CN118751717A - Preparation method of fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fastener - Google Patents
Preparation method of fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fastener Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 110
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 238000005242 forging Methods 0.000 claims abstract description 182
- 230000009466 transformation Effects 0.000 claims abstract description 44
- 238000000034 method Methods 0.000 claims abstract description 40
- 238000005098 hot rolling Methods 0.000 claims abstract description 28
- 238000005097 cold rolling Methods 0.000 claims abstract description 20
- 230000007704 transition Effects 0.000 claims abstract description 8
- 238000010304 firing Methods 0.000 claims description 27
- 238000001816 cooling Methods 0.000 claims description 20
- 238000003723 Smelting Methods 0.000 claims description 19
- 239000000243 solution Substances 0.000 claims description 18
- 238000010438 heat treatment Methods 0.000 claims description 15
- 239000000463 material Substances 0.000 claims description 12
- 238000004519 manufacturing process Methods 0.000 claims description 11
- 238000005498 polishing Methods 0.000 claims description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 9
- 238000003466 welding Methods 0.000 claims description 8
- 238000004321 preservation Methods 0.000 claims description 7
- 238000005096 rolling process Methods 0.000 claims description 7
- 239000011265 semifinished product Substances 0.000 claims description 6
- 239000006104 solid solution Substances 0.000 claims description 6
- 239000002994 raw material Substances 0.000 claims description 4
- 239000011148 porous material Substances 0.000 claims description 3
- 238000003825 pressing Methods 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 abstract description 25
- 239000000956 alloy Substances 0.000 abstract description 25
- 239000013078 crystal Substances 0.000 abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 238000007796 conventional method Methods 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- 229910052759 nickel Inorganic materials 0.000 description 5
- 230000032683 aging Effects 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 238000000879 optical micrograph Methods 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 229910001040 Beta-titanium Inorganic materials 0.000 description 2
- 241001391944 Commicarpus scandens Species 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010891 electric arc Methods 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 235000010627 Phaseolus vulgaris Nutrition 0.000 description 1
- 244000046052 Phaseolus vulgaris Species 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000007709 nanocrystallization Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 230000008093 supporting effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
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Abstract
A preparation method of a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for a fastener utilizes a hot working method below a transformation point of free forging in a temperature zone below transformation, radial forging in a temperature zone below transformation and hot rolling in a temperature zone below transformation to induce a plurality of Beta grains in Ti-5553 titanium alloy to dynamically recrystallize in the process of processing a Ti-5553 titanium alloy cast ingot into a bar, and initially refines the Beta grains in the alloy bar. After the phase transition is performed, the Beta crystal grain is enabled to reach 5-100 mu m. The Beta crystal grains in the wire are completely refined by utilizing a method of large plastic deformation cold rolling and two-phase area solution treatment. In the cold rolling process, dislocation with high density formed in coarse Beta grains is formed; the dislocations are transformed into new grain boundaries during the solution treatment. After cold rolling-solution treatment, beta grains in the wire are 5-15 mu m. The invention can obtain excellent matching of strength and plasticity, the average tensile strength of the aged state wire reaches 1482MPa, the average yield strength reaches 1393MPa, the average elongation after fracture reaches 10.3%, and the average area shrinkage reaches 37%.
Description
Technical Field
The invention relates to the technical field of titanium alloy processing, in particular to an engineering preparation method of a Ti-5Al-5V-5Mo-3Cr titanium alloy wire for a fine-grain fastener with Beta grain size in the range of 5-15 mu m.
Technical Field
The Ti-5Al-5V-5Mo-3Cr (Ti-5553) titanium alloy is a novel aviation high-strength titanium alloy. When Beta grains of the Ti-5553 titanium alloy are thinned to be less than 20 mu m, the tensile strength of the alloy after aging heat treatment can reach 1525MPa, the elongation after fracture can reach 9.5%, and the alloy has excellent strength and plasticity matching. At present, 1500 MPa-grade aviation fasteners in service in China are all manufactured by iron-based/nickel-based alloys such as PH13-8Mo iron-based alloy, GH4169 nickel-based alloy and the like. The tensile strength of the iron-based/nickel-based alloy is in the range of 1515MPa to 1650MPa, and the density is in the range of 7.9X10 3kg/m3～8.2×103kg/m3. Although the tensile strength of the fine-grain high-strength Ti-5553 titanium alloy is lower than the upper limit of the tensile strength of the above-mentioned iron-based/nickel-based alloy, the density of the Ti-5553 titanium alloy is only 4.6X10 3kg/m3, and the specific strength of the alloy is 65% higher than that of the iron-based/nickel-based alloy. Therefore, ti-5553 titanium alloy is an ideal material for manufacturing 1500MPa grade lightweight fasteners for aviation. In view of the fact that refined Beta grains are preconditions for ensuring strong plastic matching of the 1500 MPa-level Ti-5553 titanium alloy, the engineering preparation method for establishing the fine-grain Ti-5553 titanium alloy wire has an important supporting effect on manufacturing the 1500 MPa-level Ti-5553 titanium alloy fastener.
