CN116987990A - Heat treatment method for eliminating double grains of precipitation hardening type high-temperature alloy forging - Google Patents
Heat treatment method for eliminating double grains of precipitation hardening type high-temperature alloy forging Download PDFInfo
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- 238000005242 forging Methods 0.000 title claims abstract description 108
- 238000010438 heat treatment Methods 0.000 title claims abstract description 82
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 50
- 239000000956 alloy Substances 0.000 title claims abstract description 50
- 238000000034 method Methods 0.000 title claims abstract description 35
- 238000004881 precipitation hardening Methods 0.000 title claims abstract description 17
- 238000004321 preservation Methods 0.000 claims abstract description 51
- 238000001816 cooling Methods 0.000 claims abstract description 46
- 239000000243 solution Substances 0.000 claims abstract description 30
- 230000032683 aging Effects 0.000 claims abstract description 25
- 239000006104 solid solution Substances 0.000 claims abstract description 8
- 238000009826 distribution Methods 0.000 abstract description 10
- 239000011159 matrix material Substances 0.000 abstract description 5
- 229910000601 superalloy Inorganic materials 0.000 description 13
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 10
- 238000005728 strengthening Methods 0.000 description 10
- 230000000630 rising effect Effects 0.000 description 8
- 238000009792 diffusion process Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000006355 external stress Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000011534 incubation Methods 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
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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
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Abstract
The invention belongs to the technical field of heat treatment of high-temperature alloy, and particularly relates to a heat treatment method for eliminating double grains of a precipitation hardening type high-temperature alloy forging. The method comprises the steps of heating a high-temperature alloy forging to a first temperature for first heat preservation, and cooling to obtain a pretreated forging; heating the pretreated forging to a second temperature for second heat preservation, and cooling to obtain a solid solution treated forging; and heating the solution treatment forging to a third temperature for third heat preservation, then cooling to a fourth temperature for fourth heat preservation, and cooling to obtain the aging treatment forging. According to the heat treatment method provided by the invention, the matrix structure is homogenized through pretreatment and then subjected to solution treatment and aging treatment, so that double grains of the precipitation hardening type high-temperature alloy forging are eliminated, the grain size difference of grains with different sizes and different distribution forms is controlled within 3 levels, the impact performance and high-temperature durability of the forging are improved, and the product quality is greatly improved.
Description
Technical Field
The invention belongs to the technical field of heat treatment of high-temperature alloy, and particularly relates to a heat treatment method for eliminating double grains of a precipitation hardening type high-temperature alloy forging.
Background
The gas turbine is an important power device in marine ships, aerospace and power generation industries, and iron-based and nickel-based high-temperature alloys are mostly adopted as the gas turbine blade in order to meet the requirements of corrosion resistance and oxidation resistance under high-temperature conditions. Superalloys can be classified into solid solution strengthening type and precipitation hardening type according to the type of alloy strengthening. Precipitation hardening superalloys are used in gas turbines. With the development of gas turbines, the requirements on the superalloy are not only mechanical properties, but also on the metallographic structure thereof, i.e. the presence of double grains (i.e. grain size differences exceeding three levels) is not allowed. However, due to broken crystals generated in the forging process, when the high-temperature alloy is subjected to a normal heat treatment process, the broken crystals are used as particle nucleation and grow up, so that two or more grains with different sizes and distribution forms are arranged in a tissue, and when the grain size exceeds 3 levels, the problems of low impact performance, low high-temperature durability and the like of the forge piece can be caused.
Disclosure of Invention
The invention aims to provide a heat treatment method for eliminating double grains of a precipitation hardening type high-temperature alloy forging, which can control the grain size difference of grains with different sizes and different distribution forms within 3 grades, and improve the impact performance and high-temperature durability of the forging, thereby greatly improving the product quality.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a heat treatment method for eliminating double grains of a precipitation hardening type high-temperature alloy forging, which comprises the following steps:
step S1, heating the high-temperature alloy forging to a first temperature for first heat preservation, and cooling to obtain a pretreated forging; the first temperature is 80-110 ℃ above critical temperature Ac3 or Ac 1;
s2, heating the pretreated forging to a second temperature for second heat preservation, and cooling to obtain a solid solution treated forging; the second temperature is 30-50 ℃ above the critical temperature Ac3 or Ac 1;
step S3, heating the solution treatment forging to a third temperature for third heat preservation, then cooling to a fourth temperature for fourth heat preservation, and cooling to obtain an aging treatment forging; the third temperature is 800-820 ℃, and the fourth temperature is 700-750 ℃.
