CN115852286B - Optimizing method for fracture toughness of TC11 and TC17 dissimilar titanium alloy linear friction welding joint - Google Patents
Optimizing method for 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 89
- 238000003466 welding Methods 0.000 title claims abstract description 59
- 238000000034 method Methods 0.000 title claims abstract description 32
- 238000010438 heat treatment Methods 0.000 claims abstract description 179
- 238000000137 annealing Methods 0.000 claims abstract description 52
- 238000001816 cooling Methods 0.000 claims description 23
- 229910052751 metal Inorganic materials 0.000 claims description 8
- 239000002184 metal Substances 0.000 claims description 8
- 238000004321 preservation Methods 0.000 claims description 6
- 230000000630 rising effect Effects 0.000 claims 2
- 238000005457 optimization Methods 0.000 abstract description 7
- 229910000734 martensite Inorganic materials 0.000 description 4
- 230000007547 defect Effects 0.000 description 3
- 238000010008 shearing Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 2
- 230000000977 initiatory effect Effects 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 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
- 239000000306 component Substances 0.000 description 1
- 239000008358 core component Substances 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000463 material Substances 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
- 239000000758 substrate Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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Abstract
The invention discloses an optimization method of fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding head, which is implemented according to the following steps: step 1, performing linear friction welding on TC11 and TC17 titanium alloy 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 perform 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 annealing heat treatment. The invention effectively improves the uniformity of joint structure, and forms a lamellar staggered structure in the weld zone at two sides of the joint so as to improve the fracture toughness of the joint, thereby solving the problem of low toughness fracture caused by coarse grains and obvious welding interfaces of the weld zone 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
Blisks are a core component of an aircraft engine, relating to the efficiency of operation and safety reliability of the aircraft. Ti-6.5Al-3.5Mo-1.5Zr-0.3Si (TC 11) and Ti-4Mo-4Cr-5Al-2Sn-2Zr (TC 17) titanium alloys have become the materials of choice for blades and wheel discs due to their excellent properties. 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 tenon joint weight, tenon gap air flow loss, easiness in oxidization of the traditional fusion welding joint and the like, and becomes a mainstream technology for manufacturing and repairing the blisk. A large number of researches show that the titanium alloy linear friction welding head has excellent strength and fatigue performance, but low toughness, particularly fracture toughness under the defect of microcracks and the like, is easy to cause the blisk to fracture at the joint part, and the performance advantages of the two titanium alloys are difficult to fully develop.
A heat treatment method (CN 111763812A) for improving the impact toughness of a titanium alloy linear friction welding joint indicates that the impact toughness of the TC11/TC17 titanium alloy linear friction welding joint is from 9J/cm after solid solution and double aging ((790-860 ℃) X (4-8 h) water cooling+ (450-500 ℃) X (3-5 h) air cooling+ (650-700 ℃) X (3-5 h) air cooling) heat treatment 2 Increased to 25J/cm 2 The above. A heat treatment method (CN 111979401A) for optimizing microhardness of a titanium alloy linear friction welding joint is characterized in that the microhardness values of two sides of the joint are more uniform and stable by carrying out cyclic heat treatment and double annealing on the TC11/TC17 linear friction welding joint (600-860 ℃) X (10-20 min) and then (780-840 ℃) X (30-60 min) air cooling and (580-640 ℃) X (4-6 h) air cooling. While fracture toughness is the toughness value at which unstable fracture occurs starting from a crack or crack-like defect in a component, which is very important in engineering applications, the fracture toughness characteristics of a titanium alloy linear friction welding joint are still being studied.
Disclosure of Invention
The invention aims to provide an optimization method for fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding head, which solves the problem of low toughness fracture of the TC11 and TC17 titanium alloy linear friction welding head under the condition of microcrack in the prior art.
The technical scheme adopted by the invention is that the optimizing method of the fracture toughness of the linear friction welding joint of the TC11 and TC17 dissimilar titanium alloy is implemented according to the following steps:
step 1, performing linear friction welding on TC11 and TC17 titanium alloy 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 perform 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 annealing heat treatment.