A hot working method for improving the structural performance of Ti-5553 titanium alloy is disclosed in the invention with publication number CN 102517530. The method is optimized for the tissue performance of the Ti-5553 titanium alloy forged part, but is not suitable for preparing the fine-grain Ti-5553 titanium alloy wire.
The invention creation of the application number 201810431403.X discloses a preparation method of a high-strength titanium alloy wire. The method adopts a technical route that the temperatures above and below the transformation point are alternately used in the ingot cogging and hot rolling processes to break Beta grains of the alloy. Because the Beta grains of the Ti-5553 titanium alloy are easy to grow rapidly in a temperature region above the phase transition point, the Beta grains in the Ti-5553 titanium alloy wire cannot be thinned to below 20 mu m by a hot working method of alternately using the temperatures above and below the phase transition point. Therefore, this method is not suitable for preparing fine-grain Ti-5553 titanium alloy wire.
The invention creation of the publication No. CN 108580577A discloses a preparation method of a high-strength Beta titanium alloy wire for a spring. The method adopts a technical route of hot drawing in a temperature region of 650-750 ℃ to break Beta grains in the alloy. However, the deformation resistance of Ti-5553 titanium alloy in the temperature zone is too large, the alloy is easy to break in the hot drawing process, and the forming processing of the wire cannot be realized.
The invention creation of publication No. CN 101343706A discloses a preparation method of Beta titanium alloy for a fastener, which adopts hot rolling at 900-1000 ℃ to break Beta grains of the alloy. However, in this temperature range, which is above the transformation point of Ti-5553 titanium alloy, beta grains cannot be broken to 100 μm or less.
The invention with the publication number of CN 122251639A provides a high-strength titanium alloy bar and wire and a preparation method thereof, wherein the method provides a method of forging, hot rolling and hot drawing, which can realize the nanocrystallization of Alpha grains in Ti- (5.5-6.5) Al- (3.5-4.5) V- (4-6) Cu (mass fraction, the same as the following) martensitic titanium alloy, wherein the forging temperature zone is a temperature zone above 1000 ℃, the hot rolling temperature zone is (750-850 ℃), and the hot drawing temperature zone is (600-700 ℃). Firstly, the temperature area above 1000 ℃ is 155 ℃ above than the transformation point (845 ℃) of the Ti-5553 titanium alloy, the size of Beta grains in the alloy after forging in the temperature area is more than 200 mu m, and the Beta grains in the alloy are not easy to be fully refined by subsequent hot rolling and hot drawing. Secondly, the purpose of hot rolling in a (750-850 ℃) temperature zone is to break martensite laths in Ti- (5.5-6.5) Al- (3.5-4.5) V- (4-6) Cu alloy, while martensite laths are not present in Ti-5553 titanium alloy; in addition, the upper limit temperature of the temperature zone is 850 ℃ higher than the phase transition point of the Ti-5553 titanium alloy, and the Beta grains of the Ti-5553 titanium alloy cannot be effectively crushed to be less than 100 mu m by hot rolling at the temperature. Thirdly, the deformation resistance of the Ti-5553 titanium alloy in the temperature range of (600-700 ℃) is overlarge, the alloy is easy to break in the hot drawing process, and the continuous industrial production of wires is not facilitated. Therefore, this method is not suitable for preparing fine-grain Ti-5553 titanium alloy wire.
The invention creation of the publication No. CN 112981174A provides a preparation method of a high-strength plastic titanium alloy wire, wherein the method is used for preparing the high-strength plastic Ti- (3.5-5.0) Al- (2.5-4.0) V- (4.0-6.0) Mo- (4.5-6.0) Cr- (0.6-1.5) Fe alloy wire by a method of forging, hot rolling and hot drawing at a temperature zone above the transformation point of the alloy (80-150 ℃), and the hot drawing at a temperature zone of 760-820 ℃). In the method, the forging temperature zone and the hot rolling temperature zone are both in a single-phase zone, and if the method is used for preparing the Ti-5553 titanium alloy wire, beta grains are extremely coarse after the wire is hot rolled. Because of the non-uniformity of strain of the Ti-5553 titanium alloy in the deformation process of the temperature zone below the phase transition point, beta grains in the Ti-5553 titanium alloy wire cannot be fully refined only by means of hot drawing processing of the temperature zone (760-820 ℃).
