CN116397184A - Heat treatment process and application of nickel-based superalloy - Google Patents
Heat treatment process and application of nickel-based superalloy Download PDFInfo
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 95
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 71
- 229910000601 superalloy Inorganic materials 0.000 title claims abstract description 48
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 34
- 238000000034 method Methods 0.000 title claims abstract description 31
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 70
- 239000000956 alloy Substances 0.000 claims abstract description 70
- 238000001816 cooling Methods 0.000 claims abstract description 41
- 230000032683 aging Effects 0.000 claims abstract description 28
- 238000001556 precipitation Methods 0.000 claims abstract description 22
- 238000004321 preservation Methods 0.000 claims abstract description 5
- 239000002245 particle Substances 0.000 claims description 14
- 238000005516 engineering process Methods 0.000 abstract description 4
- 230000007547 defect Effects 0.000 abstract description 2
- 239000000243 solution Substances 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 9
- 239000013078 crystal Substances 0.000 description 9
- 238000012360 testing method Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 5
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 4
- 238000011161 development Methods 0.000 description 4
- 230000018109 developmental process Effects 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 230000008520 organization Effects 0.000 description 3
- 238000010248 power generation Methods 0.000 description 3
- 239000003153 chemical reaction reagent Substances 0.000 description 2
- 239000003245 coal Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000002045 lasting effect Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 230000008642 heat stress Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000000463 material Substances 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
- 230000005501 phase interface Effects 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000779 smoke Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 230000008646 thermal stress Effects 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
-
- 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
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
-
- 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%
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F27—FURNACES; KILNS; OVENS; RETORTS
- F27D—DETAILS OR ACCESSORIES OF FURNACES, KILNS, OVENS, OR RETORTS, IN SO FAR AS THEY ARE OF KINDS OCCURRING IN MORE THAN ONE KIND OF FURNACE
- F27D9/00—Cooling of furnaces or of charges therein
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
Abstract
The heat treatment process of nickel-base superalloy and its application belong to the field of heat treatment technology of heat-resisting alloy, and can overcome the defect of existent technology that its tensile property and durability can not be synchronously raised. The heat treatment process of the nickel-based superalloy comprises the following steps: (1) Heating the rolled nickel-based superalloy to 180-250 ℃ below the liquidus temperature of the alloy with a furnace at a heating rate of not higher than 20 ℃/min, preserving heat for 0.5-3h, and air cooling to room temperature after the heat preservation is finished; (2) Heating the nickel-base superalloy treated in the step (1) to a grain boundary second phase M along with a furnace at a heating rate of not higher than 20 ℃/min 6 C, carrying out high-temperature aging treatment at 120-150 ℃ below the precipitation starting temperature, and then air-cooling to room temperature; (3) Heating the nickel-base superalloy treated in the step (2) to the gamma' -phase starting precipitation temperature along with a furnace at a heating rate of not higher than 20 ℃/minAnd (3) performing low-temperature aging treatment at 200-250 ℃ below the temperature, and then performing air cooling to room temperature.
Description
Technical Field
The invention belongs to the technical field of heat-resistant alloy heat treatment, and particularly relates to a heat treatment process of a nickel-based superalloy and application thereof.
Background
In the energy consumption structure of China, coal accounts for more than 70% of primary energy, and thermal power generation accounts for more than 75% of the total power generation of China. Based on the current situation of energy structure and energy consumption in China, in order to relieve the increasingly severe environmental pressure and realize sustainable development of nature, economy and society, the development of 700 ℃ grade ultra-supercritical coal power generation technology is particularly important in China. The development of high-parameter ultra-supercritical units is largely limited by the development of materials technology in terms of design and choice of parameters. The key high-temperature parts of the boiler not only require the heat-resistant alloy to have higher high-temperature strength, smoke corrosion resistance and steam oxidation corrosion resistance, but also have better high-temperature plasticity. The key parts of the boiler bear larger stress and higher temperature, and if the heat-resistant superalloy has higher high-temperature tensile strength and lasting strength, the operation safety and economy of the thermal power generating unit can be obviously improved. For the critical parts of the ultra-supercritical power station, the conventional steel grade cannot meet the requirements, and precipitation strengthening nickel base and iron-nickel base alloy with stronger temperature bearing capability must be used.
The nickel-base superalloy for 700 ℃ grade boiler is mainly precipitation strengthening superalloy, and the strength of the superalloy is closely related to microstructure characteristic parameters of gamma' phase. When the gamma' -phase particle size is small, the alloy has excellent tensile strength, low tensile plasticity, and poor endurance strength. And when the particle size is larger, the alloy has higher endurance strength and higher plasticity, which tends to result in a decrease in the high-temperature tensile strength of the alloy.
