CN117983757A - Forging forming method for improving TC16 titanium alloy performance - Google Patents
Forging forming method for improving TC16 titanium alloy performance Download PDFInfo
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- CN117983757A CN117983757A CN202311871561.4A CN202311871561A CN117983757A CN 117983757 A CN117983757 A CN 117983757A CN 202311871561 A CN202311871561 A CN 202311871561A CN 117983757 A CN117983757 A CN 117983757A
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- 238000005242 forging Methods 0.000 title claims abstract description 379
- 238000000034 method Methods 0.000 title claims abstract description 119
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 105
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- 230000009467 reduction Effects 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims description 59
- 238000010304 firing Methods 0.000 claims description 39
- 238000001816 cooling Methods 0.000 claims description 22
- 239000000463 material Substances 0.000 claims description 16
- 238000000137 annealing Methods 0.000 claims description 12
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical group [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 claims description 10
- 229910000831 Steel Inorganic materials 0.000 claims description 8
- 238000007599 discharging Methods 0.000 claims description 8
- 239000000243 solution Substances 0.000 claims description 8
- 239000010959 steel Substances 0.000 claims description 8
- 230000032683 aging Effects 0.000 claims description 6
- 230000009466 transformation Effects 0.000 claims description 6
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- 238000010791 quenching Methods 0.000 claims description 3
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- 101000919504 Gallus gallus Beta-crystallin B1 Proteins 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000010273 cold forging Methods 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 238000010562 histological examination Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
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- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
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Abstract
The invention relates to the technical field of metallurgy, in particular to a forging forming method for improving the performance of TC16 titanium alloy, which comprises a cogging process, a forging process and a forming process, wherein the cogging forging temperature is reduced from 1150-1160 ℃ to 1060-1075 ℃, and the reduction amount of the section diameter is reduced from 190-200 mm/fire to 90-100 mm/fire; the forging temperature is reduced from 1000-1015 ℃ to 950-965 ℃, and the reduction of the section diameter is reduced from 70-80 mm/fire to 50-60 mm/fire; the temperature of forming forging is reduced from beta-30 ℃ to beta-45 ℃, and the reduction amount of the section diameter is reduced from 50-60 mm/fire to 30-35 mm/fire; chamfering is carried out in the forging process of the titanium alloy blank. The method solves the problems that the existing forging mode is easy to cause long forging period, multiple in fire, uneven in deformation and the like.
Description
Technical Field
The invention relates to the technical field of metallurgy, in particular to a forging forming method for improving the performance of TC16 titanium alloy.
Background
TC16 titanium alloy is a titanium alloy material which is designed and developed on the basis of BT16 titanium alloy, has high strength, high plasticity, fatigue resistance and good welding and hardenability, is widely applied to the fields of aviation, aerospace, chemical industry, gold treatment, ships, national defense, medical treatment, oil fields, automobiles and the like, and is one of the most ideal materials for manufacturing fasteners. The TC16 titanium alloy is a martensite type alpha+beta two-phase titanium alloy, the nominal component is Ti-3Al-5Mo-4.5V, and the component contains alpha stable element Al and isomorphous beta stable elements Mo and V; the chemical composition comprises Ti, al, mo, V, fe, si, zr, O, N, H.
The TC16 titanium alloy can be formed by hot forging and cold forging. TC16 titanium alloys are typically strengthened by cold working, which is typically done by on-hammer smelting, forging, upsetting, drawing to form the desired bar. However, the method has the defects of long period, multiple fires, uneven deformation and the like, and the required related performance of the method is difficult to meet the requirements of the required product on the materials of the forgings. In addition, before the cold working of the finished product, the blank is subjected to homogenization forging forming by utilizing forging equipment so as to meet the requirements of the product. In order to perform homogenization molding on the blank, a certain heat treatment mode is generally required to optimize the mechanical property and microstructure of the TC16 titanium alloy bar. The microstructure of the TC16 titanium alloy wire is greatly deformed after heat treatment, and the microstructure of the bar is generally smaller, so that the alloy has very high plasticity and relatively low strength.
At present, the forging forming mode is generally changed to complete the forging production of the titanium alloy with uniformity, and the forging mode is generally changed to complete the uniform refinement of the titanium alloy structure by adopting an upsetting-drawing mode, however, the forging mode is easy to lead to long forging period and multiple firing, for example, the forging is changed to be performed with at least 5 firing times, the problems of uneven deformation and the like are easy to occur, the physicochemical result of the final forging cannot meet the required requirement, and the rejection rate is higher.
Based on the method, the existing forging mode is improved to match the corresponding forging temperature, and the titanium alloy structure can be uniformly thinned under the condition of reducing the forging heat so as to meet the processing requirement.
Disclosure of Invention
The invention aims to solve the problems that the conventional forging mode is easy to cause long forging period, multiple in fire times, uneven in deformation and the like, and provides a forging forming method for improving the performance of TC16 titanium alloy.
In order to achieve the above object, the technical scheme of the present invention is as follows.
A forging forming method for improving the performance of TC16 titanium alloy is characterized by comprising the following steps:
A cogging procedure, in which the titanium alloy blank is cogged and forged by n1 times of fire, and the cogging and forging temperature is reduced from 1150-1160 ℃ to 1060-1075 ℃ and the reduction of the section diameter is reduced from 190-200 mm/time to 90-100 mm/time along with the increase of the cogging and forging time;
a forging-changing procedure, in which the titanium alloy blank is subjected to n 2-time forging-changing forging, and the temperature of the forging-changing forging is reduced from 1000-1015 ℃ to 950-965 ℃ along with the increase of the forging-changing forging firing, and the reduction of the section diameter is reduced from 70-80 mm/firing to 50-60 mm/firing;
a forming step of forming and forging the titanium alloy blank for n3 times, wherein the temperature of the forming and forging is reduced from beta-30 ℃ to beta-45 ℃ along with the increase of the forming and forging times, and the reduction of the section diameter is reduced from 50-60 mm/time to 30-35 mm/time;
n1=3 to 5, n2=3 to 5, n3=3 to 5, and β is the transformation point temperature of the titanium alloy billet;
And chamfering is carried out in the forging process of the titanium alloy blank along with the increase of forging fire.