The invention is also characterized in that:
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 800-900 ℃ from room temperature, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 800-900 ℃ again, and then preserving 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, and finishing the first heavy 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.
The step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace to 500-600 ℃ from room temperature, then placing the sample treated in the step 2 in the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 500-600 ℃ again, and then preserving heat;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace 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 beneficial effects of the invention are as follows: the invention provides an optimization method for fracture toughness of a TC11 and TC17 dissimilar titanium alloy linear friction welding joint, which effectively improves uniformity of joint structure, and forms a lamellar staggered structure in weld joints at two sides of the joint to improve the fracture toughness of the joint, thereby solving the problem of low toughness fracture caused by coarse grains and obvious welding interfaces of the weld joints at the side of the original joint TC 17.
Drawings
FIG. 1 is a graph of fracture toughness and fracture morphology of a joint after double furnace cold annealing in example 5 of an optimization method of fracture toughness of a linear friction welding joint of TC11 and TC17 dissimilar titanium alloys according to the invention;
FIG. 2 is a microstructure view of a welded original joint in example 5 of the method of optimizing fracture toughness of a linear friction weld joint of a TC11 and TC17 dissimilar titanium alloy according to the present invention;
FIG. 3 is a microstructure of a joint after double furnace cold annealing in example 5 of the method for optimizing fracture toughness of a linear friction weld joint of TC11 and TC17 dissimilar titanium alloys according to the present invention;
FIG. 4 is a schematic diagram showing the joint structure evolution of example 5 through a double furnace cold annealing process in the method for optimizing the fracture toughness of the linear friction welding joint of TC11 and TC17 dissimilar titanium alloys according to the present invention;
FIG. 5 is a graphical representation of fracture toughness and fracture morphology of an original joint in example 5 of a method for optimizing fracture toughness of a linear friction welding joint of a TC11 and TC17 dissimilar titanium alloy according to the present invention.
Detailed Description
The invention will be described in detail below with reference to the drawings and the detailed description.
The invention relates to an optimization method for 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 alloy to obtain a TC11/TC17 titanium alloy sample with an original welded joint;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 800-900 ℃ from room temperature at a speed of 1-15 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 800-900 ℃ again at a speed of 1-15 ℃/min, and then preserving heat for 3-6 hours;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
the step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace to 500-600 ℃ from room temperature at a speed of 1-15 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 500-600 ℃ again at a speed of 1-15 ℃/min, and then preserving heat for 6-10 h;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment.
The TC11 and TC17 titanium alloy linear friction welding head obtained by the steps has the TC11 parent metal fracture toughness of more than or equal to 70 MPa.m at room temperature 1/2 TC17 parent metal fracture toughness is more than or equal to 80 MPa.m 1/2 The fracture toughness of the welded joint is more than or equal to 65 MPa.m 1/2 . While the fracture toughness of the TC11 and TC17 parent metals in the prior art basically remains unchanged, the fracture toughness of the welding joint without heat treatment is 28.4+/-0.1 MPa m 1/2 Thus, the microstructure of the joint treated by the method is effectively improved, and the fracture toughness is obviously improved.
Example 1
The optimizing 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;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 800 ℃ from room temperature at a speed of 1 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 800 ℃ again at a speed of 1 ℃/min, and then preserving heat for 6 hours;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
the step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace to 500 ℃ from room temperature at a speed of 1 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 500 ℃ again at a speed of 1 ℃/min, and then preserving heat for 10 hours;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment.
Example 2
The optimizing 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;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 880 ℃ from room temperature at a speed of 15 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 880 ℃ again at a speed of 15 ℃/min, and then preserving heat for 3 hours;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
step 3.1, heating the vacuum heat treatment furnace to 600 ℃ from room temperature at a speed of 15 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 600 ℃ again at a speed of 15 ℃/min, and then preserving heat for 6 hours;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment.
