CN105506387B - A kind of nickel-base high-temperature single crystal alloy of high specific creep intensity and its preparation method and application - Google Patents
A kind of nickel-base high-temperature single crystal alloy of high specific creep intensity and its preparation method and application Download PDFInfo
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- CN105506387B CN105506387B CN201510966509.6A CN201510966509A CN105506387B CN 105506387 B CN105506387 B CN 105506387B CN 201510966509 A CN201510966509 A CN 201510966509A CN 105506387 B CN105506387 B CN 105506387B
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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%
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- 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
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- 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
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- 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
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- 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
- C30B33/00—After-treatment of single crystals or homogeneous polycrystalline material with defined structure
- C30B33/02—Heat treatment
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Abstract
Application the invention discloses a kind of nickel-base high-temperature single crystal alloy of high specific creep intensity and preparation method thereof and in aero engine turbine blades are prepared, its composition characteristics (wt%) are as follows：Cr 7~9.5%；W 0.4~1.0%；Ta 0.5~3.5%；Mo 4.0~7.0%；Al 5.5~7.0%；Ti 0.4~2.0%；Nb 0.9~2.0%；Co 2.0~5.0%；Hf 0.05 0.15%；Ni surpluses.The alloy of the present invention remelting, directional solidification, is thermally treated resulting in by vacuum induction melting.It is of the invention that there is preferable croop property compared with other existing second generation nickel-base high-temperature single crystal alloys, but alloy density and cost substantially reduce, and available for preparing in aero engine turbine blades, can meet the design needs of modern high thrust-weight ratio aero-engine.
Description
Technical field
The present invention relates to nickel-base high-temperature single crystal alloy and its preparation field, and in particular to a kind of high specific creep intensity it is Ni-based
Application of the single crystal super alloy and preparation method thereof in aero engine turbine blades are prepared.
Background technology
As aero-engine is to the development in high thrust-weight ratio direction, inlet temperature and internal pressure are continuous before engine turbine
Improve, it is desirable to which the engine thermal such as turbo blade, guide vane end pieces have higher temperature capability, therefore, these hot junction portions
Part must be prepared with high temperature alloy.
Nickel (Ni) based alloy can using a variety of reinforcing means improve alloy temperature capability, such as using a variety of high melting-points/
Precious metal element (tungsten (W), molybdenum (Mo), cobalt (Co), chromium (Cr), rhenium (Re), ruthenium (Ru) and vanadium (V) etc.) solution strengthening；Utilize aluminium
(Al), the orderly A of the formation such as titanium (Ti), niobium (Nb) and tantalum (Ta) coherence3Type B intermetallic compound γ ' (Ni3(Al, Ti)) mutually make
For precipitated phase, obtain alloy effective precipitation hardened；It is strong using elements such as boron (B), zirconium (Zr), magnesium (Mg) and rare earths (RE)
Change crystal boundary；Improve that alloy is anti-oxidant and corrosion resistance using elements such as chromium (Cr), silicon (Si).Therefore, nickel (Ni) based alloy is
Preferable, the most widely used class alloy of combination property in high temperature alloy.
