CN114309406B - Ti6242 titanium alloy disc and preparation method thereof - Google Patents
Ti6242 titanium alloy disc and preparation method thereof Download PDFInfo
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- CN114309406B CN114309406B CN202011052710.0A CN202011052710A CN114309406B CN 114309406 B CN114309406 B CN 114309406B CN 202011052710 A CN202011052710 A CN 202011052710A CN 114309406 B CN114309406 B CN 114309406B
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Abstract
The invention relates to a preparation method of a Ti6242 titanium alloy disc piece, which comprises the following steps: (1) providing a Ti6242 titanium alloy rod-shaped ingot; (2) Performing axial upsetting forging on the rod-shaped ingot for 8-12 times; (3) Carrying out the eight-direction reversing upsetting forging of the 4 th to 6 th times on the product of the previous step; (4) Upsetting and forging the product of the previous step for 1 time to obtain a cake blank; (5) placing the cake blank into a disc mold for die forging; (6) carrying out solid solution and aging treatment on the product of the last step.
Description
Technical Field
The invention relates to the field of materials, in particular to a Ti6242 titanium alloy disc and a preparation method thereof.
Background
The Ti-6Al-2Sn-4Zr-2Mo-0.08S alloy (corresponding to GB/T3620.1-2016 brand TA19, also called Ti6242 titanium alloy) is a high-temperature titanium alloy with good comprehensive performance, and has good high-temperature tensile property, fracture toughness and thermal creep resistance.
In the conventional method for forging and preparing the Ti6242 titanium alloy disc, a process of three-axis directional pier drawing of a cube is generally adopted, and in addition, an air cooling mode is generally adopted in solution treatment.
Disclosure of Invention
The invention provides a preparation method of a titanium alloy disc, which creatively adopts the following innovative characteristics:
(1) Biaxial reversing upsetting process for forging with octagon section;
(2) The cavity dimensions of the disc mold have the following characteristics: maximum thickness T of cavity area of corresponding disc body max =200 to 250mm, minimum thickness T min ＝50～80mm；
(3) And a water cooling process after solid solution.
The titanium alloy disc prepared by the method has improved microstructure and mechanical properties.
The first aspect of the present disclosure provides a method for preparing a Ti6242 titanium alloy disc, comprising the steps of:
(1) Providing a Ti6242 titanium alloy rod-shaped ingot;
(2) Performing axial upsetting forging on the rod-shaped ingot for 8-12 times, wherein the forging temperature of each time is 900-1200 ℃ (e.g. 950-1150 ℃), and the forging ratio is 1.3-1.5;
the axial upsetting forging comprises upsetting forging for one or more times and drawing forging for one or more times along the axial direction of the forging stock;
(3) Carrying out n-fire-time eight-direction reversing upsetting forging on the product of the last step, wherein n=4-6, and the forging temperature of each fire time is 950-1000 ℃;
(4) Upsetting and forging the product of the previous step for 1-2 times (for example, 1 time), wherein the forging temperature is 950-1000 ℃, and the forging ratio is 1.3-1.6, so as to obtain a cake blank;
(5) Heating the cake blank to 950-1000 ℃, placing the cake blank into a disc die for die forging, wherein the cavity size of the disc die has the following characteristics: maximum thickness T of cavity area of corresponding disc body max =200 to 250mm (e.g. 210 to 220 mm), minimum thickness T min =50 to 80mm (e.g. 60 to 70mm, e.g. 65 mm);
(6) Carrying out solid solution and aging treatment on the product of the last step, wherein the solid solution temperature is Tbeta-30 ℃ to Tbeta-20 ℃, the heat preservation time is 1-2 h, and the cooling mode is water cooling; the aging temperature is 580-600 ℃, the heat preservation time is 7-9 h, the cooling mode is air cooling, and Tbeta is Ti6242 titanium alloy beta phase transition point.
In some embodiments, the axial heading forging is one heading one drawing or two heading two drawing.