In summary, although the prior art reports processing and preparing methods of titanium alloy wires for fasteners, the processing techniques and thermal processing parameters involved in these methods are not fully suitable for engineering and preparing fine-grain Ti-5553 titanium alloy wires for fasteners. The main appearance is that: 1. the forging temperature zone is too high, and Beta grains in the wire are not thinned by forging in a temperature zone below the transformation point; 2. the hot rolling temperature is too high, and Beta grains in the hot rolled refined wire material in a temperature zone below the non-transformation point are not adopted; 3. the cold working technology of the wire is not developed, and the effect of cold working on thinning the Beta grains of the wire is ignored.
Disclosure of Invention
In order to fill the blank in the aspect of the processing method of the fine-grain Ti-5553 titanium alloy wire, the invention provides a preparation method of the fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for a fastener.
The specific process of the invention is as follows:
Step 1, preparing a finished cast ingot:
three-time cast ingots with the components of Ti-5.07Al-5.11V-5.17Mo-2.97Cr-0.0094O are obtained through three-time smelting; and (3) processing the three cast ingots to obtain finished cast ingots.
The process for preparing the finished cast ingot comprises the following steps:
pressing the raw materials of the Ti-5553 titanium alloy cast ingot into a plurality of electrode blocks; and welding the plurality of electrode blocks into three consumable electrode rods. Respectively smelting the three consumable electrode rods into cast ingots; three primary ingots were obtained.
And welding the obtained three primary cast ingots into a consumable electrode rod. And carrying out secondary smelting on the consumable electrode rod to obtain a secondary cast ingot.
And taking the obtained secondary cast ingot as a consumable electrode rod. And smelting the consumable electrode rod subjected to secondary smelting for the third time to obtain a tertiary cast ingot.
Step 2, free forging:
Heating the obtained finished ingot, and performing multi-firing forging with 9-12 forging fires by taking the transformation point of the finished ingot as a limit. Wherein: forging heat above the transformation point of the ingot is 5-7 heat, and forging temperature is 850+/-10-1200+/-10 ℃; the upsetting deformation is 60 percent, and the times of upsetting and drawing are 3 times. Forging heat below the transformation point of the ingot is 4 or 5 heat, and forging temperature is 750+/-10 ℃ to 840+/-10 ℃; the upsetting deformation is 50%, and the times of upsetting and drawing are 2.
Through free forging, a forging stock with the specification of 160mm×160mm×l is obtained.
And (3) during multi-firing forging above the transformation point of the ingot, heating the box-type resistance furnace to a preset forging temperature of 850+/-10 ℃ to 1200+/-10 ℃, and then loading the Ti-5553 titanium alloy forging stock, and preserving heat for 2 hours. Forging the Ti-5553 titanium alloy forging stock. 3 times of upsetting-drawing are carried out in each forging process, and the deformation amount of each upsetting is 60%. And (5) water cooling after forging.
And after each firing, respectively obtaining a Ti-5553 titanium alloy forging stock subjected to the firing forging, and polishing microcracks on the surface of the Ti-5553 titanium alloy forging stock subjected to the firing forging. And forging the ingot at a plurality of times above the transformation point of the ingot.
And (3) during multi-firing forging below the transformation point of the ingot, heating the box-type resistance furnace to a preset forging temperature of 750+/-10 ℃ to 840+/-10 ℃, and then loading the Ti-5553 titanium alloy forging stock which is forged above the transformation point, and preserving heat for 2 hours.
And forging the Ti-5553 titanium alloy forging stock which is forged above the transformation point. 2 times of upsetting-drawing are carried out in each forging process, and the deformation amount of each upsetting is 50%. And (5) water cooling after forging.
And after each firing, respectively obtaining a Ti-5553 titanium alloy forging stock subjected to the firing forging, and polishing microcracks on the surface of the Ti-5553 titanium alloy forging stock subjected to the firing forging. And forging the ingot under the transformation point of the ingot by multiple fires.
