CN108425037A - A kind of powder metallurgy superalloy and preparation method thereof - Google Patents
A kind of powder metallurgy superalloy and preparation method thereof Download PDFInfo
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- CN108425037A CN108425037A CN201810327365.3A CN201810327365A CN108425037A CN 108425037 A CN108425037 A CN 108425037A CN 201810327365 A CN201810327365 A CN 201810327365A CN 108425037 A CN108425037 A CN 108425037A
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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
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0433—Nickel- or cobalt-based alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
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Abstract
The present invention relates to a kind of powder metallurgy superalloys, belong to technical field of metal material, solve in current aerospace engine that the hot-end components such as turbine disk are harsh to high-temperature alloy material requirement and the technical issues of existing high-temperature alloy material cannot be satisfied its performance requirement.The chemical composition and its mass fraction of the powder metallurgy superalloy be：Cr 7~12%；Co 15~20%；W 2.5~3.5%；Mo 2.5~3.5%；Ta 2.2~2.8%；Nb 2.2~2.8%；Al 3.0~3.6%；Ti 2.8~3.4%；Hf 0.3~0.7%；C 0.03~0.08%；B 0.03~0.06%；Zr 0.03~0.06%, surplus Ni.The powder metallurgy superalloy has good elevated temperature strength and high temperature microstructure stability and excellent high temperature creep property and high temperature endurance performance, mainly for the preparation of hot-end components such as aero-engine turbine disks.
Description
Technical field
The present invention relates to technical field of metal material more particularly to it is a kind of applied to aero-engine turbine disk novel the
Four generation powder metallurgy superalloys and preparation method thereof.
Background technology
The turbine disk is one of hot-end component mostly important in aero-engine, high temperature microstructure of the operating condition to material
Stability, high specific strength, high damage tolerance, high croop property and thermal fatigue property, anti-oxidant and corrosion resistance etc. require ten
Divide harshness.Powder metallurgy superalloy have even tissue, without gross segregation, that crystal grain is tiny, yield strength is high, fatigue behaviour is good etc. is excellent
Therefore point becomes the preferred material for preparing the turbine disk.
The U.S. has formulated MATE plans (advanced turbogenerator investigation of materials plan) in the sixties in last century, starts to grind
Powder metallurgy superalloy processed.From the point of view of its development course：First generation alloy (being representative with Ren é 95) belongs to high-strength, and the second generation is closed
Gold belongs to damage tolerance type (using Ren é 88DT as representative), and the operating temperature of this two generations alloy is answered between 650~700 DEG C
The third generation engine for being 7~8 for thrust-weight ratio；Third generation alloy (being representative with Ren é 104) belongs to high-strength/high damage tolerance
The structure stability of type, the long-term work at 700 DEG C or so is significantly increased than the first and second generation alloy, service life raising 20~30 when hot
Times, maximum operating temperature is applied to the forth generation engine that thrust-weight ratio is 10 up to 760 DEG C or so.Thrust-weight ratio is up to
20 are grinding VAATE (the advanced turbogenerator plan that general, economy can be born) engine, the highest of high-pressure turbine disk
Operating temperature is up to 815 DEG C or higher.This is higher by 50 DEG C or more than the temperature capability of third generation alloy.Currently, the U.S. is
Develop the forth generation alloy for VAATE engines.
The development work of domestic powder metallurgy superalloy starts from 1977, currently, succeeded develop alloy have FGH95,
FGH96, FGH97 and FGH98；And above-mentioned four kinds of powder metallurgy superalloys far can not meet air equipment especially aero-engine
The requirement of the turbine disk, so, for powder metallurgy superalloy, we also need to put into more researchs, further increase powder height
The comprehensive performance of temperature alloy.
Invention content
In view of above-mentioned analysis, the present invention is intended to provide a kind of novel fourth generation powder applied to aero-engine turbine disk
Last high temperature alloy and preparation method thereof, the high-performance to meet domestic air mail equipment especially aero-engine turbine disk are wanted
It asks.
The purpose of the present invention is mainly achieved through the following technical solutions：
The present invention provides a kind of powder metallurgy superalloy, the chemical composition and its mass fraction of the alloy are：Cr 7~
12%；Co 15~20%；W 2.5~3.5%；Mo 2.5~3.5%；Ta 2.2~2.8%；Nb 2.2~2.8%；Al
3.0~3.6%；Ti 2.8~3.4%；Hf 0.3~0.7%；C 0.03~0.08%；B 0.03~0.06%；Zr 0.03
~0.06%, surplus Ni.
Wherein, Al, Ti, Nb, Ta are γ ' phase formation elements, Cr, Co, W, Mo in the novel fourth generation powder metallurgy superalloy
For solution strengthening element, C, B, Zr, Hf are boundary-strengthening element.
Preferably, the total mass fraction of Al, Ti, Nb, Ta are in powder metallurgy superalloy：10.4%≤(Al+Ti+Nb+Ta)
≤ 12.2%.
Preferably, the total mass fraction of Al, Ti are in powder metallurgy superalloy：6.0%≤(Al+Ti)≤6.5%, Al, Ti
Mass ratio be 1.00≤(Al/Ti)≤1.28.
Preferably, the total mass fraction of Nb, Ta, Hf are in powder metallurgy superalloy：5.0%≤(Nb+Ta+Hf)≤5.9%；
The mass ratio of Nb, Ta is：0.7≤(Nb/Ta)≤1.1.
Preferably, the total mass fraction of Cr, Co, W, Mo are in powder metallurgy superalloy：29.0%≤(Cr+Co+W+Mo)≤
38.5%.
Preferably, the total mass fraction of Cr, W, Mo are in powder metallurgy superalloy：(Cr+W+Mo)≤18.0%.
