CN109554629A - A kind of ultra supercritical coal-fired unit steel and preparation method thereof - Google Patents

A kind of ultra supercritical coal-fired unit steel and preparation method thereof Download PDF

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Publication number
CN109554629A
CN109554629A CN201710887649.3A CN201710887649A CN109554629A CN 109554629 A CN109554629 A CN 109554629A CN 201710887649 A CN201710887649 A CN 201710887649A CN 109554629 A CN109554629 A CN 109554629A
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unit steel
ultra supercritical
fired
supercritical coal
chemical component
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骆素珍
张忠铧
罗明
翟国丽
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to CN201710887649.3A priority Critical patent/CN109554629A/en
Priority to DE112018005465.9T priority patent/DE112018005465T5/en
Priority to JP2020517505A priority patent/JP7009618B2/en
Priority to PCT/CN2018/107521 priority patent/WO2019062741A1/en
Publication of CN109554629A publication Critical patent/CN109554629A/en
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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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

A kind of ultra supercritical coal-fired unit steel and preparation method thereof, the steel chemical composition mass percent are as follows: Cr:8.0~10.0%, W:2.0~3.2%, Co:2.0~4.0%, V:0.1~0.3%, Nb:0.01~0.1%, B:0.006~0.018%, Cu:0.2~1.0%, Mn:0.2~1.0%, Al:0.005~0.08%, Si:0.1~0.8%, C:0.06~0.12%, N:0.003~0.010%, P≤0.02%, S≤0.01%, Ni≤0.01%, Re≤0.01%, Ti≤0.01%, and it need to meet simultaneously: 1.6≤(Cr+1.4W+1.5Si+2 Nb+2V)/(Co+Cu+0.3Mn+30C+20N)≤3.2,0.6≤B/N≤6, surplus are Fe and inevitable impurity, inevitable total impurities≤0.015%.The steel has good anti-steam corrosion oxidation and high-temperature and durable creeping performance, and specific performance is in 620~650 DEG C of extrapolations, 100,000 hours creep rupture strength >=100MPa；650 DEG C of steam oxidations corrode 1000 hours weight gain≤18mg/cm2, boiler tube or other heat-resisting equipments especially suitable for ultra supercritical coal-fired unit.

Description

A kind of ultra supercritical coal-fired unit steel and preparation method thereof
Technical field
The invention belongs to technical field of heat-resistant steel, and in particular to a kind of ultra supercritical coal-fired unit steel and preparation method thereof, more More particularly to a kind of anti-steam corrosion oxidation and the good ultra supercritical coal-fired unit steel of high temperature creep property and preparation method thereof.
Background technique
With China's rapid development of economy, resource and energy demand speedup are also increased with it, although solar energy, wind energy etc. The development of new energy reaches the expection even beyond electric power development planning, but the absolute magnitude of these new energy is still lower.Not One period is grown very much, thermal power generation is still the main force in China Power structure, and accounting still reaches 70%, this is by China What national conditions and natural resources were determined.But coal fired generation process generates a large amount of dust, carbon dioxide, sulfur dioxide, nitrogen oxidation The pollutants such as object, and the reserves of coal resources are limited, it is non-renewable.Therefore, it in order to protect environment, economize on resources, needs to send out Open up high parameter, the large capacity fired power generating unit of high-efficiency and economic.
Technical staff have realized that improve steam parameter (pressure and temperature) be improve generating set efficiency important and Effective approach.The countries such as beauty, moral, method, day set about researching and developing extra-supercritical unit (U-USC), and main steam temperature reaches 650 DEG C, pressure 34.5MPa or more, elevated steam conditions will bring high generating efficiency and less environmental pollution, but steam parameter It improves to a certain extent by the restriction of unit price etc., but maximum bottleneck is by high-strength heat-resistant steel lagging in development Restriction.With the raising of parameter, the material property of high temperature track (such as jet chimney, valve, boiler and steam turbine) Must be correspondingly improved, they whether trouble free service, the safe operation of entire unit is of great significance to.This requires High-temperature bearing material includes 1) good high-temperature and durable and creep strength, 2) excellent high temperature microstructure stability, 3) good anti-height The performance of warm steam oxidation corrosion, 4) lesser thermal expansion coefficient, 5) good cold and hot working performance, 6) good welding performance.