Preferably, the time of the first heat preservation is 20-50 min.
Preferably, in step S1: the charging temperature of the high-temperature alloy forging piece is less than or equal to 800 ℃, and the heating rate of the high-temperature alloy forging piece to the first temperature is less than or equal to 300 ℃/h.
Preferably, in step S2, the temperature-increasing program for increasing the temperature to the second temperature is: heating the pretreated forging to an intermediate temperature for intermediate heat preservation, and then heating from the intermediate temperature to a second temperature; the intermediate temperature is 820-870 ℃, and the intermediate heat preservation time is 1-1.5 h.
Preferably, the second heat preservation time is more than or equal to 0.5h.
Preferably, in step S2: the charging temperature of the pretreated forging is less than or equal to 800 ℃, and the heating rate of the pretreated forging to the intermediate temperature and the second temperature is independently less than or equal to 100 ℃/h.
Preferably, the third heat preservation time is more than or equal to 20 hours; the fourth heat preservation time is 20-24 h.
Preferably, in step S3: the charging temperature of the solution treatment forging is less than or equal to 800 ℃, and the heating rate of the solution treatment forging to the third temperature is less than or equal to 300 ℃/h.
Preferably, in step S3: the cooling rate from the third temperature to the fourth temperature is 60-80 ℃/h.
Preferably, in step S1: the cooling mode is air cooling; in step S2: the cooling mode is oil cooling; in step S3: the cooling mode is air cooling.
The invention provides a heat treatment method for eliminating double grains of a precipitation hardening type high-temperature alloy forging, which comprises the following steps: step S1, heating the high-temperature alloy forging to a first temperature for first heat preservation, and cooling to obtain a pretreated forging; the first temperature is 80-110 ℃ above critical temperature Ac3 or Ac 1; s2, heating the pretreated forging to a second temperature for second heat preservation, and cooling to obtain a solid solution treated forging; the second temperature is 30-50 ℃ above the critical temperature Ac3 or Ac 1; step S3, heating the solution treatment forging to a third temperature for third heat preservation, then cooling to a fourth temperature for fourth heat preservation, and cooling to obtain an aging treatment forging; the third temperature is 800-820 ℃, and the fourth temperature is 700-750 ℃. The heat treatment method provided by the invention comprises three parts of pretreatment, solution treatment and aging treatment; the pretreatment temperature is controlled to be 80-110 ℃ higher than critical temperature Ac3 or Ac1, so that the atomic diffusion capacity of the high-temperature alloy forging is improved, the alloy atomic distribution tends to be uniform, and the elastic strain energy of lattice distortion is reduced, thereby reducing the initial grain size difference and reducing the precondition of forming double grains; then, the plasticity and toughness of the high-temperature alloy forging are effectively improved through solution treatment; finally, two-stage aging treatment is adopted, aging treatment is sequentially carried out at the temperature of 800-820 ℃ and at the temperature of 700-750 ℃, so that the high-temperature alloy forging can generate a second phase taking a gamma ' phase as a main strengthening phase, the two-stage aging treatment can enable the gamma ' phase in the forging to be fully precipitated, and the size of the gamma ' phase is controlled, thereby improving the strength of the forging. In conclusion, the heat treatment method provided by the invention homogenizes the matrix structure in a pretreatment mode and then carries out solution treatment and aging treatment, so that double grains of the precipitation hardening type high-temperature alloy forging are eliminated, the grain size difference of grains with different sizes and different distribution forms is controlled within 3 levels, the impact performance and high-temperature durability of the forging are improved, and the product quality is greatly improved.
Drawings
In order to more clearly illustrate the embodiments of the present invention, the drawings that are required to be used in the embodiments will be briefly described below, and it will be apparent that the drawings in the following description are only some embodiments of the present invention and that other drawings may be obtained from these drawings without inventive effort to those skilled in the art.
