CN107904448B - High-heat-strength nickel-based powder high-temperature alloy and preparation method thereof - Google Patents
High-heat-strength nickel-based powder high-temperature alloy and preparation method thereof Download PDFInfo
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- CN107904448B CN107904448B CN201711480702.4A CN201711480702A CN107904448B CN 107904448 B CN107904448 B CN 107904448B CN 201711480702 A CN201711480702 A CN 201711480702A CN 107904448 B CN107904448 B CN 107904448B
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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
- C22C—ALLOYS
- 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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
Abstract
The invention relates to a novel high-heat-strength nickel-based powder high-temperature alloy which comprises, by mass, 0.04% -0.09% of C, 9.5% -11.5% of Co, 9.5% -11.5% of Cr, 3.8% -4.2% of W, 2.8% -3.2% of Mo, 3.3% -3.7% of Al, 2.3% -2.7% of Ti, 3.8% -4.2% of Nb, 0.006% -0.015% of B, 0.03% -0.07% of Zr, 0.3% -1.5% of Hf, 0.3% of Re and the balance of Ni. Meanwhile, the invention also discloses a preparation method of the novel high-heat-strength nickel-based powder superalloy. The invention adjusts the content of solid solution and gamma 'phase strengthening elements in the designed alloy, so that the matrix and the gamma' phase have higher high-temperature strength and excellent high-temperature stability.
Description
Technical Field
The invention relates to the technical field of nickel-based powder superalloy, in particular to a novel high-heat-strength nickel-based powder superalloy and a preparation method thereof.
Background
Compared with the traditional cast high-temperature alloy, the powder high-temperature alloy has the advantages that the pre-alloyed powder of the powder high-temperature alloy is cooled and formed at a high cooling speed, so that the alloy components are uniform, the macro segregation is eliminated, the grain size reaches the micron level, the hot processing performance of the alloy is improved, and the tensile strength of the alloy is improved.
The powder high-temperature alloy is a key material of hot end rotating parts such as a turbine disc of an aero-engine, and in the actual operation of the engine, the disc center of the turbine disc bears the extremely high centrifugal force and needs high tensile strength, and the temperature of the disc edge of the turbine disc is higher than that of the disc center and needs good durability and creep resistance.
The strengthening means of the high-temperature alloy mainly comprises three types: firstly, solid solution strengthening, namely, alloying single-phase austenite is formed by adding some solid solution elements into the alloy, and the strength of the alloy matrix is improved; second phase strengthening, namely lattice mismatch is generated between the second phase and the matrix phase to form an elastic stress field or change the mechanism of dislocation movement to block the movement of dislocation; and thirdly, grain boundary strengthening, wherein the grain boundary is a weak link of the high-temperature alloy, particularly the powder high-temperature alloy, the fracture of the alloy is often in a mode of fracture along the grain, the content of harmful phases in the grain boundary is reduced, the form and distribution of grain boundary phases are improved, the grain boundary strength can be improved, and the effect of improving the alloy strength is achieved.
In the case of nickel-based powder superalloys, much research work has been done abroad to improve the strength thereof by adjusting the alloy composition. Taking russia as an example, on the basis of the components of the EP741P alloy, the strengthening effects such as solid solution strengthening and the like are realized by adjusting the contents of elements such as C, Cr, W, Mo, Co and the like, and the tensile strength of the developed VV750P alloy is obviously improved compared with that of the EP741P alloy on the premise of not obviously losing the plasticity of the alloy.
Disclosure of Invention
In view of the above analysis, the present invention aims to provide a novel high-heat-strength nickel-based powder superalloy and a method for preparing the same, which is not limited to be improved on the basis of a certain alloy, but rather, the alloy composition is adjusted by reverse thinking from the alloy performance, and then appropriate heat treatment is performed, so that the novel high-heat-strength nickel-based powder superalloy has excellent tensile strength and endurance strength.
The purpose of the invention is mainly realized by the following technical scheme:
a novel high-heat-strength nickel-based powder high-temperature alloy comprises, by mass, 0.04% -0.09% of C, 9.5% -11.5% of Co, 9.5% -11.5% of Cr, 3.8% -4.2% of W, 2.8% -3.2% of Mo, 3.3% -3.7% of Al, 2.3% -2.7% of Ti, 3.8% -4.2% of Nb, 0.006% -0.015% of B, 0.03% -0.07% of Zr, 0.3% -1.5% of Hf0, 0.3% of Re and the balance of Ni.
