CN115011886B - Precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy and preparation method thereof - Google Patents
Precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy which comprises the following elements in percentage by mass: 1.5 to 3.5 percent of Al; 1.2 to 2.8 percent of Ti; 24 to 30 percent of Ni; 13 to 16 percent of Cr; mo is less than or equal to 2.0 percent; mn is less than or equal to 1.0 percent; 0.02 to 0.2 percent of C; b is less than or equal to 0.05 percent; si is less than or equal to 1.0 percent; the balance being Fe. The invention also discloses a preparation method of the precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy. The invention reasonably regulates and controls the contents of Ni, al and Ti elements and ensures that the alloy has high volume fraction of Ni during service 3 The (Al, ti) precipitated phase exists, and good high-temperature mechanical property is obtained; through component design, an alumina oxide layer with slow growth rate and good thermal stability is formed on the surface of the alloy when the alloy is in service at high temperature, and the oxidation resistance is excellent; the mechanical property and the oxidation resistance of the alloy are obviously superior to those of precipitation hardening type iron-based high-temperature alloy GH2132 (Chinese grade) or IncoloyA-286 (American grade) widely applied to the industry at present, and meanwhile, the material cost is similar to that of IncoloyA-286/GH2132, so that the alloy has a very wide application prospect.
Description
Technical Field
The invention belongs to the technical field of high-temperature alloys, and particularly relates to a precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy and a preparation method thereof.
Background
The coal-fired thermal power generating unit provides more than 70% of electricity in China, but the thermal power generating unit has low average generating efficiency and high energy consumption and is a main emission source of sulfur dioxide, nitride NOx, carbon dioxide and mercury. Improving the steam temperature and pressure of the thermal power generating unit is an important way for improving the power generation efficiency and reducing the emission of greenhouse gases. The ultra supercritical (A-USC) coal-fired power generation technology capable of operating at the temperature of more than 650 ℃ is actively developed in all countries in the world. However, the 650 ℃ ultra-supercritical power generation technology has high requirements on high-temperature alloy materials, and the materials are required to have excellent comprehensive properties, including: high-temperature mechanical property, toughness, oxidation resistance and the like, and the austenitic heat-resistant steel widely used in the coal-fired thermal power generating unit at present can not meet the requirements far away. Although materials with stronger high-temperature mechanical property and oxidation resistance, such as nickel-based high-temperature alloy, can meet the requirements, the cost of raw materials is expensive. The development of the novel iron-based high-temperature alloy with good high-temperature mechanical property, good oxidation resistance and low raw material cost has important social and economic benefits.
The means for improving the high-temperature mechanical properties of the alloy include solid solution strengthening, precipitation strengthening, grain boundary strengthening and the like, and the precipitation strengthening is one of the most important means for improving the high-temperature mechanical properties of the alloy. If stable at high temperatures in iron-based superalloys with L1 2 Structural Ni 3 The (Al, ti) phase can obviously improve the high-temperature mechanical property of the iron-based high-temperature alloy. However, the iron-based high-temperature alloy of precipitation strengthening type usually contains refractory metal elements such as Ta, nb, V, etc., and the addition of these expensive refractory elements increases the cost of the alloy. Therefore, on the basis of reducing or not containing the content of expensive metal elements, the excellent high-temperature mechanical property of the alloy is maintained, and the design difficulty of the iron-based high-temperature alloy is difficult.
In addition, the iron-based heat-resistant alloy widely used at present mainly depends on the protection of a chromium oxide oxidation layer in service. The chromium oxide layer thickens quickly, and unstable chromium oxyhydroxide is easily formed in an environment containing steam, so that the oxidation is accelerated. The aluminum oxide film has slow growth rate and good thermal stability, and can provide enough protection for the alloy in high-temperature use.
In conclusion, through the design of alloy components, the research and development of the alloy containing a large amount of Ni are successful 3 The low-cost iron-based high-temperature alloy (Al and Ti) precipitation strengthening phase, which has the forming capability of an alumina protective layer and does not contain expensive metal elements such as Ta, nb and V (the cost of alloy raw materials is listed in table 1), has great significance in the fields such as the current coal-fired thermal power field and the like, and has wide application prospect.