Example 3
The optimizing 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;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 820 ℃ from room temperature at a speed of 3 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 820 ℃ again at a speed of 3 ℃/min, and then preserving heat for 5 hours;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
the step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace to 520 ℃ from room temperature at a speed of 3 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 520 ℃ again at a speed of 3 ℃/min, and then preserving heat for 9 hours;
3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment
Example 4
The optimizing 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;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 860 ℃ from room temperature at a speed of 12 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 860 ℃ again at a speed of 12 ℃/min, and then preserving heat for 3.5h;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
the step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace to 580 ℃ from room temperature at a speed of 12 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 580 ℃ again at a speed of 12 ℃/min, and then preserving heat for 7 hours;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment.
Example 5
The optimizing 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;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 835 ℃ from room temperature at a speed of 6 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 835 ℃ again at a speed of 6 ℃/min, and then preserving heat 4.h;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
the step 3 is specifically implemented according to the following steps:
step 3.1, heating the vacuum heat treatment furnace to 540 ℃ from room temperature at a speed of 6 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 540 ℃ again at a speed of 6 ℃/min, and then preserving heat for 8.5 hours;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment.
Example 6
The optimizing 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;
step 2: placing the titanium alloy sample obtained after the treatment in the step 1 into a vacuum heat treatment furnace for first heavy furnace cold annealing heat treatment;
the step 2 is specifically implemented according to the following steps:
step 2.1, heating the vacuum heat treatment furnace to 845 ℃ from room temperature at a speed of 9 ℃/min, then placing the titanium alloy sample in the step 1 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 845 ℃ again at a speed of 9 ℃/min, and then preserving heat for 4 hours;
step 2.2, furnace-cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the first heavy furnace cold annealing heat treatment;
step 3: placing the sample treated in the step 2 into a vacuum heat treatment furnace for second furnace cold annealing heat treatment;
step 3.1, heating the vacuum heat treatment furnace to 560 ℃ from room temperature at a speed of 9 ℃/min, then placing the titanium alloy sample in the step 2 into the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 560 ℃ again at a speed of 9 ℃/min, and then preserving heat for 7.5 hours;
and 3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment.
FIG. 1 is a graph of fracture toughness and fracture morphology of a joint after double furnace cold annealing in an annealing method for improving fracture toughness of a TC11/TC17 titanium alloy linear friction welding joint according to the invention obtained in example 5. The fracture also consists of three parts, as shown in fig. 1 (a) (b). Compared with the original joint fracture morphology, the crack extension area is coarser, and the shearing lip area width is increased. In the crack initiation region, the fatigue strip spacing gradually increases along the crack propagation direction, and a plurality of tearing edges are present, as shown in fig. 1 (c); the large amount of toughness is distinguished in the crack extension region and the shear lip region as shown in fig. 1 (d) - (e), so that the joint after heat treatment is a typical ductile fracture mode, with a sharp increase in fracture toughness.
FIG. 2 is a drawing showing the microstructure of a welded joint as-welded, in an annealing method for improving fracture toughness of a TC11/TC17 titanium alloy linear friction weld joint according to the present invention, obtained in example 5, and it can be seen from FIG. 2 that the weld joint TC11 side weld zone after welding consists of a large amount of needle-like martensite alpha 'phase and a small amount of retained beta phase, and the TC17 side weld zone consists of coarse beta grains, a small amount of primary alpha phase at grain boundaries, and an intra-granular dispersed martensite alpha' phase.
FIG. 3 is a graph showing the microstructure of the joint after double furnace cold annealing in an annealing method for improving the fracture toughness of a TC11/TC17 titanium alloy linear friction welding joint according to the invention, which is obtained in example 5, and it can be seen from FIG. 3 that the microstructure difference between the TC11 side weld zone and the TC17 side weld zone is obviously reduced after double furnace cold annealing. The TC11 side weld zone consists of supersaturated solid solution alpha ' phase and beta phase, coarse beta grains of the TC17 side weld zone disappear, and the martensite alpha ' phase is converted into lamellar alpha+alpha ' phase and is uniformly distributed on the beta substrate.