Nickel base superalloy has excellent high temperature strength and the performance of anti-steam corrosion, in aircraft engine, steam turbine The high-temperature fields such as blade have had successful application, can be used for the high-temperature component of the generating set of 650 DEG C or more higher efficiencies, but The design of unit has the process gradually developed, and in 600~650 DEG C of temperature ranges, using nickel-base alloy, that there are costs is excessively high The problem of, price factor constrains the application of nickel-base alloy.Ovshinsky heat resisting steel etc. also has higher height between 620~650 DEG C Warm intensity, but the problem that its thermal expansion coefficient is big and thermal conductivity is not high, constrain its popularization and application in fired power generating unit.? The maximum operation (service) temperature of commercialized martensite heat-resistant steel T/P92 is up to 620 DEG C, but at present in the world still without a kind of mature The upper limit can be reached 650 DEG C using temperature by economy martensite heat-resistant steel.This temperature has nearly reached martensite/ferrite All there is unprecedented challenge in the limiting temperature of type heat resisting steel, the research of strengthening mechanism and the difficulty of steel development.
For this purpose, technical staff has carried out relevant research and development.United States Patent (USP) US5591391A, which is disclosed, can manufacture use In field of thermal power, the performance material with improved high temperature creep property and good welds performance and the corrosion of anti-steam oxidation Material, from the point of view of disclosed ingredient, the principle for having used high Cr, W and Co to strengthen is also added into the rare elements such as Rd and Ta, Leaded wastewater is between 0.02~0.12%, and for ferritic heat-resistant steel, this is very high N content, this will be to production and processing Great difficulty is brought, and N, in addition to reacting with V and Nb and to form nitride, remaining N can also consume a large amount of Cr, W, weakened The effect of its solution strengthening.
Summary of the invention
The purpose of the present invention is to provide a kind of ultra supercritical coal-fired unit steel and preparation method thereof, which has good Anti- steam corrosion oxidation and high-temperature and durable creeping performance, specific performance is in 620~650 DEG C of extrapolations, 100,000 hours creep rupture strengths ≥100MPa；650 DEG C of steam oxidations corrode 1000 hours weight gain≤18mg/cm2, especially suitable for ultra supercritical coal-fired unit Boiler tube or other heat-resisting equipments.
In order to achieve the above objectives, the technical scheme is that
The present invention is strong according to the compound collaboration that heat resisting steel solution strengthening, precipitate reinforcing, dislocation strengthening and substructure are strengthened Change theory, make full use of the solution strengthening of Cr, W, Co, Co and Cu fault is strengthened, the disperse of the tiny precipitate of Cr, V, Nb, C, N The pinning invigoration effect of invigoration effect and B at crystal boundary and carbide and matrix phase boundary.It is set in the matching of each alloying element On meter, the manufacturability and high-temperature and durable creeping performance of material are comprehensively considered.Specific technical solution is as follows:
A kind of ultra supercritical coal-fired unit steel, chemical component mass percent are as follows: Cr:8.0~10.0%, W:2.0 ~3.2%, Co:2.0~4.0%, V:0.1~0.3%, Nb:0.01~0.1%, B:0.006~0.018%, Cu:0.2~ 1.0%, Mn:0.2~1.0%, Al:0.005~0.08%, Si:0.1~0.8%, C:0.06~0.12%, N:0.003~ 0.010%, P≤0.02%, S≤0.01%, Ni≤0.01%, Re≤0.01%, Ti≤0.01%, and above-mentioned element need simultaneously Meet following relationship: 1.6≤(Cr+1.4W+1.5Si+2Nb+2V)/(Co+Cu+0.3Mn+30C+20N)≤3.2,0.6≤B/N ≤ 6, surplus is Fe and inevitable impurity, inevitable total impurities≤0.015%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Cr:8.5~9.5%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: W:2.5~3.0%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Co:2.5~3.5%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: V:0.15~0.25%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Nb:0.05~0.09%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: B:0.008~0.013%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Cu:0.2~0.5%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Mn:0.3~0.8%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Al:0.01~0.05%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: Si:0.2~0.6%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: C:0.08~0.10%.
Preferably, in the ultra supercritical coal-fired unit steel chemical composition: N:0.005~0.008%.
Preferably, in the chemical component of the ultra supercritical coal-fired unit steel: 1≤B/N≤3.
Further, the ultra supercritical coal-fired unit steel 620~650 DEG C of extrapolations, 100,000 hours creep rupture strengths >= 100MPa, 650 DEG C of steam oxidations corrode 1000 hours weight gain≤18mg/cm2。
In the ingredient design of steel plate of the present invention:
The harden ability of Cr:Cr element improvement steel；There is the effect of solution strengthening, the carbide dispersion that Cr and C are formed is precipitated strong Change is main hardening constituent in steel, is conducive to the high-temperature and durable creeping performance of steel；And a certain amount of Cr element can make heat resisting steel Surface forms continuous Cr2O3Or (CrFe)3O4Oxidation film, the oxidation film can assign heat resisting steel good steam oxygen resistant to high temperatures Change the ability of corrosion.But if Cr content is too low, due solution strengthening and precipitating reinforcing effect, and material surface are not had It is not enough to be formed continuous Cr2O3Or (CrFe)3O4Film is unfavorable for the performance of the steam corrosion resistant to high temperatures of material.And Cr content is too The production and processing difficulty of height, heat resisting steel is big, is easy to produce high temperature delta ferrite, to the high temperature creep property of heat resisting steel and persistently strong It is unfavorable to spend.Therefore, the present invention controls Cr content 8.0~10%, preferably 8.5~9.5%.
