CN104004980A - Heat processing technology for nickel-base precipitation hardened high-temperature alloy - Google Patents
Heat processing technology for nickel-base precipitation hardened high-temperature alloy Download PDFInfo
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Abstract
The invention provides a heat processing technology for a nickel-base precipitation hardened high-temperature alloy. The heat processing technology includes the following steps that (1), the nickel-base precipitation hardened high-temperature alloy is heated to 480 DEG C-520 DEG C in an air furnace, and the temperature is kept for 30 min-40 min to obtain a preheated high-temperature alloy product; (2), the preheated high-temperature alloy product in the step (1) is transferred to the other heating furnace which is heated to 1080 DEG C-1100 DEG C in advance, timekeeping is started after the preheated high-temperature alloy product is put into the heating furnace, and the temperature in the heating furnace is recovered to 1080 DEG C-1100 DEG C, the temperature is kept for 10 min-15 min, and then the high-temperature alloy product is discharged out of the heating furnace and cooled through air; (3) the high-temperature alloy product after solid solution in the step (2) is heated to 740 DEG C-760 DEG C, the temperature is kept for 3 h-5 h, the high-temperature alloy product is cooled by filling argon, and ageing is carried out to obtain the high-temperature alloy finished product. The nickel-base precipitation hardened high-temperature alloy achieves good grain size distribution through the technology, and therefore the finished product good in combination property is obtained.
Description
Technical field
The invention belongs to the heat treatment technics field of superalloy, especially relate to a kind of thermal treatment process of Ni-based precipitation hardenable superalloy.
Background technology
Superalloy is called again the strong alloy of heat, refractory alloy or superalloy, it is a kind of novel fire resistant metallic substance along with modern age, Aviation Industry got up, this material can be under the hot environment of 600～1100 DEG C long-term stable operation, at high temperature bear burn into oxidation and complex stress and do not lose efficacy.Superalloy can be divided into iron-base superalloy, nickel base superalloy and cobalt base superalloy substantially by composition, can be divided into solution strengthening type, precipitation hardenable and dispersion strengthening type by schedule of reinforcement.
High-temperature alloy bolt screw product is generally examined product grains degree, hardness, high-temperature and durable and mechanical properties, wherein mechanical properties and high-temperature and durable are a kind of relations of mutual restriction, they are all relevant with grain fineness number, when crystal grain is larger, mechanical properties is lower, but high temperature endurance performance is good; Hour, mechanical properties is high for crystal grain, but high temperature endurance performance is poor.Grain fineness number is mainly subject to the impact of alloy solid solution system, and therefore the solid solution craft alloy improved combination properties of researching high-temperature alloy has very important significance.
Summary of the invention
The problem that the invention will solve is to provide a kind of thermal treatment process of Ni-based precipitation hardenable superalloy, this technique makes Ni-based precipitation hardenable superalloy obtain good Grain size distribution, thereby obtain the cooperation of good room-temperature mechanical property and high temperature endurance performance, this technique can, in order to adjust alloy grain degree, be improved the high temperature endurance performance of alloy.
For solving the problems of the technologies described above, the technical scheme that the invention adopts is: a kind of solid solution craft of Ni-based precipitation hardenable superalloy, comprises following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 480～520 DEG C in air furnace, insulation 30～40min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1080～1100 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after 1080～1100 DEG C, start timing, insulation 10～15min, the air cooling of coming out of the stove, obtains the superalloy product after solid solution;
3), by step 2) in superalloy product after solid solution at 740～760 DEG C, be incubated 3～5 hours, applying argon gas is cooling, carries out timeliness, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
Wherein, step (1) is preheating, and Main Function is to make product heart portion and surface temperature is poor reduces, thereby reduces the thermal stresses of product surface and heart portion, makes the grain fineness number of surface and heart portion be tending towards close, and what reduce product adds thermal distortion and tearing tendency simultaneously.
Step (2) is major portion of the present invention, after preheating, change stove heating and thermal insulation, because general process furnace heat-up rate is slower, in the time that solid solubility temperature is higher, be heated to from preheating temperature the overlong time that holding temperature needs, and the higher heat-up rate of temperature is slower, like this at high temperature overstand of product, grain fineness number is difficult for ensureing.
Analyze theoretically, superalloy solid solubility temperature is higher, and soaking time is longer, and product grains is larger.The tissue of large crystal grain has good high temperature endurance performance, under certain high temperature lower than aging temp, insulation loads, can keep the long period not rupture, this is mainly because intracrystalline intensity is greater than grain-boundary strength under high temperature, large grain structure has less crystal boundary, and therefore enduring quality is higher, but this tissue can reduce the room-temperature mechanical property of product, because under room temperature, the grain-boundary strength of healthy tissues is greater than intracrystalline intensity; On the contrary, close grain has good room-temperature property, and high temperature endurance performance is poor.
