CN1966750A - Third nickel-base high-temperature single crystal alloy in low cost - Google Patents
Third nickel-base high-temperature single crystal alloy in low cost Download PDFInfo
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- CN1966750A CN1966750A CN 200510047752 CN200510047752A CN1966750A CN 1966750 A CN1966750 A CN 1966750A CN 200510047752 CN200510047752 CN 200510047752 CN 200510047752 A CN200510047752 A CN 200510047752A CN 1966750 A CN1966750 A CN 1966750A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 49
- 239000000956 alloy Substances 0.000 title claims abstract description 49
- 239000013078 crystal Substances 0.000 title claims description 20
- 229910000601 superalloy Inorganic materials 0.000 claims abstract description 21
- 239000000126 substance Substances 0.000 claims abstract description 12
- 229910052702 rhenium Inorganic materials 0.000 claims abstract description 8
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 claims abstract 2
- 238000001816 cooling Methods 0.000 claims description 18
- 239000004615 ingredient Substances 0.000 claims description 9
- 238000005516 engineering process Methods 0.000 claims description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 15
- 229910000995 CMSX-10 Inorganic materials 0.000 abstract description 7
- 229910052759 nickel Inorganic materials 0.000 abstract description 6
- 230000006698 induction Effects 0.000 abstract description 3
- 238000002844 melting Methods 0.000 abstract description 3
- 230000008018 melting Effects 0.000 abstract description 3
- 230000002688 persistence Effects 0.000 abstract description 2
- 238000003723 Smelting Methods 0.000 abstract 2
- 229910052735 hafnium Inorganic materials 0.000 abstract 1
- 238000005728 strengthening Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000000034 method Methods 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000003078 antioxidant effect Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000002045 lasting effect Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 150000003839 salts Chemical class 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910001011 CMSX-4 Inorganic materials 0.000 description 1
- 208000003351 Melanosis Diseases 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000003963 antioxidant agent Substances 0.000 description 1
- 235000006708 antioxidants Nutrition 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000013021 overheating Methods 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
Abstract
The invention belong to the field of nickel-based monocrystal superalloy, specifically a kind of low-cost third generation nickel-based monocrystal superalloy, which is mainly used for producing units bearing high stress under high temperature such as impeller blade in aero-motor. The chemical components of the alloy are (wt.%): Cr 2-4%,Co 11-13%,W 5-7%,Mo 0.5-2%,Re 3- 5%,Al 5-7%,Ta 6-10%,Hf 0.05-0.2%,and Ni as balance. The invention adopts vacuum induction melting for smelting, first smelting mother alloy with chemical components meeting the requirement, growing to monocrystal units. The following technological system for heating treatment is carried out before using: 1300DEG C/8h,A.C.+1305DEG C/15h,A.C.+1310DEG C/8h, A.C.+1315DEG C/24h,A.C.+1180DEG C/4h,A.C.+870DEG C/24h,A.C.. The alloy of the invention has the advantages of excellent persistence correspondent to that of third generation monocrystal superalloy CMSX-10, little Re content, low cost and good causticity resistance.
Description
Technical field
The invention belongs to the nickel-base high-temperature single crystal alloy field, be specially a kind of third nickel-base high-temperature single crystal alloy in low cost, mainly be applicable to and at high temperature bear heavily stressed component, as the turbine blade of aircraft engine.
Background technology
In the process of single crystal super alloy development, because it is more and more higher to the requirement of use temperature, refractory element content such as W, Mo, Ta, Re increase gradually in the alloy, particularly the Re element plays important strengthening effect in alloy, and the Re that adds 3wt.% can make the use temperature of alloy improve about 30 ℃.Refractory element total content among typical first-generation single crystal super alloy CMSX-2, s-generation single crystal super alloy CMSX-4 and the third generation single crystal super alloy CMSX-10 is respectively 14.6wt.%, 16.1wt.% and 19.4wt.%, and Re content is respectively 0%, 3% and 6%.Third generation single crystal super alloy is the highest superalloy of present already used high-temperature behavior.But a large amount of addings of Re element have also brought following shortcoming when improving performance: cost height, density greatly, are easily separated out TCP and are equated.The abundance of Re in the earth's crust is very low,＜0.001g/t, and the reserves of China are more rare, and therefore under the prerequisite that obtains high high-temperature behavior, the consumption that reduces Re in the alloy is very important.
Summary of the invention
The object of the present invention is to provide a kind of low-cost third generation single crystal super alloy, when obtaining the enduring quality suitable with third generation single crystal super alloy CMSX-10, the add-on of minimizing Re is about 1/3, significantly reduces cost of alloy.