Disclosure of Invention
Therefore, in order to overcome the defect that the tensile property and the durability cannot be synchronously improved in the prior art, the invention provides a heat treatment process of a nickel-based superalloy and application thereof.
For this purpose, the invention provides the following technical scheme.
A heat treatment process of a nickel-based superalloy, comprising the steps of:
(1) Heating the rolled nickel-based superalloy to 180-250 ℃ below the liquidus temperature of the alloy with a furnace at a heating rate of not higher than 20 ℃/min, preserving heat for 0.5-3h, and cooling to room temperature after the heat preservation is finished;
(2) Heating the nickel-base superalloy treated in the step (1) to a grain boundary second phase M along with a furnace at a heating rate of not higher than 20 ℃/min 6 Performing high-temperature aging treatment at 120-150 ℃ below the initial precipitation temperature of the C carbide, and then cooling to room temperature;
(3) Heating the nickel-based superalloy treated in the step (2) with a furnace at a heating rate of not more than 20 ℃/min to 200-250 ℃ below the starting precipitation temperature of the gamma' -phase, performing low-temperature aging treatment, and then cooling to room temperature.
Further, the nickel-based superalloy comprises, in mass percent: c:0.04-0.08%, cr:19-21%, co:9-11%, mo:8-9%, ti:1.9-2.3%, al:1.3 to 1.7 percent, fe: less than or equal to 1.5 percent, mn: less than or equal to 0.3 percent, si: less than or equal to 0.15 percent, B: less than or equal to 0.005 percent, and the balance of Ni.
Further, in the step (1), the nickel-based superalloy is a nickel-based superalloy rod with a diameter of 140-160 mm.
Further, in the step (2), the time of the high-temperature aging treatment is 1-3 hours.
Further, in the step (3), the time of the low-temperature aging treatment is 24-48 hours.
Further, in the step (1) and/or (2), cooling is performed by air cooling.
Further, in the step (3), cooling is performed by air cooling.
An alloy after the heat treatment process.
Further, the grain size of the alloy is 100-130 mu m, the average grain size of gamma 'phase is 45-55nm, and the volume fraction of gamma' phase is 18-19.5%.
The alloy is applied to a 700 ℃ grade boiler.
The technical scheme of the invention has the following advantages:
1. the heat treatment process of the nickel-based superalloy provided by the invention comprises the following steps: (1) Heating the rolled nickel-base superalloy to 180-250 ℃ below the liquidus temperature of the alloy with a furnace at a heating rate of not higher than 20 ℃/min, preserving heat for 0.5-3h, and cooling to room temperature after the heat preservation is finished; (2) Heating the nickel-base superalloy treated in the step (1) to a grain boundary second phase M along with a furnace at a heating rate of not higher than 20 ℃/min 6 C, carrying out high-temperature aging treatment at 120-150 ℃ below the precipitation starting temperature, and then cooling to room temperature; (3) Heating the nickel-based superalloy treated in the step (2) with a furnace at a heating rate of not more than 20 ℃/min to 200-250 ℃ below the starting precipitation temperature of the gamma' -phase, performing low-temperature aging treatment, and then cooling to room temperature.
The control of the solution treatment temperature in the step (1) is that the solution treatment temperature ensures the solubility of the matrix to the element and activates the diffusion capacity of the element. The solution treatment time is controlled so as to dissolve a precipitated phase precipitated in the crystal grains in the hot working process in the matrix, recrystallize the structure in a rolled state, grow up the crystal grains, eliminate segregation, and simultaneously dissolve all the second phases in the crystal and the crystal boundary in the matrix. The purpose of the high-temperature aging in the step (2) is to promote the sufficient precipitation of a grain boundary precipitation phase, improve the strength of a phase interface, prevent the alloy from cracking along the grain boundary and ensure that the heat-resistant alloy has good tensile plasticity; the purpose of the low-temperature aging in the step (3) is to promote the sufficient precipitation and growth of gamma' -phase particles of the main strengthening phase of the alloy so as to improve the strength of the alloy. The average size of the gamma' -phase particles of the alloy prepared by the heat treatment process is about 45-55nm, the volume fraction of the precipitated phase is 18-19.5%, and the high-temperature tensile strength, tensile plasticity and endurance strength of the alloy are improved.
The invention adopts the heating rate of not higher than 20 ℃/min to carry out slow heating so as to reduce the thermal stress in the heating process, thereby inhibiting precipitation of harmful phase at the grain boundary, preventing the grain boundary from cracking and improving the tensile plasticity of the alloy.