Single crystal nickel-base superalloy further obviates the crystal boundary yielding in high temperature, thus with more preferable high temperature resistance
Creep, fatigue behaviour and temperature capability, are widely used in manufacture aero engine turbine blades, guide vane etc., in the modern times
Also applied in industry gas turbine, current domestic second generation single crystal nickel-base superalloy DD406 has been successfully applied to certain state
Produce new aero-engine.The composition for the single crystal nickel-base superalloy developed is analyzed as can be seen that rhenium (Re) and your other gold
The continuous improvement of category element addition is a most prominent feature in advanced single crystal super alloy evolution：First generation monocrystalline
Alloy is free of Re；The Re of 2nd generation and the 3rd generation respectively containing 3wt% and 6wt%.However, Re be metallic element rare on the earth it
First, expensive, according to measuring and calculating, the single crystal nickel-base superalloy cost of material containing 3wt%Re will improve more than 70%.Other Re's
Density reaches 20.53g/cm3, causing the density of current second generation high temperature single crystal alloy, universal larger (such as CMSX-4 is 8.7g/
cm3, PWA1484 be 8.95g/cm3, Rene N5 be 8.7g/cm3, TMS-82+ be 8.93g/cm3, DD406 be 8.78g/cm3)。
On the one hand the increase of alloy density increases leaf weight, is unfavorable for improving the thrust-weight ratio of engine；On the other hand whirlpool will be increased
Centrifugal force of the impeller blade when high speed rotates, need to research and develop new high intensity turbine disk material to support turbo blade, this is further
Increase the difficulty of research and development high thrust-weight ratio engine.Therefore, consider in terms of cost of alloy and application prospect, obtain with comprehensive
Close low-density, the single crystal super alloy of low cost of superior performance, it has also become the high thrust-weight ratio propeller for turboprop of R ＆ D design a new generation
The urgent need and research and development focus of machine.
The content of the invention
It is an object of the invention to solve, the density that second generation single crystal nickel-base superalloy in the prior art is present is big, cost
High the problems such as, there is provided a kind of low-density, low cost, the high-performance with preferable heat endurance and higher specific creep intensity are low close
Spend Ni based single-crystal high-temperature alloys and preparation method thereof and the application in aero engine turbine blades are prepared.
A kind of nickel-base high-temperature single crystal alloy of high specific creep intensity, by the element structure of following weight percentage (wt.%)
Into：
Preferably, the nickel-base high-temperature single crystal alloy of described high specific creep intensity, by following weight percentage
(wt.%) element is constituted：
The alloy of the present invention is free of Re, and under the combination of the specific components of certain content, alloy of the invention is in room temperature 25
DEG C when density be not more than 8.2g/cm3, and specific creep life-span P meets 380 >=P=(temperature+273) under 140MPa stress
(log creep lives+20) × 105/ density >=370 (unit of temperature for DEG C, the unit of creep life is hour, the list of density
Position is g/cm3), in the case where ensureing low cost and low-density, temperature capability is better than second generation Ni based single-crystal high-temperature alloys
DD406 and CMSX-4, specific creep life-span P are more than 370, and second generation Ni based single-crystal high-temperature alloys are generally less than 350 at present, can expire
The design of the modern high thrust-weight ratio aero-engine of foot needs.
The operation principle of the present invention is as follows：
Although the composition design of alloy of the present invention does not contain the Re elements that the second generation single crystal superalloy is usually contained, still
By changing precipitation phase γ ' constituent component, the precipitation of the solution strengthening and γ ' for playing alloying element comprehensive as far as possible
Invigoration effect, makes the alloy without Re elements maintain relatively low alloy while second generation single crystal alloy performance level is reached
Density.
The selection of alloys producing and its composition range in the present invention is presented below：
The main solution strengthening matrix γ phases of W, it is a small amount of to participate in forming γ ' precipitated phases, alloy initial melting temperature can be improved；W is being closed
There is relatively low diffusion velocity in gold, the diffusion velocity of other solid solution elements in the alloy can be reduced, the high temperature of alloy is effectively improved
Creep strength；But it is excessive to add the TCP phases that W easily separates out rich W；Meanwhile, W proportion is larger；Consider W effect, it is added
Measure as 0.5~1.0wt%；
Mo can be solid-solution in γ phases and available for regulation γ/γ ' lattice equations, γ/γ ' boundaries is formed the crystalline substance of densification
Lattice misfit dislocation, while γ ' coarsenings are slowed down, improves the creep rupture strength of alloy；But Mo under high-temperature oxidation environment easily
Volatile oxide is generated, hardly possible forms fine and close oxide-film, there is Na2SO4Environment in, easily cause acid frit reaction,
Produce serious heat erosion；But richness W, Mo TCP phases are easily separated out in addition W, Mo high temperature alloy at the same time；So Mo addition
Amount can not be too high, and control is advisable in 4.0~6.5wt%.