The invention has the following beneficial effects: according to the invention, the Re element and the Hf element are added into the alloy, so that the contents of Co, Cr, W, Mo, Nb and other elements are adjusted, the high-temperature stability of a gamma ' phase can be improved by trace Re, the composition of a main strengthening phase gamma ' phase and carbide in the alloy can be changed by trace Hf, the strength of the gamma ' phase is improved, the solid solution strengthening effect of a matrix can be improved by adding the W element, and the contents of Co, Cr and Nb are adjusted so as to ensure the stability of an alloy structure; compared with FGH4095 alloy, the high-heat-strength nickel-based powder superalloy of the invention has better tensile strength and endurance strength than FGH4095, and the endurance life can be improved by more than 1 time, thus being beneficial to practical production and application.
On the basis of the scheme, the invention is further improved as follows:
preferably, the nickel-based powder superalloy comprises, in mass percent: 0.05 to 0.07 percent of C, 10.0 to 11.0 percent of Co10.0 to 11.0 percent of Cr, 3.9 to 4.1 percent of W, 2.9 to 3.1 percent of Mo, 3.4 to 3.6 percent of Al, 2.4 to 2.6 percent of Ti, 3.9 to 4.1 percent of Nb, 0.008 to 0.013 percent of B, 0.04 to 0.06 percent of Zr, 0.8 to 1.5 percent of Hf0, 0.3 percent of Re and the balance of Ni.
The invention has the following beneficial effects: the invention selects the range, and the tensile strength and the lasting strength of the nickel-based powder superalloy have better effects.
Preferably, the nickel-based powder superalloy comprises, in mass percent: 0.06% of C, 10.5% of Co, 10.5% of Cr10.5%, 4.0% of W, 3.0% of Mo, 3.5% of Al, 2.5% of Ti, 4.0% of Nb, 0.011% of B, 0.05% of Zr, Hf1.5%, 0.1% of Re and the balance of Ni.
The components are selected, so that the prepared alloy has optimal mechanical property, and the service life is prolonged by more than 1 time compared with FGH 4095.
Further, the gamma' phase complete dissolution temperature of the nickel-based powder superalloy is 1163-1172 ℃.
Further, the main precipitated phase in the nickel-based powder superalloy is a gamma 'phase, and the mass fraction of the gamma' phase is 50-60%.
The beneficial effect of adopting the further scheme is that: the gamma' phase of the nickel-based powder superalloy prepared by the components in the range has high-temperature strength and excellent high-temperature stability, so that the high-temperature performance of the superalloy is relatively excellent compared with that of FGH4095 alloy.
Further, the mass fraction of the W element in the gamma matrix of the nickel-based powder superalloy is 3.13-3.76%.
The mass fraction range of the W element can improve the solid solution strengthening effect of the matrix and ensure the stable structure of the alloy prepared by the method; the trace Re element in the invention can improve the high-temperature stability of the gamma' phase and ensure the stability of the alloy structure.
A preparation method of a novel high-heat-strength nickel-based powder superalloy comprises the steps of preparing powder by a plasma rotating electrode method; hot isostatic pressing forming; and (3) heat treatment: 1130-1150 ℃/1-3 h/salt quenching/air cooling +870 ℃/1-3 h/air cooling +650 ℃/16-28 h/air cooling.
The preparation method comprises the following steps: the high-heat-strength nickel-based powder high-temperature alloy prepared by the invention has good high-temperature comprehensive performance by performing limited heat treatment in the temperature range.
Further, the heat treatment is 1135-1145 ℃/1.5 h-2.5 h/salt quenching/air cooling +870 ℃/1.3 h-2.8 h/air cooling +650 ℃/18 h-25 h/air cooling.
The nickel-based powder high-temperature alloy prepared by the heat treatment has better performance and higher tensile strength and lasting strength.
The heat treatment is 1138-1142 ℃/1.8 h-2.7 h/salt quenching/air cooling +870 ℃/1.5 h-2 h/air cooling +650 ℃/20 h-23 h/air cooling.
Further, the heat treatment is 1140 ℃/2 h/salt quenching/air cooling +870 ℃/2.5 h/air cooling +650 ℃/23.5 h/air cooling.
The invention selects the heat treatment, and the endurance strength of the prepared nickel-based superalloy is more than one time higher than that of FGH 4095.
The invention has the beneficial effects that:
(1) the novel heat-strength nickel-based powder superalloy ensures that a matrix and a gamma 'phase have higher high-temperature strength and excellent high-temperature stability by adjusting the contents of solid solution and gamma' phase strengthening elements in the designed alloy, and the high-temperature comprehensive performance of the alloy is better than that of FGH4095 alloy;
(2) compared with the FGH4095 alloy, the novel heat-strength nickel-based powder high-temperature alloy of the invention adds alloying elements Re and Hf, improves the contents of Co, Nb and W in the alloy, reduces the contents of Cr and Mo, and carries out proper heat treatment to ensure that the alloy has excellent tensile strength and durable strength, and when the Hf element and the Re element in the alloy are 1.5% and 0.1%, the durable service life of the alloy prepared by the invention is doubled.