2. In the heat treatment process provided by the invention, in the step (1), the nickel-based superalloy is a nickel-based superalloy rod with the diameter of 140-160 mm. The nickel-based superalloy with larger size can promote the grain boundary and gamma' phase particles in the crystal to grow up rapidly in the heating and cooling processes, thereby improving the strength and plasticity of the alloy.
3. The heat treatment process provided by the invention adopts an air cooling mode to cool, so that the heat stress induced in the cooling process can be reduced, the precipitation of harmful phases at the grain boundary can be further inhibited, nucleation spots are provided for the precipitation of the precipitated phases in the aging process, the precipitation and growth of gamma '-phase particles are promoted, and the average size of the gamma' -phase particles is ensured to be 45-55 nm.
Through aging treatment, tiny and continuous precipitated phases are precipitated in an alloy matrix and a grain boundary, so that the alloy strength is improved, the grain boundary and the grain boundary of the alloy have good performance matching, and the tensile strength and the lasting strength are obviously improved under the condition that the alloy has good plasticity in the deformation process.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings that are needed in the description of the embodiments or the prior art will be briefly described, and it is obvious that the drawings in the description below are some embodiments of the present invention, and other drawings can be obtained according to the drawings without inventive effort for a person skilled in the art.
FIG. 1 is a low-power tissue structure after the treatment of step 1 of example 1;
FIG. 2 is a grain boundary structure after the treatment of step 2 of example 1;
FIG. 3 is an alloy intragranular gamma/gamma' structure after the treatment of step 3 of example 1;
FIG. 4 is a grain boundary structure after the step 2 treatment of comparative example 1;
FIG. 5 shows the intra-crystalline gamma/gamma' organization after the treatment of step 3 of comparative example 1.
Detailed Description
The following examples are provided for a better understanding of the present invention and are not limited to the preferred embodiments described herein, but are not intended to limit the scope of the invention, any product which is the same or similar to the present invention, whether in light of the present teachings or in combination with other prior art features, falls within the scope of the present invention.
The specific experimental procedures or conditions are not noted in the examples and may be followed by the operations or conditions of conventional experimental procedures described in the literature in this field. The reagents or apparatus used were conventional reagent products commercially available without the manufacturer's knowledge.
The invention relates to a heat treatment process of a nickel-based superalloy, which comprises the following steps:
1) Taking a rolled nickel-based superalloy rod with the diameter of 140-160mm, wherein the deformed nickel-based superalloy comprises the following components in percentage by mass: 0.04-0.08%, cr:19-21%, co:9-11%, mo:8-9%, ti:1.9-2.3%, al:1.3 to 1.7 percent, fe: less than or equal to 1.5 percent, mn: less than or equal to 0.3 percent, si: less than or equal to 0.15 percent, B: less than or equal to 0.005 percent, and the balance of Ni.
2) Heating the alloy rod to 180-250 ℃ below the liquidus temperature of the alloy with a furnace at a speed of not higher than 20 ℃/min, preserving heat for 0.5-3h, carrying out solution treatment, and then air-cooling to room temperature to ensure that the grain size of the alloy is 100-130 mu m;
3) Heating the nickel-based superalloy treated in the step 2) to a grain boundary second phase M along with a furnace 6 And C, carrying out high-temperature aging treatment at 120-150 ℃ below the starting precipitation temperature of C, and then air-cooling to room temperature to ensure discontinuous precipitation of carbide at the grain boundary.
4) Heating the nickel-based superalloy treated in the step 3) to 200-250 ℃ below the initial precipitation temperature of the gamma ' phase of the main strengthening phase along with a furnace, performing low-temperature aging treatment, and then air-cooling to room temperature, so as to ensure that the average size of the gamma ' phase particles of the alloy is about 45-55nm, and the volume fraction of the gamma ' phase is 18-19.5%.
TABLE 1 Components of the Nickel-based alloy superalloy rods of examples 1-4 and comparative example 1 wt%
| Ni | Cr | Co | Mo | Ti | Al | Fe | Si | Mn | C | B |
| Bal. | 20 | 10 | 8.5 | 2.1 | 1.5 | 1.2 | 0.04 | 0.06 | 0.06 | 0.004 |
Alloy liquidus temperature 1346 ℃ and grain boundary second phase M 6 The starting precipitation temperature of C is 1151 ℃, and the starting precipitation temperature of gamma' -phase is 1005 ℃.