FIG. 1 is a metallographic structure (100X) of the heat treatment of comparative example 1;
FIG. 2 shows the metallographic structure (100X) after heat treatment in example 1;
FIG. 3 shows the primary carbide metallographic structure (100 x) after heat treatment in example 1;
FIG. 4 shows the metallographic structure (100X) of comparative example 2 after heat treatment.
Detailed Description
The invention provides a heat treatment method for eliminating double grains of a precipitation hardening type high-temperature alloy forging, which comprises the following steps:
step S1, heating the high-temperature alloy forging to a first temperature for first heat preservation, and cooling to obtain a pretreated forging; the first temperature is 80-110 ℃ above critical temperature Ac3 or Ac 1;
s2, heating the pretreated forging to a second temperature for second heat preservation, and cooling to obtain a solid solution treated forging; the second temperature is 30-50 ℃ above the critical temperature Ac3 or Ac 1;
step S3, heating the solution treatment forging to a third temperature for third heat preservation, then cooling to a fourth temperature for fourth heat preservation, and cooling to obtain an aging treatment forging; the third temperature is 800-820 ℃, and the fourth temperature is 700-750 ℃.
In the present invention, all preparation materials/components are commercially available products well known to those skilled in the art unless specified otherwise.
The method comprises the steps of heating a high-temperature alloy forging to a first temperature for first heat preservation, and cooling to obtain a pretreated forging; the first temperature is 80-110 ℃ above critical temperature Ac3 or Ac 1. The invention improves the atomic diffusion capacity through pretreatment, makes the atomic distribution tend to be uniform, and reduces the elastic strain energy of lattice distortion, thereby reducing the initial grain size difference and reducing the precondition of forming double grains.
In the invention, the superalloy forging is a precipitation hardening superalloy forging. The forging method and the alloy type of the precipitation hardening type high-temperature alloy forging have no special requirements. In a specific embodiment of the invention, the superalloy forging is specifically a GH2026 precipitation-strengthened superalloy forging.
In the invention, the charging temperature of the high-temperature alloy forging is preferably less than or equal to 800 ℃, more preferably 600-800 ℃, and even more preferably 650-750 ℃. And when the charging temperature is the temperature of the furnace when the high-temperature alloy forging is pretreated, the high-temperature alloy is charged into the furnace. In the invention, the charging temperature of the high-temperature alloy forging cannot be too high or too low, and the uniformity of components of the pretreated forging obtained by the too high charging temperature is poor, so that the initial grain size difference cannot be reduced, and double grains are generated; too low a charging temperature causes energy waste. In the present invention, the temperature rising rate of the temperature to the first temperature is preferably 300 ℃/h or less, more preferably 200 to 250 ℃/h. The invention can uniformly heat the high-temperature alloy forging by controlling the temperature rising rate of the first temperature, transfer energy to atoms in the high-temperature alloy more efficiently, and reduce the elastic strain energy of lattice distortion. In the invention, the heating rate of the stainless steel heated to the first temperature cannot be too fast or too slow, and when the heating rate of the stainless steel heated to the first temperature is too fast, the stainless steel is not uniform inside and outside, so that cracks are generated; when the temperature rising rate of the first temperature is slow, the crystal grains become coarse, and the heat treatment cost increases.
In the present invention, the first temperature is 80 to 110 ℃ above the critical temperature Ac3 or Ac1, preferably 90 to 105 ℃, and more preferably 95 to 100 ℃. The present invention preferably increases the atomic diffusivity by controlling the temperature of the pretreatment, tends to homogenize the atomic distribution, and reduces the lattice distortion elastic strain energy, thereby reducing the initial grain size difference. In the invention, the first temperature cannot be too low or too high, and when the first temperature is too low, atoms in the alloy cannot obtain enough energy, the diffusion capability is poor, and the micro-composition uniformity of the forging piece is poor; when the first temperature is too high, not only the energy consumption of heat treatment is increased and the cost is increased, but also the too high pretreatment temperature can cause tissue overburning and unqualified product performance.