In some preferred embodiments, the cross-sectional dimensions of the titanium alloy billet decrease in sequence as the forging firing rate increases.
In some preferred embodiments, the cross-sectional shape of the titanium alloy billet varies in four, six, eight directions as the forging firing rate increases;
And the cross section shape of the nth 3 hot forming forging is square.
In some preferred embodiments, when n1=2, n2=2, n3=4, the cross-sectional shape of the titanium alloy billet is tetragonal, hexagonal, octave, hexagonal, tetragonal as the forging firing rate increases.
In some preferred embodiments, the temperature of the cogging forging is reduced at a rate of 85 to 100 ℃/fire;
The temperature of forging is changed to be reduced at the speed of 50-65 ℃/fire;
The temperature of the forming forging is reduced at a speed of 5-10 ℃/fire.
In some preferred embodiments, the titanium alloy billet is a TC16 titanium alloy billet; the transformation point temperature of the titanium alloy blank is beta=835-885 ℃.
In some preferred embodiments, the deformation of the cogging forging is reduced from 60-55% to 55-50% as the number of cogging forging fires increases;
With the increase of forging firing time, the deformation of forging is reduced from 50-45% to 45-40%;
With the increase of the forming forging heat, the deformation of the forming forging is increased from 45-50% to 60-65%.
In some preferred embodiments, the hammer speed of the cogging forging is reduced from 55 to 50mm/s to 50 to 45mm/s as the number of cogging forging fires increases;
The hammering speed of the forging is reduced from 45-40 mm/s to 40-35 mm/s along with the increase of the forging firing time;
And the hammering speed of the forming forging is increased from 35-40 mm/s to 50-55 mm/s along with the increase of the forming forging fire.
In some preferred embodiments, the forming process is further followed by a heat treatment regime, the heat treatment regime being at least one of an annealing heat treatment, a destressing anneal, a solution heat treatment, an aging heat treatment.
In some preferred embodiments, the annealing heat treatment is carried out by preserving heat for 15-25 hours at 770-779 ℃, then cooling to 530-580 ℃, and then discharging and air cooling;
the stress relief annealing treatment is to keep the temperature at 530-670 ℃ for 0.5-4.5 h, and then discharging the material for air cooling;
the solid solution heat treatment is carried out for 1.5 to 2.5 hours at 770 to 850 ℃, and then the solution is taken out of the furnace for water quenching;
The aging heat treatment is to keep the temperature at 450-600 ℃ for 5.5-11.5 hours, and then discharge the steel plate from the furnace for air cooling.
Compared with the prior art, the invention has the following beneficial effects:
1. According to the invention, by adopting matched forging temperatures under different forging processes, the material to be forged meets the required forging requirements, so that the forging period is shortened, the hot working production is reduced, the deformation uniformity is improved, and the difficulty of production operation is reduced.
2. The invention adopts different forging modes matched with different heating temperatures, and the diameter of the blank is forged by adopting a method of decreasing the cross section. The forging temperature is controlled mainly because the forging temperature is produced in a mode of decreasing the heating temperature under the condition that the high-temperature deformation does not completely improve the refinement of the internal structure grains of the forging, and the defects of overpoor mechanical property index, unqualified physicochemical result, scrapping, long production period, high energy consumption and the like are finally caused.
3. The invention aims to improve the production efficiency, reduce waste products, fully utilize the optimized production flow of forging temperature and forging technical conditions to effectively improve the conventional forging method, and mainly adopts a method of decreasing the cross section and a method of changing the cross section shape, namely a method of square, hexagonal and octagonal, so as to effectively improve the original grain structure of cogging, improve the forging-changing qualification rate of forging production and the required related performance qualification rate, and simultaneously well control the mutual matching relation of deformation technical parameters during forging of the forging.
4. According to the invention, the heating temperature required by bar forging modification and the matching process of the forging method are comprehensively considered, and meanwhile, the deformation, hammering frequency and other factors are comprehensively considered, and the structural uniformity of the Ti-3Al-5Mo-4.5V titanium alloy bar can be improved by uniformly forging the blank.
Drawings
FIG. 1 is a low-power tissue diagram of a 1/2 section of a sample to be tested in example 1. Wherein (A) is a low-power tissue diagram of the positive section of 1/2 section A of the sample to be tested in the embodiment 1; (B) Is a low-power tissue diagram of 1/2 section A reverse section of the sample to be tested in the example 1.
FIG. 2 is a low-power tissue diagram of a 1/4 section of the sample to be tested in example 1. Wherein (A) is a low-power tissue diagram of the positive section of the 1/4 section B of the sample to be tested in the embodiment 2; (B) A low-power tissue diagram of the 1/4 section B inverse cross section of the sample to be tested in example 2.
Fig. 3 is a high-power structure diagram of a front cross section of the titanium alloy bar of example 1.
Fig. 4 is a high-power structure diagram of a front cross section of the titanium alloy bar of comparative example 1.