Example 1
The embodiment provides a heat treatment process of a nickel-based superalloy, which comprises the following steps:
step 1: taking a rolled nickel-base alloy high-temperature alloy rod with the composition shown in table 1 and the diameter of 150mm, heating to 1140 ℃ with a furnace at a heating rate of 18 ℃/min, preserving heat for 2 hours, and then air-cooling to room temperature to finish solution treatment. The morphology of the solid solution treated sample is shown in FIG. 1, and the average grain size is 120. Mu.m.
Step 2: and (2) heating the nickel-based superalloy rod treated in the step (1) to 1010 ℃ along with a furnace at a heating rate of 18 ℃/min, preserving heat for 2 hours, and then air-cooling to finish high-temperature aging heat treatment, wherein the obtained structure is shown in figure 2. As can be seen from fig. 2, the nickel-base superalloy grain boundary carbide after the treatment of step 2 is discontinuously distributed.
Step 3: and (3) heating the nickel-based superalloy rod treated in the step (1) and the step (2) to 760 ℃ along with a furnace at a heating rate of 18 ℃/min, preserving heat for 24 hours, and then performing air cooling to finish low-temperature aging heat treatment. The internal gamma/gamma' organization structure of the prepared alloy crystal grain is shown in figure 3. The average size of the gamma' -phase particles was 50nm and the volume fraction was 19.3%.
Example 2
The embodiment provides a heat treatment process of a nickel-based superalloy, which comprises the following steps:
step 1: taking a rolled nickel-base alloy high-temperature alloy rod with the composition shown in table 1 and the diameter of 150mm, heating to 1145 ℃ with a furnace at a heating rate of 20 ℃/min, preserving heat for 2 hours, and then air-cooling to room temperature to finish solution treatment. The average size of the alloy grains was 125. Mu.m.
Step 2: and (3) heating the alloy rod treated in the step (1) to 1015 ℃ along with a furnace at a heating rate of 20 ℃/min, preserving heat for 2 hours, and then performing air cooling to finish high-temperature aging heat treatment.
Step 3: and (3) heating the alloy test bar treated in the step (1) and the step (2) to 770 ℃ along with a furnace at a heating rate of 20 ℃/min, preserving heat for 24 hours, and then air-cooling to finish low-temperature aging heat treatment. The average size of the gamma' -phase particles was 53nm and the volume fraction was 19.0%.
Example 3
The embodiment provides a heat treatment process of a nickel-based superalloy, which comprises the following steps:
step 1: taking a rolled nickel-base alloy high-temperature alloy rod with the composition shown in table 1 and the diameter of 140mm, heating to 1145 ℃ with a furnace at a heating rate of 20 ℃/min, preserving heat for 2 hours, and then air-cooling to room temperature to finish solution treatment. The average size of the alloy grains was 125. Mu.m. Step 2: and (3) heating the alloy rod treated in the step (1) to 1020 ℃ along with a furnace at a heating rate of 20 ℃/min, preserving heat for 2 hours, and then air-cooling to finish high-temperature aging heat treatment.
Step 3: and (3) heating the alloy test bar treated in the step (1) and the step (2) to 780 ℃ along with a furnace at a heating rate of 20 ℃/min, preserving heat for 36 hours, and then air-cooling to finish low-temperature aging heat treatment. The average size of the gamma' -phase particles was 55nm and the volume fraction was 18.7%.
Example 4
The embodiment provides a heat treatment process of a nickel-based superalloy, which comprises the following steps:
step 1: taking a rolled nickel-base alloy high-temperature alloy rod with the composition shown in table 1 and the diameter of 140mm, heating to 1145 ℃ with a furnace at a heating rate of 20 ℃/min, preserving heat for 2 hours, and then air-cooling to room temperature to finish solution treatment. The average size of the alloy crystal grains is 125+/-5 mu m.
Step 2: and (3) heating the alloy rod treated in the step (1) to 1018 ℃ along with a furnace at a heating rate of 20 ℃/min, preserving heat for 2 hours, and then air-cooling to finish high-temperature aging heat treatment.
Step 3: and (3) heating the alloy test bar treated in the step (1) and the step (2) to 770 ℃ along with a furnace at a heating rate of 20 ℃/min, preserving heat for 24 hours, and then air-cooling to finish low-temperature aging heat treatment. The average size of the gamma' -phase particles was 53nm and the volume fraction was 19.0%.
Comparative example 1
The comparative example provides a heat treatment process of a nickel-based superalloy, comprising the following steps:
step 1: taking a rolled nickel-base alloy high-temperature alloy rod with the composition shown in table 1 and the diameter of 150mm, directly placing the rolled nickel-base alloy high-temperature alloy rod into a heat treatment furnace at 1140 ℃, preserving heat for 2 hours, and then cooling to room temperature by water to complete solution treatment. The tissue morphology of the solution treated sample is shown in fig. 4. The average size of the alloy crystal grains is 120+/-5 mu m.