FIG. 4 is a schematic view showing the evolution of joint structure through a double furnace cold annealing process in an annealing method for improving the fracture toughness of a TC11/TC17 titanium alloy linear friction welding joint according to the invention obtained in example 5. As is clear from FIG. 4, the acicular martensite alpha 'phase of the TC11 side weld zone slightly grows up after the double annealing treatment, coarse grains of the TC17 side weld zone are broken, the intragranular spherical dispersed alpha' phase is partially transformed into acicular form, and lamellar alpha phases are filled in the grain boundary. The whole weld zone consists of needle-like and lamellar basket tissue.
FIG. 5 is a graph of the fracture toughness profile of an original joint in an annealing process for improving the fracture toughness of a TC11/TC17 titanium alloy linear friction weld joint according to the present invention, as obtained in example 5. As can be seen from fig. 5 (a) (b), the fracture consists of a cracking zone, an expansion zone and a shearing lip zone, the cracking zone is extremely uneven in width, the crack expansion zone is relatively smooth, and the shearing lip zone is very narrow. A large number of tearing edges and small dimples are present in the initiation region as shown in fig. 5 (c); in the crack extension region, obvious river patterns and along-grain fracture morphology can be observed, as shown in fig. 5 (d); with smooth planar surfaces and deformed dimples distributed in the shear lip region as shown in fig. 5 (e). The entire joint thus belongs to a typical quasi-cleavage fracture mode, exhibiting brittle fracture characteristics.
The TC11 and TC17 titanium alloy linear friction welding head obtained by the steps has the TC11 parent metal fracture toughness of more than or equal to 70 MPa.m at room temperature 1/2 TC17 parent metal fracture toughness is more than or equal to 80 MPa.m 1/2 The fracture toughness of the welded joint is more than or equal to 65 MPa.m 1/2 . While the fracture toughness of the TC11 and TC17 parent metals in the prior art basically remains unchanged, the fracture toughness of the welding joint without heat treatment is 28.4+/-0.1 MPa m 1/2 Thus, the microstructure of the joint treated by the method is effectively improved, and the fracture toughness is obviously improved.
Claims (1)
- The optimizing method of the fracture toughness of the linear friction welding joint of the titanium alloy dissimilar to TC11 and TC17 is characterized by comprising the following steps:step 1, performing linear friction welding on TC11 and TC17 titanium alloy 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 perform first heavy furnace cold annealing heat treatment;the step 2 is specifically implemented according to the following steps:step 2.1, heating the vacuum heat treatment furnace to 800-900 ℃ from room temperature, 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 heat;step 2.2, furnace-cooling the sample subjected to heat preservation in the step 2.1 to room temperature in a vacuum heat treatment furnace, and completing first heavy furnace cold annealing heat treatment;the heat preservation time in the step 2.1 is 3-6 hours, and the temperature rising rate of the vacuum heat treatment furnace is 1-15 ℃/min;step 3, placing the sample treated in the step 2 in a vacuum heat treatment furnace for second furnace cold annealing heat treatment;the step 3 is specifically implemented according to the following steps:step 3.1, heating the vacuum heat treatment furnace to 500-600 ℃ from room temperature, then placing the sample treated in the step 2 in the vacuum heat treatment furnace, heating the vacuum heat treatment furnace to 500-600 ℃ again, and then preserving heat;3.2, furnace cooling the heat-preserved sample to room temperature in a vacuum heat treatment furnace to finish the second furnace cold annealing heat treatment;the heat preservation time in the step 3.1 is 6-10 hours, and the temperature rising rate of the vacuum heat treatment furnace is 1-15 ℃/min;the TC11 and TC17 titanium alloy linear friction welding head obtained by the steps has the TC11 parent metal fracture toughness of more than or equal to 70 MPa.m at room temperature 1/2 TC17 parent metal fracture toughness is more than or equal to 80 MPa.m 1/2 The fracture toughness of the welded joint is more than or equal to 65 MPa.m 1/2 。
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| WO2007082708A1 (en) * | 2006-01-17 | 2007-07-26 | Daimler Ag | Semifinished part composed of an alpha/alpha2-titanium alloy and process for producing it |
| 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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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007082708A1 (en) * | 2006-01-17 | 2007-07-26 | Daimler Ag | Semifinished part composed of an alpha/alpha2-titanium alloy and process for producing it |
| 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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