CN116871655A - Ti (titanium) 2 Welding method of AlNb-based alloy - Google Patents
Ti (titanium) 2 Welding method of AlNb-based alloy Download PDFInfo
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- CN116871655A CN116871655A CN202310904568.5A CN202310904568A CN116871655A CN 116871655 A CN116871655 A CN 116871655A CN 202310904568 A CN202310904568 A CN 202310904568A CN 116871655 A CN116871655 A CN 116871655A
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- 239000000956 alloy Substances 0.000 title claims abstract description 105
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 104
- 238000003466 welding Methods 0.000 title claims abstract description 73
- 238000000034 method Methods 0.000 title claims abstract description 33
- 239000010936 titanium Substances 0.000 title claims description 46
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims description 3
- 229910052719 titanium Inorganic materials 0.000 title claims description 3
- 238000010438 heat treatment Methods 0.000 claims abstract description 49
- 230000032683 aging Effects 0.000 claims abstract description 32
- 238000011282 treatment Methods 0.000 claims abstract description 24
- 239000006104 solid solution Substances 0.000 claims abstract description 21
- 238000004321 preservation Methods 0.000 claims abstract description 18
- 239000000243 solution Substances 0.000 claims abstract description 12
- 238000001816 cooling Methods 0.000 claims description 17
- 230000001550 time effect Effects 0.000 claims 2
- 238000009413 insulation Methods 0.000 claims 1
- 230000035882 stress Effects 0.000 abstract description 4
- 238000009826 distribution Methods 0.000 abstract description 3
- 239000010953 base metal Substances 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 26
- 239000000463 material Substances 0.000 description 13
- 238000012360 testing method Methods 0.000 description 9
- 238000004519 manufacturing process Methods 0.000 description 5
- 239000002932 luster Substances 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 239000000110 cooling liquid Substances 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910004349 Ti-Al Inorganic materials 0.000 description 1
- 229910010038 TiAl Inorganic materials 0.000 description 1
- 229910004692 Ti—Al Inorganic materials 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
- B23K20/1275—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding involving metallurgical change
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/24—Preliminary treatment
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
The invention belongs to the technical field of welding, and in particular relates to Ti 2 A welding method of an AlNb-based alloy. The invention provides a Ti 2 The welding method of the AlNb-based alloy comprises the following steps of: ti is mixed with 2 Carrying out solution treatment on the AlNb-based alloy to obtain Ti in a solid solution state 2 An AlNb-based alloy; the Ti in solid solution state 2 Welding the AlNb-based alloy to obtain welded Ti 2 An AlNb-based alloy; and welding the welded Ti 2 And carrying out heat preservation treatment, first aging heat treatment and second aging heat treatment on the AlNb-based alloy in sequence to obtain the welding alloy. The welding method provided by the invention optimizes the structure types and distribution states of the welding joint and the base metal while eliminating the residual stress of the welding joint, thereby effectively improving Ti 2 Inertia mole of AlNb-based alloyThe strength properties of the welded assembly are wiped.
Description
Technical Field
The invention belongs to the technical field of welding, and in particular relates to Ti 2 A welding method of an AlNb-based alloy.
Background
In recent years, the improvement of the performance of advanced aeroengines in the world mainly depends on new materials and new processes. The aeroengine is used as a highly complex and precise thermal energy machine, and the manufacturing material of the aeroengine needs to work under extremely complex environments such as high temperature, high pressure, high rotating speed and the like, so that the development of the aeroengine with high thrust-weight ratio is closely related to the application of high-temperature structural materials. In addition, the engine should also have the characteristics of low weight, long service life and reusability. Therefore, development and manufacture of high thrust ratio aeroengines place stringent demands on both materials used and manufacturing techniques.
With the progress of aero-manufacturing technology, high thrust-weight ratio aero-engine structures are developed towards light weight, structural integrity and compositing. Currently advanced welding technology is one of the most effective methods for achieving the integration of engine structural components. In addition, the weight of the material can be further reduced and the thrust ratio can be improved on the basis of the application of the advanced welding technology, wherein the intermetallic compound has excellent performances such as heat resistance, high specific strength, high specific life, high thermal conductivity and high oxidation resistance of high-temperature alloy, toughness, good hot workability and the like of ceramic materials, and is particularly favored by aviation departments.
