CN115383028B - Method for improving high-temperature durability of GH4780 alloy forging and obtained forging - Google Patents
Method for improving high-temperature durability of GH4780 alloy forging and obtained forging Download PDFInfo
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- CN115383028B CN115383028B CN202211114374.7A CN202211114374A CN115383028B CN 115383028 B CN115383028 B CN 115383028B CN 202211114374 A CN202211114374 A CN 202211114374A CN 115383028 B CN115383028 B CN 115383028B
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 99
- 239000000956 alloy Substances 0.000 title claims abstract description 99
- 238000005242 forging Methods 0.000 title claims abstract description 93
- 238000000034 method Methods 0.000 title claims abstract description 33
- 238000005096 rolling process Methods 0.000 claims abstract description 34
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 238000004321 preservation Methods 0.000 claims abstract description 7
- 238000010304 firing Methods 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 229910052715 tantalum Inorganic materials 0.000 abstract description 13
- 238000012545 processing Methods 0.000 abstract description 7
- 238000005516 engineering process Methods 0.000 abstract description 5
- 230000000052 comparative effect Effects 0.000 description 18
- 238000003723 Smelting Methods 0.000 description 9
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical group [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000011534 incubation Methods 0.000 description 3
- 230000006698 induction Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000005923 long-lasting effect Effects 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J13/00—Details of machines for forging, pressing, or hammering
- B21J13/02—Dies or mountings therefor
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J17/00—Forge furnaces
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
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Abstract
The invention relates to the technical field of alloy processing, in particular to a method for improving high-temperature durability of a GH4780 alloy forging and the obtained forging. The method for improving the high-temperature durability of the GH4780 alloy forging comprises the following steps: performing heat preservation treatment on GH4780 alloy cast ingots at 1150-1195 ℃, and then performing drawing and upsetting at 1160-1180 ℃ to obtain rod blanks; then carrying out hot continuous rolling, warm rolling, free forging, die forging and heat treatment; in the GH4780 alloy, the content of Si is 0.16-0.3%, the content of P is 0.016-0.036%, and the content of Ta is 1.16-3%. According to the invention, on one hand, the alloy components are optimized by adjusting the contents of Si, P and Ta, and on the other hand, the forging structure is optimized by improving the processing technology, so that the 770 ℃/470MPa durability of the GH4780 alloy forging is remarkably improved.
Description
Technical Field
The invention relates to the technical field of alloy processing, in particular to a method for improving high-temperature durability of a GH4780 alloy forging and the obtained forging.
Background
The GH4780 alloy is nickel-based superalloy, has good high-temperature mechanical property and high-temperature oxidation resistance, and has long-term service temperature reaching 770 ℃, and is mainly used for parts such as disk parts, ring parts, blades, fasteners and the like of aeroengines and ground gas turbines.
In the prior art, the GH4780 alloy forging preparation process comprises the following steps: GH4780 alloy cast ingot is smelted by adopting a Vacuum Induction (VIM) and vacuum consumable smelting (VAR) two-way process. Homogenizing GH4780 cast ingot at 1100-1250 deg.c for 500-5000 min. Drawing and upsetting the GH4780 alloy ingot at 1020-1150 ℃ under at least three firing times to ensure that the deformation is 10-50% to obtain a GH4780 alloy rod blank. At least two firings are carried out on the GH4780 alloy rod blank at 1050-1080 ℃ to ensure that the deformation of the GH4780 alloy rod blank is 10-50%, thus obtaining the GH4780 alloy forging. After solution treatment at 1080 ℃ for 8 hours, the average grain size of the forging reaches ASTM grade 4 or finer.
However, with further improvement of service lives of aeroengines and gas turbines, the durability of the GH4780 alloy developed in the prior art cannot meet the requirement of life extension, and the use of GH4780 alloy forgings is restricted.
In view of this, the present invention has been made.
Disclosure of Invention
The invention aims to provide a method for improving high-temperature durability of a GH4780 alloy forging, which aims to solve the technical problems of insufficient durability and the like of the GH4780 alloy forging in the prior art.
It is another object of the present invention to provide a GH4780 alloy forging obtained by the above method.
