CN112779385A - Heat treatment method of GH901 turbine disc forging - Google Patents
Heat treatment method of GH901 turbine disc forging Download PDFInfo
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- CN112779385A CN112779385A CN202011557008.XA CN202011557008A CN112779385A CN 112779385 A CN112779385 A CN 112779385A CN 202011557008 A CN202011557008 A CN 202011557008A CN 112779385 A CN112779385 A CN 112779385A
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 94
- 238000000034 method Methods 0.000 title claims abstract description 32
- 238000005242 forging Methods 0.000 title claims abstract description 29
- 238000001816 cooling Methods 0.000 claims abstract description 46
- 238000004321 preservation Methods 0.000 claims abstract description 7
- 238000007599 discharging Methods 0.000 claims description 15
- 239000006104 solid solution Substances 0.000 claims description 14
- 238000001556 precipitation Methods 0.000 claims description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 9
- 238000002791 soaking Methods 0.000 claims description 7
- 238000007705 chemical test Methods 0.000 claims description 2
- 238000012545 processing Methods 0.000 abstract description 2
- 230000009467 reduction Effects 0.000 abstract description 2
- 239000013078 crystal Substances 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 5
- 230000002045 lasting effect Effects 0.000 description 5
- 239000010936 titanium Substances 0.000 description 5
- 238000001514 detection method Methods 0.000 description 4
- 238000004090 dissolution Methods 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 238000003483 aging Methods 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 239000011733 molybdenum Substances 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 230000032683 aging Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 235000015895 biscuits Nutrition 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000012797 qualification Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D11/00—Process control or regulation for heat treatments
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/32—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for gear wheels, worm wheels, or the like
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Forging (AREA)
Abstract
The invention belongs to the field of forging heat treatment processing, and relates to a heat treatment method of a GH901 turbine disc forging, which adopts three-step heating heat treatment, and adopts a heat preservation control method of constant temperature raising to high temperature variable frequency heating in two links of furnace entering heat treatment and cooling; preheating at a temperature of not more than 700 ℃, charging into the furnace, heating up to 850 ℃/1000 ℃/1090 ℃ along with the furnace, keeping for a certain time, heating up to a required high temperature of 1080-1090 ℃ along with the furnace, keeping for a corresponding time, and cooling; after the heat treatment, the performance indexes of the forging are as follows: the tensile strength is more than or equal to 1190MPa, the yield strength is more than or equal to 901MPa, the elongation is more than or equal to 14 percent, and the reduction of area is more than or equal to 13 percent; HBW is more than or equal to 344.
Description
Technical Field
The invention belongs to the field of forging heat treatment processing, and relates to a mode of a heat treatment system for a GH901 alloy forging.
Background
The GH901 alloy is an austenite age hardening alloy which takes Fe-43Ni-12Cr as a matrix and is added with elements such as titanium, aluminum, molybdenum and the like, contains a trace amount of boron and lower carbon, is strengthened by metastable gamma '[ Ni3Ti, Al ] phase dispersion, and the trace amount of aluminum can inhibit the conversion of gamma' to eta-Ni 3 Ti. The initial dissolution temperature of the gamma 'phase is 940-950 ℃, and the initial dissolution temperature of the eta phase is 975-995 ℃, so that the gamma' phase and the eta phase are basically stable at 950 ℃, the gamma 'phase and the eta phase are beneficial to compensating the precipitation of the gamma' phase and the eta phase by means of residual strain, and the content is increased. The method is beneficial to releasing distortion energy difference of crystal boundary distortion energy, stabilizing grain size, improving tissue uniformity and helping to reduce ultrasonic flaw detection noise and bottom loss. The high-temperature part of the aerospace engine. Because of its excellent comprehensive performance, it can be extensively used in the fields of aviation and spaceflight, so that it is one of the most extensively-used high-temp. alloys for existent foreign aeroengines.
The GH901 alloy forging has different requirements on the internal structure, so that the control requirements on the parameters of the heat treatment system of the forging are different, if the parameters of the heat treatment system are not controlled in place, the physical and chemical properties of the forging are directly influenced by the change of each parameter,
but the conventional heat treatment system is adopted, so that the product cannot meet the final required requirements, and the product is scrapped to generate great resource waste.
Disclosure of Invention
The purpose of the invention is: the forming method is used for improving the internal structure and further improving the requirement of the flaw detection level of the forging.
In order to solve the technical problem, the technical scheme of the invention is as follows:
the method adopts three-step heating heat treatment, and adopts a heat preservation control method of constant temperature raising to high temperature variable frequency heating in two links of furnace entering heat treatment and cooling.
