CN103866392A - Low rhenium and nickel-based single crystal high-temperature alloy and preparation method thereof - Google Patents
Low rhenium and nickel-based single crystal high-temperature alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses low rhenium and nickel-based single crystal high-temperature alloy and a preparation method thereof. The alloy comprises the following raw materials by mass percent: 6.75-7.25% of Cr, 7.25-7.75% of Co, 1.3-1.7% of Mo, 5.8-6.2% of W, 5.8-6.2% of Ta, 0.85-1.15% of Re, 5.9-6.1% of Al, 1.3-1.7% of Ti, 0.12-0.18% of Hf, 0.04-0.06% of C, 0.003-0.005% of B, 0.010-0.020% of Y, and the balance of nickel. The method comprises the following preparation steps: smelting master alloy by using a vacuum induction furnace; preparing a master alloy rod by gravity casting; preparing a single-crystal test rod by adopting a seed crystal method through a Bridgeman directional solidification technology; carrying out thermal treatment on single crystal high-temperature alloy. The alloy disclosed by the invention is high in incipient melting temperature, wide in melting temperature range, small in solidification interval, low in alloy density, high in strength, good in oxidation resistance, good in phase stability and low in cost; a harmful phase is not easy to generate in long-term aging.
Description
Technical field
The present invention relates to a kind of nickel-base high-temperature single crystal alloy and technology of preparing thereof, a kind of low rhenium, high-performance nickel-base high-temperature single crystal alloy and preparation method are provided especially, belong to superalloy preparation field.
Background technology
At present, the inlet temperature of aircraft engine is up to 1400, and DEG C traditional iron-based and cobalt base superalloy can not meet the demands, in the urgent need to selecting the alloy with bearing high temperature ability more as the material of turbine blade.Nickel-base high-temperature single crystal alloy has outstanding high temperature and creep resistance and fatigue capability, demonstrates outstanding anti-oxidant and erosion resistance simultaneously, becomes the main selection of turbine blade.Between nearly 30 years of nickel base superalloy development, successively developed 5 generation nickel-base high-temperature single crystal alloy.The continuous increase of the refractory elements such as alloy interior Re, W, Mo, Ta, make the warm ability of holding of alloy and high-temperature behavior obtain great lifting, but the while has also brought structure stability reduction, alloy density is large, high in cost of production is not enough.Therefore, a large amount of interpolations of refractory element, the especially interpolation of Re element, caused widely and paid close attention to the impact of microtexture stability in superalloy cost and long service process etc., becomes the important factor of restriction nickel-base high-temperature single crystal alloy development.
Current, domestic and international application is 2nd generation nickel-base high-temperature single crystal alloy (as Ren é N5, PWA1484, CMSX-4 etc.) comparatively widely, in a particularly key issue in single crystal high temperature nickel base alloy containing rhenium of 2nd generation single crystal alloy, at high temperature strongly impel separating out of TCP phase (as σ, μ or p phase), sharply worsened the performance of nickel-base high-temperature single crystal alloy.In addition, it is estimated, 2nd generation single crystal high temperature nickel base alloy containing rhenium adds after the Re of 3.0wt%, and the cost of alloy has improved approximately 70%, has greatly reduced the competitiveness of product in market.For this reason, GE company of the U.S. has developed a series of low rhenium nickel base single crystal super alloys (patent No.: WO2009032578A1) to reduce cost of alloy and to improve structure stability, over-all properties reaches the 2nd generation monocrystalline Ren é N5 of rhenium-containing 3.0wt%, but rhenium content is only 1.5wt%, and its density is 8.6g/cm
3.The stress suffered due to military service process interalloy is directly proportional to its density, and creep speed exists corresponding relation with stress
therefore density is less, and alloy creep speed is slower, and work-ing life is longer, and especially as aero engine turbine blades material, the reduction of density is significant for promoting engine thrust-weight ratio.Therefore,, for further promoting aircraft engine serviceability, the control of alloy density is also an important directions of Composition Design.
Summary of the invention
The object of the present invention is to provide a kind of low rhenium nickel base single crystal super alloy and preparation method thereof, the high-temperature turbine working-blade material that creep strength is high for requiring, high-temperature duration life is long.
A kind of low rhenium nickel base single crystal super alloy, by mass percentage, alloying constituent is as follows: 6.5-7.5%Cr, 7.0-7.5%Co, 1.1-1.9%Mo, 5.5-6.5%W, 5.5-6.5%Ta, 0.75-1.25%Re, 5.8-6.2%Al, 1.1-1.9%Ti, 0.1-0.2%Hf, 0.02-0.08%C, 0.002-0.006%B, 0.010-0.020%Y, surplus is Ni.