In order to achieve the above object of the present invention, the following technical solutions are specifically adopted:
the method for improving the high-temperature durability of the GH4780 alloy forging comprises the following steps:
(a) Performing heat preservation treatment on GH4780 alloy cast ingots at 1150-1195 ℃, and then performing drawing and upsetting at 1160-1180 ℃ to obtain rod blanks;
(b) Performing hot continuous rolling on the rod blank at 1120-1160 ℃ to obtain a hot continuous rolled rod blank;
(c) Performing warm rolling on the hot continuous rolling bar blank at 850-950 ℃ to obtain a warm rolling bar blank;
(d) Freely forging the warm rolled bar blank at 950-1050 ℃ to obtain a freely forged blank;
(e) Forging the free forging blank at 850-1030 ℃ and then performing heat treatment to obtain an alloy forging;
in the GH4780 alloy, the content of Si is 0.16-0.3%, the content of P is 0.016-0.036% and the content of Ta is 1.16-3% by mass percent.
According to the invention, on one hand, the alloy components are optimized by adjusting the contents of Si, P and Ta, and the alloy components are adjusted, and on the other hand, the forging structure is optimized by improving the processing technology, so that the 770 ℃/470MPa durability of the GH4780 alloy forging is remarkably improved.
In a specific embodiment of the present invention, in step (a), the incubation treatment includes: preserving heat for 40-60 h at 1150-1170 ℃, and preserving heat for 50-70 h at 1175-1195 ℃.
In a specific embodiment of the invention, in step (a), said drawing and upsetting of two fires is performed. Further, the deformation of the drawing and upsetting is 30-60%.
In a specific embodiment of the present invention, in step (b), hot continuous rolling of one pass is performed. Further, the deformation of the hot continuous rolling is 40% -50%.
In a specific embodiment of the present invention, in step (c), warm rolling is performed for one firing pass. Further, the deformation of the warm rolling is 20% -40%.
In a specific embodiment of the present invention, in step (d), free forging is performed for one firing event. Further, the deformation amount of the free forging is 40% -60%.
In a specific embodiment of the present invention, in step (e), one firing step is performed. Further, the deformation amount of the die forging is 10% -40%.
In a specific embodiment of the present invention, the heat treatment includes: heat preserving at 1040-1070 deg.c for 1-8 hr, water cooling to room temperature, heat preserving at 750-850 deg.c for 8-16 hr, and air cooling to room temperature.
In a specific embodiment of the invention, the GH4780 alloy ingot is obtained by triple smelting.
GH4780 alloy forging is prepared by adopting any one of the methods.
In the specific embodiment of the invention, the 770 ℃/470MPa long-lasting life of the GH4780 alloy forging is 60-75 h, and the elongation after break is 12-15%.
Compared with the prior art, the invention has the beneficial effects that:
according to the invention, on one hand, the alloy components are optimized by adjusting the contents of Si, P and Ta, and the alloy components are adjusted, and on the other hand, the forging structure is optimized by improving the processing technology, so that the 770 ℃/470MPa durability of the GH4780 alloy forging is remarkably improved; the durability life of 770 ℃/470MPa of the obtained GH4780 alloy forging can reach 60-75 h, and the elongation after breaking can reach 12-15%.
Detailed Description
The technical solution of the present invention will be clearly and completely described in conjunction with the specific embodiments, but it will be understood by those skilled in the art that the examples described below are some, but not all, examples of the present invention, and are intended to be illustrative only and should not be construed as limiting the scope of the present invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention. The specific conditions are not noted in the examples and are carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or apparatus used were conventional products commercially available without the manufacturer's attention.
The method for improving the high-temperature durability of the GH4780 alloy forging comprises the following steps:
(a) Performing heat preservation treatment on GH4780 alloy cast ingots at 1150-1195 ℃, and then performing drawing and upsetting at 1160-1180 ℃ to obtain rod blanks;
(b) Performing hot continuous rolling on the rod blank at 1120-1160 ℃ to obtain a hot continuous rolled rod blank;
(c) Performing warm rolling on the hot continuous rolling bar blank at 850-950 ℃ to obtain a warm rolling bar blank;
(d) Freely forging the warm rolled bar blank at 950-1050 ℃ to obtain a freely forged blank;
(e) Forging the free forging blank at 850-1030 ℃ and then performing heat treatment to obtain an alloy forging;
in the GH4780 alloy, the content of Si is 0.16-0.3%, the content of P is 0.016-0.036% and the content of Ta is 1.16-3% by mass percent.
According to the invention, on one hand, the alloy components are optimized by adjusting the contents of Si, P and Ta, and the alloy components are adjusted, and on the other hand, the forging structure is optimized by improving the processing technology, so that the 770 ℃/470MPa durability of the GH4780 alloy forging is remarkably improved.