Ti 2 The AlNb-based alloy is subsequent to Ti 3 A novel light high-temperature resistant structural material of Ti-Al alloy system with high Nb content is developed after Al and TiAl alloys are prepared. The structure is characterized by taking O phase as a main phase, B 2 Phase sum alpha 2 The phase is a composite structure of auxiliary phases, wherein the long-range ordered O-phase orthorhombic lattice structure can weaken dislocation movement and prevent crack propagation, so that the alloy has higher specific strength, specific rigidity, good fracture toughness and high-temperature creep resistance, can be safely used in a temperature range of 650-750 ℃, can meet extremely high requirements of high thrust-weight ratio aeroengine cold/hot end components on manufacturing material performance to a greater extent, and is regarded as an ideal light-weight novel high-temperature resistant structural material which is favorable for realizing further improvement of engine performance through structural weight reduction.
As an advanced solid phase welding technique, the inertia friction welding process has the advantages of less process control parameters, small heat input, small deformation and narrow welding seam, and the quality of 6 sigma can be achieved by few welding seamsHorizontal processes are particularly suitable for welding dissimilar materials, such as powder alloys and superalloys. However, the welded joint also has the characteristics of lower joint strength performance and the like caused by larger residual stress. Due to Ti 2 On the basis of high specific strength, the AlNb-based alloy material has the characteristics of hardness and brittleness of intermetallic compounds, and still can remain larger stress under reasonable inertia friction welding process parameters, so that the strength performance of a welded joint is reduced.
Disclosure of Invention
The invention aims to provide Ti 2 Welding method of AlNb-based alloy, the method provided by the invention can improve Ti 2 Strength of the weld joint of the AlNb-based alloy.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a Ti 2 The welding method of the AlNb-based alloy comprises the following steps of:
ti is mixed with 2 Carrying out solution treatment on the AlNb-based alloy to obtain Ti in a solid solution state 2 An AlNb-based alloy;
the Ti in solid solution state 2 Welding the AlNb-based alloy to obtain welded Ti 2 An AlNb-based alloy;
and welding the welded Ti 2 And carrying out heat preservation treatment, first aging heat treatment and second aging heat treatment on the AlNb-based alloy in sequence to obtain the welding alloy.
Preferably, the Ti is 2 The atomic percentage of Al in the AlNb-based alloy is 18-30%, and the atomic percentage of Nb is 12.5-30%.
Preferably, the temperature of the solution treatment is 850-950 ℃, and the heat preservation time is 30min.
Preferably, the temperature of the heat preservation treatment is 680-720 ℃, and the heat preservation time is 50-70 min;
after the heat preservation treatment, the obtained alloy is cooled to room temperature.
Preferably, the temperature of the first aging heat treatment is 980-1000 ℃, and the heat preservation time is 100-120 min.
Preferably, the time from the room temperature to the first time-efficient heat treatment temperature is 90-110 min.
Preferably, after the first aging heat treatment, the alloy obtained is cooled to room temperature.
Preferably, the temperature of the second aging heat treatment is 780-800 ℃, and the heat preservation time is 1420-1450 min.
Preferably, the time from the room temperature to the second aging heat treatment temperature is 70 to 90 minutes.
Preferably, the first and second aging heat treatments are both performed under vacuum conditions.
The invention provides a Ti 2 The welding method of the AlNb-based alloy comprises the following steps of: ti is mixed with 2 Carrying out solution treatment on the AlNb-based alloy to obtain Ti in a solid solution state 2 An AlNb-based alloy; the Ti in solid solution state 2 Welding the AlNb-based alloy to obtain welded Ti 2 An AlNb-based alloy; and welding the welded Ti 2 And carrying out heat preservation treatment, first aging heat treatment and second aging heat treatment on the AlNb-based alloy in sequence to obtain the welding alloy. The welding method provided by the invention can eliminate the residual stress of the welding joint and optimize the O phase and alpha phase in the welding joint and the base metal 2 The structure and distribution state of the phase and the B2 phase are improved effectively 2 Strength properties of the AlNb-based alloy inertia friction welded assembly.