W:W element leads to very big distortion of lattice in the base, plays solid solution more significant than Mo because atomic radius is larger Strengthening effect, meanwhile, W can also form the precipitated phase Precipitation of carbonitride, play the role of disperse educt reinforcing.This is right The croop property and creep rupture strength of 620 DEG C or more of heat resisting steel are highly beneficial.If W content is too low, enough reinforcings cannot be formed Phase, if but W content it is excessively high, W can promote the generation of high temperature delta ferrite phase, generate the brittlement phases such as the σ of W, lead to material high temperature Penalty.Therefore, the present invention should control W content 2.0~3.2%, preferably 2.5~3.0%.
Co:Co element can play the role of solution strengthening in steel, and Co can reduce the solubility of Ti, Al in steel matrix, Change solubility of the Cr and C in steel, enhance solid solution strengthening effect of the Cr in steel, Co reduces the stacking fault of metallic matrix Can, play the role of fault reinforcing, and Co can inhibit the generation of high temperature delta ferrite phase, therefore, the addition of Co can significantly improve The creep resistance of alloy, and improve the hot-working character of steel and the performance of resistance to high temperature corrosion.If Co is added very little, needed for not having The effect wanted, but Co is rare precious metals, and if being added excessively, which just loses due cost-competitive.Therefore, this hair It is bright to control Co content 2.0~4.0%, preferably 2.5~3.5%.
The addition of V:V can improve the creep rupture strength at high temperatures of material.V can form tiny nitride and/or carbon in steel Nitride.V content is too low not to have a required effect, and V is added excessive, may cause that carbonitride is coarse and the crystalline substance of oxide on surface Grain is coarse, reduces the performance of anti-steam corrosion.Therefore, the present invention controls V content 0.1~0.3%, preferably 0.15~0.25%.
Nb:Nb is the stabilizing element of C, N, can form the carbonitride of Nb, plays the role of the effect of precipitation strength, with V It is similar.But if Nb additional amount is insufficient, due effect is not had.If Nb addition is excessively high, the processability of material can be reduced, may Lead to the coarse of its carbonitride, heat resistance declines instead.Therefore, the present invention controls Nb content 0.01~0.1%, preferably 0.05~0.08%.
The addition of B:B element can play invigoration effect in crystal boundary, and can take up carbide vacancy nearby, inhibit its length Greatly, play the role of stabilizing tissue.If B content is too low, required strengthening effect is not had, it, will but if B content is excessively high The hot-working character and welding performance of meeting severe exacerbation material.Therefore, the present invention by B content control 0.006~0.018% it Between, preferably 0.008~0.013%.
N:N element is austenite former, and a certain amount of N can cooperate with other austenite formers to inhibit high in steel The formation of warm delta ferrite, and the nitride of tiny energy Dispersed precipitate, these nitride can be formed with other elements such as Nb, V etc. Stability be much higher than the carbide or carbonitride of respective alloy.But N content is excessively high, may cause processing performance and welding The deterioration of performance etc..Therefore, the present invention controls N content between 0.003~0.01%, preferably 0.005~0.008%.
C:C element can form carbide with Cr, V, Nb and elements such as w and improve material by way of dispersion-strengtherning Heat resistance.But carbide is too low, and the carbide content of precipitation is few, and required strengthening effect is not achieved, and can make the second crisp of steel Property temperature range it is mobile toward high temperature section, be unfavorable for hot-working.C content is high, is conducive to the formation for inhibiting high temperature delta ferrite, and Improve the thermoplasticity of the second brittleness warm area of material；But excessively high C content will lead to Carbide Precipitation excess, consume excessive Solution strengthening element, to make comprehensive durable creeping performance decline, in addition, C content is excessively high also unfavorable to welding performance.Cause This, the present invention controls C 0.06~0.12%, preferably 0.08~0.10%.
The addition of Si:Si can improve the performance of the steam oxidation resistant to high temperatures corrosion of material, but Si is excessively high, the impact to material Toughness is unfavorable, and in high temperature long service, Si can promote the Precipitation of brittlement phase, is unfavorable for the stabilization of durable creeping performance, In addition, the SiO that oxidation corrosion generates when long2Continuous inner oxide once being formed may influence heat plus change efficiency etc..The excessively high meeting of Si The thermoplasticity for deteriorating the first high-temperature brittleness humidity province of material, is unfavorable for the hot-working of material.Therefore, the present invention is by Si content control System is 0.1~0.8%, preferably 0.2~0.6%.