In a specific embodiment of the present invention, the GH4780 alloy comprises, in mass percent: 0.16 to 0.3 percent of Si, 0.016 to 0.036 percent of P, 1.16 to 3 percent of Ta, 0.002 to 0.007 percent of B, 0.005 to 0.07 percent of Zr, 1.1 to 1.4 percent of Al, 0.06 to 0.12 percent of C, 22 to 23 percent of Cr, less than or equal to 0.2 percent of Mo, 1.8 to 2.2 percent of W, 18.5 to 19.5 percent of Co, less than or equal to 0.7 percent of Fe, 0.65 to 0.95 percent of Nb, 2.1 to 2.4 percent of Ti, less than or equal to 0.1 percent of Cu, less than or equal to 0.1 percent of Mn, less than or equal to 0.007 percent of Mg, less than or equal to 0.007 percent of S, and the balance of Ni.
As in the various embodiments, the Si content may be 0.16%, 0.18%, 0.2%, 0.22%, 0.24%, 0.25%, 0.26%, 0.28%, 0.3%, etc.; the P content may be 0.016%, 0.018%, 0.02%, 0.022%, 0.024%, 0.025%, 0.026%, 0.028%, 0.03%, 0.032%, 0.034%, 0.036%, etc.; the content of Ta may be 1.16%, 1.2%, 1.4%, 1.5%, 1.6%, 1.8%, 2%, 2.2%, 2.4%, 2.5%, 2.6%, 2.8%, 3%, etc.
In a specific embodiment of the invention, in the GH4780 alloy, the content of Si is 0.16-0.2%, the content of P is 0.016-0.022% and the content of Ta is 2.0-2.5% by mass percent.
By properly improving Si, P and Ta, on one hand, the compactness and high-temperature stability of the oxide film of the forging can be improved, the grain boundary strength is improved, and meanwhile, a proper amount of Ta can enter a gamma 'phase to strengthen and stabilize the gamma' phase, so that the intra-crystal strength is improved. The three alloy elements of Si, P and Ta cooperate with each other to play the most reasonable role, and are matched with other elements at the same time so as to realize the best effect.
In a specific embodiment of the present invention, in step (a), the incubation treatment includes: preserving heat for 40-60 h at 1150-1170 ℃, and preserving heat for 50-70 h at 1175-1195 ℃.
As in the various embodiments, the incubation of step (a) may be performed by first incubating at 1150 ℃, 1155 ℃, 1160 ℃, 1165 ℃, 1170 ℃, etc. for 40h, 45h, 50h, 55h, 60h, etc., and then incubating at 1175 ℃, 1180 ℃, 1185 ℃, 1190 ℃, 1195 ℃, etc. for 50h, 55h, 60h, 65h, 70h, etc.
In a specific embodiment of the invention, in step (a), said drawing and upsetting of two fires is performed. Further, the deformation of each firing time of the drawing and upsetting is 30-60%.
As in the various embodiments, in step (a), the drawing and upsetting temperatures may be 1160 ℃, 1165 ℃, 1170 ℃, 1175 ℃, 1180 ℃, and so forth; the deformation amount of each fire of the drawing and upsetting can be 30%, 35%, 40%, 45%, 50%, 55%, 60% and the like, and in actual operation, the deformation amounts of the two fires can be the same or different.
In a specific embodiment of the present invention, in step (b), hot continuous rolling of one pass is performed. Further, the deformation of the hot continuous rolling is 40% -50%.
As in the various embodiments, in step (b), the temperature at which hot continuous rolling is performed may be 1120 ℃, 1125 ℃, 1130 ℃, 1135 ℃, 1140 ℃, 1145 ℃, 1150 ℃, 1155 ℃, 1160 ℃, etc.; the deformation amount of the hot continuous rolling may be 40%, 42%, 44%, 45%, 46%, 48%, 50%, etc.
In a specific embodiment of the present invention, in step (c), warm rolling is performed for one firing pass. Further, the deformation of the warm rolling is 20% -40%.
As in the various embodiments, in step (c), the warm rolling may be performed at a temperature of 850 ℃, 860 ℃, 870 ℃, 880 ℃, 890 ℃, 900 ℃, 910 ℃, 920 ℃, 930 ℃, 940 ℃, 950 ℃, etc.; the deformation amount of warm rolling may be 20%, 25%, 30%, 35%, 40%, etc.
In a specific embodiment of the present invention, in step (d), free forging is performed for one firing event. Further, the deformation amount of the free forging is 40% -60%.