Drawings
FIG. 1 is a microstructure of a Ti-20Al-25Nb type alloy in solid solution in example 1;
FIG. 2 is a microstructure of a base material in the weld alloy obtained in example 1;
FIG. 3 is a microstructure view of a weld joint in the weld alloy obtained in example 1;
FIG. 4 is a sample of the weld alloy obtained in example 1 after room temperature stretching;
FIG. 5 is a test specimen of the weld alloy obtained in example 1 after being drawn at a high temperature of 650 ℃;
fig. 6 is a flow chart of the welding method in example 1.
Detailed Description
The invention provides a Ti 2 The welding method of the AlNb-based alloy comprises the following steps of:
ti is mixed with 2 Carrying out solution treatment on the AlNb-based alloy to obtain Ti in a solid solution state 2 An AlNb-based alloy;
the Ti in solid solution state 2 Welding the AlNb-based alloy to obtain welded Ti 2 An AlNb-based alloy;
and welding the welded Ti 2 And carrying out heat preservation treatment, first aging heat treatment and second aging heat treatment on the AlNb-based alloy in sequence to obtain the welding alloy.
The invention uses Ti 2 Carrying out solution treatment on the AlNb-based alloy to obtain Ti in a solid solution state 2 An AlNb-based alloy.
In the present invention, the Ti is 2 The atomic percentage of Al in the nb-based alloy is preferably 18 to 30%, more preferably 21 to 27%, and still more preferably 22 to 25%; the atom percentage of Nb is 12.5 to 30%, more preferably 15 to 27%, still more preferably 17 to 25%, and most preferably 22 to 23%. In the present invention, the Ti is 2 The AlNb-based alloy preferably includes a Ti-25Al-17 Nb-type alloy, a Ti-21Al-22 Nb-type alloy, a Ti-22Al-23 Nb-type alloy, a Ti-22Al-25 Nb-type alloy or a Ti-22Al-27 Nb-type alloy (wherein numerals represent atomic percentages).
In the present invention, the temperature of the solution treatment is preferably 850 to 950 ℃, more preferably 880 to 920 ℃, still more preferably 890 to 900 ℃, and the holding time is preferably 30 minutes. After the solution treatment, the present invention preferably further includes water-cooling the resulting alloy.
Obtaining Ti in solid solution state 2 After AlNb-based alloy, the present invention makes the Ti in solid solution state 2 Welding the AlNb-based alloy to obtain welded Ti 2 An AlNb-based alloy.
The present invention also preferably includes the step of adding Ti in a solid solution state to the steel before the welding 2 Pretreating the AlNb-based alloy; the pretreatment is preferablyComprising the following steps: turning the Ti in solid solution 2 The end face of the AlNb-based alloy shows metallic luster, and is wiped by alcohol or acetone to remove cooling liquid and greasy dirt and then dried.
In the present invention, the welding is preferably inertia friction welding. In the present invention, the condition parameters of the inertia friction welding are preferably: the rotation speed is 500rpm, and the inertia is 165 kg.m 2 The pressure was 60MPa. In a specific embodiment of the present invention, the inertia friction welding process preferably includes: and respectively clamping the pretreated alloy on the main shaft rotating side and the tailstock moving side of the inertia friction welding machine, and performing inertia friction welding.
Obtaining the welded Ti 2 After AlNb-based alloy, the invention makes the welded Ti 2 And carrying out heat preservation treatment, first aging heat treatment and second aging heat treatment on the AlNb-based alloy in sequence to obtain the welding alloy.
In the invention, the temperature of the heat preservation treatment is preferably 680-720 ℃, and more preferably 700 ℃; the holding time is preferably 50 to 70 minutes, more preferably 60 minutes. In the present invention, the heat-retaining treatment is preferably performed in a heat treatment furnace.