Preferred version: a kind of low rhenium nickel base single crystal super alloy, by mass percentage, alloying constituent is as follows: 6.75-7.25%Cr, 7.25-7.75%Co, 1.3-1.7%Mo, 5.75-6.25%W, 5.8-6.2%Ta, 0.85-1.15%Re, 5.9-6.1%Al, 1.3-1.7%Ti, 0.12-0.18%Hf, 0.04-0.06%C, 0.003-0.005%B, 0.013-0.017%Y, surplus is Ni.
A method of preparing above-mentioned low rhenium nickel base single crystal super alloy, comprises the following steps:
The first step: adopt vacuum induction melting mother alloy, prepare mother alloy casting rod by gravitational casting;
Second step: adopt seed crystal method to prepare monocrystalline coupon by Bridgeman directional solidification technique;
The 3rd step: single crystal super alloy thermal treatment.
Wherein, the mother alloy monitor system described in the first step is 20-25Kw, and smelting time is that 3-5 divides.
Single crystal preparation technique described in second step is that thermograde is 200-300K/cm, and withdrawing rate is 10-100 μ m/s.
Thermal treatment described in the 3rd step comprises solution treatment, high-temperature aging processing and low temperature aging processing, and wherein solid solution treatment process temperature is 1300-1310, and DEG C time is 2-4 hour, and the type of cooling is air cooling; High-temperature aging treatment temp is 1080-1100, and DEG C time is 2-5 hour, and the type of cooling is air cooling; Low temperature aging treatment temp is 870-900, and DEG C time is 16-24 hour, and the type of cooling is air cooling.
Alloy designs principle of the present invention: integrated use vacant electron site theory and d-electron theory, primary design nickel-base high-temperature single crystal alloy composition, calculate its salient features evaluation index, and make comparisons, analyze with typical 1st generation, Performance Evaluating Indexes that 2nd generation nickel-base high-temperature single crystal alloy is corresponding.By dominating to improve alloy high-temp performance with Second Phase Precipitation strengthening, with the content of refractory element, noble element, high-density element in its reduction alloy.Concrete grammar: microstructure stability electron vacancy number N
vweigh with alloying element d molecular orbital(MO) average level Mdt value is comprehensive, intensity is weighed by covalent linkage average bonding strength Bot value between alloying element, γ for use temperature ' phase solid solubility temperature T
γ ' solvusweigh, over-all properties is used composition performance prediction parameter P value to evaluate. concrete appraisement system: ensureing, under the stable prerequisite of alloy structure, to there is higher Mdt, Bot, T
γ ' solvus, P value, and lower density.The stability threshold value that forms σ phase is N
v<2.49, the stability threshold value N of formation Laves phase
v<2.30.
Compared with prior art, its remarkable advantage is in the present invention: (1) alloy initial melting temperature of the present invention is high, temperature of fusion wide ranges, and freezing range is little.(2) alloy density of the present invention is low, and intensity is high, and antioxidant property is good.(3) phase stability of alloy of the present invention is good, and Long-term Aging is difficult for generating harmful phase.(4) cost of alloy of the present invention is low.
Brief description of the drawings
Fig. 1 is to be low rhenium nickel base single crystal super alloy preparation flow figure of the present invention.
Embodiment
Below in conjunction with accompanying drawing, the present invention is described in further detail.
Low rhenium nickel base single crystal super alloy preparation technology of the present invention is shown in Fig. 1.
(1) design of alloy
Design of alloy adopts formula (1)-(6) to calculate.
1. alloy electron vacancy number calculates suc as formula shown in (1), in formula: m
ifor the molar fraction of i constituent element; (N
v)
ifor the average electron vacancy number of i constituent element.
2. d-electron theory is calculated suc as formula shown in (2), formula (3), in formula: Ci is the atomic fraction of i constituent element; Mdi is the d molecular orbital energy level of i constituent element;
for average d molecular orbital energy level; Boi is the parameter of covalent bonds intensity between element;
for average Boi value.
3. each element to the experimental formula of γ ' phase solid solubility temperature and Effects of Density rule suc as formula shown in (4), formula (5).
