CN115852286A - Method for optimizing fracture toughness of TC11 and TC17 dissimilar titanium alloy linear friction welding joint - Google Patents
Method for optimizing fracture toughness of TC11 and TC17 dissimilar titanium alloy linear friction welding joint Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 92
- 238000003466 welding Methods 0.000 title claims abstract description 64
- 238000000034 method Methods 0.000 title claims abstract description 35
- 238000010438 heat treatment Methods 0.000 claims abstract description 178
- 238000000137 annealing Methods 0.000 claims abstract description 52
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- 239000010953 base metal Substances 0.000 description 5
- 230000007547 defect Effects 0.000 description 4
- 230000000977 initiatory effect Effects 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 238000003303 reheating Methods 0.000 description 4
- 230000032683 aging Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000003776 cleavage reaction Methods 0.000 description 1
- 239000008358 core component Substances 0.000 description 1
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- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
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Abstract
The invention discloses a method for optimizing fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint, which is implemented according to the following steps: step 1, performing linear friction welding on TC11 and TC17 titanium alloys to obtain TC11 and TC17 titanium alloy samples with original welding joints; step 2, placing the titanium alloy sample in the step 1 in a vacuum heat treatment furnace to carry out first re-furnace cold annealing heat treatment; and 3, placing the sample treated in the step 2 in a vacuum heat treatment furnace for secondary furnace cold annealing heat treatment. The invention effectively improves the uniformity of joint tissues, forms lamellar staggered tissues in the welding seam areas at the two sides of the joint to improve the fracture toughness of the joint, and solves the problem of low-toughness fracture caused by coarse grains and obvious welding interface in the welding seam area at the TC17 side of the original joint.
Description
Technical Field
The invention belongs to the technical field of optimization methods of titanium alloy welding piece joints, and particularly relates to an optimization method of fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint.
Background
The blisk is a core component of an aircraft engine and is related to the operation efficiency, safety and reliability of an aircraft. Ti-6.5Al-3.5Mo-1.5Zr-0.3Si (TC 11) and Ti-4Mo-4Cr-5Al-2Sn-2Zr (TC 17) titanium alloy have become the preferred materials for blades and discs due to the excellent performance. The linear friction welding has the advantages of high welding efficiency, unmelted joint, self-cleaning function and the like, can overcome the defects of large weight of the joggled joint, tenon gap air flow loss, easy oxidation of the traditional fusion welding joint and the like, and becomes the mainstream technology for manufacturing and repairing the blisk. A large number of researches show that the titanium alloy linear friction welding joint has excellent strength and fatigue performance, but the low toughness, especially the fracture toughness under the defect conditions of microcracks and the like, easily causes the blisk to fracture at the joint part, and is difficult to fully exert the performance advantages of the two titanium alloys.
A heat treatment method (CN 111763812A) for improving the impact toughness of a titanium alloy linear friction welding joint indicates that after solution treatment and double aging treatment (790-860 ℃) multiplied by (4-8 h) water cooling (450-500 ℃) multiplied by (3-5 h) air cooling (650-700 ℃) multiplied by (3-5 h) air cooling, the impact toughness of the TC11/TC17 titanium alloy linear friction welding joint is 9.3J/cm 2 Increased to 25J/cm 2 The above. A heat treatment method (CN 111979401A) for optimizing the microhardness of a titanium alloy linear friction welding joint comprises the steps of carrying out circulating heat treatment and double annealing on a TC11/TC17 linear friction welding joint, then circulating (600-860 ℃) for (10-20 min) for 6-10 times and (780-840 ℃) for (30-60 min) for air cooling (580-640℃)) And (4-6 h) air cooling) to ensure that the microhardness values of two sides of the joint are more uniform and stable. The fracture toughness is a toughness value when unstable fracture occurs from a crack or crack-like defect as a starting point when the crack or crack-like defect exists in a member, and is very important in engineering application, and the fracture toughness characteristics of a titanium alloy linear friction welding joint are rarely studied.
Disclosure of Invention
The invention aims to provide an optimization method of fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint, and solve the problem of low-toughness fracture of the TC11 and TC17 titanium alloy linear friction welding joint under the condition of microcracks in the prior art.
The technical scheme adopted by the invention is that the method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1, performing linear friction welding on TC11 and TC17 titanium alloys to obtain TC11 and TC17 titanium alloy samples with original welding joints;
and 3, placing the sample treated in the step 2 in a vacuum heat treatment furnace for secondary furnace cold annealing heat treatment.
