CN104513917A - Thermal corrosion-resistant nickel-iron based high-temperature deformation alloy and preparation method and applications thereof - Google Patents
Thermal corrosion-resistant nickel-iron based high-temperature deformation alloy and preparation method and applications thereof Download PDFInfo
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Abstract
The invention discloses a thermal corrosion-resistant nickel-iron based high-temperature deformation alloy, and a preparation method and applications thereof, which belongs to the technical field of high temperature alloy materials. The nickel-iron based high-temperature deformation alloy comprises the following chemical components, by weight: 0.01-0.12% of C, 18-24% of Cr, 19-26% of Fe, 1.8-2.6% of Mo, 0.7-1.5% of Nb, 0.3-1.5% of Al, 0.7-1.8% of Ti, 0.002-0.01% of B, and 0.002-0.05% of P, and is balanced with Ni and inevitable impurities. In a suitable temperature range, the alloy has advantages such as high creep strength, excellent organization stability, good oxidation-corrosion resistance, and excellent hot and cold processing properties, and is able to serve at 600-750 DEG C for a long time.
Description
Technical field
The present invention relates to high temperature alloy technical field, be specifically related to a kind of corrosion and heat resistant ferronickel base wrought superalloy and its preparation method and application, this superalloy is used for the manufacture of the parts of being on active service under 600 ~ 750 DEG C of conditions.
Background technology
The metallic substance worked under high-temperature severe environment should have the processing performance of high hot strength, good oxidation and corrosion performance and excellence, such as, the parts such as water wall, superheater, reheater, header in ultra supercritical coal-fired electric generation furnace, the high temperature corrosion of fume side and the high temperature oxidation of steam side to be born on the one hand, the creep rupture strength (>=100MPa) and thermostability that reach more than 100,000 hours will be had on the other hand.In addition, also require that material has good fatigue property, cold and hot working performance and weldability energy etc.At present, 600 DEG C of ultra-supercritical coal-fired power generating units put into power station in a large number, and its key part adopts ferritic steel and austenitic steel.Consider generatine set heat efficiency and high-temperature steam temperature and pressure closely related, be increased to 700 ~ 750 DEG C further along with vapor temperature and pressure, conventional ferrite steel and austenitic steel no longer meet the demands, must development of new high temperature alloy.
Summary of the invention
In order to overcome weak point of the prior art, the object of the present invention is to provide a kind of corrosion and heat resistant ferronickel base wrought superalloy and its preparation method and application, this alloy has high creep strength, excellent structure stability and good antioxidant anticorrosive performance within the scope of Applicable temperature, there is excellent cold and hot working performance etc. simultaneously, can at 600 ~ 750 DEG C long service.
Technical scheme of the present invention is:
A kind of corrosion and heat resistant ferronickel base wrought superalloy, by weight percentage, alloy composition is: C0.01 ~ 0.12%, Cr18 ~ 24%, Fe19 ~ 26%, Mo1.8 ~ 2.6%, Nb0.7 ~ 1.5%, Al0.3 ~ 1.5%, Ti0.7 ~ 1.8%, B0.002 ~ 0.01%, P0.002 ~ 0.05%, surplus is Ni.
Preferably, alloy composition is by weight percentage: C0.02 ~ 0.08%, Cr19 ~ 23%, Fe19 ~ 21%, Mo2.0 ~ 2.4%, Nb1.0 ~ 1.4%, Al0.6 ~ 1.2%, Ti1.0 ~ 1.4%, B0.002 ~ 0.01%, P0.002 ~ 0.05%, and surplus is Ni.
Also containing inevitable impurity in above-mentioned alloy, foreign matter content is by weight percentage: Co≤0.5%, W≤0.5%, Ta≤0.5%, V≤0.5%, Zr≤0.5%, Mn≤0.5%, Si≤0.5%, Cu≤0.5%, S≤0.01%, Mg≤0.01%.