Cu:Cu is austenite former, can prevent to generate delta ferrite in steel, and the resistant to high temperatures of steel can be improved in the addition of Cu The performance of steam oxidation corrosion.But Cu constituent content is excessively high, and the hot-working character of material deteriorates.Therefore, the present invention is by Cu content Control is 0.2~1.0%, preferably 0.2~0.5%.
Mn:Mn is austenite former, can inhibit the formation of high temperature delta ferrite, meanwhile, Mn stablizes P, S element, avoids The formation of low melting point sulfide improves the hot-working character of material.But Mn content is too low, cannot stable P, S well, be not achieved Required effect, Mn too high levels are unfavorable for the impact flexibility of material, and reduce the creep rupture strength at high temperatures of steel.Therefore, originally Invention controls Mn content 0.2~1.0%, preferably 0.3~0.8%.
Al:Al has apparent effect for improving the steam oxidation resistant to high temperatures corrosion of steel, but the N in Al and steel is easy to combine AlN is formed, unfavorable to the high temperature creep property of material, therefore, in the present invention, Al is added not as alloying element, but usual smelting Refining can use Al deoxidation or Al, Si complex deoxidization, and Al is as relict element, therefore, needs strict control Al in process of production Content, content preferably controls 0.005~0.08%, preferably 0.01~0.05%.
P, S:P, S are the impurity elements introduced in steel supplementary material or production process, and P can make embrittlement of grain boundaries, make material Toughness and processing performance deterioration.S element forms the sulfide of low melting point, makes under material processing performance and the mechanical property of itself Drop.In addition, P, S element can promote pyrogenic steam oxidation corrosion, decline the ability of the anti-steam corrosion of heat resisting steel.Therefore, P, S It preferably controls in P≤0.02%, S≤0.01%, is preferably controlled in P≤0.01%, S≤0.005%.
The elements such as Re, Ti, Ni are added not as alloying element, and Re element can improve the performance of the anti-steam corrosion of material With improve thermoplasticity etc., but since in practical smelt production, rare earth rare earth oxide easy to form is mingled with, lead to high temperature Creeping crack reduces the creep rupture strength of steel in this forming core instead.Ti is easy to be formed TiN, TiN needs with N in high temperature Degree is lower to be dissolved, once being formed, it is not easy to be regulated and controled by heat treatment.Some researches show that Ni is to the lasting of ferritic heat-resistant steel Intensity adversely affects, therefore, Ni, Ti and Re etc. in the case where large-scale production cannot be produced with fine fodder, in supplementary material Strict supervision is wanted, the content of Ni, Ti and Re element is intended to control below 0.01%.
In addition, steel of the present invention is also possible to containing other inevitable impurity elements, such as from supplementary material and clinker, resistance to The harmful elements such as the residue that fiery material etc. generates in the fabrication process, such as Sn, Pb, As, Sb and Zn, these elements are also necessary Strict control, total amount is no more than 0.015%.
The present invention in order to control high temperature delta ferrite to the adverse effect of manufacturing property and creep rupture strength at high temperatures, at Set up the control that timing has also fully considered ferrite equivalent and austenite equivalence ratio separately, high temperature is avoid or reduced from source The quality risks such as the cracking that delta ferrite generates during the manufacturing, and ensure that steel of the present invention obtains under following manufacturing methods Obtain single tempered martensite.Therefore, the alloying component of steel of the present invention should also meet following relationship:
1.6≤(Cr+1.4W+1.5Si+2Nb+2V)/(Co+Cu+0.3Mn+30C+20N)≤3.2。
The effect that the present invention is grown up using the intercrystalline strengthening and inhibition carbide of B, improves the high-temperature behavior of material.If but N is added excessively, can form BN in conjunction with B, consume B element, do not have due effect.Therefore, the present invention ingredient design when, Fully consider being uniformly controlled for B/N, chemical component should also meet following relationship: 0.6≤B/N≤6, preferably 1≤B/N≤3.
The preparation method of ultra supercritical coal-fired unit steel of the present invention comprising following steps:
1) it is cast into ingot casting using vacuum induction furnace smelting according to above-mentioned chemical component, then by ingot casting 1000~1180 DEG C heating and thermal insulation 1~6 hour, then high temperature deformation is carried out between 920~1150 DEG C, it is processed into required size；
2) it is heat-treated
Normalized treatment: 1000~1140 DEG C of normalizing temperature, 0.5~4 hour is kept the temperature, room temperature is air-cooled to.
