CN108441779B - A kind of high intensity high-yield-ratio nuclear power station mechanical module steel and its manufacturing method - Google Patents

A kind of high intensity high-yield-ratio nuclear power station mechanical module steel and its manufacturing method Download PDF

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CN108441779B
CN108441779B CN201810154720.1A CN201810154720A CN108441779B CN 108441779 B CN108441779 B CN 108441779B CN 201810154720 A CN201810154720 A CN 201810154720A CN 108441779 B CN108441779 B CN 108441779B
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steel
yield
steel plate
temperature
nuclear power
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CN108441779A (en
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颜秉宇
孙殿东
王爽
胡海洋
刘翔
隋松言
欧阳鑫
段江涛
王勇
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Angang Steel Co Ltd
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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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Abstract

The present invention discloses a kind of high-intensitive high-yield-ratio nuclear power station mechanical module steel and its manufacturing method.Contain in steel, C:0.09%~0.12%, Si:0.30%~0.40%, Mn:0.50%~0.70%, P≤0.010%, S≤0.002%, Cr:0.60%~0.90%, Ni:0.30%~0.50%, Mo:0.26%~0.45%, V:0.005%~0.030%, B:0.001%~0.005%, Ti≤0.015%, Al:0.010%~0.025%, remaining is Fe and inevitable impurity；1565~1575 DEG C of vacuum outgas；1200~1250 DEG C of billet heating temperature, 1100~1150 DEG C of start rolling temperature, finishing temperature >=1000 DEG C, total deformation >=60%, 900~920 DEG C of hardening heat, 2~3.5min/mm of soaking time；625~660 DEG C of tempering temperature, 4~6min/mm of soaking time.20~110mm of steel plate thickness, tensile strength >=700MPa, yield tensile ratio >=0.9.