Reasonable offer process of the present invention is as follows:
Adopt the alloy pig of composition needed for vacuum induction melting, wherein, the feed postition of B is Ni-B or Fe-B binary alloy, and the feed postition of P is Ni-P or Fe-P binary alloy, and the feed postition of other elements is pure metal.Refining temperature is 1500 ~ 1550 DEG C, refining time 30 ± 10 minutes, and the teeming temperature of high-temperature fusant is 1420 ~ 1480 DEG C.The cogging forging temperature interval of alloy pig is 1200 ~ 1000 DEG C, 1200 ~ 950 DEG C, hot-rolled temperature interval.The standard thermal treatment system of alloy is as follows:
(1) 1100 DEG C ± 10 DEG C, insulation 1h, air cooling is to room temperature;
(2) 750 DEG C ± 10 DEG C, insulation 8h, air cooling is to room temperature.
Alloy of the present invention can be tubing, sheet material, wire rod, rod or band.
The principle of the invention is as follows:
Chromium (Cr) is ensureing to form fine and close Cr
2o
3oxide film and carry out solution strengthening while carrying heavy alloyed antioxidant property and hot corrosion resistance and separate out stable M at crystal boundary
23c
6improve the creep strength of alloy.Chromium content lower than 18% time, corrosion and heat resistant decline.But, when chromium content is more than 24%, not only cause the formation of the σ phase be harmful to also can impel the excessive M of crystal boundary
23c
6separate out, endanger the mechanical property of alloy of the present invention.Considered by alloy strength, phase stability and hot corrosion resistance, determine that the content range of chromium element in alloy is 18 ~ 24%.
Molybdenum (Mo) can play solution strengthening effect to matrix, improves the intensity of alloy of the present invention.Content is not enough to ensure the creep strength of alloy lower than 1.8%, and molybdenum content higher than 2.6% time not only bad for high-temperature oxidation resistance, also reduce the stability of MC type carbide, promote fragility M
6c type carbide is formed and the electron vacancy number that can improve matrix causes the precipitation of harmful σ phase.Therefore, Mo content range is 1.8 ~ 2.6%.
Niobium (Nb) can play solution strengthening and precipitation strength effect to matrix, improves the intensity of alloy of the present invention, suppresses the alligatoring of γ ˊ phase, makes alloy have higher thermostability.In addition, Nb forms MC type carbide contribute to improving hot strength by being combined with C.When Nb content lower than 0.7% time, above-mentioned effect cannot be played, if content of niobium is higher than 1.5%, then easily cause the formation of δ and the η phase be harmful to, unfavorable to creep rupture strength.Therefore, Nb content range is defined as 0.7 ~ 1.5%.
Aluminium (Al) both can promote main strengthening phase Ni
3the formation of (Al, Ti), puies forward heavy alloyed hot strength, can form again fine and close Al
2o
3oxide film, carries heavy alloyed antioxidant property.Al content lower than 0.3% time, precipitated phase γ ˊ volume fraction is lower, back dissolving temperature is low and unstable easy generation γ ˊ to η phase in version, alloy high-temp intensity can not be ensured and worsen the over-all properties of alloy.On the other hand, if add Al in a large number, then draw its γ ˊ volume fraction too high affect alloy manufacturability and easily form harmful β NiAl phase and separate out.Therefore, Al content range is defined as 0.3 ~ 1.5%.
Titanium (Ti) can promote main strengthening phase Ni
3the formation of (Al, Ti), puies forward heavy alloyed hot strength.Ti content lower than 0.7 time, cannot play above-mentioned effect, too high titanium content easily causes the η-Ni be harmful to
3the formation of Ti phase, unfavorable to creep rupture strength.Therefore, the Ti content of alloy is defined as 0.7 ~ 1.8%.
Iron (Fe) and nickel (Ni) form the matrix of alloy of the present invention.Iron can play solution strengthening effect to austenitic, also can reduce nickel content in matrix, thus reduces cost of alloy.But excessive iron easily promotes the formation of the σ phase be harmful to, low-alloyed antioxidant anticorrosive performance is also fallen.Therefore, the Fe content of alloy is defined as 19 ~ 26%.