Step3, drawing and forging:
the obtained forging stock was subjected to drawing forging in a warm region of 2 to 4 times or less of the transformation point by a rapid forging machine, and 160mm×160mm×l forging stock was drawn to obtain a forging stock having a diameter of 80mm×l.
When the forging is performed by drawing each time, the obtained forging stock is heated to 750+/-10 ℃ to 840+/-10 ℃ which is required, and the temperature is kept for 2 hours. And (5) water cooling after each forging time is finished. Obtaining forging stock with phi 80mm after drawing forging.
Step 4, radial forging:
heating the temperature of the box-type resistance furnace to 750+/-10 ℃ to 840+/-10 ℃ required by radial forging; and (5) loading the forged blank subjected to the drawing forging, and carrying out radial forging after the heat preservation time is 1 h. And (5) air cooling. Obtaining the radial forging bar blank.
The resulting diameter forged bar is sawed into sections.
Step 5, hot rolling:
Placing the obtained radial forging bar blank into a box-type resistance furnace with the temperature of 720+/-10 ℃ to 835+/-10 ℃ for heat preservation for 1h; carrying out hot rolling for 1 fire time and multiple times by a rolling mill; obtaining the hot rolled bar. And (5) cooling. The resulting hot rolled bar is sawed into sections as desired.
The hot rolling speed is 1 m/s to 3m/s, and the deformation of each pass is less than 50%.
Step 6, preparing a cold-rolled wire blank:
I thermal straightening
And (3) placing the hot rolled bar which is sawed into sections into a box-type resistance furnace at 820+/-10 ℃ for 1h. And (5) thermally straightening the hot rolled bar by a straightener. And (5) air cooling.
II, removing oxide scale of the thermally straightened bar.
And removing the oxide skin of the bar by using a centerless lathe.
III, polishing the outer surface of the bar by using a centerless grinder to ensure that the roughness Ra of the outer surface of the bar is less than 1.6, and obtaining the cold-rolled wire blank with phi 15mm multiplied by 2500 mm.
Step 7, cold rolling:
The obtained cold-rolled wire stock is continuously cold-rolled into a wire material in multiple passes by a tandem mill.
The cold rolling speed is less than 1m/s, and the deformation of each pass is less than 30%.
The obtained Ti-5553 titanium alloy wire with the diameter of 5.5mm to 8.5mm in a cold rolled state.
Sawing the cold rolled Ti-5553 titanium alloy wire to obtain a wire semi-finished product.
When the wire is cold-rolled, the wire blank sequentially enters holes of each roller in a tandem rolling mill to be subjected to multi-pass continuous cold rolling, and the cold-rolled Ti-5553 titanium alloy wire is obtained. The holes of the rolls have different pore diameters.
Step 8, solution treatment and thermal straightening:
Heating the temperature of the box-type resistance furnace to a target solution treatment temperature; and filling the obtained titanium alloy wire semi-finished product into the box-type resistance furnace for solution treatment. And taking out the titanium alloy wire subjected to solution treatment from the resistance furnace and carrying out thermal straightening. And (5) air cooling. Obtaining the titanium alloy wire with the diameter of phi 5.5mm to phi 8.5 mm.
The solution treatment temperature is 820 ℃ +/-10 ℃. The solid solution time is 30min
Compared with the prior art, the invention has the following beneficial effects:
1. The technical route of hot working and cold working in a temperature zone below the phase transition point can be used for engineering preparation of the fine-grain Ti-5553 titanium alloy wire, and the size of Beta grains in the wire is within the range of 5-15 mu m. Firstly, the invention utilizes the hot working method below the transformation point of free forging in the temperature zone below the transformation, radial forging in the temperature zone below the transformation and hot rolling in the temperature zone below the transformation, not only processes the Ti-5553 titanium alloy cast ingot into a bar material and realizes the primary forming of the wire material, but also can induce a plurality of Beta crystal grains in the Ti-5553 titanium alloy to dynamically recrystallize and primarily refine the Beta crystal grains in the alloy bar material. After the thermal processing under the phase transition, the size of Beta grains in the bar is in the range of 5-100 mu m. Secondly, the method of 'large plastic deformation cold rolling plus two-phase area solid solution treatment' is utilized to eliminate residual coarse Beta grains in the bar material, and complete refinement of Beta grains in the wire material is realized. In the cold rolling process, coarse Beta grains can form high-density dislocation inside; the high density dislocations are transformed into new grain boundaries during the solution treatment. After cold rolling-solution treatment, the Beta crystal grain size in the wire is in the range of 5-15 mu m.