Tempering: 700~820 DEG C of tempering temperature, 1~5 hour is kept the temperature, room temperature is air-cooled to.
The mentioned component system that the present invention designs steel ingot when 1200 DEG C of heating temperature > is in the first brittle temperature zone, when Steel ingot is in the second brittle temperature zone at 900 DEG C of heating temperature <, and it is 1000~1180 DEG C that the present invention, which selects Heating Steel Ingots temperature, Avoid the too low problem of first brittle temperature zone and second brittle temperature zone thermoplasticity of the steel in hot-working.
The present invention is tempered in 1000~1140 DEG C of temperature ranges progress normalized treatments, in 700~820 DEG C of temperature ranges Processing can be such that the precipitation strength, dislocation and lath substructure of steel of the present invention strengthens and reach optimum efficiency.Therefore, in order to guarantee Enough creep rupture strengths, the present invention carry out above-mentioned final heat treatment.
Steel produced by the present invention has preferable room-temperature mechanical property, mechanical behavior under high temperature, also there is excellent high temperature to hold The performance of long creep strength and steam corrosion resistant to high temperatures, specific performance index are as follows: room-temperature mechanical property is yield strength Rp0.2 >=600MPa, tensile strength Rm >=800MPa, elongation percentage A50>=15%；Ballistic work >=25J at 20-25 DEG C, ballistic work at -20 DEG C ≥15J；Mechanical property at 600~675 DEG C of high temperature are as follows: yield strength Rp0.2 >=250MPa, tensile strength Rm >=290MPa extend Rate A50>=20%；650 DEG C, stress rupture time >=15600h of 120MPa；650 DEG C of steam oxidations corrode weight gain in 1000 hours not Higher than 18mg/cm2, in 620~650 DEG C of extrapolations, 100,000 hours creep rupture strength 100MPa or more, thermal expansion coefficient is 10~15 × 10- 6K；There is preferable manufacturability energy simultaneously, it is resistance to especially suitable for 620~650 DEG C of ultra supercritical coal-fired unit boiler tubes of manufacture etc. Thermal part, but also do not limit the steel grade and applied in other environment for having resistance to heat demand other than ultra supercritical coal-fired unit.This hair Bright ingredient is designed and manufactured technological design and has taken into account the feasibility for being realized industrialization using existing industrial pipe production equipment capability.
Beneficial effects of the present invention:
Compared with the prior art, Cu constituent content is optimized in the chemical component of steel of the present invention, does not add rare earth element, reduced The difficulty of non-metallic inclusion is controlled in smelting process, and reduces N content, ensure that the impact flexibility and welding performance of steel. Each chemical component also needs to meet simultaneously: 1.6≤(Cr+1.4W+1.5Si+2Nb+2V)/(Co+Cu+0.3Mn+30C+20N)≤ 3.2 and 0.6≤B/N≤6.The chemical component system combines heating process provided by the invention, and (heating temperature is 1000~1180 DEG C, 920~1150 DEG C of deformation temperature), the formation of steel high temperature delta ferrite can be controlled well, improves the thermoplasticity of steel, dropped The risk that low-heat manufacturing deficiency is formed, while guaranteeing the high-temperature and durable creeping performance of steel.
Detailed description of the invention
Fig. 1 is the high temperature thermoplasticity schematic diagram of the embodiment of the present invention 3 and 10 steel of embodiment at different temperatures.
Specific embodiment
Below with reference to embodiment and attached drawing, the present invention will be further described.
Table 1 is the ingredient of steel of the embodiment of the present invention and comparative example steel, and table 2 is the pass of steel of the embodiment of the present invention and comparative example steel Key preparation technology parameter, table 3 are the comprehensive performance of steel of the embodiment of the present invention and comparative example steel.
Embodiment 1
Using vaccum sensitive stove, the 50~100Kg of steel ingot for reaching chemical composition shown in table 1 is smelted, by these steel ingot coggings Afterwards, 1180 DEG C are again heated to, the hot rolled plate of 16mm thickness is made in hot rolling.Then hot rolled plate is kept the temperature 1.5 hours in 1020 DEG C of normalizings, It is air-cooled to room temperature, then 2 hours is kept the temperature at 760 DEG C, is air-cooled to room temperature.Room temperature mechanics, length are intercepted from above-mentioned heat-treated steel plate When failure and high-temerature creep and enduring quality evaluate sample, the various performances measured are as shown in table 3.
The manufacture and evaluation procedure of other embodiments are similar to Example 1, and specific preparation parameter is referring to table 2, and performance is referring to table 3.