Disclosure of Invention
In order to overcome the disadvantages of the prior art, the invention provides a Ni-rich alloy 3 The precipitation strengthening iron-based high-temperature alloy has the precipitation strengthening phase (Al, ti), has the capability of forming an alumina protective layer, does not contain expensive metal elements such as Ta, nb, V and the like, and has high strength, strong oxidation resistance and low cost.
The technical scheme adopted by the invention for solving the technical problem is as follows: the precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy comprises the following elements in percentage by mass:
further, the content of Al is 2.5-3.2%.
Further, the content of Ti is 1.8-2.5%.
Further, the content of Ni is 25 to 29%.
Further, the alloy matrix is austenite, ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, and the volume fraction of the (Al, ti) strengthening phase is not less than 40%.
Furthermore, a compact alumina oxide film protective layer is formed on the surface of the alloy at the temperature of below 800 ℃.
L1 is precipitated in the iron-based superalloy of the present invention 2 Structural Ni 3 The (Al, ti) nano precipitated phase has an average size of about 30 nm and a volume fraction of not less than 40%, and is uniformly dispersed in austenite with a face-centered cubic structure (FCC) and isThe main factor of alloy strengthening. When the Al and Ti contents are high, ni is precipitated 2 The AlTi phase has a certain strengthening effect on the low-temperature mechanical property of the alloy, but coarsening at high temperature can cause the high-temperature mechanical property of the alloy to be reduced. Therefore, in order to ensure that the alloy has excellent high-temperature mechanical properties, the content of the Al element should not exceed 3.5 percent, and the content of the Ti element should not exceed 2.5 percent.
The iron-based high-temperature alloy does not contain expensive metal elements such as Ta, nb, V and the like, has low raw material cost which is similar to that of the iron-based high-temperature alloy IncoloyA-286 (American mark) or GH2132 (Chinese mark), and has low alloy density which is only 7.5g/cm 3 . The mechanical property of the alloy is improved by about 20 percent compared with the IncoloyA-286/GH2132 alloy in the temperature range of 650 to 700 ℃, and the oxidation weight gain of the alloy in air at 750 ℃ for 480 hours is less than 2.5g/m 2 The alloy is only 1/4-1/14 of IncoloyA-286/GH2132 alloy.
The invention also discloses a preparation method of the precipitation-strengthened high-strength antioxidant iron-based high-temperature alloy, which comprises the following steps of:
respectively weighing raw materials of each element according to the raw material proportion, melting and uniformly mixing the raw materials in a protective atmosphere, and casting into an alloy ingot;
homogenizing at 1100-1250 deg.c for not less than 4 hr, water quenching or air cooling, and cold and hot processing;
carrying out recrystallization annealing on the processed alloy at 900-1200 ℃ for 0.5-2 hours, and then carrying out water quenching or air cooling;
and carrying out aging treatment at the temperature range of 650-800 ℃ to obtain the alloy finished product.
The invention reasonably regulates and controls the contents of Ni, al and Ti elements, and ensures that the alloy has high volume fraction of Ni in service 3 The (Al, ti) precipitated phase exists, and good high-temperature mechanical property is obtained. Through component design, an alumina oxide layer with low growth rate and good thermal stability is formed on the surface of the alloy when the alloy is in service at high temperature, and the oxidation resistance is excellent. The mechanical property and the oxidation resistance of the alloy are very excellent, and the alloy is obviously superior to the precipitation hardening type iron-based high-temperature alloy GH2132 (China brand) or Incol widely applied to the industry at presentThe material cost of the IncoloyA-286 (American trademark) is similar to that of the IncoloyA-286/GH2132, and the IncoloyA-286/GH2132 has a very wide application prospect.
Drawings
FIG. 1 is a structural view of a microstructure of an iron-based superalloy prepared in example 1 of the present invention after aging treatment, wherein: (a) Low power BSE pattern, equiaxial crystal structure of the alloy and grain size of 2-10 micron; (b) High power SEM image, ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, the average diameter is about 25 nanometers, and the volume fraction is not less than 40%.