In some embodiments, step (2) comprises 10 firings of axial heading forging, comprising in particular the following operations:
carrying out A1 fire forging on the rod-shaped cast ingot, wherein the forging temperature is 1150-1200 ℃, the forging mode is one forging and one drawing, and the forging ratio is 1.3-1.5;
forging the product in the previous step by using an A2 fire at the forging temperature of 1100-1150 ℃ in a two-upsetting and two-pulling mode, wherein the forging ratio is 1.3-1.5;
and (3) forging the product in the last step by using an A3 fire at 1050-1100 ℃ in a two-heading and two-drawing mode, wherein the forging ratio is 1.3-1.5.
Forging the product of the previous step by A4 fire, wherein the forging temperature is 950-990 ℃, the forging mode is upsetting and pulling, the forging ratio is 1.3-1.5, and chamfering is carried out on the forging stock after the forging is finished;
forging the product in the last step by the A5 fire at 1050-1100 ℃ in a two-upsetting and two-pulling mode with the forging ratio of 1.3-1.5;
forging the product of the previous step by firing A6, A7 and A8 in sequence, wherein the forging temperature is 950-1000 ℃, the forging modes are heading and pulling, and the forging ratio is 1.3-1.5;
and (3) forging the product in the last step by sequentially carrying out A9 and A10 fires, wherein the forging temperature is 950-1000 ℃, the forging mode is drawing, and the deformation of drawing is 35-45%.
In some embodiments, in the n-fire eight-way reverse upsetting forging of step (3):
the eighth direction reversing upsetting forging of the 1 st firing time comprises the following steps: heating the forging stock to 950-980 ℃, upsetting and deforming the forging stock (such as a rod-shaped forging stock with a circular section) along the axial direction, wherein the forging ratio is 1.8-2, then radially drawing the forging stock, wherein the forging ratio is 1.5-1.6, obtaining a square section forging stock, returning to the furnace for heat preservation, radially upsetting the forging stock, wherein the forging ratio is 1.8-2, and then axially drawing the forging stock, wherein the forging ratio is 1.8-2, thus obtaining an octagon section forging stock;
in the eight-direction forging of the 2 nd to n-1 th heats, the forging of each heat includes: heating the forging stock to the forging temperature of 950-980 ℃, upsetting and deforming the forging stock along the axial direction, wherein the forging ratio is 1.7-1.9, then drawing the forging stock along the radial direction, wherein the forging ratio is 1.6-1.8 to obtain a square section forging stock, returning to the furnace for heat preservation, upsetting the forging stock along the radial direction, wherein the forging ratio is 1.8-2, and drawing the forging stock along the axial direction to obtain an octagon section forging stock, wherein the forging ratio is 1.8-2;
the eighth forging of the nth firing time includes: heating the forging stock to the forging temperature of 950-980 ℃, firstly upsetting and deforming along the axial direction, wherein the forging ratio is 1.7-1.9, then drawing the forging stock along the radial direction, wherein the forging ratio is 1.6-1.8 to obtain a square section forging stock, returning to the furnace for heat preservation, then upsetting the forging stock along the radial direction, wherein the forging ratio is 1.8-2, and then rounding along the axial direction, wherein the forging ratio is 1-1.2 to obtain a round section forging stock;
preferably, n=5.
In some embodiments, in step (3), the temperature of the tempering heat preservation is 950-1000 ℃ (e.g., 950-980 ℃) for 180-270 minutes.
In some embodiments, in step (4), the size of the biscuit is from 400 to 600mm in diameter and from 250 to 350mm in thickness.
In some embodiments, in step (1), the rod-shaped ingot refers to a cylindrical rod-shaped ingot having an aspect ratio of ∈2.
In some embodiments, in step (1), the titanium alloy rod ingot has a diameter of 500 to 1000mm (e.g., 700 to 800 mm) and a length of 2300 to 3000mm (e.g., 2800 to 2900 mm).
In some embodiments, in step (5), the number of swages is 2 and the total deformation (average) of the swages is 40% to 70%.
In some embodiments, in step (5), the disc mold is a preheated disc mold having a preheating temperature of 250 ℃ to 300 DEG C
In some embodiments, after each firing, the forging is cooled in an air-cooled manner.