Detailed Description
The present invention will be described in further detail with reference to the following examples in order to make the objects, technical solutions and advantages of the present invention more apparent. It should be understood that the specific embodiments described herein are for purposes of illustration only and are not intended to limit the scope of the invention.
All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
The TC16 titanium alloy can be formed by hot forging and cold forging. TC16 titanium alloys are typically strengthened by cold working, which is typically done by hammer-on-melting, forging, and drawing to form the desired bar. However, the method has the defects of long period, multiple fires, uneven deformation and the like, and the required related performance of the method is difficult to meet the requirements of the required product on the materials of the forgings. In addition, before the cold working of the finished product, the blank is subjected to homogenization forging forming by utilizing forging equipment so as to meet the requirements of the product. In order to perform homogenization molding on the blank, a certain heat treatment mode is generally required to optimize the mechanical property and microstructure of the TC16 titanium alloy bar. The microstructure of the TC16 titanium alloy wire is greatly deformed after heat treatment, and the microstructure of the bar is generally smaller, so that the alloy has very high plasticity and relatively low strength.
At present, the forging forming mode is generally changed to complete the forging production of the titanium alloy with uniformity, and the forging mode is generally changed to complete the uniform refinement of the titanium alloy structure by adopting an upsetting-drawing mode, however, the forging mode is easy to lead to long forging period and multiple firing, for example, the forging is changed to be performed with at least 5 firing times, the problems of uneven deformation and the like are easy to occur, the physicochemical result of the final forging cannot meet the required requirement, and the rejection rate is higher.
In order to solve the problems, the invention adopts a new matching mode for the forging heating temperature and the forging mode to finish the forging on the Ti-3Al-5Mo-4.5V titanium alloy hammer, and can lead the titanium alloy structure to be uniformly refined under the condition of reducing the forging heat, and finally achieve the required related performance requirement, and the required internal structure is as follows: martensitic a+β two-phase structure is required.
Firstly, a Ti-3Al-5Mo-4.5V titanium alloy hammer forging mode adopts: different drawing modes are adopted at different temperatures to finish the process. The forging mode adopted at present is as follows: cogging forging, forging by forging instead of forging, and forming forging; and the forging mode of upsetting and drawing is adopted in the forging process, so that the forging period is easy to be long and the number of fires is more. Based on the above, for Ti-3Al-5Mo-4.5V titanium alloy material, different temperatures are adopted under different forging modes to complete corresponding forging procedures in order to meet the requirements of the material.
The raw blank is usually cast into a cast ingot by smeltingIngot casting with diameter: from the viewpoints of energy utilization rate and economical practicability, the most direct method is/>The ingot with the diameter is forged into the required material specification, and the blank specification required for cold working and utilized by the Ti-3Al-5Mo-4.5V titanium alloy parts is/>That is, before cold working, it is necessary to mixCold working utilization/>, required for processing ingots of diameter into TC16 titanium alloy partsIs a blank of a (c).
Therefore, the forging process has higher requirements, and the scheme provides a thermoforming production scheme for shortening the period, reducing the heat production firing time, improving the deformation uniformity and reducing the production operation difficulty, and is specifically as follows: and the forging is completed by adopting different forging modes at different temperatures.
The Ti-3Al-5Mo-4.5V titanium alloy forging produced by utilizing forging equipment adopts different forging modes matched with different heating temperatures, and the total diameter of the blank is forged by adopting a cross section progressive forging method; i.e. the diameter gradually decreases from large to small; the method for changing the length from small to large adopts different forging methods for forging modes at different heating temperatures to finish the production of the blank before cold working.
The method for cogging and forging Ti-3Al-5Mo-4.5V titanium alloy blank is mainly characterized in that the forging temperature is controlled in a mode of decreasing the heating temperature under the condition that the high-temperature deformation does not completely improve the refinement of the internal structure grains of the forging, and the forging is finally produced in a mode of decreasing the heating temperature, so that the defects of poor mechanical property index, unqualified physicochemical result, scrapping, long production period, high energy consumption and the like are finally caused. In order to improve the production efficiency and reduce waste products, the invention fully utilizes the optimized production flow of forging temperature and forging technical conditions to effectively improve the conventional forging method, adopts a method of decreasing the cross section and a method of changing the cross section shape, namely a method of square, hexagonal and octagonal, to effectively improve the original grain structure of the cogged, improve the forging-changing qualification rate of the forging production and the required related performance qualification rate, and simultaneously can well control the mutual matching relation of deformation technical parameters during forging of the forging.
In conclusion, the structural uniformity of the Ti-3Al-5Mo-4.5V titanium alloy bar can be improved by uniformly forging the blank by utilizing 5000T press equipment of the forging equipment through comprehensively considering the heating temperature required by bar forging change and the matching process of the forging method and comprehensively considering the deformation, the hammering frequency and other factors.
The forging forming method for improving the performance of the TC16 titanium alloy is specifically described below.
A forging forming method for improving the performance of TC16 titanium alloy is characterized by comprising the following steps:
A cogging procedure, in which the titanium alloy blank is cogged and forged by n1 times of fire, and the cogging and forging temperature is reduced from 1150-1160 ℃ to 1060-1075 ℃ and the reduction of the section diameter is reduced from 190-200 mm/time to 90-100 mm/time along with the increase of the cogging and forging time;
a forging-changing procedure, in which the titanium alloy blank is subjected to n 2-time forging-changing forging, and the temperature of the forging-changing forging is reduced from 1000-1015 ℃ to 950-965 ℃ along with the increase of the forging-changing forging firing, and the reduction of the section diameter is reduced from 70-80 mm/firing to 50-60 mm/firing;
a forming step of forming and forging the titanium alloy blank for n3 times, wherein the temperature of the forming and forging is reduced from beta-30 ℃ to beta-45 ℃ along with the increase of the forming and forging times, and the reduction of the section diameter is reduced from 50-60 mm/time to 30-35 mm/time;
n1=3 to 5, n2=3 to 5, n3=3 to 5, and β is the transformation point temperature of the titanium alloy billet;
And chamfering is carried out in the forging process of the titanium alloy blank along with the increase of forging fire.