Preferably, the operating temperature of powder metallurgy superalloy is 815 DEG C~850 DEG C.
Preferably, the microscopic structure of powder metallurgy superalloy is mainly by γ, γ ', MC and M6C、M3B2Phase composition.
The present invention also provides a kind of preparation methods of powder metallurgy superalloy, are used to prepare above-mentioned powder metallurgy superalloy, should
Preparation method includes the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting technique
Prepare master alloy bar；
S2. use rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization that master alloy bar is made
Alloy powder.Wherein it is possible to which select plasma rotating electrode process to prepare alloy powder obtains granularity after screened, removal is mingled with
Ranging from 50 μm~150 μm of alloy powder；
S3. will meet granularity requirements alloy powder be packed into Φ 108 × 170mm low-carbon steel capsules, carry out vacuum outgas and
Soldering and sealing (for example, electron beam soldering and sealing), obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1160 DEG C~1200 DEG C, the pressure of hot isostatic pressing is 120MPa~140MPa, and the time of hot isostatic pressing is 3h~5h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1140 DEG C~1200 DEG C, and solution time is 1.0h~2.5h, and oil quenching is carried out after solid solution；The temperature of timeliness is 815 DEG C~860
DEG C, aging time is 6h~9h, and timeliness is using air-cooled.
It in the present invention, can also be combined with each other between above-mentioned each technical solution, to realize more preferred assembled schemes.This
Other feature and advantage of invention will illustrate in the following description, also, certain advantages can become from specification it is aobvious and
It is clear to, or understand through the implementation of the invention.The purpose of the present invention and other advantages can by specification, claims with
And specifically noted content is realized and is obtained in attached drawing.
Description of the drawings
Attached drawing is only used for showing the purpose of specific embodiment, and is not considered as limitation of the present invention, in entire attached drawing
In, identical reference mark indicates identical component.
Fig. 1 is the preparation technology flow chart of novel fourth generation powder metallurgy superalloy；
Fig. 2 is optical microstructure's figure of novel fourth generation powder metallurgy superalloy heat treatment state in embodiment 1；
Fig. 3 is optical microphotograph group of the novel fourth generation powder metallurgy superalloy after 850 DEG C/200h long timeliness in embodiment 1
Knit figure.
Specific implementation mode
Specifically describing the preferred embodiment of the present invention below in conjunction with the accompanying drawings, wherein attached drawing constitutes the application part, and
It is used to illustrate the principle of the present invention together with embodiments of the present invention, be not intended to limit the scope of the present invention.
On the one hand, the present invention provides a kind of novel fourth generation powder metallurgy superalloy, which is γ ' phase precipitation strength types
Ni-base P/M Superalloy, the chemical composition and its mass fraction of the alloy are：Cr 7~12%；Co 15~20%；W 2.5
~3.5%；Mo 2.5~3.5%；Ta 2.2~2.8%；Nb 2.2~2.8%；Al 3.0~3.6%；Ti 2.8~
3.4%；Hf 0.3~0.7%；C 0.03~0.08%；B 0.03~0.06%；Zr 0.03~0.06%, surplus Ni.
The main technical schemes of the present invention are by adding γ ' phase formation element Al, Ti, Nb, Ta, solution strengthening element
Cr, Co, W, Mo and boundary-strengthening element C, B, Zr, Hf realize high intensity, high damage tolerance and the senior engineer of powder metallurgy superalloy
Make temperature, while controlling Cr, W, Mo content and being inclined to the precipitation for reducing topological solid matter TCP phases, to obtain with good comprehensive
Close the composition range of performance.Specifically, Al, Ti, Nb, the Ta being added in alloy compositions can improve γ ' phases content and alloy
Change degree increases Apb Energies when dislocation cutting γ ' phases, plays precipitation enhancement；Cr, Co, W, Mo can reinforce base
Body atomic binding forces increases diffusion activation energy, plays solution strengthening effect；C, B, Zr, Hf primarily form Carbide Phases and boronation
Object phase can reduce grain boundary decision, slow down dislocation climb, play the role of intercrystalline strengthening.
Therefore, novel fourth generation powder metallurgy superalloy provided by the invention have good elevated temperature strength (at 850 DEG C, σb
Up to 950MPa or more, σ0.2Up to 800MPa or more) and high temperature microstructure stability (without apparent TCP after 850 DEG C/200h long timeliness
Mutually it is precipitated), there is high temperature creep property outstanding (ε under 815 DEG C/400MPa/50hp0.20%) and high temperature endurance performance less than
(under 815 DEG C/450MPa, creep rupture life is no less than 400h).
In conclusion forth generation novel powder high temperature alloy provided by the invention not only has good elevated temperature strength, height
Warm structure stability, and there is high temperature creep property outstanding and high temperature endurance performance, the above performance disclosure satisfy that aviation is sent out
The hot-end components such as the motivation turbine disk also accelerate China in forth generation novel powder high temperature alloy to preparing the requirement of material
The flow of research in field.