The method comprises the following steps:
the first step is as follows: solid solution:
putting the forge piece into an electric furnace, heating to 850 +/-10 ℃ at a temperature of less than or equal to 700 ℃, preserving heat for 90 +/-9 min, heating to 1000 +/-10 ℃, preserving heat for 90 +/-9 min, heating to 1090 +/-10 ℃, soaking for 60 +/-6 min, preserving heat for 180 +/-15 min, and discharging and cooling;
the second step is that: primary precipitation:
putting the forge piece into an electric furnace at the temperature of less than or equal to 690 ℃, heating to 750 +/-5 ℃ at the speed of 80-100 ℃/h, preserving heat for 90 +/-9 min, heating to 775 +/-5 ℃, preserving heat for 240 +/-15 min, and discharging and cooling;
the third step: secondary precipitation:
putting the forge piece into an electric furnace at the temperature of less than or equal to 600 ℃, heating to 690 +/-5 ℃ at the speed of 80-100 ℃/h, preserving heat for 180 +/-15 min, heating to 715 +/-5 ℃, preserving heat for 24 +/-0.25 h, and discharging and cooling.
And in the first step, water cooling and air cooling are adopted for cooling. Wherein the water cooling time is more than or equal to 20 min.
And in the second step, the cooling is realized by adopting dispersed air cooling.
And in the third step, the cooling adopts dispersed air cooling.
The method also comprises the step of finally carrying out physical and chemical tests on the forged piece.
After the heat treatment, the performance indexes of the forging are as follows:
stretching at room temperature: the tensile strength is more than or equal to 1130MPa, the yield strength is more than or equal to 810MPa, the elongation is more than or equal to 9 percent,
the reduction of area is more than or equal to 12 percent, and HBW is more than or equal to 341;
and (3) lasting high-temperature combination: the stretching time is more than or equal to 23h, the stretch-breaking is realized, the elongation is more than or equal to 4 percent, and the part is broken and smoothed.
The invention has the beneficial effects that: the method solves the problem of unqualified final physical and chemical properties of the forged piece by adopting different heat treatment regimes and controlling the solid solution time for the forged piece produced in the same flow, and further ensures the internal structure of the forged piece by groping heat treatment parameter control so as to ensure that the mechanical properties all meet the required standard requirements. The method greatly improves the qualification rate of the forged piece.
The GH901 alloy is an austenite age hardening alloy which takes Fe-43Ni-12Cr as a matrix and is added with elements such as titanium, aluminum, molybdenum and the like, contains a trace amount of boron and lower carbon, is strengthened by metastable gamma '[ Ni3Ti, Al ] phase dispersion, and the trace amount of aluminum can inhibit the conversion of gamma' to eta-Ni 3 Ti. The initial dissolution temperature of the gamma 'phase is 940-950 ℃, and the initial dissolution temperature of the eta phase is 975-995 ℃, so that the gamma' phase and the eta phase are basically stable at 950 ℃, the gamma 'phase and the eta phase are beneficial to compensating the precipitation of the gamma' phase and the eta phase by means of residual strain, and the content is increased. Is beneficial to releasing the difference of distortion energy of the grain boundary, stabilizing the grain size and improving the uniformity of the structure.
The key phase influencing the growth of the crystal grains is eta phase, the four heat treatment steps are basically equivalent, the step temperature is near the initial or undissolved eta phase, the steps are reasonable and feasible, certain influence can be generated on the final result, but the decisive influence can not be formed, and the method mainly depends on the high-temperature solid solution time. The longer the 1090 ℃ heat preservation time is, the less the crystal boundary strengthening phase is, the easier the crystal grain grows, on the contrary, because the crystal grain is long, the crystal boundary interface is reduced, the combined lasting failure mode is along the fracture of the crystal boundary, when the passing path is lengthened, the lasting life is longer, and therefore, the high-temperature lasting performance is promoted. The GH901 alloy is an austenite type age hardening alloy which takes Fe-43Ni-12Cr as a matrix and is added with elements such as titanium, aluminum, molybdenum and the like, the longer the heat preservation time at 1090 ℃ is, the more sufficient the dissolved strengthening phase is, and the later aging is realized, and the Gamma' phases with different sizes are separated out, so that the effect on the improvement of the combination lasting mechanical property is better, and particularly the elongation plasticity index is improved.
The method adopts different heat treatment regimes for the forged piece produced in the same flow, and the biggest difference is that the solid solution time is controlled, namely the longer the solid solution time is, the higher the high-temperature durability is facilitated, but the mechanical property of the forged piece is unqualified, the internal structure of the forged piece needs fine and uniform crystal grains, but the high durability needs to meet the requirement of the forged piece, the crystal grains need to be relatively coarse, the crystal boundary has gamma' phase distribution with proper size, and a parameter control balance point needs to be further searched in engineering practice to further ensure a structure balance point, so that the mechanical property can meet the required standard requirement.