As in the various embodiments, in step (d), the temperature at which the free forging is performed may be 950 ℃, 960 ℃, 970 ℃, 980 ℃, 990 ℃, 1000 ℃, 1010 ℃, 1020 ℃, 1030 ℃, 1040 ℃, 1050 ℃, etc.; the deformation amount of the free forging may be 40%, 45%, 50%, 55%, 60%, or the like.
In a specific embodiment of the present invention, in step (e), one firing step is performed. Further, the deformation amount of the die forging is 10% -40%.
As in the various embodiments, in step (e), the temperature at which the swaging is performed may be 850 ℃, 860 ℃, 880 ℃, 900 ℃, 920 ℃, 940 ℃, 950 ℃, 960 ℃, 980 ℃, 1000 ℃, 1020 ℃, 1030 ℃, etc.; the amount of deformation of the die forging may be 10%, 15%, 20%, 25%, 30%, 35%, 40%, etc.
In a specific embodiment of the present invention, the heat treatment includes: heat preserving at 1040-1070 deg.c for 1-8 hr, water cooling to room temperature, heat preserving at 750-850 deg.c for 8-16 hr, and air cooling to room temperature.
As in the various embodiments, the heat treatment may be water-cooled to room temperature after heat-preserving treatment at 1040 ℃, 1050 ℃, 1060 ℃, 1070 ℃ and the like for 1h, 2h, 3h, 4h, 5h, 6h, 7h, 8h and the like, and then air-cooled to room temperature after heat-preserving treatment at 750 ℃, 760 ℃,770 ℃, 780 ℃, 790 ℃, 800 ℃, 810 ℃, 820 ℃, 830 ℃, 840 ℃, 850 ℃ and the like for 8h, 9h, 10h, 11h, 12h, 13h, 14h, 15h, 16h and the like.
In a specific embodiment of the invention, the GH4780 alloy ingot is obtained by triple smelting.
Wherein, the triple smelting comprises vacuum induction, electroslag remelting and vacuum consumable smelting. The specific triple smelting parameters can adopt the smelting parameters of the existing conventional GH4780 cast ingot.
GH4780 alloy forging is prepared by adopting any one of the methods.
The average grain size of the GH4780 alloy forging obtained by the method can reach the ASTM grade 6 or finer.
In the specific embodiment of the invention, the 770 ℃/470MPa long-lasting life of the GH4780 alloy forging is 60-75 h, and the elongation after break is 12-15%.
For example, the 770 ℃/470MPa long-term lifetime may be 60h, 62h, 64h, 65h, 66h, 68h, 70h, 72h, 74h, 75h, etc.; the elongation after break may be 12%, 12.5%, 13%, 13.5%, 14%, 14.5%, 15%, etc.
Example 1
The embodiment provides a method for improving high-temperature durability of GH4780 alloy forgings, which comprises the following steps:
(1) Smelting by a triple process of vacuum induction, electroslag remelting and vacuum consumable smelting to obtain a GH4780 alloy ingot; wherein, the GH4780 alloy comprises the following components in percentage by mass: si0.16%, P0.016%, ta 1.16%, B0.003%, zr 0.008%, al 1.2%, C0.09%, cr 22.3%, mo 0.05%, W1.9%, co 18.5%, fe 0.1%, nb 0.8%, ti 2.2%, cu 0.05%, mn 0.05%, V0.01%, mg 0.005%, S0.0007%, and the balance Ni.
(2) Preserving heat of the ingot obtained in the step (1) for 50 hours at 1160 ℃, and preserving heat for 60 hours at 1180 ℃; and then drawing and upsetting the two fires at 1170 ℃ to ensure that the deformation of each fire is 40 percent, thus obtaining an upsetting rod blank.
(3) And performing hot continuous rolling on the rod blank at 1140 ℃ with fire so that the deformation of the rod blank is 40%, and obtaining a hot continuous rolling rod blank.
(4) And performing hot rolling on the hot continuous rolling bar blank at 900 ℃ for a fire time to ensure that the deformation of the hot continuous rolling bar blank is 30%, so as to obtain a hot rolling bar blank.
(5) And (3) performing free forging on the warm rolled bar blank at 1000 ℃ for one fire time to ensure that the deformation of the warm rolled bar blank is 50%, so as to obtain a free forging blank.
(6) And (3) performing die forging on the free forging blank at 1000 ℃ for one firing time to ensure that the deformation of the free forging blank is 40%, so as to obtain the alloy forging.