In the present invention, the time of the first heat-retaining is preferably 20 to 50 minutes, more preferably 25 to 45 minutes, and still more preferably 30 to 40 minutes. The invention preferably controls the first heat preservation time to ensure that atoms in the alloy forging have enough diffusion time to homogenize the distribution of the atoms in the alloy. In the invention, the first heat preservation time cannot be too short or too long, the first heat preservation time is too short, the atomic diffusion time is insufficient, and the homogenization of the components of the alloy forging is affected; the first heat preservation time is too long, so that the grain growth is large, the whole body is in a coarse crystal state, the grain size meeting the requirement cannot be obtained through subsequent heat treatment, and the performance cannot be ensured.
In the present invention, the mode of cooling after pretreatment is preferably air cooling, and the present invention preferably cools the pretreated forging to room temperature.
After the pretreated forging is obtained, the temperature of the pretreated forging is raised to a second temperature for second heat preservation, and the solution treatment forging is obtained after cooling; the second temperature is 30-50 ℃ above the critical temperature Ac3 or Ac 1. The invention preferably improves the plasticity and toughness of superalloy forgings by solution treatment.
In the invention, the charging temperature of the pretreated forging is preferably less than or equal to 800 ℃, more preferably 600-800 ℃. The higher the furnace charging temperature of the solution treatment is, the longer the heat preservation time is required at the high temperature, the larger the grain growth trend is, and the lower the furnace charging temperature is, so that the heat treatment cost is increased. The temperature-increasing program for increasing the temperature to the second temperature is preferably: and heating the pretreated forging to the intermediate temperature for intermediate heat preservation, and then heating from the intermediate temperature to the second temperature. The intermediate temperature is preferably 820 to 870 ℃, more preferably 830 to 860 ℃. The intermediate incubation time is preferably 1 to 1.5 hours, more preferably 1 to 1.3 hours. The temperature rising rate of the temperature rising to the intermediate temperature is preferably not more than 100 ℃/h, more preferably 80 to 100 ℃/h. According to the invention, the intermediate temperature and the intermediate heat preservation process are preferably arranged in the heating process of the solution treatment, so that the temperature rise of the whole structure of the pretreated forging is ensured to be more uniform, and the influence on the effect of the solution treatment due to the overlarge temperature difference between the inside and the outside of the pretreated forging is avoided.
In the present invention, the second temperature is preferably 35 to 45 ℃ above the critical temperature Ac3 or Ac1, and preferably 38 to 42 ℃. The invention preferably controls the heat preservation temperature of the solution treatment, and can improve the plasticity and toughness of the high-temperature alloy forging piece at the same time. In the invention, the second temperature cannot be too high or too low, and in the invention, the solution treatment is to dissolve carbide and gamma ' in the matrix to obtain uniform supersaturated solid solution, so that strengthening phases such as carbide and gamma ' with fine particles and uniform distribution are re-precipitated during aging, when the temperature is too low, the carbide and gamma ' phases cannot be dissolved in the matrix, the precipitation of the subsequent strengthening phases is affected, the grain growth refined after forging is caused when the temperature is too high, and the grain size is not in accordance with the requirements. The second heat preservation time is preferably more than or equal to 0.5h, more preferably 0.5-2 h. The second heat preservation time is mainly determined by the effective thickness of the forge piece, the heat preservation time is too long to cause coarse grains, and the heat preservation time is too short to cause incomplete solid solution, so that the heat preservation time is selected according to the requirement, and carbide and gamma' phases in a substrate are ensured to be dissolved. The heating rate from the intermediate temperature to the second temperature is preferably less than or equal to 100 ℃/h, more preferably 60-100 ℃/h, and the heating rate is too high, so that the internal and external stress of the tissue is too high, and micro cracks can be possibly caused; if the temperature rising rate is too slow, the tissue may not be completely dissolved, and the performance may not be required.
In the present invention, the means for cooling after the solution treatment is preferably oil cooling. The solution treated forging is preferably cooled to room temperature.
After a solution treatment forging is obtained, the solution treatment forging is heated to a third temperature for third heat preservation, then cooled to a fourth temperature for fourth heat preservation, and an aging treatment forging is obtained after cooling; the third temperature is 800-820 ℃, and the fourth temperature is 700-750 ℃. The invention adopts two-stage aging, and sequentially ages at 800-820 ℃ and 700-750 ℃ to generate second phases with different sizes and types, thereby obtaining the best performance combination, wherein the gamma' phase is the main strengthening phase. According to the invention, the two-stage aging treatment can improve the filling and analyzing quantity of the gamma 'phase in the high-temperature alloy, control the size of the gamma' phase and improve the strength of the forging.