The constitution element that carbon (C) is MC type carbide and grain-boundary strengthening phase M23C6, C and Nb and Ti combines and is formed in hot processing window temperature range and keeps stable MC type carbide to help control grain size, crystal boundary MC and M
23c
6be conducive to strengthening crystal boundary, put forward heavy alloyed high temperature creep strength, in addition, also can prevent the coarsening of crystal grain under hot conditions.But, cross high-carbon content not only easily cause a large amount of carbide to be formed thus reduce the quantity of solution strengthening element content and Precipitation phase in matrix, also easy at crystal boundary formation continuous print grain boundary carbide film reduction alloy property, in addition, the welding property of high carbon content alloy is also unfavorable.Therefore, C content scope is defined as 0.01 ~ 0.12%.
Boron (B) and phosphorus (P) are strong grain boundary segregation element, by forming grain-boundary strengthening phase or segregation on crystal boundary, effectively strengthening Grain-boundary Junctions and making a concerted effort and resistance to deformation, thus significantly improving intensity and the plasticity of alloy of the present invention.Low B, P content does not reach the effect of strengthening crystal boundary, and too high boron and phosphorus content easily cause segregation seriously and easily cause the formation of a large amount of low melting point precipitated phase, to mechanical property and manufacturability unfavorable.Therefore, in alloy, the content of regulation B is the content of 0.002 ~ 0.01%, P is 0.002 ~ 0.05%.
Alloy of the present invention may be used for the manufacture of the parts of being on active service under 600 ~ 750 DEG C of conditions.Such as, may be used for the manufacture of the key part such as superheater, reheater, water wall or header in 700 DEG C of ultra-supercritical coal-fired power generating units; For the manufacture of boiler superheater, reheater, header, water wall or conduit component; Or this alloy is used for the preparation of parts in internal combustion turbine and steam turbine.This alloy can also be applied to power station construction, petrochemical industry and nuclear energy technology field.
Beneficial effect of the present invention is as follows:
1, the invention provides a kind of low cost ferronickel base corrosion and heat resistant wrought superalloy of tissue stabilization.With GH2984 alloy ratio comparatively, alloy of the present invention has better tensile property and enduring quality, and high high-temp stability, be particularly suitable for making the parts such as superheater, reheater, header, water wall, pipeline in advanced ultra supercritical coal-fired electric generation furnace, can at 600 ~ 750 DEG C life-time service.
2, compare with the nickel base superalloy (containing 50 ~ 55% nickel, 12 ~ 21% cobalts, iron is impurity element) such as American-European IN740, CCA617 and Nimonic263, alloy of the present invention not only containing a large amount of iron, and does not add cobalt, has the advantages that cost is low.
3, with Naval Boiler superheater tube with compared with GH2984 alloy (Fe-19Cr-42.5Ni-2.2Mo-1.1Nb-1.1Ti-0.35Al-C), alloy of the present invention contains and up to 1.5% aluminium, can have higher hot strength and the antioxidant property of Geng Jia.
4, alloy of the present invention adds appropriate boron and phosphorus carries out alloying, and the high temperature creep strength of alloy and plasticity are significantly improved.The technical qualification regulation of GH2984 alloy does not allow to add boron, and phosphorus is residual impurity, and its content is no more than 0.01%.
5, in alloy of the present invention, Fe content is moderate, and with the GH2984 alloy phase ratio of high Fe content, thermostability significantly improves, and reduces the alligatoring speed of Precipitation Xiang γ ˊ, avoids harmful η-Ni
3the formation of Ti phase and σ phase.
Accompanying drawing explanation
Fig. 1 is the metallographic structure of the embodiment of the present invention 1 alloy; In figure: (a) low multiple; (b) high multiple.
Fig. 2 is the metallographic structure of the embodiment of the present invention 1 alloy after 700 DEG C/5000h Long-term Aging.
Fig. 3 is the metallographic structure of GH2984 alloy after 700 DEG C/5000h Long-term Aging in comparative example 1.