2. After aging heat treatment, the fine-grain Ti-5553 titanium alloy wire prepared by the invention can obtain excellent strength and plasticity matching. To verify the effect of the present invention, the mechanical properties of the phi 8mm wire after aging treatment were measured by the detection method prescribed in GB/T228.1-2021 by the company Siam Han Tang analysis detection Co., ltd, and the results are shown in Table 1. The average tensile strength of the aged phi 8mm wire can reach 1482MPa, the average yield strength can reach 1393MPa, the average elongation after fracture can reach 10.3%, and the average reduction of area can reach 37%.
TABLE 1 results of room temperature tensile testing of aging-state fine-grain Ti-5553 titanium alloy straight wires
Drawings
FIG. 1 is an optical micrograph of a solid solution Ti-5553 titanium alloy wire of Φ2.0mm.
FIG. 2 is an optical micrograph of a Phi 5.5mm solid solution Ti-5553 titanium alloy wire.
FIG. 3 is an optical micrograph of a Phi 8.5mm solid solution Ti-5553 titanium alloy wire.
Fig. 4 is a flow chart of the present invention.
Detailed Description
The invention relates to a method for preparing a phi 8.5mm fine-grain Ti-5553 titanium alloy wire, and the technical scheme thereof will be described in detail through four examples.
The specific process of the invention is as follows:
step 1, smelting a Ti-5553 titanium alloy cast ingot:
The raw materials for smelting the Ti-5553 titanium alloy cast ingot comprise 0-grade sponge titanium, al 40Mo60 intermediate alloy, al 15V85 intermediate alloy, al beans with the purity of 99.99 percent and Cr particles with the purity of 99.99 percent.
In the Al 40Mo60 intermediate alloy, the mass percentage of Mo is 60 percent, and the mass percentage of Al is 40 percent; the mass percentage of V in the Al 15V85 intermediate alloy is 85%, and the mass percentage of Al is 15%.
During smelting, a 2000 ton hydraulic press is used for pressing raw materials into electrode blocks; the electrode blocks were 50mm x 300mm in size and 21 pieces in number.
And sequentially welding every 7 electrode blocks along the length direction by utilizing a vacuum plasma welding box to form 1 consumable electrode rod, and welding three consumable electrode rods in total.
Respectively smelting the three consumable electrode rods into cast ingots by using a vacuum consumable electric arc furnace; three primary ingots with a diameter of 90mm were obtained. The vacuum degree of vacuum melting is less than or equal to 5 multiplied by 10 -1 Pa.
And welding the obtained three primary cast ingots into a consumable electrode rod. Carrying out secondary smelting on the consumable electrode rod by using a vacuum consumable arc furnace to obtain a secondary cast ingot with the diameter of 120 mm; the vacuum degree of the secondary smelting is less than or equal to 5 multiplied by 10 -2 Pa.
And taking the obtained secondary cast ingot as a consumable electrode rod. And (3) carrying out tertiary smelting on the consumable electrode rod subjected to secondary smelting by using a vacuum consumable electric arc furnace to obtain a tertiary cast ingot with the diameter of 160 mm. The vacuum degree of smelting is less than or equal to 5 multiplied by 10 -2 Pa.
The composition of the obtained tertiary cast ingot is Ti-5.07Al-5.11V-5.17Mo-2.97Cr-0.0094O. And (3) peeling the ingot, cutting a riser and cutting the ingot bottom to obtain a finished ingot.
The size of the finished cast ingot is phi 158mm multiplied by 380mm.
Step 2, free forging:
the ingot is heated by a Nabertherm LH 216/14 box-type resistance furnace, and multi-firing forging with 9-12 forging fires is implemented by taking the transformation point of the ingot as a limit. Wherein:
Forging heat above the transformation point of the ingot is 5-7 heat, and forging temperature is 850+/-10-1200+/-10 ℃; the upsetting deformation is 60 percent, and the times of upsetting and drawing are 3 times.
Forging heat below the transformation point of the ingot is 4 or 5 heat, and forging temperature is 750+/-10 ℃ to 840+/-10 ℃; the upsetting deformation is 50%, and the times of upsetting and drawing are 2.
And during multi-firing forging above the transformation point of the ingot, heating the box-type resistance furnace to a preset forging temperature of 850 ℃ +/-10 ℃ -1200 ℃ +/-10, and then loading the Ti-5553 titanium alloy forging stock, and preserving heat for 2 hours. Before forging, the time for transferring the Ti-5553 titanium alloy forging stock from the box-type resistance furnace to the rapid forging machine is less than 1min.