T
γ′solvus(℃)=1299.315-2.415wt.%Co-6.362wt.%Cr-2.224wt.%Mo+3.987wt.%W+0.985wt.%Re+2.424wt.%Ru-2.603wt.%Al-4.943wt.%Ti+3.624wt.%Ta (4)
d(g·cm
-3)=8.29604-0.00435wt.%Co-0.0164wt.%Cr+0.01295wt.%Mo+0.06274wt.%W+0.0593wt.%Re+0.01811wt.%Ru-0.06593wt.%Al-0.0236wt.%Ti+0.05441wt.%Ta (5)
4. P value employing formula (6) is calculated.
P=-200Cr+80Mo-20Mo
2-250Ti
2-50(Ti×Ta)+15Nb+200W-14W
2+30Ta-1.5Ta
2+2.5Co+1200Al-100Al
2+100Re+1000Hf-2000Hf
2+700Hf
3-2000V-500C-15000B-500Zr (6)
Low rhenium nickel base superalloy of the present invention, by mass percentage, alloying constituent is as follows: 6.5-7.5%Cr, 7.0-7.5%Co, 1.1-1.9%Mo, 5.5-6.5%W, 5.5-6.5%Ta, 0.75-1.25%Re, 5.8-6.2%Al, 1.1-1.9%Ti, 0.1-0.2%Hf, 0.02-0.08%C, 0.002-0.006%B, 0.010-0.020%Y, surplus is Ni.Composition: 6.75-7.25%Cr preferably, 7.25-7.75%Co, 1.3-1.7%Mo, 5.75-6.25%W, 5.8-6.2%Ta, 0.85-1.15%Re, 5.9-6.1%Al, 1.3-1.7%Ti, 0.12-0.18%Hf, 0.04-0.06%C, 0.003-0.005%B, 0.013-0.017%Y, surplus is Ni.
(2) mother alloy melting
Mass percent between the different-alloy element obtaining according to (1) Composition Design, adopts high pure metal constituent element to configure required alloy.Under high vacuum condition, adopt water jacketed copper crucible vacuum induction suspended smelting mother alloy, monitor system is 20-25Kw, smelting time is that 3-5 divides.
(3) mother alloy casting rod preparation
Adopt non-consumable arc furnace by after mother alloy remelting, prepare mother alloy casting rod by copper mold gravitational casting, its shape and size can design the inner chamber of copper mold as required.
(4) single crystal preparation
Monocrystalline sample of the present invention adopts seed crystal method or crystal separation method to prepare by Bridgeman directional solidification technique.Concrete preparation method is as follows: adopt mechanical pump and molecular pump to be evacuated to 3 × 10
-3mPa; Respond to heating element heating by high purity graphite, after alloy melting, by W-Re thermocouple measurement alloy melt temperature, at 1520-1580 DEG C, be incubated after 10-20 minute; Adopt silicon controlled rectifier to realize withdrawing rate stepless adjustable within the scope of 10-100 μ m/s, prepare monocrystalline sample.
(5) single crystal super alloy thermal treatment
Adopt following technique to heat-treat: air cooling+870-900 DEG C/16-24h/ of air cooling+1080-1100 DEG C/2-4h/ of 1300-1310 DEG C/2-4h/ air cooling.
Embodiment 1
(1) design of alloy
Low rhenium nickel base superalloy of the present invention, by mass percentage, alloying constituent is as follows: 7.0%Cr, 7.5%Co, 1.5%Mo, 6.0%W, 6.0%Ta, 1.0%Re, 6.0%Al, 1.5%Ti, 0.15%Hf, 0.05%C, 0.004%B, 0.015%Y, Ni surplus.Calculation result and as shown in table 1 with typical 1st generation, 2nd generation nickel-base high-temperature single crystal alloy performance prediction parameter.
The typical 1st generation of table 1,2nd generation nickel-base high-temperature single crystal alloy and the prediction of design alloy Specifeca tion speeification
(2) mother alloy melting
Mass percent between the different-alloy element obtaining according to (1) Composition Design, adopts high pure metal constituent element to configure required alloy.Under high vacuum condition, adopt water jacketed copper crucible vacuum induction suspended smelting mother alloy, monitor system is 22.5Kw, smelting time is 4 points.