After the heat preservation treatment, the invention also preferably comprises the step of cooling the obtained alloy to room temperature; after cooling to room temperature, it also preferably includes removing the weld flash from the inner and outer sides of the alloy until the weld joint is smooth and exhibits metallic luster.
In the present invention, the temperature of the first aging heat treatment is preferably 980 to 1000 ℃, more preferably 985 to 990 ℃; the time from the room temperature to the first time-efficient heat treatment temperature is preferably 90 to 110 minutes, more preferably 100 minutes; the holding time is preferably 100 to 120 minutes, more preferably 110 minutes. In the present invention, the first time-efficient heat treatment is preferably performed under vacuum. In the present invention, the first time-efficient heat treatment is preferably performed in a vacuum heat treatment furnace.
After the first aging heat treatment, the present invention further preferably includes cooling the resulting alloy to room temperature; the cooling mode is preferably air cooling or cooling under atmosphere.
In the invention, the temperature of the second aging heat treatment is preferably 780-800 ℃, and more preferably 785-790 ℃; the time from room temperature to the second aging heat treatment temperature is preferably 70 to 90 minutes, more preferably 80 minutes; the holding time is preferably 1420 to 1450min, more preferably 1430 to 1440min. In the present invention, the second aging heat treatment is preferably performed under vacuum. In the present invention, the second aging heat treatment is preferably performed in a vacuum heat treatment furnace.
After the second aging heat treatment, the present invention further preferably includes cooling the resulting alloy to room temperature; the cooling mode is preferably air cooling or cooling under atmosphere.
For further explanation of the present invention, the present invention is provided with a Ti in combination with the accompanying drawings and examples 2 The welding method of the AlNb-based alloy is described in detail, but they are not construed as limiting the scope of the invention.
Example 1
Carrying out solution treatment on the Ti-20Al-25Nb type alloy at 900 ℃ for 30min, and then carrying out water cooling to obtain the Ti-20Al-25Nb type alloy in a solid solution state;
turning the end face of the Ti-20Al-25Nb alloy in a solid solution state until the end face shows metallic luster, wiping the end face by alcohol, removing cooling liquid and greasy dirt of the end face, and airing;
respectively clamping the pretreated Ti-20Al-25Nb type alloy on the main shaft rotating side and the tailstock moving side of the inertia friction welding machine, and performing inertia friction welding to obtain the welded Ti-20Al-25Nb type alloy, wherein the inertia friction welding condition parameters are as follows: the rotation speed is 500rpm, and the inertia is 165 kg.m 2 The pressure is 60 MPa;
placing the obtained welded Ti-20Al-25Nb alloy into a heat treatment furnace with the temperature of 700 ℃ for 60min, taking out, and cooling to room temperature; after cooling, removing welding burrs on the inner side and the outer side of the alloy until the welding joint is smooth and shows metallic luster;
loading the welded alloy into a vacuum heat treatment furnace for first time-efficiency heat treatment, wherein the temperature of the first time-efficiency heat treatment is 1000 ℃, the heat preservation time is 120min, the heating time from room temperature to 1000 ℃ is 100min, and after the first time-efficiency heat treatment is finished, air cooling is carried out to room temperature;
and (3) putting the cooled alloy into a vacuum heat treatment furnace again for second aging heat treatment, wherein the temperature of the second aging heat treatment is 790 ℃, the heat preservation time is 1450min, the heating time from room temperature to 790 ℃ is 80min, and after the second aging heat treatment is finished, air cooling is carried out to room temperature, so that the welding alloy is obtained.