In the invention, the technical schemes can be combined with each other to realize more preferable combination schemes. Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and claims thereof.
Detailed Description
The following detailed description of the preferred embodiments of the invention is provided to illustrate the principles of the invention and not to limit the scope of the invention.
In the chemical composition range of the nickel-based powder superalloy, namely, in the ranges of 0.04-0.09% of C, 9.5-11.5% of Co, 9.5-11.5% of Cr, 3.8-4.2% of W, 2.8-3.2% of Mo, 3.3-3.7% of Al, 2.3-2.7% of Ti, 3.8-4.2% of Nb, 0.006-0.015% of B, 0.03-0.07% of Zr, 0.3-1.5% of Hf0.3, 0.3% of Re and the balance of Ni, 2 alloy bars with different content ratios are smelted by using a 25kg vacuum induction furnace, and for comparison, FGH 5 alloy bars with one component are smelted at the same time, wherein the alloy components of FGH 5 are shown in Table 1; the invention uses a plasma rotating electrode method to prepare alloy powder, hot isostatic pressing is carried out after the powder treatment to obtain a compact powder high-temperature alloy cylindrical ingot blank, and the ingot blank is subjected to the same heat treatment; the FGH4095 alloy has the same preparation process as the alloy of the invention, and is respectively sampled from the ingot blank after heat treatment for mechanical property test.
Example 1
The nickel-based powder superalloy Alloy-1 Alloy comprises the following chemical components in percentage by mass: 0.06 of C, 10.5 of Co, 10.5 of Cr, 4.0 of W, 3.0 of Mo, 3.5 of Al, 2.5 of Tis, 4.0 of Nb, 0.011 of B, 0.05 of Zrs, 0.9 of Hf, 0.1 of Re0, and the balance of Ni. The preparation process in the embodiment is powder preparation by a plasma rotating electrode + hot isostatic pressing forming + heat treatment, wherein the powder preparation by the plasma rotating electrode and the hot isostatic pressing forming are prepared by using a conventional method in the field, and the heat treatment regime is obtained according to a large number of creative experiments, and the heat treatment specifically comprises the following steps: 1140 ℃/2 h/salt quenching/air cooling +870 ℃/2 h/air cooling +650 ℃/24 h/air cooling.
The solid solution temperature of the gamma 'phase of the nickel-based powder superalloy Alloy-1 prepared in the embodiment is 1167 ℃, and the mass fraction of the gamma' phase is 53.96%; the mass fraction of W in the gamma matrix is 3.13 percent, and the mass fraction of Re is 0.0931 percent; since the trace Re can improve the high-temperature stability of the gamma 'phase, and the trace Hf can change the composition of the gamma' phase and carbide which are main strengthening phases in the Alloy, the solid solution temperature and the mass fraction of the gamma 'phase in the embodiment and the mass fraction of W, Re elements in the matrix show that the strength of the gamma' phase in the embodiment is improved compared with that of the existing FGH4095 Alloy, and simultaneously, the performance of the nickel-based powder superalloy Alloy-1 in the embodiment is improved due to the action of W, Re elements; the Alloy-1 and the FGH4095 Alloy prepared in the embodiment test the endurance life under the conditions of 650 ℃ and 1035MPa, and the endurance life of the Alloy-1 in the embodiment is improved by 61.8 percent compared with that of the FGH4095 Alloy.
In this example, mechanical property samples were taken from the small spindle after heat treatment, and mechanical property tests were performed.
Example 2
The nickel-based powder superalloy Alloy-2 Alloy comprises the following chemical components in percentage by mass: 0.06 of C, 10.5 of Co, 10.5 of Cr, 4.0 of W, 3.0 of Mo, 3.5 of Al, 2.5 of Ti, 4.0 of Nb, 0.011 of B, 0.05 of Zr, 1.5 of Hf, 0.2 of Re0, and the balance of Ni. The preparation process in the embodiment is powder preparation by a plasma rotating electrode + hot isostatic pressing forming + heat treatment, wherein the powder preparation by the plasma rotating electrode and the hot isostatic pressing forming are prepared by using a conventional method in the field, and the heat treatment regime is obtained according to a large number of creative experiments, and the heat treatment specifically comprises the following steps: 1140 ℃/2 h/salt quenching/air cooling +870 ℃/2 h/air cooling +650 ℃/24 h/air cooling.