It should be noted that being analyzed in terms of intercrystalline strengthening, in order to improve the grain boundary state of alloy, it is strong to improve crystal boundary
Degree, should be added suitable boundary-strengthening element C, B, Zr and Hf.C, B because with the atomic size difference of Ni it is big due to form small solubility
Interstitial solid solution.The addition of B can reduce the solubility of C and influence the precipitation of grain boundary carbide, so considering crystal boundary carbon
When influence of the compound to heat resistance, C and B should be considered.C is conducive to come in crystal boundary precipitation chain, discontinuous carbide strong
Change crystal boundary；B then causes part alloying in crystal boundary segregation, changes grain boundary state, diffusion process of the reduction element in crystal boundary strongly
And strengthening crystal boundary, B can also inhibit grain boundary carbide or intermetallic compound to be precipitated with unfavorable sheet or born of the same parents' shape and improve crystalline substance
The intensive uneven distribution state of boundary's carbide, thus it is advantageous to heat resistance.But as excessive addition C and B, can cause carbide or
A large amount of precipitations of boride, and alloy property is not further enhanced.Zr additionally helps reduction for strengthening crystal boundary
Solidus expands temperature range between solvus, and in order to improve the temperature in use of alloy, Zr contents are not easy too much.And work as B and Zr
When being added simultaneously, it is conducive to extend low-cycle fatigue life.Hf atomic radiuses are very big, can enter γ ' mutually with γ phases, increase two-phase
Lattice constant is with reinforced alloys；The MC type carbide of stable rich Hf can be formed simultaneously, strengthens crystal boundary, improve crack Propagation
Drag；Also it can be combined to form stable HfO with O2, purify crystal boundary.Therefore control element content is：0.03%≤C≤0.08%,
0.03%≤B≤0.06%, 0.03%≤Zr≤0.06%, 0.3%≤Hf≤0.7%.
Illustratively, above-mentioned chemical composition and its mass fraction are：Cr 7~10%；Co 17~20%；W 2.5~
3.5%；Mo 2.5~3.5%；Ta 2.4~2.6%；Nb 2.2~2.5%；Al 3.0~3.6%；Ti 2.8~3.1%；
Hf 0.3~0.6%；C 0.03~0.08%；B 0.03~0.05%；Zr 0.04~0.06%, surplus Ni.
In order to further control γ ' phases content and alloying level, total matter of middle Al, Ti, Nb, Ta of powder metallurgy superalloy
Measuring score is：10.4%≤(Al+Ti+Nb+Ta)≤12.2%.The total mass fraction control of Al, Ti exist in powder metallurgy superalloy
The mass ratio of 6.0%≤(Al+Ti)≤6.5%, Al, Ti are controlled in 1.00≤(Al/Ti)≤1.28.In powder metallurgy superalloy
The control of Nb, Ta, Hf total mass fraction exists：The mass ratio of 5.0%≤(Nb+Ta+Hf)≤5.9%, Nb, Ta are 0.7≤(Nb/Ta)
≤1.1。
This is because from precipitation strength analyze, γ ' phase precipitation strength effects with the raising of its content and alloying level and
Enhancing, Al, Ti, Nb, Ta are main γ ' phases intensified elements, it is therefore desirable to control middle Al, Ti, Nb, Ta of powder metallurgy superalloy
Total mass fraction be 10.4%≤(Al+Ti+Ta+Nb)≤12.2%,.Divide for powder metallurgy superalloy according to first three
Analysis, 50%~60% is limited to by the γ ' phase content ranges of forth generation alloy.
Wherein, Al+Ti contents to γ ' phase volume fractions and be completely dissolved temperature influence it is notable, increase Al+Ti contents can
The volume fraction of γ ' phases is significantly improved, γ ' is mutually completely dissolved temperature and is increased with the increase of its volume fraction, if Al+Ti contains
It measures too low, the volume fraction of γ ' phases can not be significantly improved.Different Al/Ti, which compare tissue and performance, also Different Effects.Therefore,
The total mass fraction of Al, Ti can be controlled in 6.0%≤(Al+Ti)≤6.5%, the mass ratio of Al, Ti in powder metallurgy superalloy
It can control in 1.0≤(Al/Ti)≤1.28.
The effect of Nb is chiefly to facilitate to form more γ ' phases, and alloy γ ' is caused mutually to be completely dissolved temperature raising；Increase γ '
Reversed domain boundary (APB) energy of phase, improves the elevated temperature strength of alloy.But Nb contents can increase the notch sensitivity of alloy when excessive,
Badly damaged alloy antioxygenic property causes the fatigue crack growth rate under high temperature to increase.The atomic radius of Ta is larger, can be bright
It is aobvious to increase γ ' phase-lattice constants, it improves γ ' and mutually strengthens effect.A certain amount of Ta is added, the crack propagation that can also improve alloy is anti-
Power.Nb/Ta ratios are also an important content of high-performance powder high temperature alloy composition design, emphasize Nb/Ta than balance, can be with
Ensure to obtain excellent comprehensive performance.Therefore control γ ' phase formation element contents are：0.7%≤Nb/Ta≤1.1%.In addition,
Transformation to TCP phases can occur in Long Term Aging for MC type carbide：MC+M→M23C6+TCP.It need to ensure that high Nb, Ta contain
Amount and addition Hf are to stablize MC type carbide.Therefore the total content of control Nb+Ta+Hf elements is：5.0%≤(Nb+Ta+Hf)≤
5.9%.
In order to further control solid solution strengthening effect, the total mass fraction of Cr, Co, W, Mo in above-mentioned powder metallurgy superalloy
For：29.0%≤(Cr+Co+W+Mo)≤38.5%.The total mass fraction of Cr, W, Mo are in powder metallurgy superalloy：(Cr+Mo+W)
≤ 18.0%.
This is because being analyzed from solution strengthening, Cr, Co, W, Mo are main solution strengthening elements.Cr and Ni formation has
The limit solid solution of certain solubility, main solution strengthening γ matrixes.But low-alloyed elevated temperature strength can drop in excessive Cr, due to
The High-Temperature Strengthening effect of Cr far below the refractory elements such as W, Mo, therefore need to reduce Cr contents and increase the content of refractory element with into
One step improves the elevated temperature strength of alloy.Co helps to reduce the stacking fault energy of matrix, reduces the dissolving of Al, Ti in the base
Degree helps to improve the creep resistance of alloy to increase γ ' phase amounts in a certain range and improve γ ' phase solid solubility temperatures.