As shown in Table 3, the present invention prepares gained ultra supercritical coal-fired unit steel room-temperature mechanical property are as follows: yield strength Rp0.2 >=600MPa, tensile strength Rm >=800MPa, elongation percentage A50>=15%；Ballistic work >=25J at 20~25 DEG C, at -20 DEG C Ballistic work >=15J；Mechanical property at 600~675 DEG C of high temperature are as follows: yield strength Rp0.2 >=250MPa, tensile strength Rm >= 290MPa, elongation percentage A50>=20%；650 DEG C, stress rupture time >=15600h of 120MPa；650 DEG C of steam oxidation corrosion Weight gain in 1000 hours is not higher than 18mg/cm2.It is calculated by the data of table 3 it is found that extrapolating 100,000 hours at 620~650 DEG C persistently Intensity 100MPa or more.The steel plate has the performance of excellent high-temperature and durable creeping intensity and steam corrosion resistant to high temperatures, has simultaneously There is preferable manufacturability energy, especially suitable for manufacturing the boiler tube or other heat-resisting equipments of ultra supercritical coal-fired unit.
As shown in Figure 1, mentioned component system of the present invention steel ingot at 1250 DEG C of heating temperature > is in the first brittleness temperature Area, steel ingot is in the second brittle temperature zone when 900 DEG C of heating temperature <, when Heating Steel Ingots temperature setting is 1000~1180 DEG C, avoid the too low problem of first brittle temperature zone and second brittle temperature zone thermoplasticity of the steel in hot-working.

Claims (17)

1. a kind of ultra supercritical coal-fired unit steel, chemical component mass percent are as follows: Cr:8.0~10.0%, W:2.0~ 3.2%, Co:2.0~4.0%, V:0.1~0.3%, Nb:0.01~0.1%, B:0.006~0.018%, Cu:0.2~ 1.0%, Mn:0.2~1.0%, Al:0.005~0.08%, Si:0.1~0.8%, C:0.06~0.12%, N:0.003~ 0.010%, P≤0.02%, S≤0.01%, Ni≤0.01%, Re≤0.01%, Ti≤0.01%, and above-mentioned element need simultaneously Meet following relationship: 1.6≤(Cr+1.4W+1.5Si+2Nb+2V)/(Co+Cu+0.3Mn+30C+20N)≤3.2,0.6≤B/N ≤ 6, remaining is Fe and inevitable impurity, inevitable total impurities≤0.015%.
2. ultra supercritical coal-fired unit steel according to claim 1, which is characterized in that the ultra supercritical coal-fired unit With Cr:8.5~9.5% in the chemical component of steel.
3. ultra supercritical coal-fired unit steel according to claim 1 or 2, which is characterized in that the ultra supercritical thermoelectricity W:2.5~3.0% in the chemical component of unit steel.
4. ultra supercritical coal-fired unit steel according to claim 1-3, which is characterized in that the ultra supercritical Co:2.5~3.5% in the chemical component of fired power generating unit steel.
5. ultra supercritical coal-fired unit steel according to claim 1-4, which is characterized in that the ultra supercritical V:0.15~0.25% in the chemical component of fired power generating unit steel.
6. ultra supercritical coal-fired unit steel according to claim 1-5, which is characterized in that the ultra supercritical Nb:0.05~0.09% in the chemical component of fired power generating unit steel.
7. ultra supercritical coal-fired unit steel according to claim 1-6, which is characterized in that the ultra supercritical B:0.008~0.013% in the chemical component of fired power generating unit steel.
8. ultra supercritical coal-fired unit steel according to claim 1-7, which is characterized in that the ultra supercritical Cu:0.2~0.5% in the chemical component of fired power generating unit steel.
9. ultra supercritical coal-fired unit steel according to claim 1-8, which is characterized in that the ultra supercritical Mn:0.3~0.8% in the chemical component of fired power generating unit steel.
10. -9 described in any item ultra supercritical coal-fired unit steel according to claim 1, which is characterized in that described super to face Al:0.01~0.05% in the chemical component of boundary's fired power generating unit steel.
11. -10 described in any item ultra supercritical coal-fired unit steel according to claim 1, which is characterized in that described super to face Si:0.2~0.6% in the chemical component of boundary's fired power generating unit steel.
12. -11 described in any item ultra supercritical coal-fired unit steel according to claim 1, which is characterized in that described super to face C:0.08~0.10% in the chemical component of boundary's fired power generating unit steel.
13. -12 described in any item ultra supercritical coal-fired unit steel according to claim 1, which is characterized in that described super to face N:0.005~0.008% in the chemical component of boundary's fired power generating unit steel.
14. ultra supercritical coal-fired unit steel described in -13 according to claim 1, which is characterized in that the ultra supercritical thermoelectricity In the chemical component of unit steel: 1≤B/N≤3.