In some embodiments, the titanium alloy disc is an aircraft engine compressor disc.
In some aspects, the present disclosure provides a titanium alloy disc, prepared by the method of any one of the present disclosure.
Description of the terminology:
if the following terms are used in the present invention, they may have the following meanings:
the term "beta transus" refers to the alpha + beta/beta transus temperature on the titanium alloy phase diagram.
"Ti6242", "TA19 titanium alloy" and "Ti-6Al-2Sn-4Zr-2Mo-0.08S titanium alloy" have the same meaning and specific definitions are given in GB/T3620.1-2016. The composition of the alloy is that Al 5.5-6.5%, sn 1.8-2.2%, zr 3.6-4.4%, mo 1.8-2.2%, si 0.06-0.1%, fe less than or equal to 0.1%, O less than or equal to 0.15%, C less than or equal to 0.05%, N less than or equal to 0.05% and the balance of Ti and unavoidable impurities.
The process of upsetting and pulling is to sequentially perform upsetting treatment and pulling treatment on the forging piece.
The forging piece with two piers and two drawing parts is sequentially subjected to one upsetting treatment, one drawing treatment, one upsetting treatment and one drawing treatment.
Unless otherwise specified, the directions of upsetting and elongation are along the axis of the rod blank (normal to both bottom surfaces).
"forging ratio" refers to the ratio of the cross-sectional areas of the forgings before and after forging, and is used to characterize the degree of metal deformation during forging. When the forging mode is drawing, the length of the forging before forging is L 1 The length of the forged piece after forging is L 2 Forging ratio=l 2 /L 1 The method comprises the steps of carrying out a first treatment on the surface of the When the forging mode is upsetting, the height of the forging before forging is H 1 The height of the forged piece after forging is H 2 Forging ratio=h 1 /H 2 。
The term "disc" refers to a solid of revolution part having a symmetrical cross section in the axial direction. The thickness of the disc refers to the dimension perpendicular to the axial direction of the disc.
The term "disk body" refers to the location of the disk from the center to the rim, the disk body not including "test rings" which refer to the forging and heat treatment completed with the disk as a whole, with subsequent cutting away for testing and representing the performance of the disk.
The term "web" refers to a region that transitions from the center to the rim.
The term "beta transus" refers to the alpha + beta/beta transus temperature on the titanium alloy phase diagram.
The terms "square section", "circular section", "octagonal section" refer to a section perpendicular to the central symmetry axis of the forging stock.
Advantageous effects
One or more technical solutions of the present disclosure have one or more of the following beneficial effects:
(1) The forging stock with the eight-direction cross section is axially and radially reversed in upsetting, so that the tissue uniformity in the deformation process is improved, the level of ultrasonic detection clutter is obviously reduced, the upsetting and drawing times are also reduced, and in addition, the problem that the direction is not easy to identify in actual operation due to the traditional cubic multiple reversing and the flow line is uneven due to the fact that the reversing direction is too many is also avoided.
(2) The method of air cooling after the Ti6242 alloy is subjected to solution heat treatment and solution by the traditional process (such as the traditional process specified in AMS 4976) is changed, the cooling mode after solution is changed into water cooling, the hardenability is increased, and the tensile strength of the forging is obviously improved.
(3) The problem that the creep property does not reach the standard due to thinner alpha sheet layer which is secondarily precipitated and is caused by too fast water cooling speed is solved by adopting the mold cavity with the thickness (more than or equal to 50 mm).
Drawings
FIG. 1 is a schematic view of a cubic forging stock;
FIG. 2 is a schematic illustration of an eight-sided cross-section forging stock;
FIG. 3 is a diagram of the structure of a compressor disk of one embodiment;
FIG. 4 is a metallographic photograph of the titanium alloy disc of comparative example 1;
fig. 5 is a metallographic photograph of the titanium alloy disc of example 1.
Detailed Description
Embodiments of the present invention will be described in detail below with reference to examples, but it will be understood by those skilled in the art that the following examples are only for illustrating the present invention and should not be construed as limiting the scope of the present invention. The specific conditions are not noted in the examples and are carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or apparatus used were conventional products commercially available without the manufacturer's attention.