Ta is γ ' and γ phase formation elements, in addition to the heat resistance for effectively improving alloy, while can also increase alloy
Antioxygenic property, decay resistance and casting character；But Ta is too high, eutectic content is high in alloy, becomes the heat treatment of alloy
Obtain extremely difficult, and the density of increase alloy；With reference to these factors present invention control Ta contents in 0.5~3.5wt.%.
Co elements are distributed mainly in γ matrixes in nickel base superalloy, reduce the stacking fault energy of matrix, main function bag
Include solution strengthening, increase γ ' phase amounts, the plasticity and hot-working character that improve alloy and improve structure stability, creep rupture strength
And creep resistance；But in view of the factor of cost of alloy, present invention control Co contents are in 2.0~5.0wt.%.
Cr can improve anti-oxidant, the corrosion resistance of alloy together with Al, Ta etc.；But due in single crystal super alloy simultaneously
Containing a variety of refractory elements such as higher W, Mo, Ta, adding substantial amounts of Cr then increases the tendency to form σ phases and the equal TCP phases of μ,
Low-alloyed structure stability and creep rupture strength drop；Therefore, Cr of the present invention addition is 7.5~9.5wt.%
Al and Ti elements can form γ ' aging precipitation phases by appropriate heat treatment in Ni base γ phases, and alloy is played
Precipitation enhancement, improves the elevated temperature strength and enduring quality of alloy；In addition, Al can be formed during alloy high-temp military service
Oxide film, improves that alloy is anti-oxidant and corrosion resistance；Ti is favourable to the corrosion resistance of alloy；Single crystal alloy γ '
Content is up to 65wt%, it is desirable to which Al and Ti contents are respectively that 5.5~7.0wt% and 0.5~2.0wt% are advisable.
Nb is also γ ' phase formation elements, and addition Nb can improve the creep strength and anti-oxidant corrosion resistance of alloy；But add
Plus excessive Nb is easily formed σ phases, is unfavorable for the high temperature microstructure stability and intensity of alloy；In addition, Nb is excessively added to alloy
Oxidation and hot corrosion resistance it is harmful.Therefore, Nb of the present invention addition is 1.0~2.0wt%.
Hf can with Cr and Al-rise improve alloy high temperature corrosion-resisting performance；Meanwhile, Hf addition can also improve alloy
Processing performance and mechanical property；But low-alloyed initial melting temperature can drop in excess Hf addition, it is possible to drop low-alloyed high temperature strong
Degree；Therefore, by the control of Hf contents in 0.05-0.15wt.%, most preferably 1.0%.
Further preferably, the nickel-base high-temperature single crystal alloy of described high specific creep intensity, by following weight percentage
(wt.%) element is constituted：
A kind of preparation method of the nickel-base high-temperature single crystal alloy of high specific creep intensity, comprises the following steps:
The first step:Vacuum induction melting alloy will be put into according to designed composition proportion raw material, mother is prepared in casting
Alloy bar material；
Second step:By foundry alloy bar by apparatus for directional solidification remelting, spiral crystal selector or young crystallization orientation are recycled
It is frozen into monocrystalline coupon；
3rd step:Monocrystalline coupon is carried out in the range of 1270-1370 DEG C to the solution treatment of 2-6 hours, then carried out empty
It is cold；Then the high-temperature aging carried out in the range of 920-1020 DEG C 3-8 hours is handled, and then carries out air cooling；Then in 830-910
The low temperature aging carried out in the range of DEG C 18-28 hours is handled, and is then carried out air cooling processing, is finally obtained the nickel of high specific creep intensity
Based single-crystal high-temperature alloy.