Embodiment
Below in conjunction with drawings and Examples in detail the present invention is described in detail, in embodiment, the preparation process of each alloy is as follows:
Adopt the alloy pig of composition described in each embodiment of 25kg vacuum induction melting, wherein, the feed postition of B is Ni-B or Fe-B binary alloy, and the feed postition of P is Ni-P or Fe-P binary alloy, and the feed postition of other elements is pure metal.Refining temperature is 1500 ~ 1550 DEG C, refining time 30 minutes.The teeming temperature of high-temperature fusant is 1420 ~ 1480 DEG C.The cogging forging temperature interval of alloy pig is 1200 ~ 1000 DEG C, is forged into 30mm square bar.1200 ~ 950 DEG C, the hot-rolled temperature interval of 30mm square bar, being rolled into diameter is 16mm bar.Bar is after the process of two benches heat treating regime, and being processed into diameter is 5mm standard tensile specimen and lasting sample, then tests tensile property and enduring quality.Two benches heat treating regime is as follows:
(1) 1100 DEG C ± 10 DEG C, insulation 1h, air cooling is to room temperature;
(2) 750 DEG C ± 10 DEG C, insulation 8h, air cooling is to room temperature.
Embodiment 1:
The present embodiment alloying constituent (G18): C0.041, Cr20.0, Fe20.6, Mo2.22, Nb1.22, Al0.83, Ti1.18, B0.006, P0.023, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
The metallographic structure of alloy is as shown in Fig. 1 (a)-(b), and its grain fineness number 3 ~ 5 grades, MC carbide and M23C6 distribution of carbides are on matrix or crystal boundary, and nano level γ ' strengthening phase is evenly distributed on matrix.
Fig. 2 is shown in the metallographic structure of alloy after 700 DEG C/5000h Long-term Aging, and as can be seen from Figure, alloy still keeps good structure stability.
The present embodiment alloy property is as follows:
Room temperature tensile properties: σ
b=1010MPa, σ
0.2=540MPa, δ=35.0%, ψ=47.0%.
700 DEG C of tensile property: σ
b=745MPa, σ
0.2=480MPa, δ=44.0%, ψ=42.5%.
750 DEG C of tensile property: σ
b=650MPa, σ
0.2=465MPa, δ=44.0%, ψ=45.0%.
Enduring quality: 750 DEG C/300MPa condition 105.2h lower creep rupture life, unit elongation 45.5%; 750 DEG C/250MPa condition 293.7h lower creep rupture life, unit elongation 56.4%; 750 DEG C/200MPa condition 1035.7h lower creep rupture life, unit elongation 57.6%; 700 DEG C/350MPa condition 710.48h lower creep rupture life, unit elongation 32.6%; 700 DEG C/300MPa condition 1883.4h lower creep rupture life, unit elongation 40.7%.
Comparative example 1:
GH2984 alloying constituent is: C0.05, Cr19.1, Fe34.0, Mo2.15, Nb1.08, Al0.39, Ti1.20, B0.006, P < 0.005, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.The metallographic structure of this alloy after 700 DEG C/5000h Long-term Aging, as Fig. 3, separates out more η-Ni in alloy
3ti needlelike phase, causes hot strength to reduce.
GH2984 alloy property is as follows:
Room temperature tensile properties: σ
b=945MPa, σ
0.2=540MPa, δ=30.0%, ψ=44.0%
700 DEG C of tensile property: σ
b=680MPa, σ
0.2=475MPa, δ=22.5%, ψ=22.5%
750 DEG C of tensile property: σ
b=615MPa, σ
0.2=410MPa, δ=30.4%, ψ=31.4%
Enduring quality: 750 DEG C/235MPa condition 114.0h lower creep rupture life, unit elongation 37.0%; 750 DEG C/200MPa condition 300.0h lower creep rupture life, unit elongation 32.5%; 700 DEG C/400MPa condition 32.5h lower creep rupture life, unit elongation 13.0%; 700 DEG C/350MPa condition 115.0h lower creep rupture life, unit elongation 14.0%; 700 DEG C/300MPa condition 435.4h lower creep rupture life, unit elongation 14.2%.
Embodiment 2:
Alloying constituent (G10): C0.071, Cr19.99, Fe25.1, Mo2.17, Nb1.17, Al0.67, Ti1.0, B0.006, P0.026, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=950MPa, σ
0.2=480MPa, δ=33.5%, ψ=48.5%.
