CN109280812A - Heat treatment process of nickel-iron-based deformed high-temperature alloy friction welding joint - Google Patents
Heat treatment process of nickel-iron-based deformed high-temperature alloy friction welding joint Download PDFInfo
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- CN109280812A CN109280812A CN201811296443.4A CN201811296443A CN109280812A CN 109280812 A CN109280812 A CN 109280812A CN 201811296443 A CN201811296443 A CN 201811296443A CN 109280812 A CN109280812 A CN 109280812A
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- 238000003466 welding Methods 0.000 title claims abstract description 47
- 238000000034 method Methods 0.000 title claims abstract description 31
- 238000010438 heat treatment Methods 0.000 title claims abstract description 29
- 230000008569 process Effects 0.000 title claims abstract description 27
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 25
- 239000000956 alloy Substances 0.000 title claims abstract description 25
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 title abstract 4
- 230000032683 aging Effects 0.000 claims abstract description 12
- 238000002844 melting Methods 0.000 claims abstract description 8
- 230000008018 melting Effects 0.000 claims abstract description 8
- 238000001556 precipitation Methods 0.000 claims abstract description 8
- 238000005728 strengthening Methods 0.000 claims abstract description 8
- 238000001816 cooling Methods 0.000 claims abstract description 7
- 239000006104 solid solution Substances 0.000 claims abstract description 6
- 229910000863 Ferronickel Inorganic materials 0.000 claims description 26
- 239000000463 material Substances 0.000 claims description 23
- 229910000601 superalloy Inorganic materials 0.000 claims description 23
- 238000004321 preservation Methods 0.000 claims description 20
- 239000000470 constituent Substances 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 238000010792 warming Methods 0.000 claims description 5
- 239000000126 substance Substances 0.000 claims description 3
- 238000010791 quenching Methods 0.000 claims description 2
- 230000000171 quenching effect Effects 0.000 claims description 2
- 239000010953 base metal Substances 0.000 abstract 2
- 229910001092 metal group alloy Inorganic materials 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 9
- 230000006872 improvement Effects 0.000 description 6
- 230000003014 reinforcing effect Effects 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 5
- 230000008520 organization Effects 0.000 description 5
- 239000000243 solution Substances 0.000 description 4
- 238000005242 forging Methods 0.000 description 3
- 239000004615 ingredient Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910003271 Ni-Fe Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 230000004069 differentiation Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000004880 explosion Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 210000001503 joint Anatomy 0.000 description 1
- 210000005067 joint tissue Anatomy 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 238000005476 soldering Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 210000001519 tissue Anatomy 0.000 description 1
- 238000012876 topography Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Classifications
-
- 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
- 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
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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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- 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)
- Pressure Welding/Diffusion-Bonding (AREA)
- Arc Welding In General (AREA)
Abstract
The invention discloses a heat treatment process of a nickel-iron-based deformed high-temperature alloy friction welding head, which carries out integral heat treatment on a welding line and a base metal on the nickel-iron-based deformed high-temperature alloy subjected to inertia friction welding, and comprises the following steps: firstly, carrying out two-step continuous high-temperature solid solution treatment at the temperature of 100-200 ℃ below the initial melting temperature of the base metal alloy; then continuous two-step aging heat treatment is carried out according to the temperature from low to high in the range of 150-400 ℃ below the precipitation temperature of the gamma' strengthening phase. The method can solve the problem that the nickel-iron-based wrought high-temperature alloy with aging strengthening cannot realize strengthening phase precipitation due to high cooling speed in the friction welding process, and effectively improves the comprehensive mechanical property of a welding head; the heat treatment process is simple and easy to control.
Description
Technical field
The invention belongs to technical field of heat treatment, and in particular to a kind of heat of ferronickel base wrought superalloy friction welding joint
Treatment process.
Background technique
Friction welding technology is because its welding procedure is simple, speed of welding is fast, in station boiler and chemical industry equipment manufacture etc.