Example 1
Titanium alloy ingots of phi 720mm x 2900mm Ti6242 were used. The components are as follows: al=6.26%, sn=1.95%, zr=4.18%, mo=2.03%, si=0.088%, fe=0.014%, o=0.107%, c=0.007%, n=0.005%, Y <0.001%, the balance being Ti, the average value of the β transformation points being 1008 ℃.
Forging a titanium alloy ingot by a1 st fire, heating a forging stock to a forging temperature of 1170 ℃, and drawing the forging stock to a diameter phi 480mm, wherein the forging ratio is 1.4;
2 nd forging is carried out on the product of the last step, the forging stock is heated to the forging temperature of 1120 ℃, the second forging and the second forging are pulled out until the diameter phi of the forging stock is 480mm, and the forging ratio is 1.5;
and (3) forging the product in the last step by a3 rd fire, heating the forging stock to a forging temperature of 1080 ℃, and drawing the forging stock from the second forging to a diameter phi 480mm, wherein the forging ratio is 1.5.
Forging the product in the last step by a4 th fire, heating the forging stock to the forging temperature of 980 ℃, upsetting and pulling the forging stock to the diameter phi 480mm, wherein the forging ratio is 1.5, chamfering the forging stock after the forging is finished, and air cooling after the forging;
forging the product in the last step by a5 th fire, heating the forging stock to a forging temperature of 1080 ℃, drawing the forging stock to a diameter phi 480mm by a second forging and drawing the forging stock, wherein the forging ratio is 1.5, chamfering the forging stock after the forging is finished (preventing cracking in the cooling process and reducing stress concentration), and air cooling after the forging;
forging the product in the last step by using 6 th, 7 th and 8 th fires, wherein in each firing forging, the forging stock is heated to the forging temperature of 980 ℃, and the forging stock is uniformly headed and pulled to the diameter phi 480mm, and the forging ratio is 1.5;
forging the product in the last step by 9 th and 10 th fires, wherein in each firing forging, the forging stock is heated to the forging temperature of 980 ℃, the forging mode is that the forging stock is drawn, the deformation of the drawn forging stock is 40%, and the forging stock with the specification of phi 350mm cross section is prepared;
and (3) forging the product in the last step by 11 th to 16 th fires, forging the product to a forging stock diameter phi 470mm multiplied by 440mm by eight-direction reversing upsetting, and air cooling after forging, wherein the eight-direction reversing upsetting forging process specifically comprises the following steps:
forging the product (round section forging stock) in the last step by 11 th fire, heating the forging stock to a forging temperature of 980 ℃, upsetting and deforming the forging stock along the axial direction (the direction of a central symmetry axis), wherein the forging ratio is 1.93, then drawing the forging stock along the radial direction (the direction perpendicular to the axial direction), enabling the material to flow along the axial direction during drawing to obtain a forging stock with a square section of 340 x (axis 690) mm, wherein the forging ratio is 1.6, returning to the furnace for 240min, upsetting the forging stock along the radial direction, wherein the forging ratio is 1.82, and drawing the forging stock along the axial direction to obtain a forging stock with an octagon section of 360 x (axis 740) mm, wherein the forging ratio is 1.95; FIG. 2 is a schematic view of an eight-sided cross-section billet, Z in the drawing 2 The direction represents the axial direction and the tu direction represents the radial direction.