W, Mo has larger solid solubility, solid solution strengthening effect apparent in γ phases；The High temperature diffusion speed of Al, Ti, Cr can also be slowed down, increased
The diffusion activation energy for adding creep slows down the creep softening rate of high temperature alloy to reinforce interatomic binding force.Therefore, it controls
The total content of solution strengthening element processed is：29.0%≤(Cr+Co+Mo+W)≤38.5%.In addition, powder metallurgy superalloy high temperature is long
When work after, harmful to performance TCP phases are easily precipitated, common are σ phases and μ phases, Cr, W, Mo are that it primarily forms element, because
This, (Cr+W+Mo)≤18%.
In order to further increase the comprehensive performance of powder metallurgy superalloy, the microscopic structure of powder metallurgy superalloy mainly by γ,
γ ', MC and M6C、M3B2Phase composition.Wherein, the M in MC is mainly Nb, Ta, Ti, Hf element；M6M in C is mainly W, Mo member
Element, M3B2In M be mainly Cr, W, Mo element.
It is adjusted and optimizes by each component to above-mentioned powder metallurgy superalloy, novel had excellent performance can be obtained
Four generation powder metallurgy superalloys.It is worth noting that, the powder metallurgy superalloy Long-term service temperature in the present invention is 815 DEG C, in short-term
For operating temperature up to 850 DEG C, which is higher by 50 DEG C or more than the temperature capability of third generation alloy.And thrust-weight ratio is 20 to grind
VAATE (the advanced turbogenerator plan that general, economy can be born) engine, the maximum operating temperature of high-pressure turbine disk
It is up to 815 DEG C or higher.It is new to demonstrate again that the performance for the powder metallurgy superalloy material that we prepare has had reached forth generation
The standard of type powder metallurgy superalloy.
On the other hand, the present invention also provides a kind of preparation methods of powder metallurgy superalloy, and it is high to be used to prepare above-mentioned powder
Temperature alloy, the preparation method include the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting (VIM)
Technique carries out vacuum induction melting to raw material, prepares master alloy bar；
S2. use rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization that master alloy bar is made
Alloy powder.Wherein it is possible to which select plasma rotating electrode process to prepare alloy powder obtains granularity after screened, removal is mingled with
Ranging from 50 μm~150 μm of alloy powder；
S3. will meet granularity requirements alloy powder be packed into Φ 108 × 170mm low-carbon steel capsules, carry out vacuum outgas and
Soldering and sealing (for example, electron beam soldering and sealing), obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1160 DEG C~1200 DEG C, the pressure of hot isostatic pressing is 120MPa~140MPa, and the time of hot isostatic pressing is 3h~5h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1140 DEG C~1200 DEG C, and solution time is 1.0h~2.5h, and oil quenching is carried out after solid solution；The temperature of timeliness is 815 DEG C~860
DEG C, aging time is 6h~9h, and timeliness is using air-cooled.
The powder metallurgy superalloy prepared through the invention has good elevated temperature strength, high damage tolerance performance, Yi Jiyou
Different high-temerature creep and enduring quality, and can work under 815 DEG C of high temperature for a long time, reach novel fourth generation powder metallurgy
The standard of alloy.
Powder metallurgy superalloy provided by the present application is described further below by specific embodiment.
Embodiment 1
Present embodiment discloses a kind of novel fourth generation powder metallurgy superalloy, chemical composition and its mass fraction are：Cr
9.47%；Co 17.14%；W 2.98%；Mo 3.06%；Ta 2.43%；Nb 2.49%；Al 3.19%；Ti 3.02%；
Hf 0.43%；C 0.044%；B 0.031%；Zr 0.057%, surplus Ni.
The preparation method of the novel fourth generation powder metallurgy superalloy is as follows：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting technique
Prepare master alloy bar；
S2. rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization is used to prepare alloy powder.We
Selection plasma rotating electrode process prepares alloy powder, and after screened, removal is mingled with, it is 50 μm~150 μm to obtain particle size range
Alloy powder；
S3. the alloy powder for meeting granularity requirements is packed into Φ 108 × 170mm low-carbon steel capsules, carries out vacuum outgas, electricity
Beamlet soldering and sealing obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1180 DEG C, the pressure of hot isostatic pressing is 130MPa, and the time of hot isostatic pressing is 4h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1180 DEG C, solution time 1.5h, and oil quenching is carried out after solid solution；The temperature of timeliness is 850 DEG C, aging time 8h, timeliness
Using air-cooled.
Powder metallurgy superalloy prepared by embodiment and domestic existing four kinds of powder metallurgy superalloy FGH95, FGH96,
FGH97 and FGH98 carries out performance comparison, and specific test process is as follows：
Under identical preparation process condition, above-mentioned five kinds of alloys are prepared respectively, wherein Tables 1 and 2 is respectively above-mentioned five
Tensile strength contrast table of kind alloy under the conditions of room temperature and 850 DEG C, table 3 are that the high temperature creep property of above-mentioned five kinds of alloys compares
Table, table 4 are the high temperature endurance performance contrast table of above-mentioned five kinds of alloys.