, the grain fineness number of product, room-temperature property, high temperature endurance performance, just need to grain fineness number be controlled in a relatively reasonable scope by solution treatment in the case of need to ensure simultaneously, therefore the temperature of solution treatment, time all need to control well.
Preferably, comprise following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 490～510 DEG C in air furnace, insulation 30～40min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1085～1095 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after specified temperature, start timing, insulation 10min, the air cooling of then coming out of the stove, obtains the Ni-based precipitation hardenable superalloy finished product after solid solution.
3), by step 2) in superalloy product after solid solution be heated to 750 DEG C of insulation 4h, applying argon gas is cooling, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
Preferably, step 1) described in Ni-based precipitation hardenable superalloy in each component and weight percent as follows: carbon 0.04～0.10%; Chromium 18.0～21.0%; Aluminium 1.0～1.8%; Titanium 1.8～2.7%; Silicon≤0.80%; Manganese≤0.40%; Sulphur≤0.015; Phosphorus≤0.020; Silver≤0.0005; Boron≤0.008; Bismuth≤0.0001; Cobalt≤2.0; Copper≤0.2; Iron≤1.5; Plumbous≤0.002; Nickel surplus.
Preferably, step 1) described in the model of Ni-based precipitation hardenable superalloy be .187-32UNS.
Advantage and positively effect that the invention has are: Ni-based precipitation hardenable superalloy is processed according to technical scheme disclosed by the invention, grain fineness number, room-temperature property and high temperature endurance performance that can well equilibrium product, have improved the over-all properties of Ni-based precipitation hardenable superalloy.
Embodiment
Below in conjunction with specific embodiment, the invention is described in further details.
In embodiment in the present invention and simultaneous test, use and test and illustrate with the Ni-based precipitation hardening superalloy of the one part of sample ingredient and specification, the superalloy part composition and the specification that adopt are as shown in table 1.
The superalloy part composition and the specification that in table 1 embodiment, adopt
Embodiment mono-
A solid solution craft for Ni-based precipitation hardenable superalloy, comprises following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 500 DEG C in air furnace, insulation 40min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1090 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after 1090 DEG C, start timing, insulation 10min, the air cooling of coming out of the stove, obtains the superalloy product after solid solution;
3), by step 2) in superalloy product after solid solution at 750 DEG C, be incubated 4 hours, applying argon gas is cooling, carries out timeliness, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
Embodiment bis-
A solid solution craft for Ni-based precipitation hardenable superalloy, comprises following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 480 DEG C in air furnace, insulation 30min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1090 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after 1090 DEG C, start timing, insulation 10min, the air cooling of coming out of the stove, obtains the superalloy product after solid solution;
3), by step 2) in superalloy product after solid solution at 750 DEG C, be incubated 4 hours, applying argon gas is cooling, carries out timeliness, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
Embodiment tri-
A solid solution craft for Ni-based precipitation hardenable superalloy, comprises following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 520 DEG C in air furnace, insulation 40min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1090 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after 1090 DEG C, start timing, insulation 10min, the air cooling of coming out of the stove, obtains the superalloy product after solid solution;
3), by step 2) in superalloy product after solid solution at 750 DEG C, be incubated 4 hours, applying argon gas is cooling, carries out timeliness, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
Simultaneous test
Control group 1
Part is heated to 500 DEG C, and insulation 40min, proceeds to furnace temperature and is another process furnace of 1115 DEG C subsequently, and furnace temperature starts timing after recovering, insulation 10min, the air cooling of coming out of the stove.Then carry out timeliness at 750 DEG C of insulation 4h.
Control group 2
Part is heated to 500 DEG C, and insulation 40min, proceeds to furnace temperature and is another process furnace of 1130 DEG C subsequently, and furnace temperature starts timing after recovering, insulation 10min, the air cooling of coming out of the stove.Then carry out timeliness at 750 DEG C of insulation 4h.
Control group 3
Part is heated to 500 DEG C, and insulation 40min, proceeds to furnace temperature and is another process furnace of 1150 DEG C subsequently, and furnace temperature starts timing after recovering, insulation 10min, the air cooling of coming out of the stove.Then carry out timeliness at 750 DEG C of insulation 4h.
Control group 4
Part is heated to 500 DEG C, and insulation 40min, proceeds to furnace temperature and is another process furnace of 1090 DEG C subsequently, and furnace temperature starts timing after recovering, insulation 18min, the air cooling of coming out of the stove.Then carry out timeliness at 750 DEG C of insulation 4h.
Control group 5
Part is heated to 500 DEG C, and insulation 40min, proceeds to furnace temperature and is another process furnace of 1090 DEG C subsequently, and furnace temperature starts timing after recovering, insulation 20min, the air cooling of coming out of the stove.Then carry out timeliness at 750 DEG C of insulation 4h.