The present invention, in vacuum induction melting, first pours into the satisfactory female conjunction of chemical analysis using above-mentioned alloying element
Gold, then again by apparatus for directional solidification remelting, using spiral crystal selector or young crystallization directional solidification into monocrystalline coupon.Performance is surveyed
Monocrystalline coupon need to carry out tissue adjustment through suitable heat treating regime before examination.
In second step, Bu Liziman (Bridgeman) directional solidification technique, i.e., young crystallization orientation can be passed through using seed-grain method
Solidification uses Bu Liziman directional solidification techniques, is 50-200 DEG C/cm in thermograde, withdrawing rate is 1-5mm/min scopes
Inside prepare monocrystalline coupon.
In 3rd step, monocrystalline coupon is carried out in the range of 1310-1330 DEG C to the solution treatment of 3-5 hours, then carried out
Air cooling；Then the high-temperature aging carried out in the range of 960-980 DEG C 4-6 hours is handled, and then carries out air cooling；Then in 870-
The low temperature aging carried out in the range of 890 DEG C 20-24 hours is handled, and is then carried out air cooling processing, is finally obtained high specific creep intensity
Nickel-base high-temperature single crystal alloy.
In addition, showing alloy of the present invention at high temperature than known second generation high temperature using following parameter type P in the present invention
The excellent specific creep intensity of single crystal alloy：380 >=P=(temperature+273) (log creep lives+20) × 105/ density >=370, this
In " temperature " refer to alloy creep test temperature (DEG C), creep life is hour.
The nickel-base high-temperature single crystal alloy of the high specific creep intensity of the present invention is a kind of low-density, low cost, with compared with Gao Cheng
The Ni based single-crystal high-temperature alloys of the high specific creep intensity of warm ability, can be used as the hot junctions such as high thrust-weight ratio aero engine turbine blades
The alloy material of part.
Compared with prior art, its remarkable advantage is the present invention:
(1) alloy of the invention is free of Re, and under the combination of the specific components of certain content, alloy of the invention is in room temperature
Density at 25 DEG C is not more than 8.2g/cm3, and specific creep life-span P meets 380 >=P=(temperature+273) under 140MPa stress
(log creep lives+20) × 105/ density >=370 (temperature for DEG C, creep life is hour), are ensureing low cost and low-density
In the case of, temperature capability is more than 370 better than the second generation Ni based single-crystal high-temperature alloy DD406 and CMSX-4, specific creep life-span P,
And second generation Ni based single-crystal high-temperature alloys are generally less than 350 at present, the design need of modern high thrust-weight ratio aero-engine can be met
Will.Alloy of the present invention is free of noble element Re, thus cost and density less than typical second generation single crystal alloy CMSX-4 both at home and abroad,
PWA1484, Rene N5, TMS-82+ and DD406 etc.；
(2) phase stability of alloy of the present invention is good, and Long-term Aging does not generate harmful phase；
(3) alloy of the present invention is that 140MPa has excellent specific creep intensity in stress.
Because the present invention can provide the Crystal Nickel-based Superalloy of specific creep excellent strength, the turbine prepared using this alloy
Blade can realize lightweight and high durable temperature simultaneously.
Brief description of the drawings
Fig. 1 is the density and specific creep intensity (P parameters) of nickel base superalloy prepared by the embodiment of the present invention and comparative example
Graph of a relation.
Embodiment
Below in conjunction with embodiment, the present invention is described in further detail, but does not therefore limit the present invention.
Embodiment 1~4 and comparative example
The chemical composition of the embodiment of the present invention and known Ni based single-crystal high-temperature alloys comparative example is shown in Table 1.