There are four types of the mechanical properties contrast tables of alloy with the country for 1 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 1 | 1614 | 1145.5 |
| FGH95 | 1594.5 | 1244 |
| FGH96 | 1515.5 | 1082.5 |
| FGH97 | 1446.5 | 948.5 |
| FGH98 | 1568.5 | 1159.5 |
There are four types of 850 DEG C of tensile strength contrast tables of alloy with the country for 2 alloy of the present invention of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 1 | 1000 | 803 |
| FGH95 | 957.5 | 810 |
| FGH96 | 847.5 | 742.5 |
| FGH97 | 897.5 | 722.5 |
| FGH98 | 927.5 | 787.5 |
There are four types of the high temperature creep property contrast tables of alloy with the country for 3 the present embodiment alloy of table
| Alloy | Experimental condition | Plastic elongation |
| Embodiment 1 | 815℃/400MPa/50h | 0.120% |
| FGH95 | 815℃/400MPa/50h | 0.308% |
| FGH96 | 815℃/400MPa/50h | 1.928% |
| FGH97 | 815℃/400MPa/50h | 0.417% |
| FGH98 | 815℃/400MPa/50h | 0.169% |
There are four types of the high temperature endurance performance contrast tables of alloy with the country for 4 the present embodiment alloy of table
| Alloy | Experimental condition | Creep rupture life |
| Embodiment 1 | 815℃/450MPa | 457.4h |
| FGH95 | 815℃/450MPa | 94.5h |
| FGH96 | 815℃/450MPa | 44.7h |
| FGH97 | 815℃/450MPa | 160.4h |
| FGH98 | 815℃/450MPa | 150.5h |
It can be seen that by Tables 1 and 2, novel fourth generation powder metallurgy superalloy provided in this embodiment is drawn in room temperature and 850 DEG C
It is suitable with FGH95 and FGH98 to stretch intensity, is better than FGH96 and FGH97；As seen from Table 3,815 DEG C of the present embodiment alloy/
400MPa/50h croop properties are substantially better than FGH95, FGH96, FGH97 and FGH98；As seen from Table 4, the present embodiment alloy
815 DEG C/450MPa creep rupture lives are significantly larger than FGH95, FGH96, FGH97 and FGH98.
Fig. 2 is that the optical microstructure of powder metallurgy superalloy heat treatment state manufactured in the present embodiment schemes, and Fig. 3 passes through for alloy
Optical microstructure's figure after 850 DEG C/200h long timeliness, it can be seen that the present embodiment microstructure stability is good, through 850
DEG C/200h long timeliness after be precipitated without apparent TCP phases.
Embodiment 2
Present embodiment discloses a kind of novel fourth generation powder metallurgy superalloy, chemical constituent and content (mass fraction) point
It is not：Cr 9.27%；Co 19.86%；W 3.48%；Mo 3.02%；Ta 2.51%；Nb 2.48%；Al 3.28%；Ti
3.02%；Hf 0.47%；C 0.049%；B 0.039%；Zr 0.042%, surplus Ni.
The preparation method of the novel fourth generation powder metallurgy superalloy includes the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting technique
Prepare master alloy bar；
S2. rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization is used to prepare alloy powder.We
Selection plasma rotating electrode process prepares alloy powder, and after screened, removal is mingled with, it is 50 μm~150 μm to obtain particle size range
Alloy powder；
S3. the alloy powder for meeting granularity requirements is packed into Φ 108 × 170mm low-carbon steel capsules, carries out vacuum outgas, electricity
Beamlet soldering and sealing obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1180 DEG C, the pressure of hot isostatic pressing is 130MPa, and the time of hot isostatic pressing is 4h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1180 DEG C, solution time 1.5h, and oil quenching is carried out after solid solution；The temperature of timeliness is 850 DEG C, aging time 8h, timeliness
Using air-cooled.
The existing powder metallurgy in the country that novel fourth generation powder metallurgy superalloy prepared by embodiment 2 is prepared with embodiment 1
Alloy FGH95, FGH96, FGH97 and FGH98 carry out performance comparison, and specific test process is as follows：
Table 5 and table 6 are respectively the contrast table of tensile strength of above-mentioned five kinds of alloys under the conditions of room temperature and 850 DEG C, and table 7 is
The high temperature creep property contrast table of above-mentioned five kinds of alloys, table 8 are the high temperature endurance performance contrast table of above-mentioned five kinds of alloys.
There are four types of the mechanical properties contrast tables of alloy with the country for 5 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 2 | 1610 | 1147.5 |
| FGH95 | 1594.5 | 1244 |
| FGH96 | 1515.5 | 1082.5 |
| FGH97 | 1446.5 | 948.5 |
| FGH98 | 1568.5 | 1159.5 |
There are four types of 850 DEG C of tensile strength contrast tables of alloy with the country for 6 the present embodiment alloy of table
There are four types of the high temperature creep property contrast tables of alloy with the country for 7 the present embodiment alloy of table
| Alloy | Experimental condition | Plastic elongation |
| Embodiment 2 | 815℃/400MPa/50h | 0.102% |
| FGH95 | 815℃/400MPa/50h | 0.308% |
| FGH96 | 815℃/400MPa/50h | 1.928% |
| FGH97 | 815℃/400MPa/50h | 0.417% |
| FGH98 | 815℃/400MPa/50h | 0.169% |
There are four types of the high temperature endurance performance contrast tables of alloy with the country for 8 the present embodiment alloy of table
| Alloy | Experimental condition | Creep rupture life |
| Embodiment 2 | 815℃/450MPa | 442.7h |
| FGH95 | 815℃/450MPa | 94.5h |
| FGH96 | 815℃/450MPa | 44.7h |
| FGH97 | 815℃/450MPa | 160.4h |
| FGH98 | 815℃/450MPa | 150.5h |
The comprehensive performance of novel fourth generation powder metallurgy superalloy provided in this embodiment has apparent superiority, especially
High-temerature creep and high temperature endurance performance, under conditions of 815 DEG C/450MPa the creep rupture life of the alloy be up to 442.7 hours, far
Far more than the existing alloy of other each groups, moreover, the overstrain of the powder metallurgy superalloy is 0.102%, it is ensured that material
Comprehensive performance stability.
Embodiment 3
Present embodiment discloses a kind of novel fourth generation powder metallurgy superalloy, chemical constituent and content (mass fraction) point
It is not：Cr 7.06%；Co 18.15%；W 3.01%；Mo 3.03%；Ta 2.56%；Nb 2.48%；Al 3.28%；Ti
3.08%；Hf 0.51%；C 0.042%；B 0.038%；Zr 0.043%, surplus Ni.