The Ti-5553 titanium alloy forging stock is forged by a 2000 ton quick forging machine. In each forging process, upsetting-drawing is carried out for 3 times according to a conventional method, and the deformation amount of upsetting is 60% each time. And (5) water cooling after forging.
And after each firing, respectively obtaining a Ti-5553 titanium alloy forging stock subjected to the firing forging, and polishing microcracks on the surface of the Ti-5553 titanium alloy forging stock subjected to the firing forging. And forging the ingot over the transformation point for multiple times until the ingot is completed, and obtaining a forging stock with the specification of 160mm multiplied by L.
TABLE 1 forging parameters for free forging above the transformation point of Ti-5553 titanium alloys
And in the multi-firing forging process below the transformation point of the ingot, heating the box-type resistance furnace to a preset forging temperature of 750+/-10 ℃ to 840+/-10 ℃, and then loading the Ti-5553 titanium alloy forging stock which is forged above the transformation point, and preserving heat for 2 hours. Before forging, the time for transferring the Ti-5553 titanium alloy forging stock from the box-type resistance furnace to the rapid forging machine is less than 1min.
The Ti-5553 titanium alloy forging stock is forged by a 2000 ton quick forging machine. In each forging process, upsetting-drawing is carried out for 2 times according to a conventional method, and the deformation amount of upsetting is 50% each time. And (5) water cooling after forging.
And after each firing, respectively obtaining a Ti-5553 titanium alloy forging stock subjected to the firing forging, and polishing microcracks on the surface of the Ti-5553 titanium alloy forging stock subjected to the firing forging. And forging the ingot under the transformation point of the ingot for multiple times until the ingot is completed, and obtaining a forging stock with the specification of 160mm multiplied by L.
TABLE 2 forging parameters for free forging below the transformation point of Ti-5553 titanium alloys
Step3, drawing and forging:
And (3) performing drawing forging in a temperature zone below a 2-4-heat transformation point by using a 2000-ton quick forging machine, and drawing and forging 160mm multiplied by L forging blanks into round rod-shaped blanks with phi 80mm multiplied by L.
The drawing forging temperature is 750 ℃ +/-10 ℃ to 840 ℃ +/-10 ℃. Heating to the temperature of drawing forging by a box-type resistance furnace; the heat preservation time of each firing time is 2 hours. After each forging, the forging stock is cooled by water. Obtaining forging stock with phi 80mm after drawing forging.
Before drawing forging, the time for transferring the forging stock from the box-type resistance furnace to the radial forging machine is less than 1min.
Table 3 process parameters of the examples in step3
Step 4, radial forging:
The temperature zone of the radial forging is 750+/-10 ℃ to 840+/-10 ℃. After the temperature of the box-type resistance furnace reaches the radial forging temperature, loading the forging stock subjected to drawing forging, and carrying out radial forging after the heat preservation time is 1 h. Obtaining the radial forging bar. The forging stock is forged into bars with the diameter of 50mm by a radial forging machine. And (5) air cooling.
Before radial forging, the time for transferring the forging stock from the box-type resistance furnace to the radial forging machine is less than 1min.
TABLE 4 radial forging temperature parameters
The resulting radial forged bar was sawed into hot rolled bar slabs having a diameter of 50mm X800 mm.
Step 5, hot rolling:
And hot-rolling the hot-rolled bar blank into a bar by using a cross rolling mill for 1 fire time and multiple passes. The hot rolling temperature interval is 720+/-10 ℃ to 835+/-10 ℃. After the temperature of the box-type resistance furnace is heated to the set hot rolling temperature, hot rolled rod blanks with the diameter of 50mm multiplied by 800mm are filled in and kept for 1h. And after the heat preservation is finished, loading the heated hot-rolled bar billet into a rolling mill from a box-type resistance furnace. Starting the hot rolling mill, and carrying out multi-pass hot rolling on the hot rolled bar blank. The hot rolling speed ranges from 1 m/s to 3m/s, and the deformation of each pass is less than 50%. And (5) cooling. Obtaining the hot rolled bar with the diameter meeting the requirement.
The resulting hot rolled bar is sawed into sections as desired.