Forging the product in the last step by 12-15 th fire, wherein each firing comprises the steps of heating the forging stock to the forging temperature of 980 ℃, upsetting and deforming the forging stock along the axial direction, wherein the forging ratio is 1.80, then drawing the forging stock along the radial direction to obtain a square 340X (690) forging stock, wherein the forging ratio is 1.68, returning to the furnace of 980 ℃ for 240min, then upsetting the forging stock along the radial direction, wherein the forging ratio is 1.82, and drawing the forging stock along the axial direction to obtain an eight-direction 360X (740) forging stock, wherein the forging ratio is 1.95;
forging by a 16 th fire, heating the forging stock to a forging temperature of 980 ℃, upsetting and deforming the forging stock along the axial direction, wherein the forging ratio is 1.80, then drawing the forging stock along the radial direction to obtain a square 340× (690) forging stock, wherein the forging ratio is 1.68, returning to the furnace for heat preservation for 240min, upsetting the forging stock along the radial direction, wherein the forging ratio is 1.82, rounding the forging stock along the axial direction, and the forging ratio is 1.07, thereby obtaining a round section forging stock with the size phi 470 multiplied by 440 mm;
forging the product in the last step by a 17 th fire, wherein the forging mode is upsetting and finishing, heating the forging stock to the forging temperature of 980 ℃, forging the forging ratio to be 1.4, forging to a cake blank with the diameter phi of 530mm multiplied by 310mm, and air cooling after forging;
and (3) die forging: heating the cake blank to 970 ℃, performing 2-fire die forging on a compressor disc die, wherein the die preheating temperature is 250-300 ℃, the total deformation of die forging is 60%, and performing air cooling after the die forging; the dimensions of the mold cavity are as follows:
a) Die diameter d1=852 mm;
b) Die corresponding disc main body (disc core, web)Plate and rim) maximum thickness D1 of the area max =212 mm, minimum thickness D1 min ＝65mm：
c) Thickness D of test ring Test ring ＝50mm。
Solid solution: the solid solution temperature is Tbeta-25 ℃, the heat preservation time is 1h, and the water cooling is carried out;
aging: the aging temperature is 595 ℃, the heat preservation time is 8 hours, and the air cooling is carried out to obtain the compressor disc.
Fig. 3 is a schematic view of a compressor disk. The compressor disk being about a central axis of rotation Z 3 The compressor disk comprises, in radial order from the outside to the inside, a test ring 1, a disk rim 2, a web 3 and a disk core 4. The rim 2, the web 3 and the hub 4 constitute a compressor disk body. The maximum thickness of the compressor disk main body is D1 max Minimum thickness D1 min . The test ring 1 is a radially outward projection at the rim 2, which functions to perform forging and heat treatment together with the disc, and is subsequently used for sampling test evaluation of performance.
Comparative example 1
A phi 720mm x 2900mm ti6242 titanium alloy ingot was used as in example 1.
Forging a titanium alloy ingot by a1 st fire, heating a forging stock to a forging temperature of 1170 ℃, and drawing the forging stock to a diameter phi 480mm, wherein the forging ratio is 1.4;
2 nd forging is carried out on the product of the last step, the forging stock is heated to the forging temperature of 1120 ℃, the second forging and the second forging are pulled out until the diameter phi of the forging stock is 480mm, and the forging ratio is 1.5;
and (3) forging the product in the last step by a3 rd fire, heating the forging stock to a forging temperature of 1080 ℃, and drawing the forging stock from the second forging to a diameter phi 480mm, wherein the forging ratio is 1.5. Chamfering is carried out on the forging stock after the forging is finished, and air cooling is carried out after the forging;
forging the product in the last step by a4 th fire, heating the forging stock to the forging temperature of 950-990 ℃, upsetting and pulling the forging stock to the diameter phi 480mm, wherein the forging ratio is 1.5, chamfering the forging stock after the forging is finished, and air cooling after the forging;
forging the product in the last step by a5 th fire, heating the forging stock to a forging temperature of 1080 ℃, drawing the forging stock by a second forging and drawing to a forging stock diameter phi 480mm, wherein the forging ratio is 1.5, chamfering the forging stock after the forging is finished, and cooling after the forging;
forging the product in the last step by using 6 th, 7 th and 8 th fires, heating the forging stock to the forging temperature of 980 ℃, and uniformly upsetting and drawing until the diameter phi of the forging stock is 480mm, wherein the forging ratio is 1.5;
