢铁股份有限公司 | Steel with thickness of 6mm for nuclear power containment and manufacturing method thereof |
| JP2020186453A (en) * | 2019-05-16 | 2020-11-19 | 三菱重工業株式会社 | Carbon steel, radioactive material storage container, shield performance analyzing method and shield structure designing method |
| CN112143976A (en) * | 2020-08-24 | 2020-12-29 | 江阴兴澄特种钢铁有限公司 | P265GH steel plate for nuclear power and manufacturing method thereof |
| CN112795842A (en) * | 2020-12-25 | 2021-05-14 | 鞍钢股份有限公司 | Steel for submarine quick connection pipeline and production 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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| CN1974823A (en) * | 2006-12-18 | 2007-06-06 | 马鞍山钢铁股份有限公司 | CSP production process of steel for automobile crossbeam |
| CN101210303A (en) * | 2007-12-25 | 2008-07-02 | 莱芜钢铁集团有限公司 | High-strength anti-fatigue steel products and manufacturing method thereof |
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103509994A (en) * | 2012-06-21 | 2014-01-15 | 内蒙古包钢钢联股份有限公司 | Low carbon steel plate for pressure-bearing equipment and normalizing process thereof |
| CN102912222A (en) * | 2012-10-14 | 2013-02-06 | 浙江大隆合金钢有限公司 | 18MND5 low-alloy structural steel for nuclear power and technical control method for 18MND5 low-alloy structural steel |
| CN102912222B (en) * | 2012-10-14 | 2014-06-11 | 浙江大隆合金钢有限公司 | 18MND5 low-alloy structural steel for nuclear power and technical control method for 18MND5 low-alloy structural steel |
| CN103805919A (en) * | 2014-01-16 | 2014-05-21 | 安徽省杨氏恒泰钢管扣件加工有限公司 | Corrosion-resistant high-strength seamless steel tube material and preparation method thereof |
| CN104962812A (en) * | 2015-07-16 | 2015-10-07 | 武汉钢铁(集团)公司 | Hot-continuous-rolled axle housing steel with favorable plate shape and manufacturing method thereof |
| CN106702274A (en) * | 2016-12-01 | 2017-05-24 | 武汉钢铁股份有限公司 | 14.5mm-thickness dedicated automobile spoke steel uniform in property and manufacturing method and application of spoke steel |
| CN108660382A (en) * | 2017-03-29 | 2018-10-16 | 鞍钢股份有限公司 | A kind of nuclear power station Leak-tight liner steel that anti-radiation performance is excellent and its manufacturing method |
| CN107475622A (en) * | 2017-09-05 | 2017-12-15 | 武汉钢铁有限公司 | Steel plate and its manufacture method with good thermal processability energy |
| CN108277435A (en) * | 2018-03-21 | 2018-07-13 | 包头钢铁（集团）有限责任公司 | A kind of anti-corrosion pressure-bearing seamless steel pipe and its production method |
| JP2020186453A (en) * | 2019-05-16 | 2020-11-19 | 三菱重工業株式会社 | Carbon steel, radioactive material storage container, shield performance analyzing method and shield structure designing method |
| CN111270153A (en) * | 2020-03-30 | 2020-06-12 | 南京钢铁股份有限公司 | Steel with thickness of 6mm for nuclear power containment and manufacturing method thereof |
| CN111270153B (en) * | 2020-03-30 | 2022-03-22 | 南京钢铁股份有限公司 | Steel with thickness of 6mm for nuclear power containment and manufacturing method thereof |
| CN112143976A (en) * | 2020-08-24 | 2020-12-29 | 江阴兴澄特种钢铁有限公司 | P265GH steel plate for nuclear power and manufacturing method thereof |
| CN112795842A (en) * | 2020-12-25 | 2021-05-14 | 鞍钢股份有限公司 | Steel for submarine quick connection pipeline and production method thereof |
| CN112795842B (en) * | 2020-12-25 | 2022-05-13 | 鞍钢股份有限公司 | Steel for submarine quick connection pipeline and production 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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