Performance testing
Test example 1
FIG. 1 is a microstructure of a Ti-20Al-25Nb type alloy in solid solution in example 1; FIG. 2 is a microstructure of a base material in a weld alloy of example 1; FIG. 3 is a microstructure view of a weld joint in the weld alloy of example 1;
as can be seen from FIG. 1, the structure of the Ti-20Al-25 Nb-type alloy base material in the solid solution state is composed of alpha 2 Three phases of phase, B2 phase and O phase, wherein alpha 2 The phase is approximately equiaxed and intermittently distributed at the grain boundary of the original B2 phase, and the O phase is in a rod shape and is parallel or crossed and dispersedly distributed in the B2 phase matrix;
as can be seen from FIG. 2, after the Ti-20Al-25Nb alloy is subjected to solid solution and aging treatment, the microstructure of the base material is converted into a two-phase structure of B2+O phase, and the O phase structure is distributed on the B2 phase matrix in an equiaxed and blocky manner;
as can be seen from fig. 3, the microstructure of the welded joint region has a precipitate of O-phase structure along both the equiaxed B2 phase grain boundaries and the intragranular phase, and is in a continuous network structure at the grain boundaries and is in a block-like and needle-like structure distribution in the intragranular phase.
Test example 2
The welding alloy obtained in example 1 was subjected to tensile strength test at room temperature and 650 ℃ respectively, and the test results obtained are shown in table 1, wherein fig. 4 is a test sample of the welding alloy obtained in example 1 after room temperature stretching, and fig. 5 is a test sample of the welding alloy obtained in example 1 after stretching at 650 ℃;
table 1 tensile strength test results of the welding alloy obtained in example 1
| Room temperature tensile strength/MPa | Tensile strength/MPa at 650 DEG C | |
| Example 1 | 1195 | 985 |
As can be seen from Table 1, the welding alloy obtained by the welding method provided by the invention has excellent tensile strength performance at room temperature and 650 ℃ and is Ti 2 The use of an AlNb-based alloy inertia friction welded assembly provides support for an aircraft engine rotor assembly.
Although the foregoing embodiments have been described in some, but not all embodiments of the invention, other embodiments may be obtained according to the present embodiments without departing from the scope of the invention.
Claims (10)
1. Ti (titanium) 2 The welding method of the AlNb-based alloy is characterized by comprising the following steps of:
ti is mixed with 2 Carrying out solution treatment on the AlNb-based alloy to obtain Ti in a solid solution state 2 An AlNb-based alloy;
the Ti in solid solution state 2 Welding the AlNb-based alloy to obtain welded Ti 2 An AlNb-based alloy;
and welding the welded Ti 2 Thermal insulation place for AlNb-based alloy in sequenceAnd (3) performing first time-effect heat treatment and second time-effect heat treatment to obtain the welding alloy.
2. The welding method according to claim 1, wherein the Ti 2 The atomic percentage of Al in the AlNb-based alloy is 18-30%, and the atomic percentage of Nb is 12.5-30%.
3. The welding method according to claim 1, wherein the temperature of the solution treatment is 850-950 ℃ and the holding time is 30min.
4. The welding method according to claim 1, wherein the temperature of the heat preservation treatment is 680-720 ℃ and the heat preservation time is 50-70 min;
after the heat preservation treatment, the obtained alloy is cooled to room temperature.
5. The welding method according to claim 1, wherein the temperature of the first aging heat treatment is 980-1000 ℃ and the holding time is 100-120 min.
6. The welding method according to claim 5, wherein the time from the room temperature to the first time-efficient heat treatment temperature is 90 to 110 minutes.
7. The welding method of claim 5, further comprising cooling the resulting alloy to room temperature after the first aging heat treatment.
8. The welding method according to claim 1, wherein the temperature of the second aging heat treatment is 780-800 ℃ and the holding time is 1420-1450 min.
9. The welding method according to claim 8, wherein the time from the room temperature to the second aging heat treatment temperature is 70 to 90 minutes.
10. The welding method according to any one of claims 1, 5 to 9, wherein the first aging heat treatment and the second aging heat treatment are both performed under vacuum conditions.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310904568.5A CN116871655A (en) | 2023-07-24 | 2023-07-24 | Ti (titanium) 2 Welding method of AlNb-based alloy |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310904568.5A CN116871655A (en) | 2023-07-24 | 2023-07-24 | Ti (titanium) 2 Welding method of AlNb-based alloy |
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| CN202310904568.5A Pending CN116871655A (en) | 2023-07-24 | 2023-07-24 | Ti (titanium) 2 Welding method of AlNb-based alloy |
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