(3) mother alloy casting rod preparation
Adopt non-consumable arc furnace by after mother alloy remelting, prepare mother alloy casting rod by copper mold gravitational casting, be of a size of
(4) single crystal preparation
Monocrystalline sample of the present invention adopts seed crystal method to prepare by Bridgeman directional solidification technique.Concrete preparation method is as follows: adopt mechanical pump and molecular pump to be evacuated to 3 × 10
-3mPa; Respond to heating element heating by high purity graphite, after alloy melting, by W-Re thermocouple measurement alloy melt temperature, at 1550 DEG C, be incubated after 15 minutes; Adopt the withdrawing rate of 45 μ m/s to prepare monocrystalline sample.
(5) single crystal super alloy thermal treatment
Adopt following technique to heat-treat: 1305 DEG C/3h/ air cooling+1090 DEG C/4h/ air cooling+885 DEG C/20h/ air cooling.
Embodiment 2
(1) design of alloy
Low rhenium nickel base superalloy of the present invention, by mass percentage, alloying constituent is as follows: 6.75%Cr, 7.25%Co, 1.3%Mo, 5.75%W, 5.8%Ta, 0.85%Re, 5.9%Al, 1.3%Ti, 0.12%Hf, 0.04%C, 0.003%B, 0.013%Y, Ni surplus.
(2) mother alloy melting
Mass percent between the different-alloy element obtaining according to (1) Composition Design, adopts high pure metal constituent element to configure required alloy.Under high vacuum condition, adopt water jacketed copper crucible vacuum induction suspended smelting mother alloy, monitor system is 20Kw, smelting time is 5 points.
(3) mother alloy casting rod preparation
Adopt non-consumable arc furnace by after mother alloy remelting, prepare mother alloy casting rod by copper mold gravitational casting, be of a size of
(4) single crystal preparation
Monocrystalline sample of the present invention adopts seed crystal method to prepare by Bridgeman directional solidification technique.Concrete preparation method is as follows: adopt mechanical pump and molecular pump to be evacuated to 3 × 10
-3mPa; Respond to heating element heating by high purity graphite, after alloy melting, by W-Re thermocouple measurement alloy melt temperature, at 1520 DEG C, be incubated after 20 minutes; What adopt 10 μ m/s withdrawing rates prepares monocrystalline sample.
(5) single crystal super alloy thermal treatment
Adopt following technique to heat-treat: 1300 DEG C/4h/ air cooling+1080 DEG C/5h/ air cooling+870 DEG C/24h/ air cooling.
Embodiment 3
(1) design of alloy
Low rhenium nickel base superalloy of the present invention, by mass percentage, alloying constituent is as follows: 7.25%Cr, 7.75%Co, 1.7%Mo, 6.25%W, 6.2%Ta, 1.15%Re, 6.1%Al, 1.7%Ti, 0.18%Hf, 0.06%C, 0.005%B, 0.017%Y, Ni surplus.
(2) mother alloy melting
Mass percent between the different-alloy element obtaining according to (1) Composition Design, adopts high pure metal constituent element to configure required alloy.Under high vacuum condition, adopt water jacketed copper crucible vacuum induction suspended smelting mother alloy, monitor system is 25Kw, smelting time is 3 points.
(3) mother alloy casting rod preparation
Adopt non-consumable arc furnace by after mother alloy remelting, prepare mother alloy casting rod by copper mold gravitational casting, be of a size of
(4) single crystal preparation
Monocrystalline sample of the present invention adopts seed crystal method to prepare by Bridgeman directional solidification technique.Concrete preparation method is as follows: adopt mechanical pump and molecular pump to be evacuated to 3 × 10
-3mPa; Respond to heating element heating by high purity graphite, after alloy melting, by W-Re thermocouple measurement alloy melt temperature, at 1580 DEG C, be incubated after 10 minutes; Adopt the withdrawing rate of 100 μ m/s to prepare monocrystalline sample.
(5) single crystal super alloy thermal treatment
Adopt following technique to heat-treat: 1310 DEG C/2h/ air cooling+1100 DEG C/4h/ air cooling+/ 900 DEG C/16h/ air cooling.
Embodiment 4
Low rhenium nickel base superalloy of the present invention, by mass percentage, alloying constituent is as follows: 6.5%Cr, 7.0%Co, 1.1%Mo, 5.5%W, 5.5%Ta, 5.8%Al, 1.1%Ti, 0.10%Hf, 0.02%C, 0.002%B, 0.010%Y, Ni surplus.Adopt the method identical with embodiment 2 to prepare low rhenium nickel base single crystal super alloy.