And controlling the solid solution temperature and time in the heat treatment production parameters according to different final structure requirements of the forged piece by adopting different heat treatment systems. The control of the solid solution temperature and time is the key of the internal high-power structure finally required by the material forging.
In the two links of the heat treatment and the cooling of the blank material in the furnace, the variable frequency heating method of constant heat preservation at low temperature and then heating to high temperature is adopted for heat preservation control.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the embodiments described are only a few embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Features of various aspects of embodiments of the invention will be described in detail below. In the following detailed description, numerous specific details are set forth in order to provide a thorough understanding of the present invention. It will be apparent, however, to one skilled in the art that the present invention may be practiced without these specific details. The following description of the embodiments is merely intended to better understand the present invention by illustrating examples thereof. The present invention is not limited to any particular arrangement or method provided below, but rather covers all product structures, any modifications, alterations, etc. of the method covered without departing from the spirit of the invention.
In the following description, well-known structures and techniques are not shown to avoid unnecessarily obscuring the present invention. And 6 forgings subjected to the same treatment at the earlier stage are selected to be subjected to heat treatment system test comparison, wherein 4 forgings adopt the heat treatment system of the invention, one forging adopts standard heat treatment, and the other forging adopts a conventional heat treatment system.
Firstly, the pretreatment concrete operation is as follows:
blank state, namely, after cake upsetting is carried out again on 630KJ (the height of a cake blank is 104mm), collecting the cake from 2500T, increasing the height of three-upset and three-pull cake collecting to 145mm in the cake collecting process, increasing two-fire rolling to form a rod with phi of 200 multiplied by 400 on the basis, and cooling after forging: air cooling;
upsetting cake parameters: the finished rods were re-upset in 630KJ (biscuit height 140mm) with heating parameters: charging into a furnace at the temperature of less than or equal to 800 ℃, heating to 950 ℃ and preserving heat for 160min, heating to 1080 ℃ and preserving heat for 140min, then producing, and cooling after forging: air cooling;
die forging parameters: carrying out die forging on the cake blank after flaw detection and corrosion, wherein the heating parameters are as follows: charging into a furnace at the temperature of less than or equal to 800 ℃, heating to 950 ℃ and preserving heat for 110min, heating to 1080 ℃ and preserving heat for 100min, then producing, and cooling after forging: air cooling;
secondly, different heat treatment systems are as follows:
conventional heat treatment schedule: solid solution: charging into a furnace at the temperature of less than or equal to 800 ℃, heating to 800, preserving heat for 1.5h, heating to 1000, preserving heat for 1.5h, heating to 1090, soaking for 1h, preserving heat for 2h, discharging from the furnace and cooling by water; primary precipitation: charging into a furnace at the temperature of less than or equal to 690 ℃, heating to 750 ℃ and preserving heat for 1.5h, heating to 775 ℃ and preserving heat for 4h, discharging, dispersing and air cooling; secondary precipitation: charging into the furnace at the temperature of less than or equal to 600 ℃, heating to 690, preserving heat for 3h, heating to 715, preserving heat for 24h, discharging from the furnace, dispersing and air cooling.
4 forgings (numbered as ingot nodes 3-1, 3-2, 3-3,3-4 in sequence) of the heat treatment method adopt different solid solution systems and have the same primary precipitation and secondary precipitation.
Section number of ingot: 3-1 solid solution: charging into a furnace at the temperature of less than or equal to 800 ℃, heating to 800 ℃ and preserving heat for 1h, heating to 950 ℃ and preserving heat for 2.5h, heating to 1090 soaking for 1h and preserving heat for 2h, discharging from the furnace and water cooling and air cooling;
section number of ingot: 3-2 solid solution: charging into a furnace at the temperature of less than or equal to 700 ℃, heating to 850 ℃ and preserving heat for 1.5h, heating to 1000 ℃ and preserving heat for 1.5h, heating to 1090 soaking for 1h and preserving heat for 3h, discharging from the furnace and water cooling and air cooling;
section number of ingot: 3-3 solid solution: charging into a furnace at the temperature of less than or equal to 700 ℃, heating to 800 ℃ and preserving heat for 2h, heating to 950 ℃ and preserving heat for 2.5h, heating to 1090 soaking for 1h and preserving heat for 3h, discharging from the furnace and water cooling and air cooling;
section number of ingot: 3-4 solid solution: charging into a furnace at the temperature of less than or equal to 700 ℃, heating to 800 ℃ and preserving heat for 1h, heating to 950 ℃ and preserving heat for 2.5h, heating to 1090 soaking for 1h and preserving heat for 4h, discharging from the furnace and water cooling and air cooling;
primary precipitation: charging into a furnace at the temperature of less than or equal to 690 ℃, heating to 750 ℃ and preserving heat for 1.5h, heating to 775 ℃ and preserving heat for 4h, discharging, dispersing and air cooling;
secondary precipitation: charging into the furnace at the temperature of less than or equal to 600 ℃, heating to 690, preserving heat for 3h, heating to 715, preserving heat for 24h, discharging from the furnace, dispersing and air cooling.