The preparation method of the novel fourth generation powder metallurgy superalloy includes the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting technique
Prepare master alloy bar；
S2. rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization is used to prepare alloy powder.We
Selection plasma rotating electrode process prepares alloy powder, and after screened, removal is mingled with, it is 50 μm~150 μm to obtain particle size range
Alloy powder；
S3. the alloy powder for meeting granularity requirements is packed into Φ 108 × 170mm low-carbon steel capsules, carries out vacuum outgas, electricity
Beamlet soldering and sealing obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1180 DEG C, the pressure of hot isostatic pressing is 130MPa, and the time of hot isostatic pressing is 4h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1180 DEG C, solution time 1.5h, and oil quenching is carried out after solid solution；The temperature of timeliness is 850 DEG C, aging time 8h, timeliness
Using air-cooled.
Likewise, the existing powder height that novel fourth generation powder metallurgy superalloy prepared by embodiment 3 is prepared with embodiment 1
Temperature alloy FGH95, FGH96, FGH97 and FGH98 carry out performance comparison, and specific test process is as follows：
Wherein, table 9 and table 10 are respectively the comparison of tensile strength of above-mentioned five kinds of alloys under the conditions of room temperature and 850 DEG C
Table, table 11 are the high temperature creep property contrast table of above-mentioned five kinds of alloys, and table 12 is the high temperature endurance performance pair of above-mentioned five kinds of alloys
Compare table.
There are four types of the mechanical properties contrast tables of alloy with the country for 9 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 3 | 1605 | 1150.5 |
| FGH95 | 1594.5 | 1244 |
| FGH96 | 1515.5 | 1082.5 |
| FGH97 | 1446.5 | 948.5 |
| FGH98 | 1568.5 | 1159.5 |
There are four types of 850 DEG C of tensile strength contrast tables of alloy with the country for 10 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 3 | 996.5 | 806.5 |
| FGH95 | 957.5 | 810 |
| FGH96 | 847.5 | 742.5 |
| FGH97 | 897.5 | 722.5 |
| FGH98 | 927.5 | 787.5 |
There are four types of the high temperature creep property contrast tables of alloy with the country for 11 the present embodiment alloy of table
| Alloy | Experimental condition | Plastic elongation |
| Embodiment 3 | 815℃/400MPa/50h | 0.108% |
| FGH95 | 815℃/400MPa/50h | 0.308% |
| FGH96 | 815℃/400MPa/50h | 1.928% |
| FGH97 | 815℃/400MPa/50h | 0.417% |
| FGH98 | 815℃/400MPa/50h | 0.169% |
There are four types of the high temperature endurance performance contrast tables of alloy with the country for 12 the present embodiment alloy of table
| Alloy | Experimental condition | Creep rupture life |
| Embodiment 3 | 815℃/450MPa | 445.1h |
| FGH95 | 815℃/450MPa | 94.5h |
| FGH96 | 815℃/450MPa | 44.7h |
| FGH97 | 815℃/450MPa | 160.4h |
| FGH98 | 815℃/450MPa | 150.5h |
Can be seen that by table 9 and table 10, novel fourth generation powder metallurgy superalloy mechanical properties provided in this embodiment with
FGH95, FGH98 are suitable, and 850 DEG C of tensile strengths are better than existing alloy；As can be seen from Table 11,815 DEG C of the present embodiment alloy/
400MPa/50h croop properties are substantially better than FGH95, FGH96, FGH97 and FGH98；As seen from Table 12, the present embodiment alloy
815 DEG C/450MPa creep rupture lives be significantly larger than FGH95, FGH96, FGH97 and FGH98.
Embodiment 4
Present embodiment discloses a kind of novel fourth generation powder metallurgy superalloy, chemical constituent and content (mass fraction) point
It is not：Cr 9.25%；Co 17.54%；W 2.53%；Mo 3.45%；Ta 2.48%；Nb 2.54%；Al 3.25%；Ti
3.05%；Hf 0.68%；C 0.058%；B 0.032%；Zr 0.046%, surplus Ni.
The preparation method of the novel fourth generation powder metallurgy superalloy includes the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting technique
Prepare master alloy bar；
S2. rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization is used to prepare alloy powder.We
Selection plasma rotating electrode process prepares alloy powder, and after screened, removal is mingled with, it is 50 μm~150 μm to obtain particle size range
Alloy powder；
S3. the alloy powder for meeting granularity requirements is packed into Φ 108 × 170mm low-carbon steel capsules, carries out vacuum outgas, electricity
Beamlet soldering and sealing obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1160 DEG C, the pressure of hot isostatic pressing is 140MPa, and the time of hot isostatic pressing is 5h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1140 DEG C, solution time 2.5h, and oil quenching is carried out after solid solution；The temperature of timeliness is 860 DEG C, aging time 6h, timeliness
Using air-cooled.
Likewise, the existing powder height that novel fourth generation powder metallurgy superalloy prepared by embodiment 4 is prepared with embodiment 1
Temperature alloy FGH95, FGH96, FGH97 and FGH98 carry out performance comparison, and specific test process is as follows：
Wherein, table 13 and table 14 are respectively the comparison of tensile strength of above-mentioned five kinds of alloys under the conditions of room temperature and 850 DEG C
Table, table 15 are the high temperature creep property contrast table of above-mentioned five kinds of alloys, and table 16 is the high temperature endurance performance pair of above-mentioned five kinds of alloys
Compare table.