The Ni-based powder superalloy Alloy-2 prepared by the embodiment has the gamma 'phase solid solution temperature of 1170 ℃ and the gamma' phase mass fraction of 54.86%; the mass fraction of W in the gamma matrix is 3.56 percent, and the mass fraction of Re in the gamma matrix is 0.16 percent; the addition of the Re element and the Hf element in the embodiment is more than that in the embodiment 1, because the trace Re can improve the high-temperature stability of the gamma ' phase, and the trace Hf can change the composition of the main strengthening phase gamma ' phase and carbide in the Alloy, the solid solution temperature of the gamma ' phase and the mass fraction of the gamma ' phase in the embodiment are correspondingly improved, the mass fraction of W, Re element in the matrix is also correspondingly improved, the strength of the gamma ' phase in the embodiment is improved compared with that of the existing FGH4095 Alloy, and simultaneously, the performance of the nickel-based powder superalloy Alloy-2 in the embodiment is further improved due to the action of W, Re element; the Alloy-1 and the FGH4095 Alloy prepared in the embodiment test the endurance life under the conditions of 650 ℃ and 1035MPa, and the endurance life of the Alloy-1 in the embodiment is improved by 112.1 percent compared with that of the FGH4095 Alloy.
In this example, mechanical property samples were taken from the small spindle after heat treatment, and mechanical property tests were performed.
Table 1 shows the chemical composition comparison of the Alloy of the present invention and the FGH4095 Alloy, wherein Alloy-1 and Alloy-2 are the alloys in the examples of the present invention.
TABLE 1 chemical composition comparison of the alloys of the present invention examples with FGH4095 alloys
| Alloy (I) | C | Co | Cr | W | Mo | Al | Ti | Nb | B | Zr | Hf | Re | Ni |
| Alloy-1 | 0.06 | 10.5 | 10.5 | 4.0 | 3.0 | 3.5 | 2.5 | 4.0 | 0.011 | 0.05 | 0.9 | 0.1 | Surplus |
| Alloy-2 | 0.06 | 10.5 | 10.5 | 4.0 | 3.0 | 3.5 | 2.5 | 4.0 | 0.011 | 0.05 | 1.5 | 0.2 | Surplus |
| FGH4095 | 0.060 | 7.95 | 12.85 | 3.46 | 3.57 | 3.38 | 2.47 | 3.42 | 0.0092 | 0.040 | 0 | 0 | Surplus |
Table 2, Table 3 and Table 4 show the room temperature tensile properties and 650 ℃ tensile properties of the alloy of the present invention and FGH4095 alloy, respectively, and the 650 ℃ durability (test conditions: 650 ℃, 1035MPa, smooth specimens).
TABLE 2 comparison of tensile properties at room temperature for the alloys of the examples of the invention with FGH4095 alloy
| Alloy (I) | σb/MPa | σ0.2/MPa | δ/％ | ψ/％ |
| Alloy-1 | 1600 | 1221 | 17.0 | 18 |
| Alloy-2 | 1620 | 1220 | 16.5 | 18.5 |
| FGH4095 | 1563 | 1168 | 16.0 | 18 |
TABLE 3 comparison of 650 ℃ tensile Properties of the alloys of the present example with FGH4095 alloy
| Alloy (I) | σb/MPa | σ0.2/MPa | δ/％ | ψ/％ |
| Alloy-1 | 1510 | 1150 | 13.0 | 15.5 |
| Alloy-2 | 1530 | 1170 | 11.5 | 12.0 |
| FGH4095 | 1480 | 1140 | 10.5 | 10.5 |
TABLE 4 comparison of 650 deg.C, 1020MPa durability of alloys of the present invention examples versus FGH4095 alloys
| Alloy (I) | Long life/h | Elongation after break/% |
| Alloy-1 | 267 | 5 |
| Alloy-2 | 350 | 5 |
| FGH4095 | 165 | 5 |
As can be seen from tables 2 and 3, compared with the FGH4095 alloy, the tensile strength of the alloy of the invention at room temperature and 650 ℃ is improved, and the plasticity is not obviously reduced; wherein the 650 ℃ tensile strength and yield strength of the Alloy-2 are obviously improved.