Fig. 2 is a cross-sectional shape and an element distribution diagram of the iron-based superalloy prepared in example 1 of the present invention after being oxidized at 750 ℃ for 480 hours, wherein the oxide scale is mainly alumina.
Fig. 3 is a cross-sectional profile and an element distribution diagram of the iron-based superalloy prepared in comparative example 1 of the present invention after being oxidized at 750 ℃ for 480 hours, wherein the oxide scale is mainly chromium oxide.
FIG. 4 is a graph comparing the yield stress versus temperature curves of the iron-based superalloys prepared in examples 1-4 of the present invention and comparative examples 1-2.
Detailed Description
In order to make the technical solutions of the present invention better understood, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
The raw materials are prepared from metal materials with the purity of more than or equal to 99.5 percent according to the following alloy components (mass percentage).
Ni: 24-30%, cr:13 to 16%, mo: less than or equal to 2 percent, al:1.5 to 3.5%, ti:1.8 to 2.5%, mn: less than or equal to 1.0 percent, C:0.02 to 0.2%, B: less than or equal to 0.05 percent, si: less than or equal to 1.0 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, and melting in a protective atmosphereMelting and mixing uniformly, and casting into an alloy ingot; secondly, homogenizing at 1100 ℃ -1250 ℃ for not less than 4 hours, then carrying out water quenching or air cooling, and carrying out cold and hot processing; then, the processed alloy is subjected to recrystallization annealing at 900-1200 ℃ for 0.5-2 hours and then water quenching or air cooling is carried out; finally, carrying out aging treatment at the temperature of 650-800 ℃ to obtain the alloy finished product. The alloy matrix is austenite, ni 3 The (Al, ti) strengthening phase is uniformly dispersed and distributed in the crystal, the volume fraction is not less than 40%, and a compact alumina oxide film protective layer can be formed on the surface when the alloy is used at the temperature of below 800 ℃. The alloy has excellent high-temperature mechanical property and oxidation resistance, and the yield strength sigma of the alloy is 680 DEG C 0.2 Above 630MPa and an oxidative weight gain of less than 2.5g/m in air at 750 ℃ over 480h 2 。
Example 1
The method comprises the steps of preparing a raw material by using a metal material with the purity of more than or equal to 99.5% according to the following alloy components (in percentage by mass).
Ni:26%, cr:15%, mo:1.5%, al:3.0%, ti:2.35%, mn:1.0%, C:0.08%, B:0.005%, si:0.5 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, smelting and uniformly mixing in a protective atmosphere, and casting the melt into an alloy ingot; secondly, homogenizing for 8 hours at 1225 ℃ and water quenching, then cold rolling the homogenized alloy ingot, homogenizing for 1 hour at 1225 ℃ after the deformation amount is about 50%, and then cold rolling to the total deformation amount of about 85%; then, carrying out recrystallization annealing on the alloy after cold rolling at 1000 ℃ for 1 hour, and then carrying out water quenching; finally, water quenching is carried out after 24 hours of aging treatment at the temperature of 700 ℃. The alloy matrix finally obtained is austenite, ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, the volume fraction is not less than 40%, and the alloy contains carbide and trace Ni 2 An AlTi phase.
FIG. 1 is a structural view of the microstructure of example 1 after aging treatment, and it can be seen that the alloy obtained has an average grain size of about 2 to 10 μm, carbides and a trace amount of Ni 2 The AlTi phase is uniformly distributed; ni 3 The (Al, ti) strengthening phase is uniformly dispersed and distributed in the crystal and is uniformly straightThe diameter is about 25 nm, and the volume fraction is not less than 40%.
FIG. 2 is the cross-sectional morphology and elemental distribution plot of example 1 after 480 hours of oxidation at 750 deg.C, which shows that a dense alumina oxide film protective layer with a thickness less than 400nm is formed on the alloy surface at high temperature. The mechanical properties and oxidation resistance of the alloy are shown in Table 2, and the yield strength sigma at 680 ℃ is 0.2 Above 650MPa, significantly above comparative examples 1, 2; the oxidation weight gain in air at 750 ℃ for 480h is less than 2.0g/m 2 This is only 1/5 of comparative example 1.