In a preferred embodiment, in the cogging process, the 2-shot cogging forging is the 1 st-shot cogging forging and the 2 nd-shot cogging forging, respectively;
the first firing cogging forging is to preheat the blank at the temperature of less than or equal to 800 ℃ to 830-850 ℃ along with the furnace, then heat the blank to 1150-1160 ℃, and then perform the first firing cogging forging;
the 2 nd firing cogging forging is to preheat the steel at 800-830 ℃ with the temperature of the furnace, then heat the steel to 1060-1075 ℃, and then perform the 2 nd firing cogging forging;
in the forging-changing procedure, 2-fire forging-changing forging is respectively 1 st fire forging-changing forging and 2 nd fire forging-changing forging;
the 1 st fire forging is performed by preheating the steel at the temperature of less than or equal to 800 ℃ along with the temperature rise of a furnace to 800 ℃, then heating the steel to 1000-1015 ℃, and then performing the 1 st fire forging;
the forging and forging of the 2 nd fire time is carried out by heating to 950-965 ℃ from 800 ℃ or less along with a furnace, and then carrying out the forging and forging of the 2 nd fire time;
The forming process comprises 4 times of forming forging, wherein the 4 times of forming forging are respectively 1 st time of forming forging, 2 nd time of forming forging, 3 rd time of forming forging and 4 th time of forming forging;
the 1 st hot forming forging is to heat the furnace to beta-30 ℃ from the temperature of less than or equal to 800 ℃ and then to perform the 1 st hot forming forging;
The 2 nd fire forming forging is to heat the furnace to beta-35 ℃ from the temperature of less than or equal to 800 ℃ and then to perform the 2 nd fire forming forging;
The 3 rd fire forming forging is to heat the furnace to beta-40 ℃ from the temperature of less than or equal to 800 ℃ and then to perform the 3 rd fire forming forging;
the 4 th fire forming forging is carried out after the temperature is increased to beta-45 ℃ from 800 ℃ or less along with the furnace.
In some preferred embodiments, the cross-sectional dimensions of the titanium alloy billet decrease in sequence as the forging firing rate increases.
In a preferred embodiment, the reduction in cross-sectional dimensions of the titanium alloy ingot as the forging process proceeds is determined byGradually decrease to/>
In some preferred embodiments, the cross-sectional shape of the titanium alloy billet varies in four, six, eight directions as the forging firing rate increases;
And the cross section shape of the nth 3 hot forming forging is square.
In some preferred embodiments, when n1=2, n2=2, n3=4, the cross-sectional shape of the titanium alloy billet is tetragonal, hexagonal, octave, hexagonal, tetragonal as the forging firing rate increases.
In a preferred embodiment, the cross-sectional shape of the titanium alloy blank in the cogging process is tetragonal or hexagonal; the cross section shape of the titanium alloy blank in the forging process is changed into eight directions and six directions; the cross section shape of the titanium alloy blank in the forming process is tetragonal, hexagonal, tetragonal and tetragonal.
In some preferred embodiments, the temperature of the cogging forging is reduced at a rate of 85 to 100 ℃/fire;
The temperature of forging is changed to be reduced at the speed of 50-65 ℃/fire;
The temperature of the forming forging is reduced at a speed of 5-10 ℃/fire.
In some preferred embodiments, the titanium alloy billet is a TC16 titanium alloy billet; the transformation point temperature of the titanium alloy blank is beta=835-885 ℃.
In some preferred embodiments, the deformation of the cogging forging is reduced from 60-55% to 55-50% as the number of cogging forging fires increases;
With the increase of forging firing time, the deformation of forging is reduced from 50-45% to 45-40%;
With the increase of the forming forging heat, the deformation of the forming forging is increased from 45-50% to 60-65%.
In some preferred embodiments, the hammer speed of the cogging forging is reduced from 55 to 50mm/s to 50 to 45mm/s as the number of cogging forging fires increases;
The hammering speed of the forging is reduced from 45-40 mm/s to 40-35 mm/s along with the increase of the forging firing time;
And the hammering speed of the forming forging is increased from 35-40 mm/s to 50-55 mm/s along with the increase of the forming forging fire.
In a preferred embodiment, the technical method of open forging is as follows:
The first firing cogging forging method is to axially flatten, forge to square and axially draw to square; chamfering is carried out once, the forging deformation is 60-55%, and the forging hammering speed is 55-50 mm/s;
the 2 nd firing cogging forging method is that the square chamfering is axially drawn into a hexagon after the square chamfering, the chamfering is carried out once, the forging deformation is 55 to 50 percent, and the forging hammering speed is 50 to 45mm/s.
In a preferred embodiment, the technical scheme of forging is as follows:
the forging method for the first forging is that the hexagonal chamfer is axially drawn into eight directions, the chamfer is performed once, the forging deformation is 50 to 45 percent, and the forging hammering speed is 45 to 40mm/s;
The 2 nd forging method is that the forging is carried out by axially drawing, chamfering in eight directions, axially drawing into a hexagon, chamfering once, forging deformation 45-40%, and hammering speed for silver manufacture 40-35 mm/s.