The results of physicochemical detection performances are shown in tables 1 and 2 below:
TABLE 1
TABLE 2
After the heat treatment system of 4 forgings is implemented, the following steps can be seen: all performance indexes after the heat treatment system is adjusted are improved, and the requirement of the final physical and chemical performance of the forging is met.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solutions of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive various equivalent modifications or substitutions within the technical scope of the present invention, and these modifications or substitutions should be covered within the scope of the present invention.
Claims (8)
- The heat treatment method of the GH901 turbine disc forging is characterized by comprising the following steps: the method adopts three-step heating heat treatment, and adopts a heat preservation control method of constant temperature raising to high temperature variable frequency heating in two links of furnace entering heat treatment and cooling.
- 2. The heat treatment method according to claim 1, characterized in that: the method comprises the following steps:the first step is as follows: solid solution:putting the forge piece into an electric furnace, heating to 850 +/-10 ℃ at a temperature of less than or equal to 700 ℃, preserving heat for 90 +/-9 min, heating to 1000 +/-10 ℃, preserving heat for 90 +/-9 min, heating to 1090 +/-10 ℃, soaking for 60 +/-6 min, preserving heat for 180 +/-15 min, and discharging and cooling;the second step is that: primary precipitation:putting the forge piece into an electric furnace at the temperature of less than or equal to 690 ℃, heating to 750 +/-5 ℃ at the speed of 80-100 ℃/h, preserving heat for 90 +/-9 min, heating to 775 +/-5 ℃, preserving heat for 240 +/-15 min, and discharging and cooling;the third step: secondary precipitation:putting the forge piece into an electric furnace at the temperature of less than or equal to 600 ℃, heating to 690 +/-5 ℃ at the speed of 80-100 ℃/h, preserving heat for 180 +/-15 min, heating to 715 +/-5 ℃, preserving heat for 24 +/-0.25 h, and discharging and cooling.
- 3. The heat treatment method according to claim 2, characterized in that: and in the first step, water cooling and air cooling are adopted for cooling.
- 4. The heat treatment method according to claim 3, characterized in that: the water cooling time is more than or equal to 20 min.
- 5. The heat treatment method according to claim 2, characterized in that: and in the second step, the cooling is realized by adopting dispersed air cooling.
- 6. The heat treatment method according to claim 2, characterized in that: and in the third step, the cooling adopts dispersed air cooling.
- 7. The heat treatment method according to claim 2, characterized in that: and finally, carrying out physical and chemical test on the forging.
- 8. The heat treatment method according to claim 2, characterized in that: after the forging is processed by the method, the performance indexes of the forging are as follows:stretching at room temperature: the tensile strength is more than or equal to 1130MPa, the yield strength is more than or equal to 810MPa, and the elongation is more than or equal to 9 percent.
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| CN202011557008.XA CN112779385A (en) | 2020-12-24 | 2020-12-24 | Heat treatment method of GH901 turbine disc forging |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114231866A (en) * | 2021-10-25 | 2022-03-25 | 陕西宏远航空锻造有限责任公司 | Heat treatment method for GH99 alloy annular forging |
| CN114277232A (en) * | 2021-12-15 | 2022-04-05 | 陕西宏远航空锻造有限责任公司 | Method and device for improving strength of GH2909 alloy forging |
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|---|---|---|---|---|
| EP0387976A2 (en) * | 1989-03-15 | 1990-09-19 | Institute Of Metal Research Academia Sinica | New superalloys and the methods for improving the properties of superalloys |
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| US20080163963A1 (en) * | 2007-01-08 | 2008-07-10 | Ling Yang | Heat Treatment Method and Components Treated According to the Method |
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2020
- 2020-12-24 CN CN202011557008.XA patent/CN112779385A/en active Pending
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| CN104878174A (en) * | 2014-02-28 | 2015-09-02 | 钢铁研究总院 | Method for controlling heat treatment cooling speed of high temperature alloy product |
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| Title |
|---|
| 《工程材料实用手册》编辑委员会: "《工程材料实用手册2 变形高温合金 铸造高温合金》", 31 March 1989 * |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114231866A (en) * | 2021-10-25 | 2022-03-25 | 陕西宏远航空锻造有限责任公司 | Heat treatment method for GH99 alloy annular forging |
| CN114277232A (en) * | 2021-12-15 | 2022-04-05 | 陕西宏远航空锻造有限责任公司 | Method and device for improving strength of GH2909 alloy forging |
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Application publication date: 20210511 |