TABLE 5 technical parameters of hot Rolling
Step 6, preparing a cold-rolled wire blank:
I thermal straightening
The thermal straightening temperature is 820+/-10 ℃. And when the temperature of the box-type resistance furnace reaches the target thermal straightening temperature, loading the hot rolled bar with the diameter of 15.5mm multiplied by 2500mm, wherein the heat preservation time is 1h. And thermally straightening the hot rolled bar by using a straightening machine. And after the thermal straightening is finished, air cooling is carried out, and the bar for cold rolling is obtained.
II, removing oxide scale of the thermally straightened bar.
And removing the oxide skin of the bar by using a centerless lathe according to a conventional method.
And III, polishing the outer surface of the bar by using a centerless grinder, and ensuring that the roughness Ra of the outer surface of the bar is less than 1.6 to obtain a cold-rolled wire blank with phi 15mm multiplied by 2500 mm.
Step 6, cold rolling:
And continuously cold-rolling the obtained cold-rolled wire blank for multiple times to obtain the wire material.
The continuous cold rolling is carried out by adopting a conventional method, and continuously and multiply hot-rolling the obtained wire blank into a wire material by utilizing a tandem mill.
In the cold rolling process, the cold-rolled wire blank sequentially enters holes of each roller in a tandem rolling mill to be subjected to multi-pass continuous cold rolling, and the titanium alloy wire of the cold-rolled Ti-5553 is obtained. And after the cold rolling is finished, sawing the titanium alloy wire of the cold rolled Ti-5553 according to the required length to obtain a wire semi-finished product.
The holes of the rolls have different pore diameters.
The cold rolling speed is less than 1m/s, and the deformation of each pass is less than 30%.
The surface of the obtained titanium alloy wire material of the cold-rolled Ti-5553 has no microcrack.
Table 6 technical parameters of step 6 of each example
Step 7, solution treatment and thermal straightening
The solution treatment temperature is 820 ℃ +/-10 ℃. And after the temperature of the box-type resistance furnace reaches the target solution treatment temperature, loading the obtained titanium alloy wire semi-finished product into the box-type resistance furnace, and carrying out solution treatment according to a conventional method for 30min.
And after the solution treatment is finished, taking the titanium alloy wire subjected to the solution treatment out of the resistance furnace, and carrying out thermal straightening by a straightening machine. And (5) air cooling. Obtaining Ti-5553 titanium alloy wire.
Claims (9)
1. A preparation method of a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for a fastener is characterized by comprising the following specific steps of:
Step 1, preparing a finished cast ingot:
three-time cast ingots with the components of Ti-5.07Al-5.11V-5.17Mo-2.97Cr-0.0094O are obtained through three-time smelting; processing the three cast ingots to obtain finished cast ingots;
step 2, free forging:
Heating the obtained finished cast ingot, and carrying out multi-firing forging of 9-12 forging fires by taking the phase transition point of the finished cast ingot as a limit; wherein: forging heat above the transformation point of the ingot is 5-7 heat, and forging temperature is 850+/-10-1200+/-10 ℃; the upsetting deformation is 60 percent, and the times of upsetting and drawing are 3 times; forging heat below the transformation point of the ingot is 4 or 5 heat, and forging temperature is 750+/-10 ℃ to 840+/-10 ℃; the upsetting deformation is 50%, and the times of upsetting and drawing are 2 times;
Free forging is carried out to obtain a forging stock;
step3, drawing and forging:
Drawing forging is carried out on the obtained forging stock by utilizing a rapid forging machine in a temperature zone below a heat transformation point of 2-4 times;
step 4, radial forging:
heating the temperature of the box-type resistance furnace to 750+/-10 ℃ to 840+/-10 ℃ required by radial forging; filling forging stock subjected to drawing forging, and preserving heat for 1h; air cooling to obtain a radial forging bar blank;
sawing the obtained radial forging bar into sections;
Step 5, hot rolling:
Placing the obtained radial forging bar into a box-type resistance furnace with the temperature of 720+/-10 ℃ to 835+/-10 ℃ for heat preservation for 1h; carrying out hot rolling for 1 fire time and multiple times by a rolling mill; obtaining a hot rolled bar; cooling; sawing the obtained hot rolled bar into sections according to requirements;
The hot rolling speed is 1 m/s to 3m/s, and the deformation of each pass is less than 50%;
Step 6, preparing a cold-rolled wire blank:
I thermal straightening
Placing the hot rolled bar which is sawed into sections into a box-type resistance furnace at 820+/-10 ℃ for 1h; thermally straightening the hot rolled bar by a straightener; air cooling;
II, removing oxide skin of the hot straightening bar;
Removing oxide skin of the bar by using a centerless lathe;
III, polishing the outer surface of the bar by using a centerless grinder to ensure that the roughness Ra of the outer surface of the bar is less than 1.6, thereby obtaining a cold-rolled wire blank;
Step 7, cold rolling:
continuously cold-rolling the obtained cold-rolled wire blank into a wire material in multiple passes through a tandem rolling mill;
The cold rolling speed is less than 1m/s, and the deformation of each pass is less than 30%;
The obtained cold-rolled Ti-5553 titanium alloy wire with the diameter of 5.5mm to 8.5 mm;
Sawing the titanium alloy wire of the Ti-5553 in a cold rolled state to obtain a wire semi-finished product;
Step 8, solution treatment and thermal straightening:
Heating the temperature of the box-type resistance furnace to a target solution treatment temperature; putting the obtained titanium alloy wire semi-finished product into the box-type resistance furnace for solution treatment; taking out the titanium alloy wire subjected to solution treatment from the resistance furnace and carrying out thermal straightening; air cooling; obtaining the titanium alloy wire with the diameter of phi 5.5mm to phi 8.5 mm.