Technical scheme of the present invention is:
According to purpose of the present invention, consider the effect of each alloying element simultaneously, the content of Re is reduced to 3～5wt.%, suitably improve the content of W and Ta simultaneously.Its concrete chemical ingredients (wt.%) is as follows:
Cr2～4%, Co11～13%, W5～7%, Mo0.5～2%, Re3～5%, Al5～7%, Ta6～10%, Hf0.05～0.2%, all the other are Ni.
The chemical composition design of alloy of the present invention (alloy designations is named as DD90) is mainly based on following reason:
Re is the important strengthening element in the nickel base superalloy, and it reduces bulk diffusion coefficient, slows down the process by diffusion control, thereby has reduced the coarsening rate of γ ' strengthening phase, the velocity of diffusion of the control creep mechanism that also slowed down.Re gathers partially in the γ matrix, form elementide, hinder dislocation motion, can obtain than traditional more obvious strengthening effect of solid solution effect, it is necessary adding a certain amount of Re in the high-performance single crystal super alloy, can significantly improve the high-temperature behavior of alloy, but consider the Re scarcity of resources, cost an arm and a leg, the add-on of Re is controlled at about 4wt.%.
W is the strong molten strengthening element in the nickel base superalloy, and also a large amount of simultaneously solid solutions are in γ ' strengthening phase.Under the relatively low situation of Re content, give full play to the strengthening effect of W.But W adds excessive meeting with Re and causes γ supersaturation mutually, makes the microstructure instability, easily forms σ phase, μ phase, the equal TCP fragility phase of P, reduces alloy property.The excessive adding of W and Re also can influence the castability of alloy, occurs " freckle " defectives such as (chain equi-axed crystal) in single crystal growing.Therefore control the content of W at 5～7wt.%.
Mo is the solution strengthening element, and can increase the mismatch of γ/γ ', makes the misfit dislocation net intensive, can hinder dislocation motion effectively, improves alloy property; But Mo has disadvantageous effect to the hot corrosion resistance of alloy, should not add too much, therefore controls the content of Mo at 1～2wt.%.
Al is shape γ ' strengthening phase Ni in nickel base superalloy
3The fundamental element of Al, its content plays an important role to the alloy high-temperature behavior, Al content is also most important to the antioxidant property of alloy simultaneously, therefore must add a certain amount of Al in the alloy, but excessive Al can reduce alloy organizing stability, cause being harmful to and separate out mutually, therefore the Al content in the alloy is controlled at 5～7wt.%.
Ta by solution strengthening with improve γ ' mutually intensity improve the hot strength of alloy, can promote simultaneously the persistence of anti-oxidant, the hot corrosion resistance and the aluminum coating of alloy effectively, and do not cause the formation of TCP phase, therefore in alloy, add the Ta of 6～10wt.%.
Cr is the key element that improves the alloy hot corrosion resistance, in alloy, must add proper C r, but because it is many to add refractory metal elements such as Re, W, Mo in the high-strength alloy, adding a large amount of Cr can make alloy organizing stability reduce, therefore the content with Cr is controlled at 2～4wt%, to obtain good comprehensive performances.
Co can stablize the matrix of nickel base superalloy, adds the Co of 11～13wt.% in alloy, has improved alloy organizing stability, and can obtain uniform tissue under relatively low solid solution temperature, makes other alloying elements give full play to strengthening effect.
For improving the castability of alloy, in alloy, also added a spot of Hf.
The present invention adopts vacuum induction melting, is cast into the satisfactory mother alloy of chemical ingredients earlier, and then grows into the monocrystalline component, must heat-treat through following process system before using:
(1) temperature 1295-1300 ℃, time 8-16h, air cooling is to room temperature;
(2) temperature 1303-1305 ℃, time 12-16h, air cooling is to room temperature;
(3) temperature 1308-1310 ℃, time 8-16h, air cooling is to room temperature;
(4) temperature 1312-1317 ℃, time 20-28h, air cooling is to room temperature;
(5) temperature 1150-1180 ℃, time 4-6h, air cooling is to room temperature;
(6) temperature 850-870 ℃, time 20-24h, air cooling is to room temperature.
Advantage of the present invention and beneficial effect are:
(1) compare with existing other nickel-base high-temperature single crystal alloys, alloy of the present invention has the heat and corrosion resistant performance of very high medium and high temperature strength, excellence, can use under the high-temperature and high-stress environment.