In the present invention, the charging temperature of the solution treated forging is preferably 800 ℃ or less, more preferably 600 to 800 ℃. The longer the holding time at high temperatures is required, the greater the tendency for grain growth, and the lower the charging temperature will result in increased heat treatment costs. The third temperature is preferably 815 ℃. The time of the third heat preservation is preferably more than or equal to 20 hours, more preferably 20-24 hours. The temperature rising rate of the temperature rising to the third temperature is preferably not more than 300℃C/h, more preferably 100 to 300℃C/h, still more preferably 120 to 300℃C/h. The fourth temperature is preferably 730 ℃, and the fourth heat preservation time is preferably 20-24 h. The cooling rate from the third temperature to the fourth temperature is preferably 60 to 80℃per hour, particularly preferably 60℃per hour, 65℃per hour, 70℃per hour, 75℃per hour or 80℃per hour. In a specific embodiment of the present invention, the implementation of the cooling from the third temperature to the fourth temperature is preferably furnace-cooling. According to the invention, the temperature of the first stage ageing treatment of the two stage ageing treatment is controlled to be 800-820 ℃, and the temperature of the second stage ageing treatment is controlled to be 700-750 ℃, and according to researches, the precipitation quantity of gamma 'strengthening phases in the single stage ageing process is less than that of gamma' strengthening phases in the two stage ageing process, so that the requirement on high-temperature service performance is high when the engine is used, and the two stage ageing is needed.
In the present invention, the cooling means after the aging treatment is preferably air cooling.
The heat treatment method provided by the invention comprises three parts of pretreatment, solution treatment and pretreatment; the invention improves the atomic diffusion capacity of the high-temperature alloy forging by controlling pretreatment, can lead the alloy atomic distribution to be uniform, and reduces the elastic strain energy of lattice distortion, thereby reducing the initial grain size difference and reducing the precondition of forming double grains; then, the plasticity and toughness of the high-temperature alloy forging are effectively improved through solution treatment; finally, the invention adopts two-stage aging, which can lead the high-temperature alloy forging to generate different second phases taking the gamma ' phase as the main strengthening phase, and the two-stage aging treatment can lead the gamma ' phase in the forging to be fully separated out, and the size of the gamma ' phase is controlled not to be excessively large, thereby improving the strength of the forging. In conclusion, the heat treatment method provided by the invention homogenizes the matrix structure in a pretreatment mode and then carries out solution treatment and aging treatment, so that double grains of the precipitation hardening type high-temperature alloy forging are eliminated, the grain size difference of grains with different sizes and different distribution forms is controlled within 3 levels, the impact performance and high-temperature durability of the forging are improved, and the product quality is greatly improved.
The technical solutions provided by the present invention are described in detail below in conjunction with examples for further illustrating the present invention, but they should not be construed as limiting the scope of the present invention.
The following experiments were performed using GH2026 precipitation-strengthened superalloy as an example in the following examples and comparative examples. GH2026 is Fe-Ni-Co-Cr base precipitation hardening deformation superalloy, the long-term use temperature range is 540-570 ℃, and the maximum use temperature can reach 677 ℃. In the following examples and comparative examples, a GH2026 precipitation-strengthened superalloy was forged to yield a GH2026 precipitation-strengthened superalloy forging. Comparative example 1 is a conventional heat treatment system (see table 1), the structure of the forging subjected to the heat treatment method is shown in fig. 1, and it can be seen from fig. 1 that coarse grains and fine grains are unevenly distributed, and the size scale exceeds three or more stages. Example 1 and comparative example 2 forgings obtained by conventional heat treatment were subjected to heat treatment by taking 3 samples of 20mm×20mm×100mm on the forgings obtained in comparative example 1 for eliminating double crystal grains, and the heat treatment schedule is shown in table 1.