(7) Carrying out heat preservation treatment on the alloy forging at 1040 ℃ for 2 hours, and then cooling the alloy forging to room temperature; then heat-preserving treatment is carried out for 8 hours at 820 ℃, and then air cooling is carried out to room temperature.
Example 2
This example provides a method for improving the high temperature durability performance of a GH4780 alloy forging, with reference to example 1, except that the content of Si, P, and Ta in the GH4780 alloy composition is different.
The GH4780 alloy of the embodiment comprises the following components in percentage by mass: si 0.3%, P0.036%, ta 3%.
Example 3
This example provides a method for improving the high temperature durability performance of a GH4780 alloy forging, with reference to example 1, except that the content of Si, P, and Ta in the GH4780 alloy composition is different.
The GH4780 alloy of the embodiment comprises the following components in percentage by mass: si 0.18%, P0.019%, ta 2.2%.
Comparative example 1
Comparative example 1 referring to example 1, the difference is that the content of Si, P and Ta in the GH4780 alloy component is different.
The GH4780 alloy of comparative example 1 comprises the following components in percentage by mass: si 0.15%, P0.015%, ta 1.15%.
Comparative example 2
Comparative example 2 referring to example 1, the difference is that the content of Si, P and Ta in the GH4780 alloy component is different.
The GH4780 alloy of comparative example 2 comprises the following components in percentage by mass: si 0.15%, P0.036%, ta 1.15%.
Comparative example 3
Comparative example 3 referring to example 1, the difference is that the content of Si, P and Ta in the GH4780 alloy component is different.
The GH4780 alloy of comparative example 3 comprises the following components in percentage by mass: si 0.31%, P0.037%, ta 3.1%.
Comparative example 4
Comparative example 4 reference example 1, except that the process was different.
The process of comparative example 4 includes:
homogenizing GH4780 cast ingot at 1175 ℃ for 60 hours;
drawing and upsetting the GH4780 alloy ingot at 1150 ℃ under three firing times to ensure that the deformation of each firing time is 30%, thus obtaining a GH4780 alloy rod blank;
forging the GH4780 alloy rod blank at 1065 ℃ by two fires, so that the deformation of each fire is 30%, and obtaining the GH4780 alloy forging;
carrying out solution treatment on the GH4780 alloy forging for 8 hours at 1080 ℃, and then cooling to room temperature; then heat-preserving at 800 ℃ for 8 hours, and then air-cooling to room temperature.
Experimental example 1
To comparative illustrate the effect of the method of the present invention on the durability of GH4780 alloy forgings, the durability life and elongation after break of 770 ℃/470MPa of GH4780 alloy forgings treated in different examples and comparative examples were tested, and the test results are shown in Table 1 with reference to the standard measurement methods of creep, creep rupture and durability tests of ASTM E139 metal materials.
Table 1 results of performance testing of different GH4780 alloy forgings
| Numbering device | Long life time | Elongation after break |
| Example 1 | 60h | 12％ |
| Example 2 | 67h | 13％ |
| Example 3 | 75h | 15％ |
| Comparative example 1 | 35h | 7％ |
| Comparative example 2 | 40h | 4％ |
| Comparative example 3 | 25h | 2％ |
| Comparative example 4 | 30h | 6％ |
According to the test results, on one hand, the alloy composition is optimized by adjusting the contents of Si, P and Ta, and the alloy composition is adjusted, and on the other hand, the forging structure is optimized by improving the processing technology, so that the 770 ℃/470MPa durability of the GH4780 alloy forging is remarkably improved.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solution of the present invention, and not for limiting the same; although the invention has been described in detail with reference to the foregoing embodiments, it will be understood by those of ordinary skill in the art that: the technical scheme described in the foregoing embodiments can be modified or some or all of the technical features thereof can be replaced by equivalents; such modifications and substitutions do not depart from the spirit of the invention.
Claims (14)
1. The method for improving the high-temperature durability of the GH4780 alloy forging is characterized by comprising the following steps of:
(a) Performing heat preservation treatment on GH4780 alloy cast ingots at 1150-1195 ℃, and then performing drawing and upsetting at 1160-1180 ℃ to obtain rod blanks;
(b) Performing hot continuous rolling on the rod blank at 1120-1160 ℃ to obtain a hot continuous rolled rod blank;
(c) Performing warm rolling on the hot continuous rolling bar blank at 850-950 ℃ to obtain a warm rolling bar blank;
(d) Freely forging the warm rolled bar blank at 950-1050 ℃ to obtain a freely forged blank;
(e) Forging the free forging blank at 850-1030 ℃ and then performing heat treatment to obtain an alloy forging; the heat treatment includes: performing heat preservation at 1040-1070 ℃ for 1-8 h, cooling to room temperature by water, performing heat preservation at 750-850 ℃ for 8-16 h, and cooling to room temperature by air;
in the GH4780 alloy, the content of Si is 0.16-0.3%, the content of P is 0.016-0.036% and the content of Ta is 1.16-3% by mass percent.