Example 2
The method comprises the steps of preparing a raw material by using a metal material with the purity of more than or equal to 99.5% according to the following alloy components (in percentage by mass).
Ni:26%, cr:15%, mo:1.5%, al:2.8%, ti:2.35%, mn:1.0%, C:0.08%, B:0.005%, si:0.5 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, smelting and uniformly mixing in a protective atmosphere, and casting the melt into an alloy ingot; secondly, homogenizing for 8 hours at 1225 ℃ and water quenching, then cold rolling the homogenized alloy ingot, homogenizing for 1 hour at 1225 ℃ after the deformation amount is about 50%, and then cold rolling to the total deformation amount of about 85%; then, carrying out recrystallization annealing on the alloy after cold rolling at 1000 ℃ for 1 hour, and then carrying out water quenching; finally, water quenching is carried out after 24 hours of aging treatment at the temperature of 700 ℃. The alloy matrix finally obtained is austenite, the average grain size of the alloy is about 2-10 mu m, ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, the volume fraction is not less than 40%, and the carbide is uniformly distributed. The mechanical properties and oxidation resistance of the alloy are shown in Table 2, and the yield strength sigma at 680 ℃ is 0.2 Above 660MPa, significantly above comparative examples 1, 2; an oxidative weight gain of less than 2.5g/m over 480h in air at 750 DEG C 2 (ii) a It is only 1/4 of comparative example 1.
Example 3
A metal material with the purity of more than or equal to 99.5 percent is adopted, and raw materials are prepared according to the following alloy components (in percentage by mass).
Ni:26%, cr:15%, mo:1.5%, al:3.2%, ti:2.35%, mn:1.0%, C:0.08%, B:0.005%, si:0.5 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, smelting and uniformly mixing in a protective atmosphere, and casting the melt into an alloy ingot; secondly, homogenizing for 8 hours at 1225 ℃ and water quenching, then cold rolling the homogenized alloy ingot, homogenizing for 1 hour at 1225 ℃ after the deformation amount is about 50%, and then cold rolling to the total deformation amount of about 85%; then, carrying out recrystallization annealing on the cold-rolled alloy at 1000 ℃ for 1 hour, and then carrying out water quenching; finally, water quenching is carried out after 24 hours of aging treatment at the temperature of 700 ℃. The alloy matrix finally obtained is austenite, the average grain size of the alloy is about 2-10 mu m, and Ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, the volume fraction is not less than 40%, and simultaneously, the carbide and a small amount of Ni are added 2 The AlTi phase is uniformly distributed in the alloy. The mechanical properties and oxidation resistance of the alloy are shown in Table 2, and the yield strength sigma at 680 ℃ is 0.2 Above 650MPa; the oxidation weight gain in air at 750 ℃ for 480h is less than 2.0g/m 2 This is only 1/7 of comparative example 1.
Example 4
The method comprises the steps of preparing raw materials according to the following alloy components (in percentage by mass) by using metal materials with the purity of more than or equal to 99.5%.
Ni:26%, cr:15%, mo:1.5%, al:3.5%, ti:2.35%, mn:1.0%, C:0.08%, B:0.005%, si:0.5 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, smelting in a protective atmosphere, uniformly mixing, and casting the melt into an alloy ingot; secondly, homogenizing for 8 hours at 1225 ℃ and water quenching, then cold rolling the homogenized alloy ingot, homogenizing for 1 hour at 1225 ℃ after the deformation amount is about 50%, and then cold rolling to the total deformation amount of about 85%; then, carrying out recrystallization annealing on the alloy after cold rolling at 1000 ℃ for 1 hour, and then carrying out water quenching; finally, water quenching is carried out after 24 hours of aging treatment at the temperature of 700 ℃. The alloy matrix finally obtained is austenite, the average grain size of the alloy is about 2-10 mu m, and Ni 3 The (Al, ti) strengthening phase is uniformly dispersed and distributed in the crystal, and the volume fraction thereofNot less than 40%, and carbide and a large amount of Ni 2 The AlTi phase is uniformly distributed in the alloy. The mechanical property and the oxidation resistance of the alloy are shown in table 2, and the yield strength sigma of the alloy is at 680 DEG C 0.2 Above 630MPa, significantly above comparative examples 1, 2; the oxidation weight gain in air at 750 ℃ for 480h is less than 1g/m 2 This is only 1/14 of comparative example 1.