Step 2: and (2) directly placing the alloy rod treated in the step (1) into a heat treatment furnace at 1010 ℃, preserving heat for 2 hours, then cooling to room temperature by water, and completing high-temperature aging heat treatment to obtain a structure at a grain boundary as shown in figure 4.
Step 3: and (3) placing the alloy test bar treated in the step (1) and the step (2) into a 788 ℃ heat preservation chamber for 8 hours, and then air cooling to finish low-temperature aging heat treatment. The internal gamma/gamma' organization structure of the alloy crystal grain is shown in figure 5. The average size of the gamma' -phase particles was 21nm and the volume fraction was 18.7%.
Test examples
The tensile strength and tensile plasticity at 760 ℃ of the alloys treated in the examples and comparative examples are shown in Table 2.
Table 2 alloy high temperature tensile plasticity at 760 ℃ and strength test results
| Tensile strength/MPa | Yield strength ofdegree/MPa | Tensile elongation at break/% | |
| Example 1 | 880 | 660 | 34 |
| Example 2 | 875 | 625 | 31 |
| Comparative example 1 | 821 | 598 | 21 |
The alloys treated in the examples and comparative examples were tested for long-term life (i.e., time to fracture) at 760 c/386 MPa and the test results are shown in table 3.
Table 3 durability of alloys at 760 ℃ per 386MPa
As can be seen from comparison between example 1 and comparative example 1, the heat-resistant alloy obtained by the process of the invention has an improved structure at 760 ℃ and high temperature yield strength of 62MPa, an improved tensile strength of 59MPa and an improved high temperature elongation of 61% or more; under 760 ℃/386MPa, the alloy has a prolonged service life of 103% or more, and the high-temperature strength is improved while the alloy is ensured to have excellent tensile plasticity.
It is apparent that the above examples are given by way of illustration only and are not limiting of the embodiments. Other variations or modifications of the above teachings will be apparent to those of ordinary skill in the art. It is not necessary here nor is it exhaustive of all embodiments. And obvious variations or modifications thereof are contemplated as falling within the scope of the present invention.
Claims (10)
1. The heat treatment process of the nickel-based superalloy is characterized by comprising the following steps of:
(1) Heating the rolled nickel-based superalloy to 180-250 ℃ below the liquidus temperature of the alloy with a furnace at a heating rate of not higher than 20 ℃/min, preserving heat for 0.5-3h, and cooling to room temperature after the heat preservation is finished;
(2) Heating the nickel-base superalloy treated in the step (1) to a grain boundary second phase M along with a furnace at a heating rate of not higher than 20 ℃/min 6 Performing high-temperature aging treatment at 120-150 ℃ below the initial precipitation temperature of the C carbide, and then cooling to room temperature;
(3) Heating the nickel-based superalloy treated in the step (2) with a furnace at a heating rate of not more than 20 ℃/min to 200-250 ℃ below the starting precipitation temperature of the gamma' -phase, performing low-temperature aging treatment, and then cooling to room temperature.
2. The heat treatment process according to claim 1, wherein the nickel-base superalloy comprises, in mass percent: c:0.04-0.08%, cr:19-21%, co:9-11%, mo:8-9%, ti:1.9-2.3%, al:1.3 to 1.7 percent, fe: less than or equal to 1.5 percent, mn: less than or equal to 0.3 percent, si: less than or equal to 0.15 percent, B: less than or equal to 0.005 percent, and the balance of Ni.
3. The heat treatment process according to claim 1, wherein in the step (1), the nickel-base superalloy is a nickel-base superalloy rod having a diameter of 140-160 mm.
4. A heat treatment process according to any one of claims 1-3, wherein in step (2), the time for the high temperature ageing treatment is 1-3 hours.
5. A heat treatment process according to any one of claims 1-3, wherein in step (3), the time for the low temperature ageing treatment is 24-48 hours.
6. A heat treatment process according to any one of claims 1-3, wherein in step (1), and/or (2), cooling is performed by means of air cooling.
7. A heat treatment process according to any one of claims 1-3, wherein in step (3), cooling is performed by means of air cooling.
8. An alloy after the heat treatment process according to any one of claims 1 to 7.
9. The alloy of claim 8, wherein the alloy has a grain size of 100-130 μm, a gamma prime phase particle average size of 45-55nm, and a gamma prime phase volume fraction of 18-19.5%.
10. Use of an alloy according to claim 8 or 9 in a 700 ℃ grade boiler.
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