As can be seen from Table 4, the endurance life of the Alloy of the invention under the conditions of 650 ℃ and 1035MPa is much longer than that of the FGH4095 Alloy, wherein the endurance life of the Alloy-2 Alloy is improved by more than 1 time, and the endurance plasticity is not obviously changed, that is, when the nickel-based powder superalloy is prepared by selecting the content of each component in the embodiment 2, the performance of the nickel-based powder superalloy reaches the optimal value, and the endurance life of the nickel-based powder superalloy is improved by 121.1 percent compared with that of the FGH4095 Alloy, thereby being beneficial to practical industrial application; meanwhile, the alloy and the FGH4095 alloy in the embodiment of the invention are tested for the endurance life at 650 ℃, and the endurance life in the embodiment of the invention is greatly improved, which shows that the endurance life of the invention under the high temperature condition is obviously improved.
In conclusion, the invention provides a novel high-heat-strength nickel-based powder superalloy and a preparation method thereof, and a large number of creative labor experiments prove that the novel high-heat-strength nickel-based powder superalloy is designed, and the matrix and the gamma 'phase have higher high-temperature strength and excellent high-temperature stability by adjusting the contents of solid solution and gamma' phase strengthening elements in the designed alloy, so that the tensile strength and the lasting strength of the nickel-based powder superalloy are improved compared with FGH4095 alloy.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention.
Claims (5)
1. The high-heat-strength nickel-based powder superalloy is characterized by comprising, by mass, 0.04% -0.09% of C, 9.5% -11.5% of Co, 9.5% or more and less than 10% of Cr, 3.8% -4.2% of W, 2.8% -3.2% of Mo, 3.3% -3.7% of Al, 2.3% -2.7% of Ti, 3.8% -4.2% of Nb, 0.006% -0.015% of B, 0.03% -0.07% of ZrC, 1.5% of Hf, 0.1% of Re and the balance of Ni;
the gamma' phase complete dissolution temperature of the nickel-based powder superalloy is 1163-1172 ℃;
the main precipitated phase in the nickel-based powder superalloy is a gamma 'phase, and the mass fraction of the gamma' phase is 53.96-60%;
the mass fraction of the W element in the gamma matrix of the nickel-based powder superalloy is 3.13-3.76%, and the mass fraction of Re in the gamma matrix of the nickel-based powder superalloy is 0.0931;
the preparation method of the high-heat-strength nickel-based powder superalloy comprises the steps of preparing powder by a plasma rotating electrode method; hot isostatic pressing forming; and (3) heat treatment: 1130-1150 ℃/1-3 h/salt quenching/air cooling +870 ℃/1-3 h/air cooling +650 ℃/16-28 h/air cooling.
2. The method for preparing the high-heat-strength nickel-based powder superalloy as claimed in claim 1, wherein the method comprises preparing powder by a plasma rotating electrode method; hot isostatic pressing forming; and (3) heat treatment: 1130-1150 ℃/1-3 h/salt quenching/air cooling +870 ℃/1-3 h/air cooling +650 ℃/16-28 h/air cooling.
3. The method for preparing the high-heat-strength nickel-based powder superalloy as claimed in claim 2, wherein the heat treatment is 1135 ℃ to 1145 ℃/1.5h to 2.5 h/salt quenching/air cooling +870 ℃/1.3h to 2.8 h/air cooling +650 ℃/18h to 25 h/air cooling.
4. The method for preparing the high-heat-strength nickel-based powder superalloy as claimed in claim 2, wherein the heat treatment is 1138-1142 ℃/1.8-2.7 h/salt quenching/air cooling +870 ℃/1.5-2 h/air cooling +650 ℃/20-23 h/air cooling.
5. The method for preparing the high-heat-strength nickel-based powder superalloy as claimed in claim 2, wherein the heat treatment is 1140 ℃/2 h/salt quenching/air cooling +870 ℃/2.5 h/air cooling +650 ℃/23.5 h/air cooling.
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| CN110218910A (en) * | 2018-11-24 | 2019-09-10 | 西部超导材料科技股份有限公司 | A kind of novel powder high temperature alloy and preparation method thereof |
| CN110205523B (en) * | 2019-07-04 | 2020-08-07 | 北京钢研高纳科技股份有限公司 | Nickel-based powder superalloy with high tensile strength and preparation method thereof |
| DE102020116868A1 (en) | 2019-07-05 | 2021-01-07 | Vdm Metals International Gmbh | Nickel-cobalt alloy powder and method of manufacturing the powder |
| CN110241331B (en) * | 2019-07-25 | 2020-10-02 | 北京钢研高纳科技股份有限公司 | Nickel-based powder superalloy and preparation method and application thereof |
| CN113265564B (en) * | 2021-05-06 | 2022-04-29 | 中国联合重型燃气轮机技术有限公司 | High-temperature alloy with good long-term stability and preparation method thereof |
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