Specific preparation method:
The first step:Using vacuum induction melting alloy, the satisfactory various Ni bases high temperature of chemical composition are first poured into
Foundry alloy bar is prepared in alloy foundry alloy, casting；
Second step:By foundry alloy bar by apparatus for directional solidification remelting, then Bu Liziman passed through using seed-grain method
(Bridgeman) directional solidification technique, thermograde be 100 DEG C/cm, withdrawing rate be 3mm/min under prepare monocrystalline coupon；
3rd step:Monocrystalline coupon prepared by embodiment 1~4 is carried out in the range of 1310-1330 DEG C at the solid solution of 4 hours
Reason, then carries out air cooling；Then the high-temperature aging carried out in the range of 960-980 DEG C 5 hours is handled, and then carries out air cooling；So
The low temperature aging carried out afterwards in the range of 870-890 DEG C 22 hours is handled, and is then carried out air cooling processing, is finally obtained high specific creep
The nickel-base high-temperature single crystal alloy of intensity.Microstructure observation after heat treatment shows only there are γ/γ ' duplex structures in alloy,
Have no TCP phases.
Monocrystalline coupon prepared by comparative example is heat-treated according to its disclosed heat treating regime, finally obtains corresponding nickel
Based high-temperature alloy.
To the alloy measurement density after heat treatment and creep test is carried out under 140MPa, obtained creep life is utilized
The conventional Miller parameter of Larsen one (L.M.P, Larson-Miller parameter):L.M.P=(temperature+273) (log creeps
Life-span+20) × 103(temperature for DEG C, creep life is hour) is evaluated and calculates specific creep life parameter P=
100L.M.P/ density.The density of embodiment and comparative example, creep evaluation result L.M.P and parameter P are included in table 1.Density and P
The relation of parameter is as shown in Figure 1.
Shown in table 1 and Fig. 1, the nickel base single crystal phase of embodiment and the super conjunction of nickel-based monocrystal known to reference example
Metallographic is than with relatively low density, preferable creep strength (high L.M.P. values) and higher specific creep intensity (P parameters).
Chemical composition, density, croop property and the P parameter lists of the embodiment of the present invention of table 1 and comparative example
Note：" remaining " implication on the column of Ni contents one is " surplus " in table, and reference example is comparative example.
Claims (8)
1. a kind of nickel-base high-temperature single crystal alloy of high specific creep intensity, it is characterised in that by the element of following weight percentage
Constitute：
The nickel-base high-temperature single crystal alloy of described high specific creep intensity, its density in 25 DEG C of room temperature is not more than 8.2g/cm3, and
Specific creep life-span P meets 380 >=P=(temperature+273) (log creep lives+20) × 10 under 140MPa stress5/ density >=
370, wherein, the unit of temperature for DEG C, the unit of creep life is hour, and the unit of density is g/cm3。
2. the nickel-base high-temperature single crystal alloy of high specific creep intensity according to claim 1, it is characterised in that by following weight
The element of percentage composition is constituted：
3. the nickel-base high-temperature single crystal alloy of high specific creep intensity according to claim 2, it is characterised in that by following weight
The element of percentage composition is constituted：
4. the preparation method of the nickel-base high-temperature single crystal alloy of the high specific creep intensity according to any one of claims 1 to 3, its
It is characterised by, comprises the following steps：
The first step:Vacuum induction melting alloy will be put into according to designed composition proportion raw material, foundry alloy is prepared in casting
Bar；
Second step:By foundry alloy bar by apparatus for directional solidification remelting, spiral crystal selector or young crystallization directional solidification are recycled
Into monocrystalline coupon；
3rd step:Monocrystalline coupon is carried out in the range of 1270-1370 DEG C to the solution treatment of 2-6 hours, air cooling is then carried out；Connect
The high-temperature aging processing carried out in the range of 920-1020 DEG C 3-8 hours, air cooling is then carried out；Then in 830-910 DEG C of model
The low temperature aging processing of interior progress 18-28 hours is enclosed, air cooling processing is then carried out, finally obtains the Ni-based list of high specific creep intensity
Brilliant high temperature alloy.
5. preparation method according to claim 4, it is characterised in that in second step, young crystallization directional solidification is used in cloth
Hereby graceful directional solidification technique.