Comparative example 1IncoloyA-286 (U.S. designation) or GH2132 (Chinese designation) alloy
The method comprises the steps of preparing raw materials according to the following alloy components (in percentage by mass) by using metal materials with the purity of more than or equal to 99.5%.
Ni:26%, cr:15%, mo:1.5%, al:0.35%, ti:2.35%, mn:1.0%, C:0.08%, B:0.005%, si:0.5 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, smelting in a protective atmosphere, uniformly mixing, and casting the melt into an alloy ingot; secondly, homogenizing for 8 hours at 1225 ℃ and carrying out water quenching, then carrying out cold rolling on the homogenized alloy ingot, homogenizing for 1 hour at 1225 ℃ after the deformation amount is about 50%, and then carrying out cold rolling until the total deformation amount is about 85%; then, carrying out recrystallization annealing on the alloy after cold rolling at 1000 ℃ for 1 hour, and then carrying out water quenching; finally, water quenching is carried out after 24 hours of aging treatment at the temperature of 700 ℃. The alloy matrix finally obtained is austenite, the average grain size of the alloy is about 2-10 mu m, and a small amount of Ni is contained 3 And (Al, ti) strengthening phase (volume fraction is not more than 20%). The mechanical properties of the alloy are shown in Table 2, and the yield strength sigma at 680 DEG C 0.2 Less than 570MPa; after 480 hours of oxidation in air at 750 ℃, the oxide skin is mainly chromium oxide (as shown in figure 3), and the oxidation weight is increased by more than 11g/m 2 (as shown in table 2). After 480 hours of oxidation in air at 750 ℃, the oxidation weight increase is respectively 5.8, 4.8, 7.3 and 14.4 times of that of the examples 1, 2, 3 and 4
Comparative example 2
The method comprises the steps of preparing raw materials according to the following alloy components (in percentage by mass) by using metal materials with the purity of more than or equal to 99.5%.
Ni:26%, cr:15%, mo:1.5%, al:3.0%, ti:1.0%, mn:1.0%, C:0.08%, B:0.005%, si:0.5 percent and the balance of Fe.
Respectively weighing raw materials of each element according to the raw material proportion, smelting in a protective atmosphere, uniformly mixing, and casting the melt into an alloy ingot; secondly, homogenizing for 8 hours at 1225 ℃ and water quenching, then cold rolling the homogenized alloy ingot, homogenizing for 1 hour at 1225 ℃ after the deformation amount is about 50%, and then cold rolling to the total deformation amount of about 85%; then, carrying out recrystallization annealing on the alloy after cold rolling at 1000 ℃ for 1 hour, and then carrying out water quenching; finally, water quenching is carried out after 24 hours of aging treatment at the temperature of 700 ℃. The alloy matrix finally obtained is austenite, the average grain size of the alloy is about 2-10 mu m, and Ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, the volume fraction is about 20%, and the carbide is dispersed and distributed. The mechanical properties and oxidation resistance of the alloy are shown in Table 2, and the yield strength sigma at 680 ℃ is 0.2 Below 440MPa, an oxidative weight gain of about 1g/m in air at 750 ℃ over 480h 2 。
The yield stress of the iron-based high-temperature alloys prepared in examples 1-4 and comparative examples 1-2 varies with temperature as shown in fig. 4, and the yield strength of the alloy of the invention is higher than that of the iron-based high-temperature alloy IncoloyA-286 (U.S. brand) or GH2132 (Chinese brand) (comparative example 1) widely used in the industry at room temperature to 700 ℃. The alloy does not contain Ta, V, nb and other raw materials with higher cost (Table 1), and the cost of the alloy raw materials is lower. As can be seen from Table 2 and FIG. 2, the alloy of the present invention forms a dense alumina oxide film protective layer on the surface at 800 ℃ or below, and has excellent oxidation resistance.