There are four types of the mechanical properties contrast tables of alloy with the country for 13 the present embodiment alloy of table
There are four types of 850 DEG C of tensile strength contrast tables of alloy with the country for 14 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 4 | 1010 | 809 |
| FGH95 | 957.5 | 810 |
| FGH96 | 847.5 | 742.5 |
| FGH97 | 897.5 | 722.5 |
| FGH98 | 927.5 | 787.5 |
There are four types of the high temperature creep property contrast tables of alloy with the country for 15 the present embodiment alloy of table
| Alloy | Experimental condition | Plastic elongation |
| Embodiment 4 | 815℃/400MPa/50h | 0.112% |
| FGH95 | 815℃/400MPa/50h | 0.308% |
| FGH96 | 815℃/400MPa/50h | 1.928% |
| FGH97 | 815℃/400MPa/50h | 0.417% |
| FGH98 | 815℃/400MPa/50h | 0.169% |
There are four types of the high temperature endurance performance contrast tables of alloy with the country for 16 the present embodiment alloy of table
| Alloy | Experimental condition | Creep rupture life |
| Embodiment 4 | 815℃/450MPa | 450.3h |
| FGH95 | 815℃/450MPa | 94.5h |
| FGH96 | 815℃/450MPa | 44.7h |
| FGH97 | 815℃/450MPa | 160.4h |
| FGH98 | 815℃/450MPa | 150.5h |
It can be seen that by table 13 and table 14, novel fourth generation powder metallurgy superalloy room temperature tensile properties provided in this embodiment are excellent
Gesture unobvious, 850 DEG C of tensile strengths are better than existing alloy；From table 15 and table 16 as can be seen that 815 DEG C of the present embodiment alloy/
400MPa/50h croop properties and 815 DEG C/450MPa creep rupture lives are all substantially better than FGH95, FGH96, FGH97 and FGH98.
Embodiment 5
Present embodiment discloses a kind of novel fourth generation powder metallurgy superalloy, chemical constituent and content (mass fraction) point
It is not：Cr 9.31%；Co 17.29%；W 3.04%；Mo 2.54%；Ta 2.48%；Nb 2.23%；Al 3.58%；Ti
2.81%；Hf 0.32%；C 0.032%；B 0.047%；Zr 0.044%, surplus Ni.
The preparation method of the novel fourth generation powder metallurgy superalloy includes the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, using vacuum induction melting technique
Prepare master alloy bar；
S2. rotary electrode method (for example, plasma rotating electrode process) or Powder In Argon Atomization is used to prepare alloy powder.We
Selection plasma rotating electrode process prepares alloy powder, and after screened, removal is mingled with, it is 50 μm~150 μm to obtain particle size range
Alloy powder；
S3. the alloy powder for meeting granularity requirements is packed into Φ 108 × 170mm low-carbon steel capsules, carries out vacuum outgas, electricity
Beamlet soldering and sealing obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank, specifically, the temperature of hot isostatic pressing
It it is 1200 DEG C, the pressure of hot isostatic pressing is 120MPa, and the time of hot isostatic pressing is 4h.
S5. the ingot blank after forming is heat-treated.Heat treatment process includes solid solution and timeliness, specifically, the temperature of solid solution
Degree is 1200 DEG C, solution time 1h, and oil quenching is carried out after solid solution；The temperature of timeliness is 815 DEG C, and aging time 9h, timeliness is adopted
With air-cooled.
Likewise, the existing powder height that novel fourth generation powder metallurgy superalloy prepared by embodiment 5 is prepared with embodiment 1
Temperature alloy FGH95, FGH96, FGH97 and FGH98 carry out performance comparison, and specific test process is as follows：
Wherein, table 17 and table 18 are respectively the comparison of tensile strength of above-mentioned five kinds of alloys under the conditions of room temperature and 850 DEG C
Table, table 19 are the high temperature creep property contrast table of above-mentioned five kinds of alloys, and table 20 is the high temperature endurance performance pair of above-mentioned five kinds of alloys
Compare table.
There are four types of the mechanical properties contrast tables of alloy with the country for 17 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 5 | 1612 | 1149 |
| FGH95 | 1594.5 | 1244 |
| FGH96 | 1515.5 | 1082.5 |
| FGH97 | 1446.5 | 948.5 |
| FGH98 | 1568.5 | 1159.5 |
There are four types of 850 DEG C of tensile strength contrast tables of alloy with the country for 18 the present embodiment alloy of table
| Alloy | σb/MPa | σ0.2/MPa |
| Embodiment 5 | 1035.5 | 812 |
| FGH95 | 957.5 | 810 |
| FGH96 | 847.5 | 742.5 |
| FGH97 | 897.5 | 722.5 |
| FGH98 | 927.5 | 787.5 |
There are four types of the high temperature creep property contrast tables of alloy with the country for 19 the present embodiment alloy of table
| Alloy | Experimental condition | Plastic elongation |
| Embodiment 5 | 815℃/400MPa/50h | 0.105% |
| FGH95 | 815℃/400MPa/50h | 0.308% |
| FGH96 | 815℃/400MPa/50h | 1.928% |
| FGH97 | 815℃/400MPa/50h | 0.417% |
| FGH98 | 815℃/400MPa/50h | 0.169% |
There are four types of the high temperature endurance performance contrast tables of alloy with the country for 20 the present embodiment alloy of table
| Alloy | Experimental condition | Creep rupture life |
| Embodiment 5 | 815℃/450MPa | 438.2h |
| FGH95 | 815℃/450MPa | 94.5h |
| FGH96 | 815℃/450MPa | 44.7h |
| FGH97 | 815℃/450MPa | 160.4h |
| FGH98 | 815℃/450MPa | 150.5h |
Can be seen that by table 17 and table 18, novel fourth generation powder metallurgy superalloy room temperature tensile properties provided in this embodiment with
FGH95, FGH98 compare advantage unobvious, but 850 DEG C of tensile strengths are better than existing powder metallurgy superalloy；It can from table 19 and table 20
To find out, the 815 DEG C/400MPa/50h croop properties of the present embodiment alloy and 815 DEG C/450MPa creep rupture lives are all substantially better than
Has powder metallurgy superalloy.
