CN106636759B - A kind of high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element is strengthened - Google Patents
A kind of high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element is strengthened Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 118
- 239000000956 alloy Substances 0.000 title claims abstract description 118
- 239000013078 crystal Substances 0.000 title claims abstract description 65
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 title claims abstract description 42
- 229910052697 platinum Inorganic materials 0.000 title claims abstract description 21
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims description 46
- 229910052759 nickel Inorganic materials 0.000 title claims description 18
- 229910052741 iridium Inorganic materials 0.000 claims abstract description 21
- 229910052707 ruthenium Inorganic materials 0.000 claims abstract description 19
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 15
- 229910052702 rhenium Inorganic materials 0.000 claims abstract description 13
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 13
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 11
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 11
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 11
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 11
- 230000032683 aging Effects 0.000 claims description 24
- 238000005275 alloying Methods 0.000 claims description 9
- 238000007711 solidification Methods 0.000 claims description 8
- 230000008023 solidification Effects 0.000 claims description 8
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 230000006698 induction Effects 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims description 3
- 229910052797 bismuth Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 239000004615 ingredient Substances 0.000 claims description 2
- 229910052745 lead Inorganic materials 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 238000002360 preparation method Methods 0.000 claims description 2
- 238000000926 separation method Methods 0.000 claims description 2
- 239000002994 raw material Substances 0.000 claims 1
- 229910000601 superalloy Inorganic materials 0.000 abstract description 12
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 230000007774 longterm Effects 0.000 description 19
- 230000000052 comparative effect Effects 0.000 description 13
- 239000000126 substance Substances 0.000 description 6
- 229910052804 chromium Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 239000000470 constituent Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000013021 overheating Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 230000008859 change Effects 0.000 description 2
- 230000008878 coupling Effects 0.000 description 2
- 238000010168 coupling process Methods 0.000 description 2
- 238000005859 coupling reaction Methods 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 2
- 229910052737 gold Inorganic materials 0.000 description 2
- 239000010931 gold Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000005764 inhibitory process Effects 0.000 description 2
- 230000000977 initiatory effect Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910000714 At alloy Inorganic materials 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 239000003963 antioxidant agent Substances 0.000 description 1
- 230000003078 antioxidant effect Effects 0.000 description 1
- 235000006708 antioxidants Nutrition 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000001739 density measurement Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 230000010534 mechanism of action Effects 0.000 description 1
- 230000008450 motivation Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/52—Alloys
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Inorganic Chemistry (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
Abstract
The invention discloses the high thermal stability high intensity single crystal super alloys that a kind of platinum family element is strengthened, and belong to nickel-base high-temperature single crystal alloy technical field.Weight percentage, the alloy composition are：Cr 2~6%, Co 7~14%, Mo 1~3%, W 4.5~6.5%, Al 4.7~6.7%, Ta 5~9%, Re 5.4~7%, Ru 2~5%, Ir 1~3%, Hf 0 0.2%, Y 0 0.2%, remaining is Ni.The alloy has many advantages, such as that high temperature microstructure stability height, having excellent high-temperature strength, inoxidizability are strong, is particularly suitable for the hot junction high-temperature component in the fields such as manufacture Aeronautics and Astronautics, the energy.
Description
Technical field
The present invention relates to nickel-base high-temperature single crystal alloy technical fields, and in particular to a kind of high heat stability that platinum family element is strengthened
Property high-strength nickel based single-crystal high-temperature alloy, which is suitable for manufacturing the hot junction high-temperature component in the fields such as Aeronautics and Astronautics, the energy.
Background technology
With the development of the industrial circles such as Aeronautics and Astronautics, the energy, the requirement to high temperature alloy temperature capability is also constantly carrying
Height, cast nickel-base alloy successively experienced casting equiax crystal, orientation several developing stage such as column crystal and monocrystalline.Ni-based list
Brilliant high temperature alloy is had gradually developed along with the application of directional solidification processes.Crystal Nickel-based Superalloy since the advent of the world,
With its higher temperature capability, superior creep-resistant property and good anti-oxidant corrosion resistance become advanced aviation hair
The preferred material of motivation and industry gas turbine hot-end component.So far the conjunction of five generations also has been developed in nickel-base high-temperature single crystal alloy
Gold.