The invention is also characterized in that:
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 800-900 ℃, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 800-900 ℃ again, and then preserving the heat;
and 2.2, furnace-cooling the sample subjected to heat preservation in the step 2.1 to room temperature in a vacuum heat treatment furnace to finish the first re-furnace cold annealing heat treatment.
The heat preservation time in the step 2.1 is 3-6h, and the two heating rates of the vacuum heat treatment furnace are 1-15 ℃/min.
Step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace from room temperature to 500-600 ℃, then placing the sample treated in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace again to 500-600 ℃, and then preserving the heat;
and 3.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
The heat preservation time in the step 3.1 is 6-10h, and the two heating rates of the vacuum heat treatment furnace are 1-15 ℃/min.
The invention has the beneficial effects that: the invention provides an optimization method of the fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint, which effectively improves the uniformity of joint tissues, forms a lamellar staggered structure in welding seam zones on two sides of the joint to improve the fracture toughness of the joint, and solves the problem of low-toughness fracture caused by coarse grains and obvious welding interface in the welding seam zone on the TC17 side of the original joint.
Drawings
FIG. 1 is a fracture morphology of fracture toughness of a linear friction welded joint of TC11 and TC17 dissimilar titanium alloys after dual furnace cold annealing in example 5 of the optimization method of fracture toughness of the linear friction welded joint of TC11 and TC17 of the present invention;
FIG. 2 is a microstructure diagram of a post-weld raw joint in example 5 of the optimization method of fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction weld joint according to the present invention;
FIG. 3 is a microstructure diagram of the joint after double furnace cooling annealing in example 5 of the method for optimizing fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welded joint according to the present invention;
FIG. 4 is a schematic diagram showing the structural evolution of the linear friction welded joint of example 5 subjected to a double furnace cold annealing process in the method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welded joint of the present invention;
FIG. 5 is a fracture morphology diagram of fracture toughness of an original joint in example 5 of the optimization method of fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint of the present invention.
Detailed Description
The present invention will be described in detail below with reference to the accompanying drawings and specific embodiments.
The invention discloses a method for optimizing the fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint, which is implemented by the following steps:
step 1: performing linear friction welding on the TC11 and TC17 titanium alloys to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 800-900 ℃ at the speed of 1-15 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 800-900 ℃ at the speed of 1-15 ℃/min, and then preserving the heat for 3-6 h;
step 2.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and 3, step 3: placing the sample treated in the step 2 in a vacuum heat treatment furnace for second reheating cold annealing heat treatment;
step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace from room temperature to 500-600 ℃ at the speed of 1-15 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 500-600 ℃ at the speed of 1-15 ℃/min, and then preserving the heat for 6-10 hours;
and 3.2, cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
The TC11 and TC17 titanium alloy linear friction welding joint obtained after the treatment of the steps has the fracture toughness of the TC11 base metal of more than or equal to 70 MPa.m at room temperature 1/2 The fracture toughness of the TC17 base metal is more than or equal to 80 MPa.m 1/2 The fracture toughness of the welding joint is more than or equal to 65 MPa.m 1/2 . The fracture toughness of the base metals TC11 and TC17 in the prior art is basically kept unchanged, but the fracture toughness of the non-heat-treated welding joint is 28.4 +/-0.1 MPa.m 1/2 It can be seen that the joint microstructure treated according to the present invention is obtainedEffectively improves the fracture toughness and obviously improves the fracture toughness.