700 DEG C of tensile property: σ
b=690MPa, σ
0.2=440MPa, δ=46.5%, ψ=53.0%.
750 DEG C of tensile property: σ
b=590MPa, σ
0.2=420MPa, δ=52.0%, ψ=58.5%.
Enduring quality: 700 DEG C/225MPa condition 4148.7h lower creep rupture life, unit elongation 47.8%; 750 DEG C/300MPa condition 89.3.3h lower creep rupture life, unit elongation 47.8%; 750 DEG C/250MPa condition 217.7h lower creep rupture life, unit elongation 69.8%.
Embodiment 3:
Alloying constituent (G21): C0.047, Cr21.7, Fe20.5, Mo2.2, Nb1.19, Al0.97, Ti1.29, B0.005, P0.024, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=1030MPa, σ
0.2=545MPa, δ=34.0%, ψ=45.0%
650 DEG C of tensile property: σ
b=890MPa, σ
0.2=520MPa, δ=34.0%, ψ=41.3%.
700 DEG C of tensile property: σ
b=840MPa, σ
0.2=550MPa, δ=36.8%, ψ=38.8%.
750 DEG C of tensile property: σ
b=705MPa, σ
0.2=525MPa, δ=34.0%, ψ=38.5%.
Enduring quality: 750 DEG C/300MPa condition 138.6h lower creep rupture life, unit elongation 39.7%; 700 DEG C/300MPa condition 2388.4h lower creep rupture life, unit elongation 29.2%.
Embodiment 4:
Alloying constituent (G22): C0.041, Cr21.8, Fe25.6, Mo2.19, Nb1.21, Al0.71, Ti1.3, B0.005, P0.023, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=1080MPa, σ
0.2=555MPa, δ=34.5%, ψ=52.5%
700 DEG C of tensile property: σ
b=800MPa, σ
0.2=500MPa, δ=36.5%, ψ=43.5%.
750 DEG C of tensile property: σ
b=670MPa, σ
0.2=470MPa, δ=36.0%, ψ=39.5%.
Enduring quality: 700 DEG C/300MPa condition 215.0h lower creep rupture life, unit elongation 30.0%.
Embodiment 5:
Alloying constituent (G23): C0.12, Cr23.9, Fe19.4, Mo2.22, Nb1.23, Al1.5, Ti1.29, B0.005, P0.027, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=1130MPa, σ
0.2=640MPa, δ=30.5%, ψ=44.5%
700 DEG C of tensile property: σ
b=865MPa, σ
0.2=590MPa, δ=36.3%, ψ=36.5%.
750 DEG C of tensile property: σ
b=730MPa, σ
0.2=550MPa, δ=40.8%, ψ=38.8%.
Embodiment 6:
Alloying constituent (G27): C0.035, Cr21.6, Fe20.7, Mo2.16, Nb1.15, Al0.95, Ti1.29, B0.005, P0.014, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=1085MPa, σ
0.2=580MPa, δ=32.5%, ψ=45.5%
700 DEG C of tensile property: σ
b=795MPa, σ
0.2=570MPa, δ=35.0%, ψ=36.0%.
750 DEG C of tensile property: σ
b=695MPa, σ
0.2=540MPa, δ=35.5%, ψ=34.3%.
Enduring quality: 750 DEG C/300MPa condition 82.1h lower creep rupture life, unit elongation 39.3%.
Embodiment 7:
Alloying constituent (G25): C0.1, Cr18, Fe19, Mo1.8, Nb1.5, Al0.3, Ti1.8, B0.01, P0.002, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=1030MPa, σ
0.2=600MPa, δ=27.0%, ψ=28.0%.
700 DEG C of tensile property: σ
b=755MPa, σ
0.2=555MPa, δ=34.5%, ψ=35.5%.