Description

A kind of high intensity high-yield-ratio nuclear power station mechanical module steel and its manufacturing method
Technical field
The invention belongs to ferrous material fields, in particular to nuclear power station mechanical module steel and its manufacturing method.
Background technique
Module refers to the sub-assembly assembled by material and component.Module is single as a whole after shop-fabricated Member, construction that is convenient and accelerating scene.To its prefabricated and assembling before module is in place, avoid in the narrow of its final position Space carries out excessive work, allows for installation and civil engineering concurrent job in this way.
China is building nuclear power station based on three generations's nuclear power at present, and system complex, construction period are long, construction quality requires Height, under the premise of guaranteeing quality, it is one of the target that nuclear power owner pursues that how to shorten the construction period, which reduces project cost, and tradition is applied The Combination Welding work of work mode, a large amount of valves and pipeline in nuclear island factory building carries out at the scene, need to put into more welder, and Long construction period improves installation effectiveness to reduce nuclear island on-site installation work amount, and foreign boiling water reactor of nuclear power plant implements pipeline The successful experience of root module technology has carried out system research to nuclear power station pipeline root module construction technology, has formulated pipeline The selected principle and design cycle of root module develop the duct section module design function based on three dimensional design platform, propose The technical conditions for implementing pipeline root module, provide reference for nuclear power station application module construction technology.
External boiling water reactor of nuclear power plant starts gradually to use modular construction technology, and take with the development of application technology Good engineering effort was obtained, with the accumulation of the increasingly mature and application experience of modular technology, boiling water reactor of nuclear power plant is used The range that modularized design is built is more and more wider, and the module of design is also increasing, and the distinguishing feature of nuclear power mechanical module is exactly Steel itself have preferable weldability and mouldability, need to there is apparent strict demand, finished steel to Design of Chemical Composition in this way Plate needs preferable fatigue performance and low-temperature flexibility, and mechanical module is mostly in the application reciprocation cycle formula with steel, and is usually located In low frequency high-stress state, so certain high-yield-ratio is conducive to the comprehensive performance of material.At present both at home and abroad to midium-carbon steel Form more patent:
Application No. is 201310083274.7, it is entitled " a kind of nuclear power station mechanical module supporting element high strength steel plate and its Manufacturing method ", the patent relate generally to a kind of production method of nuclear power station module supporting element steel plate, and ingredient 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 properly added alloying element in low carbon content design basis, reaches the tensile strength of steel 800MPa or more.The steel plate thickness of the patent is 6~65mm, and the thickness of steel plate is lower, and nuclear power machinery mould can not be completely covered The thickness range of block, while the heat-treatment temperature range of the patent is very big, in this temperature range, will cause the tissue of steel plate It is unstable.
Application No. is 201110117614.4, entitled " tensile strength is greater than 690MPa grades of nuclear vessel steel and producer Method ", the patent essentially disclose a kind of production method of nuclear vessel steel plate, chemical element mass percentage are as follows: and C≤ 0.08%, Si:0.15%~0.50%, Mn:1.30%~1.60%, Alt: 0.01%~0.05%, Ni:0.42%~ 0.70%, Mo:0.32%~0.60%, Cr:0.10%~0.30%, Ti:0.01%~0.04% control P≤0.008%, S ≤ 0.005%, N≤0.005%, Cu≤0.03%, V≤0.007%, Sn≤0.005%, Sb≤0.005%, As≤ 0.010%, Pb≤0.005%, remaining is Fe and inevitable impurity.Steel plate yield strength >=570MPa of the invention resists Tensile strength: 690~860MPa, -20 DEG C of impact >=100J.The chemical component of the invention requires the elements such as P, S, N, Cu very tight Lattice, the larger and requirement to raw material of smelting difficulty is more stringent, the raising cost of meeting by a relatively large margin, under the chemical component Carbon equivalent it is higher, influence the weldability of steel plate, at the same in the invention there is no consider the steel plate Simulated post-weld heat treatment time pair The influence of mechanical property.
It is entitled " a kind of modulation processing method of thick steel plates for pressure container " application No. is 201010154420.7, The patent essentially discloses a kind of nuclear power thick steel plates hardening and tempering method, it include the steps that it is following successively: Ι quenching: Steel plate is heated to 920~930 DEG C, keeps the temperature 45~55 minutes, then be quenched；II tempering: by quenched steel Plate is heated to 630~650 DEG C, keeps the temperature 40~50 minutes, takes out steel plate and is cooled to room temperature；III secondary quenching: by heating steel sheet plus Heat keeps the temperature 50~60 minutes, steel plate is quenched to 920 DEG C~930 DEG C；IV double tempering: after secondary quenching Steel plate is in chamber furnace, it is desirable that temperature control fluctuation is not more than ± 5 DEG C, is heated to 615~625 DEG C, keeps the temperature 40~50 minutes, take Room temperature is naturally cooled to out.The tensile strength Rm of steel plate is increased to by 630MPa using modifier treatment twice in the patent, is extended Rate A is increased to 20%~23%, it is secondary it is quenched the performance of steel plate is influenced less, and repeatedly heat treatment can be to surface of steel plate matter Amount is affected, and will lead to steel plate thickness and is not able to satisfy tolerance conditions, while the heat-treatment temperature range is too low, can only be for spy Determine steel plate thickness implementation.
Summary of the invention
The present invention provides a kind of high-intensitive high-yield-ratio core machinery power station module steel and its manufacturing methods, pass through chemistry The design of ingredient, rolling mill practice and heat treatment process makes the intensity, toughness and spy of the steel plate condition of delivery and Simulated post-weld heat treatment Hurt performance and obtain good matching, performance indicator can satisfy technical indicator, be fully able to meet three generations's pressurized-water reactor nuclear power plant The requirement of module steel.
Specific technical solution is:
A kind of high intensity high-yield-ratio nuclear power station mechanical module steel, chemical component is by mass percentage are as follows: C: 0.09%~0.12%, Si:0.30%~0.40%, Mn:0.50%~0.70%, P≤0.010%, S≤0.002%, Cr: 0.60%~0.90%, Ni:0.30%~0.50%, Mo:0.26%~0.45%, V:0.005%~0.030%, B: 0.001%~0.005%, Ti≤0.015%, Al:0.010%~0.025%, remaining content be Fe and inevitably it is miscellaneous Matter.
It is as follows using mentioned component design reason:
C: it is main intensified element in steel, the intensity and harden ability of steel can be effectively improved, but also reduce steel simultaneously Plasticity, toughness and weldability, the intensity that C content is relatively low to will lead to steel plate is insufficient, and C content is excessively high, and brittle transition temperature is obvious It increasing, weld seam fire check sensibility also greatly improves, and welding performance is poor, under the premise of the intensity needed for guaranteeing steel plate and toughness, It is 0.09%~0.12% the present invention claims C content.
Si: being one of intensified element in steel, can play the role of deoxidation and solution strengthening, element silicon diffusion is slow, In Silicate inclusion object is also easy to produce in steel, thus Si content be not easy it is excessively high, the present invention by Si control be 0.30%~0.40%.