Control group 6
Part is heated to 500 DEG C, and insulation 40min, proceeds to furnace temperature and is another process furnace of 1090 DEG C subsequently, and furnace temperature starts timing after recovering, insulation 25min, the air cooling of coming out of the stove.Then carry out timeliness at 750 DEG C of insulation 4h.
In order better to verify effect of the present invention, to the above embodiment of the present invention one～tri-, heat-treat process certification, embodiment mono-～embodiment tri-and control group 1～6 have carried out respectively the experiment of 10 batches, each checking indices is got 5 parts and is tested, and inspection is carried out according to GB/T228-2002 " metallic substance tensile testing at ambient temperature ", ASTM E112-10 " metal mean grain size measuring method ".Assay is as shown in table 2, and the data in table are all the mean value of each testing data.
Performance perameter after the thermal treatment of table 2 superalloy part
Note: the main technical requirements of finished product is as follows, tensile strength: σ
b>=1000MPa; Stress cracking: load the axial tension of 340MPa at 750 DEG C, product 30h does not rupture qualified; Grain fineness number: head connecting arc place, screw thread position>=4 grade, bar portion, core>=2 grade.(grain size number is larger, and crystal grain is more tiny.)
2. test draw-pulling fatigue experimental of fatigue property, single-piece cycle index should exceed 45000 times, and average time should exceed 65000 times, exceedes 130000 times and calculates by 130000 times.
Because embodiment 1 can ensure that product is qualified, control group 4～6, only in order to explore the impact of soaking time on grain fineness number, has therefore only done grain fineness number grading and lasting experiment, and from cost-saving and angle practicality, 4～6 do not do tensile mechanical properties.
As can be seen from Table 2, embodiments of the invention one～embodiment tri-, it is all qualified that property indices requires, and simultaneously room-temperature mechanical property all reaches maximum as tensile strength, yield strength.
And control group 1～3 is compared with embodiment 1, when solution time is the same, be that solid solubility temperature constantly raises, visible in table 2, along with solid solubility temperature raises, early stage, grain fineness number slowly increased, and then sharply grew up, in control group 2 and control group 3, grain fineness number is all defective, meanwhile, along with solid solubility temperature improves, enduring quality improves gradually, fatigue and tensile property reduce gradually, but all in acceptability limit.
Control group 4～6 is compared with embodiment 1, and solid solubility temperature is consistent, and solution time continues to increase, visible in table, and along with the increase of solution time, grain-size only has growth by a small margin, and it is very slow to grow up, and considerable change does not appear in enduring quality simultaneously.By contrasting with control group 1～6, can find that the impact of soaking time alloy is much smaller than holding temperature, alloy is more responsive to temperature, therefore considers from the angle reducing production costs, and selects less soaking time.
Can find out by above-mentioned analysis, use the present invention to heat-treat nickel base superalloy, can obtain good effect, after thermal treatment, alloy can obtain good Grain size distribution, obtain desirable high temperature endurance performance and room-temperature mechanical property simultaneously and coordinate, can also reach the effect reducing production costs.
Above the embodiment of the invention is had been described in detail, but described content is only for the preferred embodiment of the invention, can not be considered to for limiting practical range of the present invention.All equalization variation and improvement etc. of doing according to the invention scope, within all should still belonging to this patent covering scope.
Claims (4)
1. a thermal treatment process for Ni-based precipitation hardenable superalloy, is characterized in that: comprise following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 480～520 DEG C in air furnace, insulation 30～40min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1080～1100 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after 1080～1100 DEG C, start timing, insulation 10～15min, the air cooling of coming out of the stove, obtains the superalloy product after solid solution;
3), by step 2) in superalloy product after solid solution at 740～760 DEG C, be incubated 3～5 hours, applying argon gas is cooling, carries out timeliness, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
2. the thermal treatment process of Ni-based precipitation hardenable superalloy according to claim 1, is characterized in that: comprise following processing step:
1), Ni-based precipitation hardenable superalloy is heated to 490～510 DEG C in air furnace, insulation 30～40min, obtains the superalloy product after preheating;
2), by step 1) in superalloy transferred product after preheating to another process furnace, in this process furnace, be heated in advance 1085～1095 DEG C, put into after the superalloy product after preheating, in stove to be heated, temperature returns to after specified temperature, start timing, insulation 10min, the air cooling of then coming out of the stove, obtains the Ni-based precipitation hardenable superalloy finished product after solid solution.
3), by step 2) in superalloy product after solid solution be heated to 750 DEG C of insulation 4h, applying argon gas is cooling, obtains the Ni-based precipitation hardenable superalloy finished product after thermal treatment.