Embodiment 8:
Alloying constituent (G26): C0.01, Cr20, Fe26, Mo2.6, Nb0.7, Al1.5, Ti0.7, B0.002, P0.05, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=850MPa, σ
0.2=390MPa, δ=42.0%, ψ=36.0%
700 DEG C of tensile property: σ
b=640MPa, σ
0.2=370MPa, δ=29.0%, ψ=31.0%.
Embodiment 9:
Alloying constituent (G17): C0.04, Cr20.1, Fe20.5, Mo2.2, Nb1.21, Al0.98, Ti0.99, B0.006, P0.022, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=989MPa, σ
0.2=530MPa, δ=35.5%, ψ=47.0%
700 DEG C of tensile property: σ
b=735MPa, σ
0.2=480MPa, δ=40.0%, ψ=45.0%.
750 DEG C of tensile property: σ
b=645MPa, σ
0.2=460MPa, δ=44.0%, ψ=46.5%.
Enduring quality: 750 DEG C/300MPa condition 69.22h lower creep rupture life, unit elongation 52.72%;
Embodiment 10:
Alloying constituent (G12): C0.078, Cr19.94, Fe20.6, Mo2.15, Nb1.14, Al0.69, Ti0.96, B0.004, P0.022, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=949MPa, σ
0.2=484MPa, δ=35.0%, ψ=49.0%
700 DEG C of tensile property: σ
b=685MPa, σ
0.2=425MPa, δ=47.0%, ψ=47.5%.
750 DEG C of tensile property: σ
b=580MPa, σ
0.2=410MPa, δ=49.0%, ψ=58.0%.
Embodiment 11:
Alloying constituent (G13): C0.081, Cr21.8, Fe20.7, Mo2.17, Nb1.17, Al0.68, Ti0.99, B0.006, P0.023, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni
Room temperature tensile properties: σ
b=961MPa, σ
0.2=478MPa, δ=35.0%, ψ=45.0%
700 DEG C of tensile property: σ
b=700MPa, σ
0.2=415MPa, δ=41.0%, ψ=47.5%.
750 DEG C of tensile property: σ
b=595MPa, σ
0.2=405MPa, δ=56.0%, ψ=58.0%.
Embodiment 12:
Alloying constituent (G19): C0.046, Cr20.1, Fe20.6, Mo2.21, Nb1.22, Al0.95, Ti1.0, B0.005, P0.034, Mn < 0.05, Si < more than 0.1, S≤0.003, Ni.
Room temperature tensile properties: σ
b=1033MPa, σ
0.2=548MPa, δ=33.0%, ψ=45.0%
700 DEG C of tensile property: σ
b=765MPa, σ
0.2=500MPa, δ=45.0%, ψ=44.0%.
750 DEG C of tensile property: σ
b=655MPa, σ
0.2=465MPa, δ=45.0%, ψ=44.0%.
Enduring quality: 750 DEG C/300MPa condition 125.57h lower creep rupture life, unit elongation 39.04%;
Above-described embodiment is that the present invention is at magnesium alloy matrix surface preferably embodiment; but embodiments of the present invention are not restricted to the described embodiments; change, the modification done under other any does not deviate from spirit of the present invention and principle, substitute, combine, simplify; all should be the substitute mode of equivalence, be included within protection scope of the present invention.
Claims (9)
1. a corrosion and heat resistant ferronickel base wrought superalloy, it is characterized in that: by weight percentage, this alloy composition is: C0.01 ~ 0.12%, Cr18 ~ 24%, Fe19 ~ 26%, Mo1.8 ~ 2.6%, Nb0.7 ~ 1.5%, Al0.3 ~ 1.5%, Ti0.7 ~ 1.8%, B0.002 ~ 0.01%, P0.002 ~ 0.05%, surplus is Ni.
2. corrosion and heat resistant ferronickel base wrought superalloy according to claim 1, it is characterized in that: by weight percentage, alloy composition is: C0.02 ~ 0.08%, Cr19 ~ 23%, Fe19 ~ 21%, Mo2.0 ~ 2.4%, Nb1.0 ~ 1.4%, Al0.6 ~ 1.2%, Ti1.0 ~ 1.4%, B0.002 ~ 0.01%, P0.002 ~ 0.05%, surplus is Ni.