With the continuous improvement of single crystal super alloy generation, the refractory elements total amount such as W, Mo, Re, Cr gradually increases,
Elevated temperature strength is gradually improved.But with the raising of the refractory elements total amount such as Re, W, Mo, inclining for TCP phases is precipitated in alloy
To significantly increasing, TCP phases can become crack initiation position, while also reduce alloy strengthening effect, lead to alloy mechanical property
It can especially croop property be remarkably decreased.Therefore, it is future development to obtain high thermal stability high-strength nickel based single-crystal high-temperature alloy
Trend.
Invention content
In order to solve existing the problems such as nickel-base high-temperature single crystal alloy high temperature microstructure stability is poor in the art, intensity is low, this hair
Bright is designed to provide a kind of high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element is strengthened, and is based on Ru, Ir
The inhibiting effect that equal platinum family elements form TCP phases, it is comprehensive in conjunction with the facilitation that the elements such as Re, W, Mo, Cr form TCP phases
Close each element coordinate coupling, obtain high thermal stability high-strength nickel based single-crystal high-temperature alloy, the alloy be suitable for manufacture aviation,
The hot junction high-temperature component in the fields such as space flight, the energy.
To achieve the above object, the technical solution adopted in the present invention is as follows：
A kind of high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element is strengthened, weight percentage,
The alloy composition is as follows：
Cr 2~6%, Co 7~14%, Mo 1~3%, W 4.5~6.5%, Al 4.7~6.7%, Ta 5~9%,
Re 5.4~7%, Ru 2~5%, Ir 1~3%, Hf 0-0.2%, Y 0-0.2%, remaining is Ni.
Weight percentage, the preferred chemical composition of the alloy are as follows：
Cr 2.5~5.5%, Co 8~12%, Mo 1.5~3%, W 5~6%, Al 5~6.5%, Ta 5~
8.5%, Re 5~7%, Ru 2~5%, Ir 1~3%, Hf 0-0.2%, Y 0-0.2%, remaining is Ni.
In the nickel-base high-temperature single crystal alloy, total content >=4wt.% of Ru and Ir.
In the above-mentioned nickel-base high-temperature single crystal alloy of the present invention, the ingredient of impurity meets claimed below：
O≤0.003wt.%, N≤0.002wt.%, S≤0.003wt.%, P≤0.002wt.%, Si≤0.2wt.%,
Pb≤0.0003wt.%, Bi≤0.00005wt.%.
Alloy (DD495) Design of Chemical Composition Main Basiss are as follows in the present invention：
Ru is a kind of platinum family element, and big 7% or so, the Ru of atomic radius ratio Ni, which are dissolved into Ni, can play stronger solid solution by force
Change acts on, in addition, reporting that Ru can reduce alloying element microsegregation, significantly reduces TCP phase formabilities in alloy, improves nickel
The structure stability of based single-crystal high-temperature alloy adds Ru elements in forth generation single crystal super alloy, significantly improves alloy
Elevated temperature strength, therefore Ru also becomes one of the representative element of advanced single crystal super alloy.Ir is also a kind of platinum family element, Ir tools
Have a face-centred cubic structure, Ni and Ir can infinitely dissolve, Ir has ideal distribution coefficient in γ/γ ' binary systems, two
Generally equal distribution between phase.A kind of Ir as intensified element is added to the research in nickel-base high-temperature single crystal alloy few, applicant
Previous work shows that Ir can inhibit the formation of TCP phases, plays the role of stable alloy tissue.Recently, applicants have discovered that in higher
In generation single crystal alloy, synergistic effect Ir, Ru element interaction more independent to the inhibition of TCP phases of Ru and Ir are notable, meanwhile, in Ru
Under Ir collective effects, the high temperature microstructure stability of single crystal super alloy is significantly improved.But Ru, Ir are platinum family element, valence
Lattice are relatively high, therefore in order to control cost of alloy, and the content of Ru elements should be controlled and should be controlled in 3~5%, Ir constituent contents
1~3%.