15. -14 described in any item ultra supercritical coal-fired unit steel according to claim 1, which is characterized in that described super to face Boundary's fired power generating unit steel is in 620~650 DEG C of extrapolations, 100,000 hours creep rupture strength >=100MPa, 650 DEG C of steam oxidation corrosion 1000 Weight gain≤18mg/cm of hour2。
16. such as the preparation method of the described in any item ultra supercritical coal-fired unit steel of claim 1-15 comprising following step It is rapid:
1) it is cast into ingot casting using vacuum induction furnace smelting according to the described in any item chemical components of claim 1-14, then will Ingot casting keeps the temperature 1~6 hour at 1000~1180 DEG C, then high temperature deformation is carried out between 920~1150 DEG C, is processed into required ruler It is very little；
2) it is heat-treated
Normalized treatment: 1000~1140 DEG C of normalizing temperature, 0.5~4 hour is kept the temperature, room temperature is air-cooled to；
Tempering: 700~820 DEG C of tempering temperature, 1~5 hour is kept the temperature, room temperature is air-cooled to.
17. the preparation method of ultra supercritical coal-fired unit steel according to claim 16, which is characterized in that described super Critical fired power generating unit steel is in 620~650 DEG C of extrapolations, 100,000 hours creep rupture strength >=100MPa, 650 DEG C of steam oxidation corrosion 1000 hours weight gain≤18mg/cm2。
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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111057827A (en) * 2019-11-27 2020-04-24 中国科学院金属研究所 Method for regulating and controlling distribution state of boron element in 9Cr3W3CoB heat-resistant steel for ultra-supercritical unit
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Citations (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0806490A1 (en) * 1996-05-07 1997-11-12 Hitachi, Ltd. Heat resisting steel and steam turbine rotor shaft
CN101525727A (en) * 2009-04-22 2009-09-09 四川江油六合汽轮机材料有限公司 Heat-resisting steel material used as vane or bolt of ultra-supercritical steam turbine and preparation method thereof
CN102011063A (en) * 2010-10-19 2011-04-13 钢铁研究总院 Ferrite-free heavy caliber thick-wall heat resistant steel pipe material
CN102517508A (en) * 2011-12-30 2012-06-27 钢铁研究总院 Ferrite refractory steel for vane of steam turbine of ultra supercritical fossil power plant and manufacturing method
CN102517517A (en) * 2011-12-30 2012-06-27 山东理工大学 Refractory steel for vane of steam turbine of ultra supercritical fossil power plant and manufacturing method
CN103045962A (en) * 2012-12-26 2013-04-17 钢铁研究总院 Steel for steam-temperature ultra-supercritical thermal power unit and preparation method thereof
CN103131953A (en) * 2011-11-24 2013-06-05 江苏星火特钢有限公司 Ferrite heat-resistant steel and production method thereof
CN103215519A (en) * 2013-04-10 2013-07-24 内蒙古包钢钢联股份有限公司 Main steam pipeline for supercritical thermal power generating unit
CN103667967A (en) * 2013-12-28 2014-03-26 无锡透平叶片有限公司 Heat-resistant steel for ultra-supercritical steam turbine rotor
CN103789708A (en) * 2014-02-10 2014-05-14 浙江大隆合金钢有限公司 13Cr9Mo2Co1NiVNbNB super martensite heat-resisting steel and production method thereof
CN104043672A (en) * 2014-04-10 2014-09-17 内蒙古北方重工业集团有限公司 Manufacturing method of high-quality P92 large-aperture thick-wall seamless steel pipe of ultra-supercritical unit
CN104726779A (en) * 2015-04-21 2015-06-24 武汉科技大学 High-Cr ferritic heat-resisting steel and production method thereof
CN105420638A (en) * 2015-11-20 2016-03-23 钢铁研究总院 Heat-resisting alloy for 700-DEG C ultra-supercritical boiler water-cooling wall and tubing manufacturing method
CN106016236A (en) * 2016-06-01 2016-10-12 哈尔滨锅炉厂有限责任公司 Container of above-623 DEG C advanced ultra-supercritical unit boiler
WO2017074738A1 (en) * 2015-10-30 2017-05-04 Northwestern University High temperature steel for steam turbine and other applications
CN109321831A (en) * 2018-11-16 2019-02-12 哈尔滨汽轮机厂有限责任公司 A kind of martensite heat resisting cast steel material and preparation method of the supercritical turbine containing B and N