In a preferred embodiment, the technical method of forming forging is as follows:
The 1 st fire forming forging method is that the axial drawing is carried out, the hexagonal chamfering is axially drawn into four directions, the chamfering is carried out once, the forging deformation is 45-50%, and the forging hammering speed is 35-40 mm/s;
The 2 nd fire forming forging method is that the square chamfer is axially drawn into a hexagon, the chamfer is performed once, the forging deformation is 50 to 55 percent, and the forging hammering speed is 40 to 45mm/s;
the 3 rd fire forming forging method is that the axial drawing is carried out, the hexagonal chamfering is axially drawn into four directions, the chamfering is carried out once, the forging deformation is 55 to 60 percent, and the forging striking speed is 45 to 50mm/s;
The fourth firing forming forging method is that the square chamfer is axially drawn into square, the chamfer is performed once, and the forging deformation is 60-65%; the forging hammering speed is 50-55 mm/s.
In some preferred embodiments, the forming process is further followed by a heat treatment regime, the heat treatment regime being at least one of an annealing heat treatment, a destressing anneal, a solution heat treatment, an aging heat treatment.
In some preferred embodiments, the annealing heat treatment is carried out by preserving heat for 15-25 hours at 770-779 ℃, then cooling to 530-580 ℃, and then discharging and air cooling;
the stress relief annealing treatment is to keep the temperature at 530-670 ℃ for 0.5-4.5 h, and then discharging the material for air cooling;
the solid solution heat treatment is carried out for 1.5 to 2.5 hours at 770 to 850 ℃, and then the solution is taken out of the furnace for water quenching;
The aging heat treatment is to keep the temperature at 450-600 ℃ for 5.5-11.5 hours, and then discharge the steel plate from the furnace for air cooling.
The method changes the cross section shape required by production according to the characteristics of production equipment, namely: the production method combining the technical method of tetragonal-hexagonal-octave and the matching of heating parameters solves the problems of uneven final macrostructure and unqualified flaw detection of the forging stock caused by uneven deformation of the forging stock at high temperature.
The invention optimizes the forging forming method, adopts the method of changing the square-hexagonal-octagonal cross section form, effectively improves the original grain structure which is left undeformed at the high temperature of cogging, and improves the forging-changing qualification rate and the required internal structure qualification rate of the forging production.
The invention can well control the mutual matching relation between the deformation method and the heating temperature and deformation technical parameters during forging of the forging piece. By comprehensively considering the process of decreasing the cross section required by the forging modification of the bar and simultaneously comprehensively considering the deformation, the technical points of the forging process and other factors: to improve the requirements of the bar material for final physical and chemical requirements.
In summary, the invention utilizes 5000T press equipment to optimize the forging process of the bar, and adopts a method of changing the square-hexagonal-octagonal cross section form to effectively improve the original grain structure which is not deformed at the high temperature of cogging, and improve the forging-improving qualification rate and the required internal structure qualification rate of the forging production. The requirements of bar material for final physical and chemical are improved by comprehensively considering the heating temperature and heating times required by bar material forging, technical key points in the production process and other factors. As a result, the forging qualification rate is improved, the waste loss is reduced, the energy is saved, and the economic benefit is improved.
DETAILED DESCRIPTION OF EMBODIMENT (S) OF INVENTION
The technical solution of the present invention will be described in detail below for a clearer understanding of technical features, objects and advantageous effects of the present invention, but should not be construed as limiting the scope of the present invention.
It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. In addition, for numerical ranges in this disclosure, it is understood that each intermediate value between the upper and lower limits of the ranges is also specifically disclosed. Every smaller range between any stated value or stated range, and any other stated value or intermediate value within the stated range, is also encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
The methods described in the examples below are conventional, unless otherwise specified; the reagents and materials are commercially available unless otherwise specified.
TC16 titanium alloy with nominal composition of Ti-3Al-5Mo-4.5V.
The technical scheme of the invention is further described in detail by the following examples:
Production details: material Ti-3Al-5Mo-4.5V titanium alloy; blank specification, phi 690 multiplied by 900; weight: 1682.7kg; standard: AMS54928; name: ti-3Al-5Mo-4.5V titanium alloy-phi 10-titanium rod; the bar specification: phi 100 x 2000; phase transition point: beta=880℃.
Example 1
A forging forming method for improving the performance of TC16 titanium alloy comprises the following steps:
Step one, cogging forging:
Fire 1: charging the blank into a furnace at the temperature of less than or equal to 800 ℃, heating to 850 ℃ along with the furnace, and preserving heat for 120min; then heating to 1150 ℃ along with the furnace, and preserving heat for 415min. Then performing the 1 st firing cogging forging, wherein the specific forging method comprises the following steps: upsetting the blank from phi 690×900 to ≡695×700+ -15, then drawing, axially forging, and drawing and forging the blank to-four ≡490×1395+ -15; chamfering is carried out once in the forging process, the forging deformation is 60%, and the forging hammering speed is 55mm/s.
Fire 2: and (3) feeding the forging stock obtained by the fire 1 into a furnace at the temperature of less than or equal to 800 ℃, heating to 830 ℃ along with the furnace, preserving heat for 120min, heating to 1060 ℃ along with the furnace, and preserving heat for 295min. Then performing the 2 nd fire cogging forging, wherein the specific forging method comprises the following steps: drawing and forging the forging stock from square ≡490×1395 ± 15 axial forging direction to hexagonal v400×2090 ± 15: the blanking is equally divided once, and the single piece is in a shape of hexagonal ≡400 multiplied by 1040 plus or minus 15. Chamfering is carried out once in the forging process; the forging deformation is 55%; the forging hammering speed was 50mm/s.