6. preparation method according to claim 5, it is characterised in that in thermograde be 50-200 DEG C/cm, withdrawing rate
To prepare monocrystalline coupon in the range of 1-5mm/min.
7. preparation method according to claim 4, it is characterised in that in the 3rd step, by monocrystalline coupon at 1310-1330 DEG C
In the range of carry out the solution treatment of 3-5 hours, then carry out air cooling；Then the height of 4-6 hours is carried out in the range of 960-980 DEG C
Warm hardening processing, then carries out air cooling；Then the low temperature aging carried out in the range of 870-890 DEG C 20-24 hours is handled, then
Air cooling processing is carried out, the nickel-base high-temperature single crystal alloy of high specific creep intensity is finally obtained.
8. the nickel-base high-temperature single crystal alloy of the high specific creep intensity according to any one of claims 1 to 3 is preparing aviation hair
Application in motivation turbo blade.
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| CN107034388A (en) * | 2017-03-17 | 2017-08-11 | 泰州市金鹰精密铸造有限公司 | The preparation technology of nickel-base high-temperature single crystal alloy turbo blade |
| CN107805770B (en) * | 2017-10-17 | 2020-01-07 | 中国华能集团公司 | Overaging heat treatment process suitable for casting high-temperature alloy |
| CN109518015A (en) * | 2018-10-10 | 2019-03-26 | 安徽鑫国合金有限公司 | A kind of nickel chromium triangle-nisiloy compensator alloy silk synthesis technology |
| CN110484776A (en) * | 2019-09-02 | 2019-11-22 | 深圳市万泽中南研究院有限公司 | A kind of Ni-base Superalloy Powder and application method of increasing material manufacturing |
| CN111027198B (en) * | 2019-12-03 | 2022-07-19 | 西北工业大学 | Nickel-based single crystal alloy creep life prediction method considering topological close-packed phase evolution |
| CN111004944A (en) * | 2019-12-31 | 2020-04-14 | 长安大学 | High-molybdenum second-generation nickel-based single crystal superalloy and preparation method thereof |
| CN113913942A (en) * | 2021-01-13 | 2022-01-11 | 中国航发北京航空材料研究院 | Nickel-based single crystal alloy, use and heat treatment method |
| CN113265564B (en) * | 2021-05-06 | 2022-04-29 | 中国联合重型燃气轮机技术有限公司 | High-temperature alloy with good long-term stability and preparation method thereof |
| CN113444888B (en) * | 2021-06-29 | 2022-06-24 | 重庆大学 | Method for purifying magnesium melt by adopting directional solidification |
| CN113957364B (en) * | 2021-10-13 | 2022-05-10 | 浙江大学 | Thermal strain damage repair method for nickel-based single crystal alloy |
| CN115747687B (en) * | 2022-10-31 | 2024-02-20 | 浙江大学 | Heat treatment process for improving high-temperature durable service life of second-generation nickel-base single crystal superalloy |
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| GB2151659B (en) * | 1983-12-24 | 1987-03-18 | Rolls Royce | An alloy suitable for making single crystal castings |
| JPH0770679A (en) * | 1993-09-07 | 1995-03-14 | Hitachi Metals Ltd | High corrosion resistant and high strength cemented carbide, high corrosion resistant and high strength single crystal casting, gas turbine and combined cycle generating system |
| US20060011271A1 (en) * | 2002-12-06 | 2006-01-19 | Toshiharu Kobayashi | Ni-based single crystal superalloy |
| JP5467307B2 (en) * | 2008-06-26 | 2014-04-09 | 独立行政法人物質・材料研究機構 | Ni-based single crystal superalloy and alloy member obtained therefrom |
| CN103436740B (en) * | 2013-08-08 | 2015-12-09 | 南京理工大学 | A kind of without rhenium nickel-base high-temperature single crystal alloy and preparation method thereof |
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