2. The method for preparing the fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for the fastener according to claim 1, wherein the process for preparing the finished cast ingot is as follows:
Pressing the raw materials of the Ti-5553 titanium alloy cast ingot into a plurality of electrode blocks; welding the plurality of electrode blocks into three consumable electrode rods; respectively smelting the three consumable electrode rods into cast ingots; three primary ingots are obtained; welding the obtained three primary cast ingots into a consumable electrode rod; carrying out secondary smelting on the consumable electrode rod to obtain a secondary cast ingot;
taking the obtained secondary cast ingot as a consumable electrode rod; and smelting the consumable electrode rod subjected to secondary smelting for the third time to obtain a tertiary cast ingot.
3. The method for producing a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, wherein in step 2, when forging more than the transformation point of the ingot, heating a box-type resistance furnace to a preset forging temperature of 850+ -10 ℃ to 1200+ -10 ℃, then loading a Ti-5553 titanium alloy forging stock, and preserving heat for 2 hours; forging a Ti-5553 titanium alloy forging stock; 3 times of upsetting-drawing are carried out in each forging process, and the upsetting deformation amount is 60% each time; water cooling after forging;
After each firing, respectively obtaining a Ti-5553 titanium alloy forging stock subjected to the firing forging, and polishing microcracks on the surface of the Ti-5553 titanium alloy forging stock subjected to the firing forging; and forging the ingot at a plurality of times above the transformation point of the ingot.
4. The method for producing a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, wherein in step 2, when forging under the transformation point of the ingot with multiple fires, heating a box-type resistance furnace to a preset forging temperature of 750+ -10 ℃ to 840+ -10 ℃, then loading the titanium alloy wire into a Ti-5553 titanium alloy forging stock forged over the transformation point, and preserving the heat for 2 hours;
forging the Ti-5553 titanium alloy forging stock which is subjected to forging above the transformation point; 2 times of upsetting-drawing are carried out in each forging process, and the deformation of each upsetting is 50%; water cooling after forging;
after each firing, respectively obtaining a Ti-5553 titanium alloy forging stock subjected to the firing forging, and polishing microcracks on the surface of the Ti-5553 titanium alloy forging stock subjected to the firing forging; and forging the ingot under the transformation point of the ingot by multiple fires.
5. The method for producing a fine-grained Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, characterized in that in step 3, when the forging is drawn with each firing, the obtained forging stock is heated to 750±10 ℃ to 840±10 ℃ as required, and is kept warm for 2 hours; water cooling is carried out after each forging time is finished; obtaining forging stock with phi 80mm after drawing forging.
6. The method for producing a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, wherein in step 4, the radial forging temperature zone is 750.+ -. 10 ℃ to 840.+ -. 10 ℃.
7. The method for producing a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, wherein in step 5, the hot rolling temperature zone is 720.+ -. 10 ℃ to 835.+ -. 10 ℃.
8. The method for producing a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, wherein, when cold rolling the wire in step 6, the wire blank is sequentially put into the holes of each roll in a tandem mill to perform multi-pass continuous cold rolling, thereby obtaining a cold rolled Ti-5553 titanium alloy wire; the holes of the rolls have different pore diameters.
9. The method for producing a fine-grain Ti-5Al-5V-5Mo-3Cr titanium alloy wire for fasteners according to claim 1, wherein the solution treatment temperature is 820 ℃ ± 10 ℃; the solid solution time is 30min.
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