(2) alloy of the present invention instantaneous stretching performance in the time of 700 ℃: σ b＞1000MPa, δ 5 〉=15%; Enduring quality: 982 ℃/248MPa following creep rupture life＞470h; 1038 ℃/172MPa following creep rupture life＞280h; 1100 ℃/150MPa following creep rupture life＞90h.
(3) alloy of the present invention has excellent enduring quality, and enduring quality is suitable with third generation single crystal super alloy CMSX-10.CMSX-10 compares with third generation single crystal super alloy, and noble element Re content is lower in the alloy of the present invention, thereby cost is relatively low.
Embodiment
Below by embodiment the present invention is described in further details.
The present invention adopts vacuum induction melting, be cast into the satisfactory mother alloy of chemical ingredients earlier, and then grow into the monocrystalline component, must heat-treat through following process system before using: 1300 ℃/8h, A.C. (air cooling is to room temperature)+1305 ℃/15h, A.C. (air cooling is to room temperature)+1310 ℃/8h, A.C. (air cooling is to room temperature)+1315 ℃/24h, A.C. (air cooling is to room temperature)+1180 ℃/4h, A.C. (air cooling is to room temperature)+870 ℃/24h, A.C. (air cooling is to room temperature).
According to the chemical ingredients scope, prepared the monocrystalline sample of alloy of the present invention, concrete chemical ingredients sees Table 1, in order to contrast conveniently, has also listed the chemical ingredients of CMSX-12C in the CMSX-10 series in the table 1.The monocrystalline sample carries out enduring quality, instantaneous mechanical property and anti-molten salt hot corrosion performance test respectively after Overheating Treatment and machining, the gained result lists table 2, table 4, table 5 respectively in.In order to contrast, the 982 ℃/248MPa enduring quality data that contain the CMSX-12C of 6wt.%Re in alloy of the present invention and the CMSX-10 series are listed in table 3.
The chemical ingredients of table 1 embodiment of the invention and comparative alloy CMSX-12C (wt%)
| Alloy | Al | Cr | Co | Mo | Ta | W | Re | Hf | Ti | Ni |
| Embodiment 1 | 6.05 | 3.18 | 12.1 | 1.01 | 7.95 | 5.95 | 4.00 | 0.079 | 0 | Surplus |
| Embodiment 2 | 5.07 | 4.00 | 11.2 | 0.98 | 7.04 | 7.00 | 4.02 | 0.096 | 0 | Surplus |
| Embodiment 3 | 6.10 | 3.11 | 12.78 | 1.02 | 8.01 | 5.04 | 4.96 | 0.086 | 0 | Surplus |
| Embodiment 4 | 6.07 | 3.03 | 12.01 | 1.01 | 7.98 | 6.97 | 3.05 | 0.078 | 0 | Surplus |
| CMSX-12C | 5.62 | 2.7 | 3.5 | 0.45 | 8.8 | 5.4 | 6 | 0.04 | 0.75 | Surplus |
The enduring quality of table 2 embodiment of the invention 1
| Lasting condition | Creep rupture life (h) | Unit elongation (%) | Relative reduction in area (%) |
| 1100℃/150MPa | 103.22 | 31.76 | 27.7 |
| 100.52 | 25.36 | 25.13 | |
| 1100℃/160MPa | 62.16 | 26.88 | 27.26 |
| 71.77 | 23.6 | 27.23 | |
| 1093℃/138MPa | 140.45 | 31.2 | 26.99 |
| 146.58 | 31.68 | 32.61 | |
| 1038℃/172MPa | 287.18 | 36.88 | 36.75 |
| 350.27 | 32.96 | 34.42 | |
| 982℃/248MPa | 474.46 | 39.36 | 30.22 |
| 575.75 | 26.24 | 30.04 | |
| 950℃/414MPa | 78.13 | 31.12 | 27.96 |
| 96.72 | 34.64 | 30.83 | |
| 871℃/551MPa | 176.16 | 28.16 | 25.39 |
| 215.75 | 32.32 | 28.25 | |
| 850℃/586MPa | 288.5 | 27.28 | 24.79 |
| 168.68 | 25.6 | 24.87 |
982 ℃/248MPa the enduring quality of table 3 embodiment of the invention 1 and comparative alloy CMSX-12C
| Lasting condition | Creep rupture life (h) | Unit elongation (%) | Relative reduction in area (%) |
| The present invention | 474.46 | 39.36 | 30.22 |
| 575.75 | 26.24 | 30.04 | |
| CMSX-12C | 465.2 | 31.8 | 21.0 |
| 518.0 | 26.1 | 31.2 | |
| 480.9 | 28.3 | 33.6 | |
| 713.3 | 30.0 | 28.0 |
The tensile property of table 4 alloy embodiment 1 of the present invention
| Temperature, ℃ | σ 0.2，MPa | σ b，MPa | δ 5，％ | Ψ，％ |
| Room temperature | 785 | 835 | 24 | 19.5 |
| 765 | 805 | 22 | 19.5 | |
| 700 | 885 | 1010 | 17 | 29 |
| 870 | 1010 | 15 | 30 | |