Many industrial departments are used widely.After especially solving the problems, such as welding point toughness in recent years, this welding technique
It is applied in multiple components such as boiler water wall, economizer.Researcher reports the weldering of boiler 12Cr1MoV tube fraction
The high temperature internal pressure explosion enduring quality of connector is studied, the results showed that friction welding joint is reliable, affirmative within phase projected life
Application prospect of the friction welding technological in boiler welding.In view of more high parameter boiler will largely use Ni-Fe base, even
Ni based alloy, and contain solution strengthening element (such as Cr, Mo, W, Al) and the members such as trace P, S, C, B in nickel base superalloy
Element, thus have larger crack sensitivity, and be also easy to produce microstructure segregation after melting welding, brittlement phase and other defect is precipitated, lead to connector
Mechanical property and high temperature endurance performance decline.Therefore, application of the friction welding technology in Nickel-based Alloy Welding need deeply to grind
Study carefully, the still rare report of research of the joint microstructure characteristic aspect formed under the conditions of difference welding operating condition.For most representative
Nickel-base alloy GH4169 (IN718), both at home and abroad for the side such as joint microstructure, mechanical property, numerical simulation of its inertia friction welding
Face has carried out part and has studied.Disclosed research reports the microscopic structure of IN718 linear friction welding heat-mechanical affected zone and overlap, refers to
The tissue predominantly oxide skin(coating) of Al on the inside of overlap out, outside overlap is then mainly the oxide of Nb, in the model of weld seam two sides 1mm
Dynamic recrystallization has occurred in enclosing.Document report GH4169 high temperature alloy inertia friction welding connector nearby has along axial soldering area
Have Ultra-fine Grained-fine grain grain Distribution, despite the presence of the inhomogeneities of grain structure, but do not find in fusion welding process because
Liquid phase solidification and caused by coarse-grain and mixed crystal phenomenon.Although friction welding technology is not related to alloy melting process, but still can be to timeliness
The institutional framework of enhanced type high temperature alloy connector, the dissolution of precipitated phase and redistribution produce bigger effect: IN718 alloy inertia rubs
The hardening constituent γ ' and γ " for wiping weldering interface are mutually completely dissolved under elevated temperature thermal cycles effect, are not found in weld dimensions
Remaining γ ' and γ " phase；Research shows that it is strong to help to improve connector mechanics to IN718 alloy progress aging treating after welding appropriate
Degree, alleviates above-mentioned welding joint softened effect.There is data to suggest that mechanics of the heat resisting steel friction welding joint under the effect of long term high temperature timeliness
Performance extends at any time and is remarkably decreased, and performance degradation and its structure stability in heat exposure, joint area precipitated phase
Type, distribution and differentiation have direct relation.In view of ferronickel base wrought superalloy design generally use ageing strengthening mechanism,
And friction welding technology cannot achieve the characteristics of hardening constituent is precipitated because of cooling rate fastly, seam organization based on heat treatment process regulates and controls come excellent
Change the institutional framework of plumb joint and realizes that high-intensitive target has significant innovative significance and engineering application value.
Summary of the invention
It is an object of the invention to overcome the above-mentioned prior art, provides a kind of ferronickel base wrought superalloy and rub
The heat treatment process of plumb joint is wiped, which can be effectively improved the institutional framework and intensity of friction welding joint.
The present invention adopts the following technical scheme that realize:
A kind of heat treatment process of ferronickel base wrought superalloy friction welding joint becomes the ferronickel base of inertia friction postwelding
Shape high temperature alloy, carry out weld seam and base material bulk heat treatmet, comprising the following steps: firstly, base material alloy initial melting temperature with
Carry out the continuous higher temperature solid solution of two steps within the scope of 100-200 DEG C lower from high to low by temperature；Then respectively in γ ' hardening constituent
Carry out continuous two steps aging strengthening model below Precipitation Temperature within the scope of 150-400 DEG C from low to high by temperature.
A further improvement of the present invention lies in that the ferronickel base wrought superalloy chemical component meets following require:
By mass fraction, the Nb of the Ti of the Al of the Cr of the Fe containing 18-35%, 20-25%, 1-2.5%, 0.8-2.2%, 0.5-2%,
(Mo+W) of 0.5-4%, the Mn of the Si of 0-0.5%, 0-1% ,≤0.1% C ,≤0.01% B ,≤0.05% P, remaining
For Ni.
A further improvement of the present invention lies in that the friction welding technological satisfaction of the ferronickel base wrought superalloy is wanted as follows
It asks: friction pressure >=150MPa, revolving speed >=1000r/min, upset pressure >=300MPa.
A further improvement of the present invention lies in that the detailed process of the continuous higher temperature solid solution of two steps is 1120-
1200 DEG C of heat preservation 30min-4h, then cool to 1000-1050 DEG C of heat preservation 30min-4h, water quenching cooling with the furnace by 1-5 DEG C/min.