Table 1 Heat treatment System for comparative examples and examples
The mechanical properties of the samples subjected to the heat treatment process provided by the embodiment 1 are shown in the table 1, and the samples subjected to the heat treatment of the invention have higher mechanical properties and meet the requirements of a steam turbine on high-temperature alloy. And (3) injection: the customer criteria in table 1 are related requirements of the current market for GH2026 precipitation strengthening superalloys mechanical properties.
TABLE 1 mechanical Properties of example 1 after Heat treatment
The metallographic structure of the sample 1 after the heat treatment in the example 1 is shown in fig. 2, the double grain size in the metallographic structure of the sample 1 after the heat treatment in the example 1 is reduced from the original 2.5-6 grade (shown in fig. 1) to 3-5.5 grade (shown in fig. 2), the requirement of customers is met, and primary carbide in the high-power structure does not exceed the 6 grade requirement (shown in fig. 3) specified in GB/T14999.6.
Samples 1 and 2 after the heat treatment of this example 1 were not broken after the high temperature endurance test at 650℃and 380MPa for 100 hours.
The metallographic structure of the sample 3 after the heat treatment of the comparative example 2 is shown in fig. 4, the double grain size of the metallographic structure of the sample 1 after the heat treatment of the comparative example 2 is reduced from the original 2.5-6 level (shown in fig. 1) to 2-5.5 level (shown in fig. 4), the double grain size is more than three levels, and the individual grains exceed 1 level, so that the requirements of customers are not met.
The process and embodiments of the present invention are illustrated in this specification by specific examples, which are presented only to aid in understanding the process and core concepts of the present invention; also, it is within the scope of the present invention to be modified by those of ordinary skill in the art in light of the present teachings. In view of the foregoing, this description should not be construed as limiting the invention.
Claims (10)
1. The heat treatment method for eliminating the double grains of the precipitation hardening type high-temperature alloy forging is characterized by comprising the following steps of:
step S1, heating the high-temperature alloy forging to a first temperature for first heat preservation, and cooling to obtain a pretreated forging; the first temperature is 80-110 ℃ above critical temperature Ac3 or Ac 1;
s2, heating the pretreated forging to a second temperature for second heat preservation, and cooling to obtain a solid solution treated forging; the second temperature is 30-50 ℃ above the critical temperature Ac3 or Ac 1;
step S3, heating the solution treatment forging to a third temperature for third heat preservation, then cooling to a fourth temperature for fourth heat preservation, and cooling to obtain an aging treatment forging; the third temperature is 800-820 ℃, and the fourth temperature is 700-750 ℃.
2. The heat treatment method according to claim 1, wherein the first heat preservation time is 20 to 50 minutes.
3. The heat treatment method according to claim 1 or 2, wherein in step S1: the charging temperature of the high-temperature alloy forging piece is less than or equal to 800 ℃, and the heating rate of the high-temperature alloy forging piece to the first temperature is less than or equal to 300 ℃/h.
4. The heat treatment method according to claim 1, wherein in step S2, the temperature-increasing program for increasing the temperature to the second temperature is: heating the pretreated forging to an intermediate temperature for intermediate heat preservation, and then heating from the intermediate temperature to a second temperature; the intermediate temperature is 820-870 ℃, and the intermediate heat preservation time is 1-1.5 h.
5. The heat treatment method according to claim 1 or 4, wherein the second heat preservation time is not less than 0.5 hours.
6. The heat treatment method according to claim 1 or 4, wherein in step S2: the charging temperature of the pretreated forging is less than or equal to 800 ℃, and the heating rate of the pretreated forging to the intermediate temperature and the second temperature is independently less than or equal to 100 ℃/h.
7. The heat treatment method according to claim 1, wherein the time of the third heat preservation is not less than 20 hours; the fourth heat preservation time is 20-24 h.
8. The heat treatment method according to claim 1 or 7, wherein in step S3: the charging temperature of the solution treatment forging is less than or equal to 800 ℃, and the heating rate of the solution treatment forging to the third temperature is less than or equal to 300 ℃/h.
9. The heat treatment method according to claim 1 or 7, wherein in step S3: the cooling rate from the third temperature to the fourth temperature is 60-80 ℃/h.
10. The heat treatment method according to claim 1, wherein in step S1: the cooling mode is air cooling; in step S2: the cooling mode is oil cooling; in step S3: the cooling mode is air cooling.
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