| 1000 | 565 | 710 | 27 | 36 |
| 595 | 745 | 29 | 39 | |
| 1100 | 360 | 495 | 36 | 54 |
| 370 | 505 | 34 | 57 |
The hot corrosion resistance of table 5 alloy embodiment 1 of the present invention
(fused salt weight item: 75%Na
2SO
4+ 25%K
2SO
4)
| Test period, h | 0 | 5 | 10 | 20 | 30 | 40 |
| Weightening finish, mg/cm 2 | 0 | 0.12552 | 2.08423 | 3.37916 | 5.75308 | -2.84996 |
| Test period, h | 50 | 60 | 70 | 80 | 90 | 100 |
| Weightening finish, mg/cm 2 | -8.25752 | -7.03202 | -5.77041 | -4.38645 | -4.11473 | -3.43837 |
Claims (3)
1, a kind of low-cost third generation single crystal super alloy is characterized in that, by weight percentage, its chemical ingredients is: Cr 2～4%, Co 11～13%, and W 5～7%, and Mo 0.5～2%, and Re 3～5%, Al 5～7%, and Ta 6～10%, Hf0.05～0.2%, and all the other are Ni.
According to the described low-cost third generation single crystal super alloy of claim 1, it is characterized in that 2, by weight percentage, its preferable chemical ingredients is: Cr 3%, Co 12%, and W 6%, and Mo 1%, and Re 4%, Al6%, and Ta 8%, Hf0.1%, all the other are Ni.
3, according to the described low-cost third generation single crystal super alloy of claim 1, it is characterized in that heat treatment of alloy technology concrete steps are as follows:
(1) temperature 1295-1300 ℃, time 8-16h, air cooling is to room temperature;
(2) temperature 1303-1305 ℃, time 12-16h, air cooling is to room temperature;
(3) temperature 1308-1310 ℃, time 8-16h, air cooling is to room temperature;
(4) temperature 1312-1317 ℃, time 20-28h, air cooling is to room temperature;
(5) temperature 1150-1180 ℃, time 4-6h, air cooling is to room temperature;
(6) temperature 850-870 ℃, time 20-24h, air cooling is to room temperature.
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| CNB2005100477524A CN100430500C (en) | 2005-11-18 | 2005-11-18 | Third nickel-base high-temperature single crystal alloy in low cost |
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| CNB2005100477524A CN100430500C (en) | 2005-11-18 | 2005-11-18 | Third nickel-base high-temperature single crystal alloy in low cost |
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| CN1966750A true CN1966750A (en) | 2007-05-23 |
| CN100430500C CN100430500C (en) | 2008-11-05 |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100557092C (en) * | 2007-12-17 | 2009-11-04 | 北京航空航天大学 | Adopt the method for seed crystal method and spiral crystal separation method combined preparation Ni based single-crystal high-temperature alloy |
| CN101935770A (en) * | 2010-08-31 | 2011-01-05 | 西安诺博尔稀贵金属材料有限公司 | Method for manufacturing aluminum and yttrium-containing multi-element nickel-based alloy ingot blank |
| CN102732750A (en) * | 2011-04-08 | 2012-10-17 | 中国科学院金属研究所 | Nickel base single crystal superalloy with low cost and low density |
| EP2218798B1 (en) | 2008-12-01 | 2016-09-14 | United Technologies Corporation | Lower cost high strength single crystal superalloys with reduced Re and Ru content |
| CN106198605A (en) * | 2016-08-04 | 2016-12-07 | 中国科学院金属研究所 | The method of evaluating performance of single crystal super alloy under a kind of special environment |
| CN106756249A (en) * | 2016-12-09 | 2017-05-31 | 中国科学院金属研究所 | A kind of nickel-base high-temperature single crystal alloy of high intensity and tissue stabilization and preparation method thereof |
| CN111500896A (en) * | 2020-05-19 | 2020-08-07 | 西北工业大学 | Gamma' phase reinforced third generation nickel base single crystal high temperature alloy and preparation method thereof |
| CN112226648A (en) * | 2020-09-08 | 2021-01-15 | 中国科学院金属研究所 | Low-Re low-S heat-corrosion-resistant nickel-based single crystal superalloy |
| CN112746328A (en) * | 2020-12-01 | 2021-05-04 | 中国科学院金属研究所 | Single crystal high temperature alloy with low density and excellent hot corrosion resistance and preparation process thereof |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP3184882B2 (en) * | 1997-10-31 | 2001-07-09 | 科学技術庁金属材料技術研究所長 | Ni-based single crystal alloy and method for producing the same |