Mn: in steel can by way of solution strengthening reinforced ferrite, the tough of steel can be improved in quenched and tempered steel Property and harden ability, therefore, the present invention by steel Mn content control 0.50%~0.70%.
P, S: being the harmful element in steel, can reduce the impact flexibility of steel, and easily aggravation is centrally formed segregation and loose wait lacks It falls into, while radiation embrittlement can be caused, therefore it is required that the lower P, S content the better, but considers production cost, the present invention designs P and contains It is≤0.002% that amount, which is≤0.010%, S content,.
Cr: can significantly improve the antioxidation of steel in steel, increase resistance to corrosion.Austenite phase field is reduced simultaneously, Improve harden ability, intensity and the hardness of steel.But Cr too high levels will increase the postwelding crack sensitivity of steel, therefore the present invention wants Asking Cr content control in steel is 0.60%~0.90%.
Ni: can be obviously improved the low-temperature flexibility of steel, while improve the low-temperature flexibility of thick section steel plate, have steel plate While sufficient intensity can also toughness with higher, meet the requirement of index, therefore from actual needs, the present invention is by Ni Content control is 0.30%~0.50%.
Mo: the harden ability and heat resistance of steel mainly be can be improved, steel belt roof bolt brittleness is prevented, can be improved in quenched and tempered steel Steel belt roof bolt stability improves plasticity, therefore the present invention controls Mo content to more effectively reduce residual stress 0.26%~0.45%.
V: mainly improving the intensity and yield tensile ratio of steel in quenched and tempered steel, refines crystal grain, improves the effect of obdurability, but vanadium There is stronger affinity with carbon and oxygen, will affect harden ability in the presence of with carbide form, therefore V will be added in the present invention in steel Scope control be 0.005%~0.030%.
B: can properly increase the harden ability of steel in steel, to save other more expensive metals, therefore the present invention is by the model of B It contains and is made as 0.001%~0.005%.
Ti: can be improved plasticity and toughness in ordinary low-alloy steel, since titanium secures nitrogen and sulphur formation titanium carbide, mention The intensity of Gao Gang, thus in the present invention by the scope control of Ti≤0.015%.
Al: nitrogen agent is determined in deoxidation when being mainly used for steel-making in steel, and can refine crystal grain, suppress mild steel when Effect, improves the low-temperature flexibility of steel, while Al content should not be excessive, in order to avoid generate Al2O3It is mingled with.The present invention is by Al content control in steel It is made as 0.010%~0.025%.
The manufacturing method of high-intensitive high-yield-ratio nuclear power station mechanical module steel includes: converter smelting-vacuum processing-company Casting-rolling-Tempering and Quenching.
It smelts aspect: being produced using converter smelting, external refining, vacuum processing and continuous casting process；Molten steel is completed to turn Furnace carries out external refining after smelting, and vacuum outgas is carried out when liquid steel temperature reaches 1565~1575 DEG C, enters after completing degassing Continuous casting is casting continuously to form steel billet.
Rolling mill practice: 1200~1250 DEG C of billet heating temperature, start rolling temperature: 1100~1150 DEG C, finishing temperature >= 1000℃.Total deformation >=60%, 3 pass deformation >=15% of arbitrary continuation；
Tempering and Quenching: steel plate carries out stacking slow cooling after rolling, and carries out modifier treatment to steel plate after slow cooling.
Quenching treatment:, reaching the complete austenitizing temperature of steel plate by 900~920 DEG C, 2~3.5min/mm of soaking time, Sufficiently heat preservation, after coming out of the stove immediately water cooling until steel billet temperature is to 100 DEG C or less.
Tempering:, sufficiently keeping the temperature in the temperature range by 625~660 DEG C, 4~6min/mm of soaking time, guarantees in steel Carbide Precipitation, and form high tempering Soxhlet body tissue.
The tensile strength of steel plate reaches 700MPa or more, and yield tensile ratio is not less than 0.9.
The utility model has the advantages that
The present invention provides a kind of high-intensitive high-yield-ratio nuclear power station mechanical module steel and its manufacturing method, the steel of production Plate thickness is 20~110mm, and width and length can be produced according to actual needs.Compared with prior art, beneficial effect is such as Under:
(1) steel grade of the present invention is conditioned with after Simulated post-weld heat treatment, and preferable obdurability water is all had under two states It is flat.Yield strength and tensile strength are respectively 739MPa and 799MPa after the conditioned processing of 90mm steel plate；Simulated post-weld heat treatment Afterwards, yield strength and tensile strength are respectively 671MPa and 732MPa；Under modifier treatment and Simulated post-weld heat treatment two states Yield tensile ratio be 0.92, -20 DEG C of ballistic work >=132J, from the results of view, steel plate obdurability matching preferably, yield tensile ratio intensity compared with It is high.
(2) 350 DEG C high temperature tensile properties of the steel grade of the present invention under different conditions are equally maintained at higher level.90mm The yield strength and tensile strength of 350 DEG C of drawing by high temperature are respectively 607MPa and 702MPa after the conditioned processing of steel plate；Yield tensile ratio It is 0.86.
(3) flaw detection of steel plate requires to be fully able to meet I grade of acceptance criteria in NB/T 47013.
Detailed description of the invention
Fig. 1 is the metallographic structure of embodiment 1；Tissue is tempered sorbite.
Specific embodiment
For following embodiment for illustrating the content of present invention, these embodiments are only the general description of the content of present invention, The content of present invention is not limited.
The production method of the present embodiment, molten steel pass through converter smelting, LF+VD external refining, vacuum processing and casting, rolling Finished steel plate specification is 20~110mm.Simulated post-weld heat treatment technique is 610 DEG C of temperature, and soaking time 12h, 425 DEG C to rise Rate of temperature fall≤55 DEG C/h.Table 1 is embodiment steel smelting chemical component；Table 2 is the rolling mill practice of embodiment steel plate；Table 3 is real Apply the heat treatment process of a steel plate；Table 4 is the tensile property of embodiment steel plate.Table 5 is the impact property of embodiment steel plate.
Each embodiment steel smelting chemical component (wt%) of table 1
Embodiment C Si Mn P S Cr Ni Mo V B Ti Al
1 0.09 0.31 0.50 0.005 0.0015 0.60 0.30 0.26 0.005 0.001 0.007 0.015
2 0.10 0.37 0.60 0.008 0.0010 0.67 0.32 0.30 0.020 0.005 0.006 0.020
3 0.09 0.33 0.55 0.007 0.0017 0.79 0.38 0.37 0.017 0.004 0.021
4 0.11 0.39 0.65 0.006 0.0013 0.85 0.49 0.45 0.025 0.002 0.008 0.019
5 0.12 0.35 0.70 0.009 0.0009 0.90 0.50 0.42 0.029 0.003 0.015 0.022
Each embodiment steel rolling technique of table 2
Each embodiment steel modifier treatment technique of table 3
Each embodiment steel plate stretching performance of table 4
Each embodiment steel plate impact property of table 5
According to 20~110mm specification steel plate produced by the invention it can be seen from table, by modifier treatment and simulation postwelding Heat treatment, yield strength >=717MPa that quality adjustment condition room temperature stretches, tensile strength >=762MPa, yield tensile ratio >=0.92；Simulation Yield strength >=662MPa that post weld heat treatment state room temperature stretches, tensile strength >=709MPa, yield tensile ratio >=0.92；350℃ Yield strength >=603MPa of drawing by high temperature, tensile strength >=679MPa, yield tensile ratio >=0.80；- 20 DEG C of impacts of steel plate >= 123J, steel plate have good comprehensive mechanical property.