In order to obtain higher temperature in use, it is necessary to improve the elevated temperature strength of Ni-based single crystal super alloy.Re、W、Mo、
The elements such as Cr can be solid-solution in Crystal Nickel-based Superalloy, on the one hand inhibited diffusion of alloy elements, on the other hand can be passed through solid solution
Invigoration effect improves alloy strength, inhibits the alloy high-temp deformation of creep.Therefore, with the continuous hair of nickel-base high-temperature single crystal alloy
Exhibition, the total content of above-mentioned refractory element are also being continuously increased.However, the increase of refractory element also brings high temperature microstructure unstable
Alloy is easy that TCP phases are precipitated in problem, especially high temperature Long Term Aging, and TCP phases are rich in the refractory elements such as Re, W, Mo, Cr,
Refractory element content in alloy is reduced, reinforcing effect is reduced, meanwhile, TCP phases can also become the position of crack initiation, make
It fails at alloy.In order to obtain higher elevated temperature strength, alloy of the present invention has considered the work of above-mentioned intensified element when designing
With, therefore Re contents should control the content in 5.4~7%, Cr and should control and be controlled in 4.5~6.5% and 1 in 2~6%, W and Mo
~3%.
Al, Ta etc. are that hardening constituent γ ' in alloy primarily forms element.γ ' is mutually the important hardening constituent of high temperature alloy,
The γ ' for obtaining certain volume score is the key that mutually alloy excellent high temperature intensity, and therefore, the content of the elements such as Al, Ta should be distinguished
Control is in 4.7~6.7% and 5~9%.Co elements can reduce the segregation of other alloying elements, play what inhibition TCP phases were formed
Effect, therefore Co content should be controlled 7~14%.The addition of Hf, Y can improve alloy Production Practice of Casting Technologies and antioxygen
Change performance, but excessively high Hf, Y content may result in the reduction of alloy initial melting temperature, heat treatment window narrows, therefore Hf, Y contain
Amount should be controlled in 0-0.2% and 0-0.02%.
Nickel-base high-temperature single crystal alloy of the present invention is existed using elements such as pure Ni, Co, Cr, W, Mo, Ta, Al, Re, Ru, Ir
Melting in vacuum induction melting furnace pours into the satisfactory master alloy of chemical composition, is closed using apparatus for directional solidification remelting mother
Gold, using spiral crystal separation method or seed-grain method directional solidification at monocrystal rod.It needs, through Overheating Treatment, vacuum or common to can be used before use
Muffle furnace is heat-treated.
Carry out preparing single crystal alloy on industrial directional solidification furnace, orient the temperature gradient of stove 40 DEG C/cm~
Between 80 DEG C/cm, pouring temperature is 1480~1550 DEG C, and mould shell temperature is consistent with pouring temperature, growth rate for 3~
Within the scope of 8mm/min, monocrystalline coupon is prepared.
The heat treating regime of single crystal alloy DD495 of the present invention is as follows：
(1) solution treatment keeps the temperature 6~10 hours at 1310~1320 DEG C；Then raise temperature to 1320-1345 DEG C heat preservation 8~
16 hours, then it is air-cooled to room temperature；
(2) high-temperature aging is handled, and is kept the temperature 2~6 hours at 1100~1160 DEG C, is then air-cooled to room temperature；
(3) low temperature aging is handled, and is kept the temperature 16~26 hours at 850~900 DEG C, is then air-cooled to room temperature.
Beneficial effects of the present invention are as follows：
(1) the present invention is based on platinum family elements cooperates with coupling with infusibility intensified element between high temperature microstructure stability and elevated temperature strength
The mechanism of action is closed, a kind of high thermal stability, high-strength nickel based single-crystal high-temperature alloy have been developed, mechanical behavior under high temperature is more than typical case
Four generation single crystal super alloys are horizontal.
(2) compared with existing other nickel-base high-temperature single crystal alloys, alloy of the present invention has enduring quality than typical case the 4th
It is high for single crystal alloy intensity；
(3) alloy of the present invention is precipitated after 1100 DEG C of Long-term Aging 500h without TCP phases, there is minute quantity TCP after timeliness 1000h
Mutually it is precipitated；
(4) alloy of the present invention creep life under the conditions of 1150 DEG C/137MPa is more than 100h；
(5) alloy of the present invention reaches grade of oxidation resistance at 1000 DEG C.
Description of the drawings
Fig. 1 is 5 alloy of embodiment of the present invention casting state tissue；
Fig. 2 is organized after 5 alloy of the embodiment of the present invention is heat-treated；
Fig. 3 is embodiment 1 alloy, 1100 DEG C/180MPa deformation of creep curves；
Fig. 4 is embodiment 2 in 1100 DEG C/180MPa deformation of creep curves；
Fig. 5 is 5 alloy of embodiment in 1150 DEG C/137MPa deformation of creep curves；
Fig. 6 is the strong curve comparison of heat of alloy of the present invention and typical forth generation single crystal super alloy；
Fig. 7 is 1000 DEG C of high-temperature oxydation weightening curves of alloy of the present invention；
Fig. 8 is alloy of the present invention microstructure after 1100 DEG C of Long-term Aging 200h；
Fig. 9 is alloy of the present invention microstructure after 1100 DEG C of Long-term Aging 500h；
Figure 10 is alloy of the present invention microstructure after 1100 DEG C of Long-term Aging 1000h.