Embodiment 5
Low rhenium nickel base superalloy of the present invention, by mass percentage, alloying constituent is as follows: 7.5%Cr, 7.5%Co, 1.9%Mo, 6.5%W, 6.5%Ta, 6.4%Al, 1.9%Ti, 0.20%Hf, 0.08%C, 0.006%B, 0.020%Y, Ni surplus.Adopt the method identical with embodiment 3 to prepare low rhenium nickel base single crystal super alloy.
Claims (10)
1. a low rhenium nickel base single crystal super alloy, is characterized in that by mass percentage, alloying constituent is as follows: 6.5-7.5%Cr, 7.0-7.5%Co, 1.1-1.9%Mo, 5.5-6.5%W, 5.5-6.5%Ta, 0.75-1.25%Re, 5.8-6.2%Al, 1.1-1.9%Ti, 0.1-0.2%Hf, 0.02-0.08%C, 0.002-0.006%B, 0.010-0.020%Y, surplus is Ni.
2. low rhenium nickel base single crystal super alloy according to claim 1, is characterized in that by mass percentage, alloying constituent is as follows: 6.75-7.25%Cr, 7.25-7.75%Co, 1.3-1.7%Mo, 5.75-6.25%W, 5.8-6.2%Ta, 0.85-1.15%Re, 5.9-6.1%Al, 1.3-1.7%Ti, 0.12-0.18%Hf, 0.04-0.06%C, 0.003-0.005%B, 0.013-0.017%Y, surplus is Ni.
3. low rhenium nickel base single crystal super alloy according to claim 1, is characterized in that described alloy adopts following steps preparation:
The first step: adopt vacuum induction melting mother alloy, prepare mother alloy casting rod by gravitational casting;
Second step: adopt seed crystal method to prepare monocrystalline coupon by Bridgeman directional solidification technique;
The 3rd step: single crystal super alloy thermal treatment.
4. low rhenium nickel base single crystal super alloy according to claim 3, is characterized in that the mother alloy monitor system described in the first step is 20-25Kw, and smelting time is 3-5 minute.
5. low rhenium nickel base single crystal super alloy according to claim 3, is characterized in that the single crystal preparation technique described in second step is that thermograde is 200-300K/cm, and withdrawing rate is 10-100 μ m/s.
6. low rhenium nickel base single crystal super alloy according to claim 3, it is characterized in that the thermal treatment described in the 3rd step comprises solution treatment, high-temperature aging processing and low temperature aging processing, wherein solid solution treatment process temperature is 1300-1310, and DEG C time is 2-4 hour, and the type of cooling is air cooling; High-temperature aging treatment temp is 1080-1100, and DEG C time is 2-5 hour, and the type of cooling is air cooling; Low temperature aging treatment temp is 870-900, and DEG C time is 16-24 hour, and the type of cooling is air cooling.
7. a preparation method for low rhenium nickel base single crystal super alloy, is characterized in that comprising the following steps:
The first step: adopt vacuum induction melting mother alloy, prepare mother alloy casting rod by gravitational casting;
Second step: adopt seed crystal method to prepare monocrystalline coupon by Bridgeman directional solidification technique;
The 3rd step: single crystal super alloy thermal treatment.
8. the preparation method of low rhenium nickel base single crystal super alloy according to claim 7, is characterized in that the mother alloy monitor system described in the first step is 20-25Kw, and smelting time is 3-5 minute; By mass percentage, alloying constituent is as follows: 6.5-7.5%Cr, 7.0-7.5%Co, 1.1-1.9%Mo, 5.5-6.5%W, 5.5-6.5%Ta, 0.75-1.25%Re, 5.8-6.2%Al, 1.1-1.9%Ti, 0.1-0.2%Hf, 0.02-0.08%C, 0.002-0.006%B, 0.010-0.020%Y, surplus is Ni.
9. the preparation method of low rhenium nickel base single crystal super alloy according to claim 7, is characterized in that the single crystal preparation technique described in second step is that thermograde is 200-300K/cm, and withdrawing rate is 10-100 μ m/s.
10. the preparation method of low rhenium nickel base single crystal super alloy according to claim 7, it is characterized in that the thermal treatment described in the 3rd step comprises solution treatment, high-temperature aging processing and low temperature aging processing, wherein solid solution treatment process temperature is 1300-1310, DEG C time is 2-4 hour, and the type of cooling is air cooling; High-temperature aging treatment temp is 1080-1100, and DEG C time is 2-5 hour, and the type of cooling is air cooling; Low temperature aging treatment temp is 870-900, and DEG C time is 16-24 hour, and the type of cooling is air cooling.