| JP4003318B2 (en) * | 1998-10-30 | 2007-11-07 | 株式会社Ｉｈｉ | Nickel-based single crystal superalloy |
| US20030041930A1 (en) * | 2001-08-30 | 2003-03-06 | Deluca Daniel P. | Modified advanced high strength single crystal superalloy composition |
| EP1451382A1 (en) * | 2001-11-09 | 2004-09-01 | Alstom Technology Ltd | Method for developing a nickel-base super alloy |
| CN1274859C (en) * | 2004-07-30 | 2006-09-13 | 沈阳工业大学 | Monocrystalline nickel-base alloy with high flexing antioxygenizing and its preparation |
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2005
- 2005-11-18 CN CNB2005100477524A patent/CN100430500C/en active Active
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100557092C (en) * | 2007-12-17 | 2009-11-04 | 北京航空航天大学 | Adopt the method for seed crystal method and spiral crystal separation method combined preparation Ni based single-crystal high-temperature alloy |
| EP2218798B1 (en) | 2008-12-01 | 2016-09-14 | United Technologies Corporation | Lower cost high strength single crystal superalloys with reduced Re and Ru content |
| CN101935770A (en) * | 2010-08-31 | 2011-01-05 | 西安诺博尔稀贵金属材料有限公司 | Method for manufacturing aluminum and yttrium-containing multi-element nickel-based alloy ingot blank |
| CN101935770B (en) * | 2010-08-31 | 2012-04-18 | 西安诺博尔稀贵金属材料有限公司 | Method for manufacturing aluminum and yttrium-containing multi-element nickel-based alloy ingot blank |
| CN102732750A (en) * | 2011-04-08 | 2012-10-17 | 中国科学院金属研究所 | Nickel base single crystal superalloy with low cost and low density |
| CN102732750B (en) * | 2011-04-08 | 2015-06-10 | 中国科学院金属研究所 | Nickel base single crystal superalloy with low cost and low density |
| CN106198605A (en) * | 2016-08-04 | 2016-12-07 | 中国科学院金属研究所 | The method of evaluating performance of single crystal super alloy under a kind of special environment |
| CN106756249A (en) * | 2016-12-09 | 2017-05-31 | 中国科学院金属研究所 | A kind of nickel-base high-temperature single crystal alloy of high intensity and tissue stabilization and preparation method thereof |
| CN111500896A (en) * | 2020-05-19 | 2020-08-07 | 西北工业大学 | Gamma' phase reinforced third generation nickel base single crystal high temperature alloy and preparation method thereof |
| CN111500896B (en) * | 2020-05-19 | 2021-09-17 | 西北工业大学 | Gamma' phase reinforced third generation nickel base single crystal high temperature alloy and preparation method thereof |
| CN112226648A (en) * | 2020-09-08 | 2021-01-15 | 中国科学院金属研究所 | Low-Re low-S heat-corrosion-resistant nickel-based single crystal superalloy |
| CN112746328A (en) * | 2020-12-01 | 2021-05-04 | 中国科学院金属研究所 | Single crystal high temperature alloy with low density and excellent hot corrosion resistance and preparation process thereof |
| CN112746328B (en) * | 2020-12-01 | 2022-03-08 | 中国科学院金属研究所 | Single crystal high temperature alloy with low density and excellent hot corrosion resistance and preparation process thereof |
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| CN100430500C (en) | 2008-11-05 |
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Effective date of registration: 20210810 Address after: 110172 block C12, south of Shendong Sixth Road, west of Zhongxing Street, Shenfu new area, Shenyang City, Liaoning Province Patentee after: Liaoning Hongyin Metal Co.,Ltd. Address before: 110016 No. 72, Wenhua Road, Shenhe District, Liaoning, Shenyang Patentee before: INSTITUTE OF METAL RESEARCH CHINESE ACADEMY OF SCIENCES |
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Denomination of invention: A low cost third generation nickel base single crystal superalloy Effective date of registration: 20220225 Granted publication date: 20081105 Pledgee: Fushun Bank Co.,Ltd. Development Zone sub branch Pledgor: Liaoning Hongyin Metal Co.,Ltd. Registration number: Y2022210000012 |
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