3. corrosion and heat resistant ferronickel base wrought superalloy according to claim 1 and 2, it is characterized in that: also containing inevitable impurity in alloy, foreign matter content is by weight percentage: Co≤0.5%, W≤0.5%, Ta≤0.5%, V≤0.5%, Zr≤0.5%, Mn≤0.5%, Si≤0.5%, Cu≤0.5%, S≤0.01%, Mg≤0.01%.
4. corrosion and heat resistant ferronickel base wrought superalloy according to claim 1 and 2, is characterized in that: described alloy is tubing, sheet material, wire rod, rod or band.
5. the preparation method of corrosion and heat resistant ferronickel base wrought superalloy according to claim 1, is characterized in that: the method preparation process is as follows:
Adopt the alloy pig of composition needed for vacuum induction melting, wherein, the feed postition of B is Ni-B or Fe-B binary alloy, and the feed postition of P is Ni-P or Fe-P binary alloy, and the feed postition of other elements is pure metal; Refining temperature is 1500 ~ 1550 DEG C, refining time 30 ± 10 minutes, and the teeming temperature of high-temperature fusant is 1420 ~ 1480 DEG C; The cogging forging temperature interval of alloy pig is 1200 ~ 1000 DEG C; 1200 ~ 950 DEG C, hot-rolled temperature interval; The standard thermal treatment system of alloy is as follows:
(1) 1100 DEG C ± 10 DEG C, insulation 1h, air cooling is to room temperature;
(2) 750 DEG C ± 10 DEG C, insulation 8h, air cooling is to room temperature.
6. the application of corrosion and heat resistant ferronickel base wrought superalloy according to claim 1, is characterized in that: this alloy is used for the manufacture of the parts of being on active service under 600 ~ 750 DEG C of conditions.
7. the application of corrosion and heat resistant ferronickel base wrought superalloy according to claim 6, is characterized in that: this alloy is for the manufacture of the key parts such as superheater, reheater, water wall or header in 700 DEG C of ultra-supercritical coal-fired power generating units.
8. the application of corrosion and heat resistant ferronickel base wrought superalloy according to claim 6, is characterized in that: this alloy is used for the manufacture of boiler superheater, reheater, header, water wall or conduit component; Or this alloy is used for the preparation of parts in internal combustion turbine and steam turbine.
9. the application of corrosion and heat resistant ferronickel base wrought superalloy according to claim 6, is characterized in that: this Alloyapplication is in power station construction, petrochemical industry and nuclear energy technology field.
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| CN201310468308.4A Pending CN104513917A (en) | 2013-10-08 | 2013-10-08 | Thermal corrosion-resistant nickel-iron based high-temperature deformation alloy and preparation method and applications thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN104988356A (en) * | 2015-05-27 | 2015-10-21 | 钢铁研究总院 | Method for manufacturing large high-purity nickel base alloy forging |
| CN106399801A (en) * | 2016-09-18 | 2017-02-15 | 华能国际电力股份有限公司 | High-strength wear-resisting high-temperature alloy |
| CN108179303A (en) * | 2017-12-13 | 2018-06-19 | 贵研铂业股份有限公司 | A kind of novel platinum base high temperature resistance strain alloy and preparation method thereof |
| CN109023001A (en) * | 2018-08-14 | 2018-12-18 | 中国科学院金属研究所 | A kind of high strong anti-oxidation Ni-Cr-Fe based heat resistant alloy |
| CN110129535A (en) * | 2019-06-17 | 2019-08-16 | 陕西新精特钢研精密合金有限公司 | A kind of high intensity 1J22 bar and preparation method thereof |