Figure 11 is precipitation TCP phases after the 1100 DEG C of Long-term Aging 200h of single crystal alloy of comparative example 1 without Ru and Ir.
Figure 12 is precipitation TCP phases after the 1100 DEG C of Long-term Aging 500h of single crystal alloy of comparative example 1 without Ru and Ir.
Figure 13 is comparative example 1 without precipitation TCP phases after 1100 DEG C of Long-term Aging 1000h of Ru and Ir single crystal alloys.
Figure 14 is that TCP phases are precipitated after comparative example 2 is free of 1100 DEG C of Long-term Aging 200h of Ru single crystal alloys containing Ir.
Figure 15 is that TCP phases are precipitated after comparative example 2 is free of 1100 DEG C of Long-term Aging 500h of Ru single crystal alloys containing Ir.
Figure 16 is that TCP phases are precipitated after comparative example 2 is free of 1100 DEG C of Long-term Aging 1000h of Ru single crystal alloys containing Ir.
Figure 17 is that TCP phases are precipitated after comparative example 3 is free of 1100 DEG C of Long-term Aging 200h of Ir single crystal alloys containing Ru.
Figure 18 is that TCP phases are precipitated after comparative example 3 is free of 1100 DEG C of Long-term Aging 500h of Ir single crystal alloys containing Ru.
Figure 19 is that TCP phases are precipitated after comparative example 3 is free of 1100 DEG C of Long-term Aging 1000h of Ir single crystal alloys containing Ru.
Specific implementation method
Following embodiment will be further described the present invention, not thereby limiting the invention.
Following embodiment and the requirement of the specific preparation method of comparative example alloy：Using vacuum induction melting furnace melting former material
Material, first pours into the satisfactory master alloy of chemical composition, then prepare monocrystal rod using directional solidification furnace, needs to carry out before use
Heat treatment.
Carry out preparing single crystal alloy on industrial directional solidification furnace, orient the temperature gradient of stove 40 DEG C/cm~
Between 80 DEG C/cm, pouring temperature is 1480~1550 DEG C, and mould shell temperature is consistent with pouring temperature, growth rate for 3~
Within the scope of 8mm/min, monocrystalline coupon is prepared.
The heat treating regime of single crystal alloy DD495 of the present invention is as follows：
(1) solution treatment keeps the temperature 6~10 hours at 1310~1320 DEG C；Then raise temperature to 1320-1345 DEG C heat preservation 8~
16 hours, then it is air-cooled to room temperature；
(2) high-temperature aging is handled, and is kept the temperature 2~6 hours at 1100~1160 DEG C, is then air-cooled to room temperature；
(3) low temperature aging is handled, and is kept the temperature 16~26 hours at 850~900 DEG C, is then air-cooled to room temperature.
Embodiment 1-6：
The chemical composition of 1-6 nickel-base high-temperature single crystal alloys of the embodiment of the present invention is referring to table 1.
The chemical composition composition list (wt.%) of 1 alloy (embodiment 1-6) of the present invention of table
| Embodiment 1 | Embodiment 2 | Embodiment 3 | Embodiment 4 | Embodiment 5 | Embodiment 6 | |
| Cr | 5.5 | 5.5 | 5 | 5 | 5 | 3.5 |
| Co | 10 | 10 | 10 | 10 | 9 | 9 |
| Mo | 1.5 | 1.5 | 1.5 | 1.5 | 2 | 2.2 |
| W | 6 | 6 | 6 | 6 | 5.5 | 5.6 |
| Al | 6 | 6 | 6 | 6 | 5.6 | 6 |
| Ta | 8.5 | 8.5 | 8.5 | 8.5 | 8.5 | 7 |
| Re | 5.5 | 5.5 | 5.5 | 5.5 | 6 | 6 |
| Ru | 2.5 | 2.5 | 3 | 3 | 4 | 4.5 |
| Ir | 1.5 | 3 | 1.5 | 3 | 3 | 3 |
| Hf | 0.1 | 0.1 | 0.1 | 0.1 | 0.1 | 0.1 |
| Y | 0.02 | 0.02 | 0.02 | 0.02 | 0.02 | 0.02 |
| Ni | Surplus | Surplus | Surplus | Surplus | Surplus | Surplus |
Alloy in above example is tested for the property, it is as a result as follows：
1, the density measurement of 2 alloy of embodiment is 9.1g/cm3。
2,5 alloy of embodiment carries out enduring quality test after Overheating Treatment and mechanical processing, the results are shown in Table 2.