Claims (3)

1. a kind of high intensity high-yield-ratio nuclear power station mechanical module steel, which is characterized in that chemical component presses quality percentage in steel Than for, C:0.09%~0.11%, Si:0.31%~0.40%, Mn:0.55%~0.70%, P≤0.010%, S≤ 0.002%, Cr:0.60%~0.90%, Ni:0.30%~0.50%, Mo:0.26%~0.45%, V:0.005%~ 0.029%, B:0.001%~0.005%, Ti≤0.007%, Al:0.010%~0.025%, remaining is for Fe and unavoidably Impurity；Steel plate passes through modifier treatment and Simulated post-weld heat treatment, and yield strength >=717MPa that quality adjustment condition room temperature stretches resists Tensile strength >=762MPa, yield tensile ratio >=0.92；Yield strength >=662MPa that Simulated post-weld heat treatment state room temperature stretches, tension Intensity >=709MPa, yield tensile ratio >=0.92；Yield strength >=603MPa of 350 DEG C of drawing by high temperature, tensile strength >=679MPa are bent Strong ratio >=0.80；- 20 DEG C of impact >=123J of steel plate.
2. a kind of high-intensitive high-yield-ratio nuclear power station mechanical module steel as described in claim 1, which is characterized in that steel plate With a thickness of 20~110mm.
3. a kind of high-intensitive high-yield-ratio nuclear power station module bearing as claimed in claim 1 or 2 preparation method of steel, steel plate Production technology are as follows: converter smelting-vacuum processing-continuous casting-rolling-Tempering and Quenching, which is characterized in that
Molten steel carries out external refining after completing converter smelting, and vacuum outgas is carried out when liquid steel temperature reaches 1565~1575 DEG C, Enter continuous casting after completing degassing, is casting continuously to form steel billet；
Billet heating temperature is 1200~1245 DEG C, and start rolling temperature is 1100~1145 DEG C, finishing temperature >=1000 DEG C, total deformation Amount >=60%, 3 pass deformation >=15% of arbitrary continuation；Steel plate carries out stacking slow cooling after rolling, and carries out after slow cooling to steel plate Modifier treatment；
Hardening heat be 900~920 DEG C, 2~3.1min/mm of soaking time, steel plate come out of the stove after immediately water cooling until steel billet temperature To 100 DEG C or less；Tempering temperature is 625~660 DEG C, 4.1~6min/mm of soaking time.
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