A further improvement of the present invention lies in that the continuous aging heat treatment detailed process of two steps is 620-680
DEG C heat preservation 4-20h, be then warming up to 730-800 DEG C of heat preservation 4-20h with furnace by 1-5 DEG C/min, be air-cooled to room temperature.
A further improvement of the present invention lies in that plumb joint grain size obtained is suitable with base material.
A further improvement of the present invention lies in that plumb joint intensity obtained and base material maintain an equal level.
The present invention has following beneficial technical effect:
A kind of heat treatment process of ferronickel base wrought superalloy friction welding joint of the present invention, having significantly has
Beneficial effect.Specific manifestation are as follows: the ferronickel base wrought superalloy friction welding joint that the present invention is directed to, successively by base material alloy
Carry out the continuous higher temperature solid solution of two steps below initial melting temperature within the scope of 100-200 DEG C from high to low by temperature, and in γ '
It carries out continuous two steps aging strengthening model below hardening constituent Precipitation Temperature within the scope of 150-400 DEG C from low to high by temperature, guarantees
Seam organization is controllably grown up, so as to avoid the unfavorable shadow of the seam organization butt joint creep rupture strength of crystal grain refinement
It rings；It ensure that seam organization crystal boundary and transgranular hardening constituent are precipitated, so that it is suitable with base material to realize plumb joint intensity.Meanwhile with
The technologies such as existing TIG weldering are compared, and the friction welding process that the present invention is relied on is automatic quickly, flexibly, welding process it is stable and
It can review, be not necessarily to solder flux or protective gas, and can achieve and weld comparable plumb joint intensity with TIG.
Detailed description of the invention
Fig. 1 is that plumb joint tissue topography is obtained in the embodiment of the present invention one；
Fig. 2 is that plumb joint welded seam area crystal boundary and matrix precipitate pattern are obtained in the embodiment of the present invention one；
Fig. 3 is that base material crystal boundary and matrix precipitate pattern are obtained in the embodiment of the present invention one；
Fig. 4 is that 750 DEG C of tensile strengths of plumb joint are obtained in the embodiment of the present invention one；
Fig. 5 is to obtain plumb joint in the embodiment of the present invention one to stretch style fracture position.
Specific embodiment
Below with reference to embodiment and attached drawing, the present invention will be further described:
Embodiment one
Take a kind of ferronickel base deformation high temperature met in heretofore described ferronickel base wrought superalloy composition range
Alloy, the ingredient of the alloy are as follows: press mass fraction, the Al of the Cr of the Fe containing 18-35%, 20-25%, 1-2.5%, 0.8-
(Mo+W) of the Nb of 2.2% Ti, 0.5-2%, 0.5-4%, the Mn of the Si of 0-0.5%, 0-1% ,≤0.1% C ,≤
0.01% B ,≤0.05% P, remaining is Ni.Wherein, the initial melting temperature of the alloy is 1320 DEG C, and the Precipitation Temperature of γ ' is
980℃.Plumb joint is prepared using inertia friction welder, the friction pressure of butt welding is 200MPa, sample rotation rate 180r/min, pushes up
Forging and stamping are 300MPa by force.
It will be by the plumb joint bulk heat treatmet of weld seam and base material formed, solution heat treatment: 1200 DEG C of heat preservations
Then 30min cools to 1020 DEG C of heat preservation 1h, water cooling with the furnace by 2 DEG C/min；Aging thermal treating process: 640 DEG C of heat preservation 16h, so
760 DEG C of heat preservation 16h are warming up to furnace by 2 DEG C/min afterwards, are air-cooled to room temperature.