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Cited By (10)
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| CN104975248A (en) * | 2015-06-30 | 2015-10-14 | 西北工业大学 | Solution treatment method of third generation nickel-base single crystal high temperature alloy |
| CN105420554A (en) * | 2015-12-29 | 2016-03-23 | 钢铁研究总院 | Heat corrosion resistant directionally-solidified nickel-based high temperature alloy and preparation method thereof |
| CN106239036A (en) * | 2016-07-28 | 2016-12-21 | 中国科学院金属研究所 | A kind of preparation technology of sheet porous structural single crystal super alloy part |
| CN107805770A (en) * | 2017-10-17 | 2018-03-16 | 中国华能集团公司 | A kind of overaging Technology for Heating Processing suitable for cast superalloy |
| CN110396623A (en) * | 2018-04-25 | 2019-11-01 | 中国科学院金属研究所 | A kind of high-temperature protection coating material suitable for monocrystal nickel-base high-temperature alloy blade |
| CN111235434A (en) * | 2020-03-02 | 2020-06-05 | 北京钢研高纳科技股份有限公司 | Preparation method of nickel-based deformed superalloy wheel disc forging used at high temperature |
| CN112877781A (en) * | 2021-01-13 | 2021-06-01 | 中国航发北京航空材料研究院 | Nickel-based single crystal alloy, method for producing same, use thereof and heat treatment method |
| CN112981187A (en) * | 2021-04-25 | 2021-06-18 | 中国航发北京航空材料研究院 | Modified nickel-based single crystal superalloy, modification method for medium-temperature endurance performance of nickel-based single crystal superalloy and application of modified nickel-based single crystal superalloy |
| 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 |
| CN115572850A (en) * | 2022-10-27 | 2023-01-06 | 惠州市惠阳协力精密铸造有限公司 | High-temperature alloy casting and preparation method thereof |
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| CN104975248A (en) * | 2015-06-30 | 2015-10-14 | 西北工业大学 | Solution treatment method of third generation nickel-base single crystal high temperature alloy |
| CN104975248B (en) * | 2015-06-30 | 2017-01-25 | 西北工业大学 | Solution treatment method of third generation nickel-base single crystal high temperature alloy |
| CN105420554B (en) * | 2015-12-29 | 2017-05-17 | 钢铁研究总院 | Heat corrosion resistant directionally-solidified nickel-based high temperature alloy and preparation method thereof |
| CN105420554A (en) * | 2015-12-29 | 2016-03-23 | 钢铁研究总院 | Heat corrosion resistant directionally-solidified nickel-based high temperature alloy and preparation method thereof |
| CN106239036B (en) * | 2016-07-28 | 2018-07-03 | 中国科学院金属研究所 | A kind of preparation process of sheet porous structural single crystal super alloy part |
| CN106239036A (en) * | 2016-07-28 | 2016-12-21 | 中国科学院金属研究所 | A kind of preparation technology of sheet porous structural single crystal super alloy part |
| CN107805770A (en) * | 2017-10-17 | 2018-03-16 | 中国华能集团公司 | A kind of overaging Technology for Heating Processing suitable for cast superalloy |
| 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 |
| CN110396623A (en) * | 2018-04-25 | 2019-11-01 | 中国科学院金属研究所 | A kind of high-temperature protection coating material suitable for monocrystal nickel-base high-temperature alloy blade |
| CN110396623B (en) * | 2018-04-25 | 2021-09-17 | 中国科学院金属研究所 | High-temperature protective coating material suitable for single crystal nickel-based high-temperature alloy blade |
| CN111235434A (en) * | 2020-03-02 | 2020-06-05 | 北京钢研高纳科技股份有限公司 | Preparation method of nickel-based deformed superalloy wheel disc forging used at high temperature |
| 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 |
| CN112877781A (en) * | 2021-01-13 | 2021-06-01 | 中国航发北京航空材料研究院 | Nickel-based single crystal alloy, method for producing same, use thereof and heat treatment method |
| CN112981187A (en) * | 2021-04-25 | 2021-06-18 | 中国航发北京航空材料研究院 | Modified nickel-based single crystal superalloy, modification method for medium-temperature endurance performance of nickel-based single crystal superalloy and application of modified nickel-based single crystal superalloy |
| CN115572850A (en) * | 2022-10-27 | 2023-01-06 | 惠州市惠阳协力精密铸造有限公司 | High-temperature alloy casting and preparation method thereof |
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