2 embodiment of table, 5 alloy enduring quality
3,1 alloy of the embodiment of the present invention carries out tension test performance test through Overheating Treatment and mechanical processing, as a result such as table 3
It is shown.
3 embodiment of table, 1 alloy tensile performance
4,5 alloy of embodiment of the present invention casting state and microstructure after Overheating Treatment are as depicted in figs. 1 and 2.
5,1 alloy 1100 DEG C/180MPa deformations of creep curve such as Fig. 3 of embodiment, embodiment 2 are compacted in 1100 DEG C/180MPa
Become deformation curve such as Fig. 4, the increase of Ir constituent contents makes the creep life of alloy increase；5 alloy of embodiment 1150 DEG C/
137MPa deformations of creep curve such as Fig. 5, Ir and Ru element coordinative role causes alloy high-temp creep life to be improved.
6, strong curve comparison such as Fig. 6 of heat of 5 alloy of the embodiment of the present invention and typical forth generation single crystal super alloy, the present invention
Alloy strength is apparently higher than typical forth generation single crystal super alloy；
5 alloy of the embodiment of the present invention, 1000 DEG C of high-temperature oxydation weightening curve such as Fig. 7；5 alloy of the embodiment of the present invention is 1100
Microstructure such as Fig. 8 after DEG C Long-term Aging 200h, has no that harmful TCP phases are precipitated；5 alloy of the embodiment of the present invention is long-term at 1100 DEG C
Microstructure such as Fig. 9 after timeliness 500h has no that harmful TCP phases are precipitated；5 alloy of the embodiment of the present invention is in 1100 DEG C of Long-term Agings
Microstructure such as Figure 10 after 1000h, only minute quantity graininess TCP phases are precipitated.
Comparative example 1：
Platinum family element Ru and Ir element is free of in this example alloying component, specific alloying component is following (wt.%)：
Cr 5.5%, Co 10%, Mo 1.5%, W 6%, Al 6%, Ta 8.5%, Re 5.5%, Hf 0.1%, Y
0.02%, remaining is Ni.
Nickel-base high-temperature single crystal alloy of this example without Ru and Ir elements is observed after 1100 DEG C of timeliness 200h, 500h, 1000h
TCP phases, respectively as shown in Figure 11, Figure 12, Figure 13.
Comparative example 2：
Contain platinum family element Ir in this example alloying component, but be free of Ru elements, specific alloying component is following (wt.%)：
Cr 5.5%, Co 10%, Mo 1.5%, W 6%, Al 6%, Ta 8.5%, Re 5.5%, Ir 3%, Hf
0.1%, Y 0.02%, remaining is Ni.
This example has TCP phases to be formed after being free of 1100 DEG C of timeliness 200h of Ru elements nickel-base high-temperature single crystal alloy containing Ir, such as Figure 14.
There are TCP phases to be formed after 1100 DEG C of Long-term Aging 500h of the alloy and after 1100 DEG C of timeliness 1000h, such as Figure 15-16.
Comparative example 3：
Contain platinum family element Ru in this example alloying component, but be free of Ir elements, specific alloying component is following (wt.%)：
Cr 5.5%, Co 10%, Mo 1.5%, W 6%, Al 6%, Ta 8.5%, Re 5.5%, Ru 3%, Hf
0.1%, Y 0.02%, remaining is Ni.
This example has TCP phases to be formed after being free of 1100 DEG C of timeliness 200h of Ir elements nickel-base high-temperature single crystal alloy containing Ru, such as Figure 17
It is shown.There are TCP phases to be formed after 1100 DEG C of Long-term Aging 500h of the alloy and after 1100 DEG C of timeliness 1000h, such as Figure 18-19.
Claims (7)
1. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that a kind of platinum family element is strengthened, it is characterised in that：By weight hundred
Divide content meter, the alloy composition as follows：
Cr 2~6%, Co 7~14%, Mo 1~3%, W 4.5~6.5%, Al 4.7~6.7%, Ta 5~9%, Re
5.4~7%, Ru 2~5%, Ir 1~3%, Hf 0~0.2%, Y 0~0.2%, remaining is Ni.
2. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element according to claim 1 is strengthened, special
Sign is：Weight percentage, the alloy composition are as follows：
Cr 2.5~5.5%, Co 8~12%, Mo 1.5~3%, W 5~6%, Al 5~6.5%, Ta 5~8.5%, Re
5~7%, Ru 2~5%, Ir 1~3%, Hf 0~0.2%, Y 0~0.2%, remaining is Ni.
3. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element according to claim 1 or 2 is strengthened,
It is characterized in that：In the nickel-base high-temperature single crystal alloy, total content >=4wt.% of Ru and Ir.
4. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element according to claim 1 or 2 is strengthened,
It is characterized in that：In the nickel-base high-temperature single crystal alloy, the ingredient of impurity meets claimed below：
O≤0.003wt.%, N≤0.002wt.%, S≤0.003wt.%, P≤0.002wt.%, Si≤0.2wt.%, Pb≤
0.0003wt.%, Bi≤0.00005wt.%.
5. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element according to claim 1 or 2 is strengthened,
It is characterized in that：The preparation process of the nickel-base high-temperature single crystal alloy is：Alloy raw material, vacuum are weighed first, in accordance with required alloying component
Master alloy is poured into a mould in induction melting furnace after melting；Using apparatus for directional solidification remelting master alloy, using spiral crystal separation method or seed crystal
It is legal to being frozen into monocrystal rod；It is heat-treated using vacuum or common Muffle furnace using preceding.
6. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element according to claim 5 is strengthened, special
Sign is：When preparing nickel-base high-temperature single crystal alloy on directional solidification furnace, the temperature gradient for orienting stove is 40 DEG C/cm~80
DEG C/cm, pouring temperature is 1480~1550 DEG C, and mould shell temperature is consistent with pouring temperature, is 3~8mm/ in growth rate
Within the scope of min, monocrystalline coupon is prepared.
7. the high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element according to claim 5 is strengthened, special
Sign is：The heat treating regime of the nickel-base high-temperature single crystal alloy carries out in accordance with the following steps：
(1) solution treatment：6~10 hours are kept the temperature at 1310~1320 DEG C；It is small to then raise temperature to 1320-1345 DEG C of heat preservation 8~16
When, then it is air-cooled to room temperature；
(2) high-temperature aging is handled：2~6 hours are kept the temperature at 1100~1160 DEG C, is then air-cooled to room temperature；
(3) low temperature aging is handled：16~26 hours are kept the temperature at 850~900 DEG C, is then air-cooled to room temperature.
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| CN109628799A (en) * | 2019-01-23 | 2019-04-16 | 深圳市万泽中南研究院有限公司 | Monocrystal nickel-base high-temperature alloy and aero-turbine component |
| CN111074332B (en) * | 2019-12-31 | 2022-08-02 | 东莞材料基因高等理工研究院 | Heat treatment method for rapidly eliminating microsegregation in single crystal high-temperature alloy |
| CN113512669A (en) * | 2020-04-09 | 2021-10-19 | 辽宁红银金属有限公司 | Hydrogen embrittlement resistant high-temperature alloy and preparation method thereof |
| CN111961920B (en) * | 2020-08-09 | 2022-02-11 | 浙江大学 | Nickel-based single crystal superalloy with high temperature bearing capacity and preparation method thereof |
| CN114164356B (en) * | 2020-09-10 | 2023-03-14 | 中国科学院金属研究所 | High-strength nickel-based single crystal superalloy |
| CN113564717B (en) * | 2021-07-27 | 2022-08-12 | 北航（四川）西部国际创新港科技有限公司 | Ni 3 Al-based single crystal high-temperature alloy and preparation method thereof |
| CN115044804B (en) * | 2022-05-18 | 2023-02-03 | 苏州高晶新材料科技有限公司 | Nickel-based directional columnar crystal superalloy and preparation method and application thereof |
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Denomination of invention: A platinum group element strengthened nickel base single crystal superalloy with high thermal stability and high strength Effective date of registration: 20220225 Granted publication date: 20180921 Pledgee: Fushun Bank Co.,Ltd. Development Zone sub branch Pledgor: Liaoning Hongyin Metal Co.,Ltd. Registration number: Y2022210000012 |