After heat treatment, seam organization is uniform, such as Fig. 1；10 μm of weld seam average grain size, γ ' reinforcing phase size 10-
20nm, such as Fig. 2；100 μm of base material average grain size, γ ' reinforcing phase size 10-20nm, such as Fig. 3；After room temperature and 750 DEG C of stretchings
Plumb joint stretches style fracture position in base material side, and 750 DEG C of yield strengths of plumb joint are 615MPa, under identical heat treatment parameter
750 DEG C of yield strengths of base material are 615MPa, such as Fig. 4 and Fig. 5.
Embodiment two
Take a kind of ferronickel base deformation high temperature met in heretofore described ferronickel base wrought superalloy composition range
Alloy, the ingredient of the alloy are as follows: press mass fraction, the Al of the Cr of the Fe containing 18-35%, 20-25%, 1-2.5%, 0.8-
(Mo+W) of the Nb of 2.2% Ti, 0.5-2%, 0.5-4%, the Mn of the Si of 0-0.5%, 0-1% ,≤0.1% C ,≤
0.01% B ,≤0.05% P, remaining is Ni.Wherein, the initial melting temperature of the alloy is 1320 DEG C, and the Precipitation Temperature of γ ' is
980℃.Plumb joint is prepared using inertia friction welder, the friction pressure of butt welding is 200MPa, sample rotation rate 180r/min, pushes up
Forging and stamping are 300MPa by force.
It will be by the plumb joint bulk heat treatmet of weld seam and base material formed, solution heat treatment: 1180 DEG C of heat preservations
Then 30min cools to 1050 DEG C of heat preservation 1h, water cooling with the furnace by 2 DEG C/min；Aging thermal treating process: 620 DEG C of heat preservation 18h, so
780 DEG C of heat preservation 8h are warming up to furnace by 2 DEG C/min afterwards, are air-cooled to room temperature.
After heat treatment, 20 μm of weld seam average grain size, γ ' reinforcing phase size 10-20nm；Base material average grain size
140 μm, γ ' reinforcing phase size 10-20nm；Plumb joint stretches style fracture position in base material side after room temperature and 750 DEG C stretch,
750 DEG C of yield strengths of plumb joint are 629MPa, and 750 DEG C of yield strengths of base material are 633MPa under identical heat treatment parameter.
Embodiment three
Take a kind of ferronickel base deformation high temperature met in heretofore described ferronickel base wrought superalloy composition range
Alloy, the ingredient of the alloy are as follows: press mass fraction, the Al of the Cr of the Fe containing 18-35%, 20-25%, 1-2.5%, 0.8-
(Mo+W) of the Nb of 2.2% Ti, 0.5-2%, 0.5-4%, the Mn of the Si of 0-0.5%, 0-1% ,≤0.1% C ,≤
0.01% B ,≤0.05% P, remaining is Ni.Wherein, the initial melting temperature of the alloy is 1320 DEG C, and the Precipitation Temperature of γ ' is
980℃.Plumb joint is prepared using inertia friction welder, the friction pressure of butt welding is 200MPa, sample rotation rate 180r/min, pushes up
Forging and stamping are 300MPa by force.
By by the plumb joint bulk heat treatmet of weld seam and base material formed, solution heat treatment: 1150 DEG C of heat preservation 4h, so
1020 DEG C of heat preservation 2h, water cooling are cooled to the furnace by 2 DEG C/min afterwards；Aging thermal treating process: 620 DEG C of heat preservation 18h, then by 2 DEG C/
Min is warming up to 740 DEG C of heat preservation 16h with furnace, is air-cooled to room temperature.
After heat treatment, 15 μm of weld seam average grain size, γ ' reinforcing phase size 10-20nm；Base material average grain size
110 μm, γ ' reinforcing phase size 10-20nm；Plumb joint stretches style fracture position in base material side after room temperature and 750 DEG C stretch,
750 DEG C of yield strengths of plumb joint are 625MPa, and 750 DEG C of yield strengths of base material are 624MPa under identical heat treatment parameter.
Claims (7)
1. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint, which is characterized in that by inertia friction postwelding
Ferronickel base wrought superalloy, carry out weld seam and base material bulk heat treatmet, comprising the following steps: firstly, in base material alloy
Carry out the continuous higher temperature solid solution of two steps below initial melting temperature within the scope of 100-200 DEG C from high to low by temperature；Then respectively
Carry out continuous two steps aging strengthening model within the scope of 150-400 DEG C from low to high by temperature below γ ' hardening constituent Precipitation Temperature.
2. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint according to claim 1, feature
It is, the ferronickel base wrought superalloy chemical component meets following require: by mass fraction, the Fe containing 18-35%,
(Mo+W) of the Nb of the Ti of the Al of the Cr of 20-25%, 1-2.5%, 0.8-2.2%, 0.5-2%, 0.5-4%, 0-0.5%'s
The Mn of Si, 0-1% ,≤0.1% C ,≤0.01% B ,≤0.05% P, remaining is Ni.
3. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint according to claim 1, feature
It is, the friction welding technological of the ferronickel base wrought superalloy meets following require: rub pressure >=150MPa, revolving speed >=
1000r/min, upset pressure >=300MPa.
4. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint according to claim 1, feature
It is, the detailed process of the continuous higher temperature solid solution of two steps is 1120-1200 DEG C of heat preservation 30min-4h, then presses 1-
5 DEG C/min cools to 1000-1050 DEG C of heat preservation 30min-4h, water quenching cooling with the furnace.
5. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint according to claim 1, feature
It is, the continuous aging heat treatment detailed process of two steps is 620-680 DEG C of heat preservation 4-20h, then presses 1-5 DEG C/min
It is warming up to 730-800 DEG C of heat preservation 4-20h with furnace, is air-cooled to room temperature.
6. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint according to claim 1, feature
It is, plumb joint grain size obtained is suitable with base material.
7. a kind of heat treatment process of ferronickel base wrought superalloy friction welding joint according to claim 1, feature
It is, plumb joint intensity obtained and base material maintain an equal level.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110257743A (en) * | 2019-03-15 | 2019-09-20 | 西北工业大学 | Heat-treating methods after a kind of GH4169 alloy brazed |
| CN112609064A (en) * | 2020-12-08 | 2021-04-06 | 中国石油天然气集团有限公司 | Friction welding type all-titanium alloy drill rod weld joint heat treatment process |
| CN113005380A (en) * | 2019-12-20 | 2021-06-22 | 佛山科学技术学院 | Solution heat treatment method for nickel-based alloy |
| WO2021121185A1 (en) * | 2019-12-16 | 2021-06-24 | 西安热工研究院有限公司 | High-strength and high-toughness antioxidant iron-nickel-based high-temperature alloy, and preparation method thereof |
| CN114085965A (en) * | 2021-11-19 | 2022-02-25 | 华能国际电力股份有限公司 | Two-stage solution treatment process for aging-strengthened high-temperature alloy |
| CN114807581A (en) * | 2021-01-18 | 2022-07-29 | 中国航发上海商用航空发动机制造有限责任公司 | Electron beam welding method, welded rotor, and gas turbine engine |
| CN115647566A (en) * | 2022-11-08 | 2023-01-31 | 中国航发沈阳黎明航空发动机有限责任公司 | Method for prolonging high-temperature endurance life of inertia friction welding joint |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103898426A (en) * | 2014-03-26 | 2014-07-02 | 西安热工研究院有限公司 | Heat treatment process of wrought nickel-iron-chromium based high temperature alloy |
| CN105385973A (en) * | 2015-11-27 | 2016-03-09 | 钢铁研究总院 | Thermal treatment process for nickel-based superalloy |
| CN106834990A (en) * | 2017-01-19 | 2017-06-13 | 华能国际电力股份有限公司 | Heat treatment process for improving high-temperature tensile plasticity of nickel-iron-chromium-based wrought high-temperature alloy |
| CN106939396A (en) * | 2017-02-16 | 2017-07-11 | 华能国际电力股份有限公司 | Heat treatment process for obtaining bending sawtooth crystal boundary of nickel-iron-chromium-based wrought high-temperature alloy |
| JP2017190493A (en) * | 2016-04-13 | 2017-10-19 | 株式会社日本製鋼所 | Ni-BASED SUPER ALLOY AND MANUFACTURING METHOD OF Ni-BASED SUPER ALLOY |
-
2018
- 2018-11-01 CN CN201811296443.4A patent/CN109280812A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103898426A (en) * | 2014-03-26 | 2014-07-02 | 西安热工研究院有限公司 | Heat treatment process of wrought nickel-iron-chromium based high temperature alloy |
| CN105385973A (en) * | 2015-11-27 | 2016-03-09 | 钢铁研究总院 | Thermal treatment process for nickel-based superalloy |
| JP2017190493A (en) * | 2016-04-13 | 2017-10-19 | 株式会社日本製鋼所 | Ni-BASED SUPER ALLOY AND MANUFACTURING METHOD OF Ni-BASED SUPER ALLOY |
| CN106834990A (en) * | 2017-01-19 | 2017-06-13 | 华能国际电力股份有限公司 | Heat treatment process for improving high-temperature tensile plasticity of nickel-iron-chromium-based wrought high-temperature alloy |
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