2. The method of improving the high temperature durability performance of a GH4780 alloy forging according to claim 1, wherein in step (a), the heat retaining treatment comprises: preserving heat for 40-60 h at 1150-1170 ℃, and preserving heat for 50-70 h at 1175-1195 ℃.
3. The method of improving the high temperature durability of a GH4780 alloy forging according to claim 1, wherein in step (a), said drawing and upsetting for two firings is performed.
4. The method for improving high temperature durability of GH4780 alloy forgings according to claim 3, wherein the deformation per firing time of drawing and upsetting is 30% -60%.
5. The method of improving the high temperature durability performance of a GH4780 alloy forging according to claim 1, wherein in step (b), said hot continuous rolling is performed for one pass.
6. The method for improving high-temperature durability of a GH4780 alloy forging according to claim 5, wherein the deformation amount of hot continuous rolling is 40% -50%.
7. The method of improving the high temperature durability of a GH4780 alloy forging according to claim 1, wherein in step (c), said warm rolling is performed for one firing pass.
8. The method for improving the high-temperature durability of a GH4780 alloy forging according to claim 7, wherein the deformation amount of warm rolling is 20% -40%.
9. The method of improving the high temperature durability of a GH4780 alloy forging according to claim 1, wherein in step (d), said free forging is performed for one firing event.
10. The method for improving the high-temperature durability of a GH4780 alloy forging according to claim 9, wherein the deformation amount of free forging is 40% -60%.
11. The method of improving the high temperature durability of a GH4780 alloy forging according to claim 1, wherein in step (e), said swaging of one shot is performed.
12. The method for improving the high temperature durability of a GH4780 alloy forging according to claim 11, wherein the die forging deformation is 10% -40%.
A gh4780 alloy forging, prepared by the method of any one of claims 1 to 12.
14. The GH4780 alloy forging according to claim 13, wherein the long-life of 770 ℃/470MPa for the GH4780 alloy forging is 60-75 hours and the elongation after break is 12% -15%.
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| CN202211114374.7A CN115383028B (en) | 2022-09-14 | 2022-09-14 | Method for improving high-temperature durability of GH4780 alloy forging and obtained forging |
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103132148A (en) * | 2011-12-05 | 2013-06-05 | 中国科学院金属研究所 | Nickel base single crystal superalloy with low density, low cost and high strength |
| CN110484841A (en) * | 2019-09-29 | 2019-11-22 | 北京钢研高纳科技股份有限公司 | A kind of heat treatment method of GH4780 alloy forged piece |
| CN110592506A (en) * | 2019-09-29 | 2019-12-20 | 北京钢研高纳科技股份有限公司 | GH4780 alloy blank and forging and preparation method thereof |
| CN111270105A (en) * | 2020-04-10 | 2020-06-12 | 北京钢研高纳科技股份有限公司 | Method for homogenizing GH4780 alloy cast ingot, GH4780 alloy casting and application thereof |
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| JP4417977B2 (en) * | 2007-04-25 | 2010-02-17 | 株式会社日立製作所 | Gas turbine blade and method for manufacturing the same |
| DE102014001330B4 (en) * | 2014-02-04 | 2016-05-12 | VDM Metals GmbH | Curing nickel-chromium-cobalt-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and processability |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103132148A (en) * | 2011-12-05 | 2013-06-05 | 中国科学院金属研究所 | Nickel base single crystal superalloy with low density, low cost and high strength |
| CN110484841A (en) * | 2019-09-29 | 2019-11-22 | 北京钢研高纳科技股份有限公司 | A kind of heat treatment method of GH4780 alloy forged piece |
| CN110592506A (en) * | 2019-09-29 | 2019-12-20 | 北京钢研高纳科技股份有限公司 | GH4780 alloy blank and forging and preparation method thereof |
| CN111270105A (en) * | 2020-04-10 | 2020-06-12 | 北京钢研高纳科技股份有限公司 | Method for homogenizing GH4780 alloy cast ingot, GH4780 alloy casting and application thereof |
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