| CN111304496A (en) * | 2020-03-30 | 2020-06-19 | 重庆市北碚区阿尔发合金材料研究所 | Nickel-based wrought superalloy for neodymium iron boron magnet hot-pressing mold |
| CN111411265A (en) * | 2020-03-21 | 2020-07-14 | 交大材料科技(江苏)研究院有限公司 | Nickel-based alloy ultrathin sheet |
| CN111748720A (en) * | 2019-03-27 | 2020-10-09 | 中国科学院金属研究所 | Hot working process and application of nickel-iron-based alloy |
| CN112593120A (en) * | 2020-12-09 | 2021-04-02 | 上海蓝铸特种合金材料有限公司 | Nickel-based multi-element alloy, pipe made of nickel-based multi-element alloy and preparation method of pipe |
| CN113403503A (en) * | 2021-03-04 | 2021-09-17 | 江苏银环精密钢管有限公司 | Iron-nickel alloy seamless tube for 700 ℃ advanced ultra-supercritical boiler and manufacturing method thereof |
| CN115011825A (en) * | 2022-08-09 | 2022-09-06 | 无锡凯斯特铸业有限公司 | 0Cr20Ni55Mo3Nb5Ti nickel-based alloy forming method |
| CN115418531A (en) * | 2022-09-20 | 2022-12-02 | 中国联合重型燃气轮机技术有限公司 | Low-density nickel-based high-temperature alloy and preparation method and application thereof |
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Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104988356A (en) * | 2015-05-27 | 2015-10-21 | 钢铁研究总院 | Method for manufacturing large high-purity nickel base alloy forging |
| CN104988356B (en) * | 2015-05-27 | 2017-03-22 | 钢铁研究总院 | Method for manufacturing large high-purity nickel base alloy forging |
| CN106399801A (en) * | 2016-09-18 | 2017-02-15 | 华能国际电力股份有限公司 | High-strength wear-resisting high-temperature alloy |
| CN108179303A (en) * | 2017-12-13 | 2018-06-19 | 贵研铂业股份有限公司 | A kind of novel platinum base high temperature resistance strain alloy and preparation method thereof |
| CN109023001A (en) * | 2018-08-14 | 2018-12-18 | 中国科学院金属研究所 | A kind of high strong anti-oxidation Ni-Cr-Fe based heat resistant alloy |
| CN111748720A (en) * | 2019-03-27 | 2020-10-09 | 中国科学院金属研究所 | Hot working process and application of nickel-iron-based alloy |
| CN111748720B (en) * | 2019-03-27 | 2021-09-24 | 中国科学院金属研究所 | Hot working process and application of nickel-iron-based alloy |
| CN110129535A (en) * | 2019-06-17 | 2019-08-16 | 陕西新精特钢研精密合金有限公司 | A kind of high intensity 1J22 bar and preparation method thereof |
| CN111411265A (en) * | 2020-03-21 | 2020-07-14 | 交大材料科技(江苏)研究院有限公司 | Nickel-based alloy ultrathin sheet |
| CN111411265B (en) * | 2020-03-21 | 2021-11-26 | 交大材料科技(江苏)研究院有限公司 | Nickel-based alloy ultrathin sheet |
| CN111304496A (en) * | 2020-03-30 | 2020-06-19 | 重庆市北碚区阿尔发合金材料研究所 | Nickel-based wrought superalloy for neodymium iron boron magnet hot-pressing mold |
| CN112593120A (en) * | 2020-12-09 | 2021-04-02 | 上海蓝铸特种合金材料有限公司 | Nickel-based multi-element alloy, pipe made of nickel-based multi-element alloy and preparation method of pipe |
| CN113403503A (en) * | 2021-03-04 | 2021-09-17 | 江苏银环精密钢管有限公司 | Iron-nickel alloy seamless tube for 700 ℃ advanced ultra-supercritical boiler and manufacturing method thereof |
| CN115011825A (en) * | 2022-08-09 | 2022-09-06 | 无锡凯斯特铸业有限公司 | 0Cr20Ni55Mo3Nb5Ti nickel-based alloy forming method |
| CN115418531A (en) * | 2022-09-20 | 2022-12-02 | 中国联合重型燃气轮机技术有限公司 | Low-density nickel-based high-temperature alloy and preparation method and application thereof |
| CN115418531B (en) * | 2022-09-20 | 2024-02-27 | 中国联合重型燃气轮机技术有限公司 | Low-density nickel-based superalloy, and preparation method and application thereof |
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Application publication date: 20150415 |