Step two, forging by forging:
Fire 1: and (3) feeding the forging stock obtained by cogging and forging by the 2 nd fire into a furnace at the temperature of less than or equal to 800 ℃, heating to 800 ℃ along with the furnace, preserving heat for 120min, heating to 1000 ℃ along with the furnace, and preserving heat for 240min. Then forging by changing the first forging into forging by the first forging method, wherein the specific forging method comprises the following steps: drawing the forging stock from a hexagonal ≡400 multiplied by 1040 plus or minus 15 axial forging direction to a forging direction of-eight directions ≡330 multiplied by 1560 plus or minus 15; chamfering is carried out once in the forging process. The forging deformation was 50%, and the forging hammering speed was 45mm/s.
Fire 2: and (3) feeding the forging stock obtained by forging and forging with the 1 st fire into a furnace at the temperature of less than or equal to 800 ℃, heating to 950 ℃ along with the furnace, and preserving the heat for 200min. Then forging by changing the second forging into forging by the fire 2, wherein the specific forging method comprises the following steps: drawing and forging the forging stock from eight directions ≡330×1560 ± 15 axial forging directions to-six directions ≡280×2185 ± 15; chamfering is carried out once in the forging process. The forging deformation was 45%, and the forging hammering speed was 40mm/s. The middle uses a chopper to divide the hexagons ≡280×2185+ -15 evenly into 2 pieces, the single piece size is ≡280×1080±15.
Step three, forming forging
Fire 1: and (3) feeding the forging stock obtained by forging and forging with the 2 nd fire into a furnace at the temperature of less than or equal to 800 ℃, heating to beta-30 ℃ below the phase transition point along with the furnace, namely, keeping the temperature for 170min at 850+/-10 ℃. Then carrying out fire forming forging 1, wherein the specific forging method comprises the following steps: and (3) axially drawing the forging stock from the hexagonal direction of ≡280 multiplied by 1080+/15 to the square direction of ≡230 multiplied by 1560+/15, and chamfering once in the forging process. The forging deformation was 45%, and the forging impact rate was 35mm/s.
Fire 2: and (3) feeding the forging stock obtained by the 1 st hot forming forging into a furnace at the temperature of less than or equal to 800 ℃, heating to beta-35 ℃ below the phase transition point along with the furnace, namely, keeping the temperature for 140min at 845+/-10 ℃. And then carrying out fire forming forging of the 2 nd step, wherein the specific forging method comprises the following steps: axially drawing the forging stock from square ≡230X140+/15, chamfering the square, and axially drawing the forging stock into hexagonal ≡185 +.2340+/15; chamfering is carried out once in the forging process; the forging deformation was 50%, and the forging hammering speed was 40mm/s. The middle uses a chopper to divide the hexagons ≡185 multiplied by 2340 ± 15 evenly into 2 pieces, the single piece size is ≡185×1160±15.
Fire 3: and (3) feeding the forging stock obtained by the 2 nd hot forming forging into a furnace at the temperature of less than or equal to 800 ℃, heating to beta-40 ℃ below the phase transition point along with the furnace, namely 840+/-10 ℃, and preserving heat for 110min. Then carrying out fire forming forging on the steel plate, wherein the specific forging method comprises the following steps: axially drawing the forging stock from the direction of the square of ≡185 multiplied by 1160+/15, axially drawing the forging stock into the direction of the square of ≡150 multiplied by 1790+/15 after chamfering the square, and chamfering once in the forging process. The forging deformation was 55%, and the forging hammering speed was 45mm/s.
Fire 4: and (3) feeding the forging stock obtained by the 3 rd hot forming forging into a furnace at the temperature of less than or equal to 800 ℃, heating to beta-45 ℃ below the phase transition point along with the furnace, namely 835+/-10 ℃, and preserving heat for 90min. And then carrying out the 4 th fire forming forging, wherein the specific forging method comprises the following steps: axially drawing the forging stock from the square of ≡150X109 + -15, chamfering the square, and axially drawing the forging stock into the square of ≡115X 2860 + -15; chamfering is carried out once in the forging process; the forging deformation was 60%, and the forging hammering speed was 50mm/s.
After hot material is returned to the furnace, a special-purpose crash ball is used for breaking the round and axially pulling the hot material, and phi 100+2/-1X 4576+/-15 (the completion of returning to the furnace is allowed for 1 time).
And step four, adopting annealing heat treatment for a heat treatment system, wherein the specific operation is as follows: preserving heat for 1.5h at 770 ℃; and then cooling at a speed of 1.5 ℃/min, cooling to 530 ℃, and discharging and air cooling.
Step five, machining: machining an outer circle and two end faces; the surface roughness Ra3.2.
Comparative example 1
A forging forming method of TC16 titanium alloy comprises the following steps:
Step one, cogging forging:
The blank is put into a 1150 ℃ resistance furnace to be insulated for 415min. Then performing first-fire cogging forging of three piers and three drawing, wherein the working procedures are upsetting firstly, drawing hexagonal rolling, then repeating upsetting and drawing for 2 times, and air cooling after forging. The forging deformation was 60%.
And then preserving heat at 1060 ℃ for 295min, then performing second-firing cogging forging with three piers and three drawing steps, wherein the working procedures are upsetting firstly, drawing hexagonal rolling, then repeating upsetting and drawing for 2 times, and performing air cooling after forging to obtain the titanium alloy forging stock. The forging deformation was 55%.
Step two, forging by forging:
Forging the titanium alloy forging stock obtained in the step one by five times of forging:
First fire: and (3) preserving heat at 1000 ℃ for 240min, taking out the first fire forging for upsetting and drawing, wherein the working procedure is upsetting firstly, then turning over 180 degrees for upsetting, drawing a hexagon along the axial direction, rounding and then air cooling.