Example 1
The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1: performing linear friction welding on the TC11 titanium alloy and the TC17 titanium alloy to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
and 2, step: placing the titanium alloy sample treated in the step 1 into a vacuum heat treatment furnace to perform first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 800 ℃ at the speed of 1 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 800 ℃ at the speed of 1 ℃/min, and then preserving the heat for 6 hours;
step 2.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and step 3: placing the sample treated in the step 2 in a vacuum heat treatment furnace for second reheating cold annealing heat treatment;
step 3 is implemented specifically according to the following steps:
step 3.1, heating the vacuum heat treatment furnace from room temperature to 500 ℃ at the speed of 1 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 500 ℃ at the speed of 1 ℃/min again, and then preserving the temperature for 10 hours;
and 3.2, cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
Example 2
The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1: performing linear friction welding on the TC11 titanium alloy and the TC17 titanium alloy to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
and 2, step: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 880 ℃ at a speed of 15 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 880 ℃ again at a speed of 15 ℃/min, and then preserving the heat for 3 hours;
step 2.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for secondary furnace cold annealing heat treatment;
step 3.1, heating the vacuum heat treatment furnace from room temperature to 600 ℃ at a speed of 15 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 600 ℃ at a speed of 15 ℃/min, and then preserving the heat for 6 hours;
and 3.2, cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
Example 3
The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1: performing linear friction welding on the TC11 titanium alloy and the TC17 titanium alloy to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 820 ℃ at the speed of 3 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 820 ℃ at the speed of 3 ℃/min, and then preserving the heat for 5 hours;
step 2.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for secondary furnace cold annealing heat treatment;
step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace from room temperature to 520 ℃ at the speed of 3 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 520 ℃ at the speed of 3 ℃/min, and then preserving the heat for 9 hours;
step 3.2, furnace cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish second furnace cold annealing heat treatment
Example 4
The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1: performing linear friction welding on the TC11 titanium alloy and the TC17 titanium alloy to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 860 ℃ at the speed of 12 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 860 ℃ at the speed of 12 ℃/min, and then preserving the heat for 3.5 hours;
step 2.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and step 3: placing the sample treated in the step 2 in a vacuum heat treatment furnace for second reheating cold annealing heat treatment;
step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace from room temperature to 580 ℃ at the speed of 12 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 580 ℃ at the speed of 12 ℃/min, and then preserving the heat for 7 hours;
and 3.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
Example 5
The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1: performing linear friction welding on the TC11 titanium alloy and the TC17 titanium alloy to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
and 2, step: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace from room temperature to 835 ℃ at the speed of 6 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 835 ℃ at the speed of 6 ℃/min again, and then preserving the heat for 4.h;
step 2.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for secondary furnace cold annealing heat treatment;
step 3 is implemented specifically according to the following steps:
step 3.1, heating the vacuum heat treatment furnace from room temperature to 540 ℃ at the speed of 6 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 540 ℃ at the speed of 6 ℃/min again, and then preserving the heat for 8.5 hours;
and 3.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
Example 6
The optimization method of the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is implemented according to the following steps:
step 1: performing linear friction welding on the TC11 titanium alloy and the TC17 titanium alloy to obtain a TC11/TC17 titanium alloy sample with an original welding joint;
and 2, step: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;
the step 2 is implemented according to the following steps:
2.1, heating the vacuum heat treatment furnace to 845 ℃ from room temperature at the speed of 9 ℃/min, then putting the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 845 ℃ at the speed of 9 ℃/min, and then keeping the temperature for 4 hours;
step 2.2, furnace cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the first heavy furnace cold annealing heat treatment;
and step 3: placing the sample treated in the step 2 in a vacuum heat treatment furnace for second reheating cold annealing heat treatment;
step 3.1, heating the vacuum heat treatment furnace from room temperature to 560 ℃ at the speed of 9 ℃/min, then putting the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 560 ℃ at the speed of 9 ℃/min, and then preserving the heat for 7.5h;
and 3.2, cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
FIG. 1 is a fracture morphology of fracture toughness of a joint after double furnace cold annealing in an annealing method for improving fracture toughness of a TC11/TC17 titanium alloy linear friction weld joint of the present invention obtained in example 5. The break also consists of three parts, as shown in FIG. 1 (a) (b). Compared with the fracture morphology of the original joint, the crack propagation area is rougher, and the width of the shearing lip area is increased. In the crack initiation region, the fatigue stripe spacing gradually increases along the crack propagation direction, and a large number of tearing edges appear, as shown in fig. 1 (c); a large amount of toughness is distributed in the crack propagation region and the shear lip region as shown in fig. 1 (d) - (e), and thus the heat-treated joint is a typical ductile fracture mode, and its fracture toughness is sharply increased.
FIG. 2 is a microstructure diagram of an as-welded joint obtained in example 5 according to the annealing method for improving fracture toughness of a TC11/TC17 titanium alloy linear friction welded joint of the present invention, and it can be seen from FIG. 2 that a large amount of acicular martensite alpha 'phase and a small amount of retained beta phase are formed in a welded zone at the TC11 side of the as-welded joint without heat treatment, and a TC17 side welded zone is formed by coarse beta grains, a small amount of primary alpha phase at grain boundaries and intra-granular martensite alpha' phase.
FIG. 3 is a microstructure diagram of a joint obtained in example 5 after double furnace cold annealing in the annealing method for improving fracture toughness of a TC11/TC17 titanium alloy linear friction welded joint of the present invention, and it can be seen from FIG. 3 that after double furnace cold annealing, the microstructure difference of the TC11 and TC17 side weld zones is significantly reduced. The TC11 side welding seam area consists of a supersaturated solid solution alpha ' phase and a beta phase, coarse beta grains in the TC17 side welding seam area disappear, and the martensite alpha ' phase is converted into a lamellar alpha + alpha ' phase and is uniformly distributed on a beta substrate.