TABLE 1 prices of raw materials for several common metal elements, data from gold casting (5 month, 21 days 2022)
TABLE 2 test results of mechanical properties and oxidation resistance of the iron-based superalloy prepared in examples 1-4 and comparative examples 1-2
The foregoing detailed description is intended to illustrate and not limit the invention, which is intended to be within the spirit and scope of the appended claims, and any changes and modifications that fall within the true spirit and scope of the invention are intended to be covered by the following claims.
Claims (6)
1. The precipitation-strengthened high-strength oxidation-resistant iron-based high-temperature alloy is characterized by comprising the following elements in percentage by mass:
Al 1.5~3.5%；
Ti 1.2~2.8%；
Ni 24~30%；
Cr 13~16%；
Mo ＜2.0%；
Mn ≤ 1.0%；
C 0.02~0.2%；
B ≤0.05%；
Si ≤ 1.0%；
the balance being Fe;
the alloy matrix is austenite, ni 3 The (Al, ti) strengthening phase is uniformly dispersed in the crystal, and the volume fraction of the (Al, ti) strengthening phase is not less than 40%.
2. The precipitation-strengthened, high-strength, oxidation-resistant iron-based superalloy of claim 1, wherein: the content of Al is 2.5-3.2%.
3. The precipitation-strengthened, high-strength, oxidation-resistant iron-based superalloy of claim 1, wherein: the content of Ti is 1.8-2.5%.
4. The precipitation-strengthened, high-strength, oxidation-resistant iron-based superalloy of claim 1, wherein: the Ni content is 25-29%.
5. The precipitation-strengthened, high-strength, oxidation-resistant iron-based superalloy of claim 1, wherein: and forming a compact alumina oxide film protective layer on the surface of the alloy at the temperature below 800 ℃.
6. A method of making a precipitation-strengthened, high-strength, oxidation-resistant iron-based superalloy as in any of claims 1-5, comprising the steps of:
respectively weighing raw materials of each element according to the raw material proportion, melting and uniformly mixing the raw materials in a protective atmosphere, and casting into an alloy ingot;
homogenizing at 1100-1250 deg.c for not less than 4 hr, water quenching or air cooling, and cold and hot processing;
carrying out recrystallization annealing on the processed alloy at 900-1200 ℃ for 0.5-2 hours, and then carrying out water quenching or air cooling;
and carrying out aging treatment at the temperature of 650-800 ℃ to obtain the alloy finished product.
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| US20130266477A1 (en) * | 2012-04-05 | 2013-10-10 | Ut-Battelle, Llc | Alumina Forming Iron Base Superalloy |
| CN110343907A (en) * | 2019-07-17 | 2019-10-18 | 浙江大学 | High-strength casting Ni containing W3Al based high-temperature alloy and preparation method thereof |
| CN110408850A (en) * | 2019-07-17 | 2019-11-05 | 浙江大学 | The super-steel and preparation method thereof of nanocrystalline intermetallics precipitation strength |
| CN112359296A (en) * | 2020-11-10 | 2021-02-12 | 华能国际电力股份有限公司 | Precipitation strengthening iron-based high-temperature alloy and preparation method thereof |
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| US20130266477A1 (en) * | 2012-04-05 | 2013-10-10 | Ut-Battelle, Llc | Alumina Forming Iron Base Superalloy |
| CN110343907A (en) * | 2019-07-17 | 2019-10-18 | 浙江大学 | High-strength casting Ni containing W3Al based high-temperature alloy and preparation method thereof |
| CN110408850A (en) * | 2019-07-17 | 2019-11-05 | 浙江大学 | The super-steel and preparation method thereof of nanocrystalline intermetallics precipitation strength |
| CN112359296A (en) * | 2020-11-10 | 2021-02-12 | 华能国际电力股份有限公司 | Precipitation strengthening iron-based high-temperature alloy and preparation method thereof |
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