Novel fourth generation powder metallurgy superalloy provided by the invention is due to steady with good elevated temperature strength and high temperature microstructure
Qualitative, high temperature creep property and high temperature endurance performance outstanding can be used for manufacturing the turbine disk etc. of aero-engine of new generation
Hot-end component.Promote fast development of the China in forth generation powder metallurgy superalloy field.
The foregoing is only a preferred embodiment of the present invention, but scope of protection of the present invention is not limited thereto,
Any one skilled in the art in the technical scope disclosed by the present invention, the change or replacement that can be readily occurred in,
It should be covered by the protection scope of the present invention.
Claims (10)
1. a kind of powder metallurgy superalloy, which is characterized in that the chemical composition and its mass fraction of the alloy be：Cr 7~
12%；Co 15~20%；W 2.5~3.5%；Mo 2.5~3.5%；Ta 2.2~2.8%；Nb 2.2~2.8%；Al
3.0~3.6%；Ti 2.8~3.4%；Hf 0.3~0.7%；C 0.03~0.08%；B 0.03~0.06%；Zr 0.03
~0.06%, surplus Ni.
2. powder metallurgy superalloy according to claim 1, it is characterised in that：Middle Al, Ti of the powder metallurgy superalloy,
The total mass fraction of Nb, Ta is：10.4%≤(Al+Ti+Nb+Ta)≤12.2%.
3. powder metallurgy superalloy according to claim 2, which is characterized in that Al, Ti's is total in the powder metallurgy superalloy
Mass fraction is：6.0%≤(Al+Ti)≤6.5%；
The mass ratio of Al, Ti is：1.00≤(Al/Ti)≤1.28.
4. powder metallurgy superalloy according to claim 1, which is characterized in that Nb, Ta, Hf in the powder metallurgy superalloy
Total mass fraction is：5.0%≤(Nb+Ta+Hf)≤5.9%；
The mass ratio of Nb, Ta is：0.7≤(Nb/Ta)≤1.1.
5. powder metallurgy superalloy according to claim 1, which is characterized in that Cr, Co, W, Mo in the powder metallurgy superalloy
Total mass fraction be：29.0%≤(Cr+Co+W+Mo)≤38.5%.
6. powder metallurgy superalloy according to claim 5, which is characterized in that Cr, W, Mo in the powder metallurgy superalloy
Total mass fraction is：(Cr+W+Mo)≤18.0%.
7. according to claim 1-6 any one of them powder metallurgy superalloys, which is characterized in that the work of the powder metallurgy superalloy
It is 815 DEG C~850 DEG C to make temperature.
8. a kind of powder metallurgy superalloy preparation method, which is characterized in that be used to prepare as described in any one of claim 1 to 7
Powder metallurgy superalloy, the preparation method comprises the following steps：
S1. the chemical composition and its mass fraction preparation raw material for pressing powder metallurgy superalloy, are prepared using vacuum induction melting technique
Master alloy bar；
S2. alloy powder is made in master alloy bar；
S3. alloy powder is packed into low-carbon steel capsule, carries out vacuum outgas and soldering and sealing, obtains the alloy powder after soldering and sealing；
S4. hot isostatic pressing forming is carried out to the alloy powder after soldering and sealing, obtains ingot blank；
S5. the ingot blank after forming is heat-treated, obtains powder metallurgy superalloy.
9. powder metallurgy superalloy preparation method according to claim 8, which is characterized in that in the S2, using electric rotating
Alloy powder is made in master alloy bar by pole method, and the granularity of the alloy powder is 50 μm~150 μm.
10. powder metallurgy superalloy preparation method according to claim 8, which is characterized in that in the S4, hot isostatic pressing
Temperature is 1160 DEG C~1200 DEG C, and the pressure of hot isostatic pressing is 120MPa~140MPa, and the time of hot isostatic pressing is 3h~5h.
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| CN111378873B (en) * | 2020-04-23 | 2021-03-23 | 北京钢研高纳科技股份有限公司 | Deformed high-temperature alloy, preparation method thereof, hot-end rotating part of engine and engine |
| CN111378873A (en) * | 2020-04-23 | 2020-07-07 | 北京钢研高纳科技股份有限公司 | Deformed high-temperature alloy, preparation method thereof, hot-end rotating part of engine and engine |
| CN111579323B (en) * | 2020-05-09 | 2022-11-01 | 中国航发北京航空材料研究院 | High-throughput preparation and test method of powder superalloy inclusion sample |
| CN111579323A (en) * | 2020-05-09 | 2020-08-25 | 中国航发北京航空材料研究院 | High-throughput preparation and test method of powder superalloy inclusion sample |
| CN112326384A (en) * | 2020-10-30 | 2021-02-05 | 中国航发北京航空材料研究院 | Preparation method of standard substance for nickel-based superalloy metal content detection |
| CN112326384B (en) * | 2020-10-30 | 2024-01-19 | 中国航发北京航空材料研究院 | Preparation method of standard substance for detecting oxygen content of nickel-based superalloy |
| CN113186431A (en) * | 2021-05-06 | 2021-07-30 | 哈尔滨工业大学（深圳） | Nickel-based high-temperature alloy powder suitable for powder metallurgy and preparation method thereof |
| CN115652147A (en) * | 2022-12-29 | 2023-01-31 | 北京钢研高纳科技股份有限公司 | Powder high-temperature alloy and preparation method and application thereof |
| CN115679157A (en) * | 2022-12-29 | 2023-02-03 | 北京钢研高纳科技股份有限公司 | Nickel-based high-temperature alloy, preparation method thereof and structural member |
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