FIG. 4 is a schematic diagram showing the structure evolution of the joint after the double furnace cold annealing process in the annealing method for improving the fracture toughness of the TC11/TC17 titanium alloy linear friction welded joint of the invention obtained in example 5. As clearly seen from FIG. 4, after the double annealing treatment, the acicular martensite alpha 'phase in the TC11 side weld zone is slightly enlarged, the coarse grains in the TC17 side weld zone are crushed, the intragranular globular dispersed alpha' phase is partially converted into acicular, and the lamellar alpha phase is filled in the grain boundary. The whole welding seam area is composed of needle-shaped and lamellar basket tissues.
FIG. 5 is a fracture morphology of fracture toughness of an original joint in an annealing method for improving the fracture toughness of a TC11/TC17 titanium alloy linear friction weld joint obtained in example 5. As can be seen from FIGS. 5 (a) (b), the fracture is composed of three parts, a fracture initiation region, a propagation region and a shear lip region, the fracture initiation region is extremely non-uniform in width, the crack propagation region is relatively smooth, and the shear lip region is very narrow. A large number of tearing ridges and fine dimples appear in the initiation region, as shown in fig. 5 (c); in the crack propagation zone, a distinct river pattern and morphology along the fracture can be observed, as shown in FIG. 5 (d); smooth surfaces and deformed dimples are distributed in the shear lip region as shown in FIG. 5 (e). The entire linker thus belongs to the typical quasi-cleavage mode of fracture, exhibiting brittle fracture characteristics.
The TC11 and TC17 titanium alloy linear friction welding joint obtained after the treatment of the steps has the fracture toughness of the TC11 base metal of more than or equal to 70 MPa-m at room temperature 1/2 The fracture toughness of the TC17 base metal is more than or equal to 80 MPa.m 1/2 The fracture toughness of the welding joint is more than or equal to 65 MPa.m 1/2 . The fracture toughness of the parent metal TC11 and TC17 in the prior art is basically kept unchanged, but the fracture toughness of the non-heat-treated welding joint is 28.4 +/-0.1 MPa.m 1/2 Therefore, the microstructure of the joint treated by the method is effectively improved, and the fracture toughness is obviously improved.
Claims (5)
- The optimization method of the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint is characterized by comprising the following steps:step 1, performing linear friction welding on TC11 and TC17 titanium alloys to obtain TC11 and TC17 titanium alloy samples with original welding joints;step 2, placing the titanium alloy sample in the step 1 in a vacuum heat treatment furnace for first re-furnace cold annealing heat treatment;and 3, placing the sample treated in the step 2 in a vacuum heat treatment furnace for secondary furnace cold annealing heat treatment.
- 2. The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction weld joint according to claim 1, wherein the step 2 is specifically implemented according to the following steps:2.1, heating the vacuum heat treatment furnace from room temperature to 800-900 ℃, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 800-900 ℃ again, and then preserving the heat;and 2.2, furnace-cooling the sample subjected to heat preservation in the step 2.1 to room temperature in a vacuum heat treatment furnace to finish the first re-furnace cold annealing heat treatment.
- 3. The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint according to claim 2, wherein the heat preservation time in the step 2.1 is 3-6h, and the two heating rates of the vacuum heat treatment furnace are 1-15 ℃/min.
- 4. The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction weld joint according to claim 1, wherein the step 3 is specifically implemented according to the following steps:step 3.1, heating the vacuum heat treatment furnace from room temperature to 500-600 ℃, then placing the sample treated in the step 2 into the vacuum heat treatment furnace, heating the temperature of the vacuum heat treatment furnace to 500-600 ℃ again, and then preserving the heat;and 3.2, furnace-cooling the heat-preserved sample in a vacuum heat treatment furnace to room temperature to finish the second furnace cold annealing heat treatment.
- 5. The method for optimizing the fracture toughness of the TC11 and TC17 dissimilar titanium alloy linear friction welding joint according to claim 4, wherein the heat preservation time in the step 3.1 is 6-10h, and the two heating rates of the vacuum heat treatment furnace are 1-15 ℃/min.
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| US20080000558A1 (en) * | 2006-06-30 | 2008-01-03 | Nan Yang | Friction welding |
| CN113084458A (en) * | 2021-04-12 | 2021-07-09 | 西部金属材料股份有限公司 | Titanium alloy gas cylinder and preparation method thereof |
| CN114164381A (en) * | 2021-11-29 | 2022-03-11 | 西安理工大学 | Method for optimizing mechanical properties of TC21 titanium alloy linear friction welding joint |
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