Second fire: and (3) preserving heat for 200min at 950 ℃, taking out the second fire forging for two upsetting and two drawing, wherein the working procedures are upsetting firstly, then turning over 180 degrees for upsetting, drawing the hexagon along the axial direction and rounding, repeating the upsetting and drawing for one time, and then air cooling.
Third fire: and (3) preserving heat at 930 ℃ for 170min, taking out the third fire for forging, upsetting, turning over 180 degrees, axially pulling the hexagon, and returning to the furnace.
Fourth fire: and (3) preserving heat at 910 ℃ for 150min, taking out the forging by changing the fourth fire for upsetting and pulling, wherein the working procedure is upsetting firstly, then turning over 180 degrees for upsetting, pulling the hexagon along the axial direction, and then returning to the furnace.
Fifth fire: and (3) preserving heat at 900 ℃ for 120min, taking out the blank, performing forging by replacing the fifth fire for drawing, namely drawing the hexagon of the blank along the axial direction, and rounding.
And step three, adopting annealing heat treatment for a heat treatment system, wherein the specific operation is as follows: preserving heat for 1.5h at 770 ℃; and then cooling at a speed of 1.5 ℃/min, cooling to 530 ℃, and discharging and air cooling.
Fourth, machining: machining an outer circle and two end faces; the surface roughness Ra3.2.
The titanium alloy bars prepared in the above examples were subjected to performance testing.
The test method is performed according to GB/T 2039-2012,GB/T 228.1-2021,GB/T 228.2-2015,GB/T 229-2020,GB/T 23605-2020,GB/T 4698.15-2011,GB/T 5168-2020.
Test 1: impact test:
the titanium alloy bar prepared in example 1 was used as a sample to be tested, the sample to be tested was cut at one time, and impact test was performed on two cut samples at 23℃and the results are shown in Table 1.
Table 1 impact test results
Note that: t1 represents the front cross section of the sample to be tested of example 1; t2 represents the reverse side cross section of the sample to be tested of example 1.
As can be seen from the results of FIG. 1, the titanium alloy bar prepared in example 1 of the present invention has excellent impact resistance. Impact tests were also performed on the titanium alloy bars prepared in example 2, and the results also met the standard value range. Therefore, the embodiment of the invention utilizes the mutual matching relation between the forging temperature and the deformation technical parameters during forging, and adopts a method of decreasing the section and a mode of changing the section shape, namely a method of square, hexagonal and octave, to effectively improve the original grain structure during cogging, thereby effectively improving the impact resistance of the forging.
Test 2: low power tissue examination:
The titanium alloy bar prepared in the embodiment 1 is taken as a sample to be detected, 1/2 section of the sample to be detected is cut, and the two cut surfaces are marked as A positive and A negative; the 1/4 section of the sample to be measured is cut, and the two cut surfaces are marked as B positive and B negative.
The 4 sections were examined for a low-power tissue, respectively, as shown in FIGS. 1 and 2.
FIG. 1 is a low-power tissue diagram of a 1/2 section of a sample to be tested in example 1. Wherein (A) is a low-power tissue diagram of the positive section of 1/2 section A of the sample to be tested in the embodiment 1; (B) Is a low-power tissue diagram of 1/2 section A reverse section of the sample to be tested in the example 1.
FIG. 2 is a low-power tissue diagram of a 1/4 section of the sample to be tested in example 1. Wherein (A) is a low-power tissue diagram of the positive section of the 1/4 section B of the sample to be tested in the embodiment 2; (B) A low-power tissue diagram of the 1/4 section B inverse cross section of the sample to be tested in example 2.
As can be seen from the results of the low-power histological examination of fig. 1 and 2, the sample to be tested in example 1 has no delamination, cracks, pores, segregation, metallic and nonmetallic inclusions and other macroscopic metallurgical defects, no obvious and macroscopic clear grains, and meets the standard requirements in the low-power examination of sections 1/2 and 1/4. From this, it is further verified that the embodiment of the present invention uses the mutual matching relationship between the forging temperature and the deformation technical parameters during forging, and adopts a method of decreasing the cross section and a method of changing the cross section shape, that is, a method of "tetragonal-hexagonal-octave", to effectively improve the original grain structure during cogging.
Test 3: high magnification tissue examination
The titanium alloy bars prepared in example 1 and comparative example 1 were cut, and the cut surfaces were subjected to high-power histological examination, and the examination results are shown in fig. 3 and 4.
Fig. 3 is a high-power structure diagram of a cross section of the titanium alloy bar of example 1.
Fig. 4 is a high-power structure diagram of a cross section of the titanium alloy bar of comparative example 1.
As can be seen from the results of high-power tissue examination in fig. 3 and 4, the microstructure of the cross section of the titanium alloy bar in example 1 is a uniform structure processed by the α+β two-phase region, all β grains are fully broken, no continuous grain boundary α exists, the length of the flaky primary α phase is very short, and the ultrafine flaky structure has plasticity equivalent to or even better than that of the equiaxed structure, and meets the standard requirements.
Compared with the microstructure of the titanium alloy bar of comparative example 1, the microstructure of example 1 is more uniform, mainly because the internal structure determines the flaw detection result, the more uniform the structure is, the flaw detection result is more than the standard degree, and different structures can obtain different flaw detection results. Therefore, the better high-power structure of example 1 is more uniform and finer than the relatively worse structure of comparative example 1, and the flaw detection result is superior to that of the forging represented by the worse high-power structure.