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3480061B2 (en) 1994-09-20 2003-12-15 住友金属工業株式会社 High Cr ferritic heat resistant steel
JPH08239715A (en) * 1995-03-01 1996-09-17 Nippon Steel Corp Hot working method for high cr ferritic heat resistant steel containing tungsten
JP5097017B2 (en) 2008-06-03 2012-12-12 住友金属工業株式会社 Manufacturing method of high Cr ferritic heat resistant steel
KR101091863B1 (en) 2009-03-06 2011-12-12 포스코특수강 주식회사 Stainless steel having excellent high temperature strength and manufacturing method for the same
CN102409257B (en) 2010-09-21 2013-05-29 宝山钢铁股份有限公司 Austenite-series heat-resistant steel and manufacturing method thereof
CN102527956B (en) 2012-02-21 2013-08-21 衡阳华菱钢管有限公司 Continuous-cast P91-steel round pipe billet and production process thereof
KR102197204B1 (en) * 2013-06-25 2021-01-04 테나리스 커넥션즈 비.브이. High-chromium heat-resistant steel
CN104561839B (en) * 2015-02-09 2017-04-05 中国第一重型机械股份公司 A kind of rare earth modified 9%Cr martensites heat resisting cast steel and its manufacture method

Patent Citations (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0806490A1 (en) * 1996-05-07 1997-11-12 Hitachi, Ltd. Heat resisting steel and steam turbine rotor shaft
CN101525727A (en) * 2009-04-22 2009-09-09 四川江油六合汽轮机材料有限公司 Heat-resisting steel material used as vane or bolt of ultra-supercritical steam turbine and preparation method thereof
CN102011063A (en) * 2010-10-19 2011-04-13 钢铁研究总院 Ferrite-free heavy caliber thick-wall heat resistant steel pipe material
CN103131953A (en) * 2011-11-24 2013-06-05 江苏星火特钢有限公司 Ferrite heat-resistant steel and production method thereof
CN102517508A (en) * 2011-12-30 2012-06-27 钢铁研究总院 Ferrite refractory steel for vane of steam turbine of ultra supercritical fossil power plant and manufacturing method
CN102517517A (en) * 2011-12-30 2012-06-27 山东理工大学 Refractory steel for vane of steam turbine of ultra supercritical fossil power plant and manufacturing method
CN103045962A (en) * 2012-12-26 2013-04-17 钢铁研究总院 Steel for steam-temperature ultra-supercritical thermal power unit and preparation method thereof
CN103215519A (en) * 2013-04-10 2013-07-24 内蒙古包钢钢联股份有限公司 Main steam pipeline for supercritical thermal power generating unit
CN103667967A (en) * 2013-12-28 2014-03-26 无锡透平叶片有限公司 Heat-resistant steel for ultra-supercritical steam turbine rotor
CN103789708A (en) * 2014-02-10 2014-05-14 浙江大隆合金钢有限公司 13Cr9Mo2Co1NiVNbNB super martensite heat-resisting steel and production method thereof
CN104043672A (en) * 2014-04-10 2014-09-17 内蒙古北方重工业集团有限公司 Manufacturing method of high-quality P92 large-aperture thick-wall seamless steel pipe of ultra-supercritical unit
CN104726779A (en) * 2015-04-21 2015-06-24 武汉科技大学 High-Cr ferritic heat-resisting steel and production method thereof
WO2017074738A1 (en) * 2015-10-30 2017-05-04 Northwestern University High temperature steel for steam turbine and other applications
CN105420638A (en) * 2015-11-20 2016-03-23 钢铁研究总院 Heat-resisting alloy for 700-DEG C ultra-supercritical boiler water-cooling wall and tubing manufacturing method
CN106016236A (en) * 2016-06-01 2016-10-12 哈尔滨锅炉厂有限责任公司 Container of above-623 DEG C advanced ultra-supercritical unit boiler
CN109321831A (en) * 2018-11-16 2019-02-12 哈尔滨汽轮机厂有限责任公司 A kind of martensite heat resisting cast steel material and preparation method of the supercritical turbine containing B and N

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111057827A (en) * 2019-11-27 2020-04-24 中国科学院金属研究所 Method for regulating and controlling distribution state of boron element in 9Cr3W3CoB heat-resistant steel for ultra-supercritical unit
CN111057827B (en) * 2019-11-27 2022-04-05 中国科学院金属研究所 Method for regulating and controlling distribution state of boron element in 9Cr3W3CoB heat-resistant steel for ultra-supercritical unit
CN112063921A (en) * 2020-08-10 2020-12-11 上海交通大学 Air-cooled hardened steel plate with ultrahigh-strength high-toughness ultrafine structure and preparation process thereof
CN112063921B (en) * 2020-08-10 2022-06-17 上海交通大学 Air-cooled hardened steel plate with ultrahigh-strength high-toughness ultrafine structure and preparation process thereof
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