3. the thermal treatment process of Ni-based precipitation hardenable superalloy according to claim 1, is characterized in that: step 1) described in Ni-based precipitation hardenable superalloy in each component and weight percent as follows: carbon 0.04～0.10%; Chromium 18.0～21.0%; Aluminium 1.0～1.8%; Titanium 1.8～2.7%; Silicon≤0.80%; Manganese≤0.40%; Sulphur≤0.015; Phosphorus≤0.020; Silver≤0.0005; Boron≤0.008; Bismuth≤0.0001; Cobalt≤2.0; Copper≤0.2; Iron≤1.5; Plumbous≤0.002; Nickel surplus.
4. according to the thermal treatment process of the Ni-based precipitation hardenable superalloy described in claim 1～3 any one, it is characterized in that: step 1) described in the specification of Ni-based precipitation hardenable superalloy be .187-32UNS.
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Cited By (9)
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| CN106244854A (en) * | 2016-07-29 | 2016-12-21 | 上海屹禾合金材料科技有限公司 | There is nickel-base alloy and the manufacture method thereof of high-wear resistance |
| CN107604278A (en) * | 2017-10-11 | 2018-01-19 | 南通聚星铸锻有限公司 | A kind of technique for controlling high temperature alloy product heat treatment cooling velocity |
| CN107641780A (en) * | 2017-10-11 | 2018-01-30 | 南通聚星铸锻有限公司 | A kind of Ni-based precipitation hardenable high temperature alloy Technology for Heating Processing |
| CN107699828A (en) * | 2017-10-16 | 2018-02-16 | 太原钢铁(集团)有限公司 | The method for handling nickel base superalloy hot extrusion hollow forging |
| CN108220690A (en) * | 2017-12-28 | 2018-06-29 | 沪东重机有限公司 | The forging material and forging method of a kind of exhasut valve stem peculiar to vessel |
| CN108396269A (en) * | 2018-03-02 | 2018-08-14 | 河北工业大学 | A kind of enhancing polycrystalline Ni3The heat treatment method of Al based high-temperature alloy deformation stabilities |
| CN113025848A (en) * | 2021-05-24 | 2021-06-25 | 北京钢研高纳科技股份有限公司 | Iron-nickel-based precipitation strengthening type high-temperature alloy and preparation method and application thereof |
| CN113151762A (en) * | 2021-04-12 | 2021-07-23 | 西北工业大学 | Method for inhibiting rheological phenomenon of nickel-based superalloy sawtooth |
| CN113862590A (en) * | 2021-07-16 | 2021-12-31 | 北京科技大学 | Heat treatment process for prolonging fatigue life of GH4738 alloy |
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106244854A (en) * | 2016-07-29 | 2016-12-21 | 上海屹禾合金材料科技有限公司 | There is nickel-base alloy and the manufacture method thereof of high-wear resistance |
| CN107604278A (en) * | 2017-10-11 | 2018-01-19 | 南通聚星铸锻有限公司 | A kind of technique for controlling high temperature alloy product heat treatment cooling velocity |
| CN107641780A (en) * | 2017-10-11 | 2018-01-30 | 南通聚星铸锻有限公司 | A kind of Ni-based precipitation hardenable high temperature alloy Technology for Heating Processing |
| CN107699828A (en) * | 2017-10-16 | 2018-02-16 | 太原钢铁(集团)有限公司 | The method for handling nickel base superalloy hot extrusion hollow forging |
| CN107699828B (en) * | 2017-10-16 | 2019-03-15 | 太原钢铁(集团)有限公司 | The method for handling nickel base superalloy hot extrusion hollow forging |
| CN108220690A (en) * | 2017-12-28 | 2018-06-29 | 沪东重机有限公司 | The forging material and forging method of a kind of exhasut valve stem peculiar to vessel |
| CN108396269A (en) * | 2018-03-02 | 2018-08-14 | 河北工业大学 | A kind of enhancing polycrystalline Ni3The heat treatment method of Al based high-temperature alloy deformation stabilities |
| CN108396269B (en) * | 2018-03-02 | 2019-11-08 | 河北工业大学 | A kind of enhancing polycrystalline Ni3The heat treatment method of Al based high-temperature alloy deformation stability |
| CN113151762A (en) * | 2021-04-12 | 2021-07-23 | 西北工业大学 | Method for inhibiting rheological phenomenon of nickel-based superalloy sawtooth |
| CN113025848A (en) * | 2021-05-24 | 2021-06-25 | 北京钢研高纳科技股份有限公司 | Iron-nickel-based precipitation strengthening type high-temperature alloy and preparation method and application thereof |
| CN113862590A (en) * | 2021-07-16 | 2021-12-31 | 北京科技大学 | Heat treatment process for prolonging fatigue life of GH4738 alloy |
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