Test 4: mechanical property test
The titanium alloy bars prepared in example 1 and comparative example 1 were subjected to room temperature mechanical property test, and the results are shown in table 2.
Table 2 results of room temperature mechanical properties test of TC16 titanium alloy bars
| Tensile strength R m/MPa | Elongation A/% | |
| Example 1 | 910.2 | 21.4 |
| Comparative example 1 | 830 | 12 |
| Standard of | 815～930 | ≥14 |
Note that: the temperature at room temperature was 23 ℃.
From the results in table 2, it can be seen that the tensile strength and elongation of the TC16 titanium alloy bar prepared in example 1 are significantly higher than the standard requirements, while the elongation of comparative example 1 is relatively lower. Presumably, this is probably due to the fact that under the condition that the high-temperature deformation does not completely improve the grain refinement of the internal structure of the forging due to the control of the forging temperature, the forging is produced in a manner of decreasing the heating temperature, and finally, the problem that local coarse crystals or the structure are uneven, so that the mechanical property index is relatively low exists.
The foregoing description of the preferred embodiments of the invention is not intended to be limiting, but rather is intended to cover all modifications, equivalents, and alternatives falling within the spirit and principles of the invention.
Claims (10)
1. A forging forming method for improving the performance of TC16 titanium alloy is characterized by comprising the following steps:
A cogging procedure, in which the titanium alloy blank is cogged and forged by n1 times of fire, and the cogging and forging temperature is reduced from 1150-1160 ℃ to 1060-1075 ℃ and the reduction of the section diameter is reduced from 190-200 mm/time to 90-100 mm/time along with the increase of the cogging and forging time;
a forging-changing procedure, in which the titanium alloy blank is subjected to n 2-time forging-changing forging, and the temperature of the forging-changing forging is reduced from 1000-1015 ℃ to 950-965 ℃ along with the increase of the forging-changing forging firing, and the reduction of the section diameter is reduced from 70-80 mm/firing to 50-60 mm/firing;
a forming step of forming and forging the titanium alloy blank for n3 times, wherein the temperature of the forming and forging is reduced from beta-30 ℃ to beta-45 ℃ along with the increase of the forming and forging times, and the reduction of the section diameter is reduced from 50-60 mm/time to 30-35 mm/time;
n1=3 to 5, n2=3 to 5, n3=3 to 5, and β is the transformation point temperature of the titanium alloy billet;
And chamfering is carried out in the forging process of the titanium alloy blank along with the increase of forging fire.
2. The forging forming method for improving the performance of a TC16 titanium alloy according to claim 1, wherein the cross-sectional dimensions of the titanium alloy billet decrease in sequence with increasing forging firing times.
3. The forging forming method for improving the performance of a TC16 titanium alloy according to claim 1, wherein the cross-sectional shape of the titanium alloy billet is changed in four directions, six directions and eight directions with increasing forging firing times;
And the cross section shape of the nth 3 hot forming forging is square.
4. The forging forming method for improving the performance of a TC16 titanium alloy according to claim 3, wherein when n1=2, n2=2, n3=4, the cross-sectional shape of the titanium alloy ingot is tetragonal, hexagonal, octagon, hexagonal, tetragonal with an increase in forging heat.
5. The forging forming method for improving the performance of a TC16 titanium alloy according to claim 1, wherein the temperature of cogging forging is lowered at a rate of 85 to 100 ℃/fire;
The temperature of forging is changed to be reduced at the speed of 50-65 ℃/fire;
The temperature of the forming forging is reduced at a speed of 5-10 ℃/fire.
6. The forging forming method for improving the performance of a TC16 titanium alloy according to claim 1, wherein said titanium alloy ingot is a TC16 titanium alloy ingot; the transformation point temperature of the titanium alloy blank is beta=835-885 ℃.
7. The forging forming method for improving the performance of the TC16 titanium alloy according to claim 1, wherein the deformation amount of the cogging forging is reduced from 60 to 55% to 55 to 50% with the increase of the cogging forging firing time;
With the increase of forging firing time, the deformation of forging is reduced from 50-45% to 45-40%;
With the increase of the forming forging heat, the deformation of the forming forging is increased from 45-50% to 60-65%.
8. The forging forming method for improving the performance of the TC16 titanium alloy according to claim 1, wherein the hammering speed of the cogging forging is reduced from 55 to 50mm/s to 50 to 45mm/s with the increase of the cogging forging firing time;
The hammering speed of the forging is reduced from 45-40 mm/s to 40-35 mm/s along with the increase of the forging firing time;
And the hammering speed of the forming forging is increased from 35-40 mm/s to 50-55 mm/s along with the increase of the forming forging fire.
9. The forging forming method for improving the performance of a TC16 titanium alloy according to claim 1, further comprising a heat treatment schedule after the forming process, wherein the heat treatment schedule is at least one of an annealing heat treatment, a destressing annealing, a solution heat treatment, and an aging heat treatment.
10. The forging forming method for improving the performance of the TC16 titanium alloy according to claim 9, wherein the annealing heat treatment is carried out by preserving heat for 15-25 h at 770-779 ℃, and then cooling to 530-580 ℃ and then discharging for air cooling;
the stress relief annealing treatment is to keep the temperature at 530-670 ℃ for 0.5-4.5 h, and then discharging the material for air cooling;
the solid solution heat treatment is carried out for 1.5 to 2.5 hours at 770 to 850 ℃, and then the solution is taken out of the furnace for water quenching;
The aging heat treatment is to keep the temperature at 450-600 ℃ for 5.5-11.5 hours, and then discharge the steel plate from the furnace for air cooling.
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