forging the product in the last step by 9 th and 10 th fires, heating the forging stock to the forging temperature of 980 ℃, and obtaining a rod blank with the diameter phi of 260mm, wherein the deformation of the drawn rod blank is 40%;
forging the product in the last step by 11 th to 20 th fires, heating the forging stock to the forging temperature of 950 ℃, and performing 3-axial upsetting by taking a cube as a reference, wherein the deformation of each firing is 40 to 50 percent, and performing air cooling after forging; the axial upsetting and pulling is specifically as follows:
forging by 11 th fire, heating the forging stock to the forging temperature of 950 ℃, upsetting the phi 260mm rod stock along the axial direction, and the forging ratio is 1.4;
forging by 12 th fire, heating the forging stock to the forging temperature of 950 ℃, continuing to upsetting along the axial direction, forging the forging ratio of 1.4, and finishing to obtain a cubic forging stock, wherein in the middle, the normal line of 3 mutually perpendicular faces of the cubic forging stock is defined as an A axis, a B axis and a C axis, and FIG. 1 is a schematic diagram of the cubic forging stock;
forging by a 13 th fire, namely heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the direction of the B axis to obtain a cube forging stock, wherein the forging ratio is 1.4;
forging by a 14 th fire, namely heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the direction of the C axis to obtain a cube forging stock, wherein the forging ratio is 1.4;
forging by 15 th fire, heating the forging stock to the forging temperature of 950 ℃, and upsetting and pulling the forging stock along the A axis direction to obtain a cube forging stock, wherein the forging ratio is 1.4;
forging by a 16 th fire, namely heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the direction of the B axis to obtain a cube forging stock, wherein the forging ratio is 1.4;
forging by a 17 th fire, heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the direction of the C axis to obtain a cube forging stock, wherein the forging ratio is 1.4;
forging by 18 th fire, heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the A axis direction to obtain a cube forging stock with a forging ratio of 1.4;
forging by a19 th fire, namely heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the direction of the B axis to obtain a cube forging stock, wherein the forging ratio is 1.4;
forging by a 20 th fire, namely heating the forging stock to a forging temperature of 950 ℃, and upsetting and pulling the forging stock along the direction of the C axis to obtain a cube forging stock, wherein the forging ratio is 1.4;
upsetting and finishing the product in the last step for 1 time, heating the forging stock to the forging temperature of 950 ℃, forging to a cake blank with the diameter phi of 500mm multiplied by 260mm, and air cooling after forging;
heating the cake blank to 970 ℃, performing 2-fire die forging on a compressor disc die, wherein the die preheating temperature is 250-300 ℃, the total deformation of die forging is 60%, and performing air cooling after the die forging;
the dimensions of the compressor disc mold cavity are as follows:
a) Diameter d2=690 mm;
b) Maximum thickness D3 of the mold corresponding to the area of the disk body (hub, web and rim) max =201 mm, minimum thickness D2 min ＝42mm：
c) Thickness D of test ring Test ring ＝30mm。
Solid solution aging: the solid solution temperature is Tbeta-25 ℃, the heat preservation time is 1h, the air cooling is carried out, the aging temperature is 595 ℃, the heat preservation is carried out for 8h at the aging temperature, and the air cooling is carried out, thus obtaining the compressor disc.
And (3) analysis and detection:
1. water immersion ultrasonic detection
The compressor disks of comparative example 1 and example 1 were subjected to water immersion ultrasonic testing, with the following results:
TABLE 1
In the table, 38.1mm or less refers to the clutter level in the region within 38.1mm of the depth from the outer surface of the forging, and > 38.1mm refers to the clutter level in the region beyond 38.1mm from the outer surface of the surface.
As shown by the results of the above table, the compressor disk of example 1 has a lower clutter level than the compressor disk of comparative example 1.
2. Tensile Property test
A schematic structural diagram of the compressor disks of example 1 and comparative example 1 is shown in fig. 3. With central axis of rotation Z 3 As an axis, in a radial outside-in direction, the compressor disk comprises: test ring 1, rim 2, web 3 and hub 4.
The test ring 1, rim 2, web 3 and core 4 positions of the compressor disks of comparative example 1 and example 1 were sampled according to ASTM E8/E8M test standard, with the following results:
TABLE 2
σ b ，σ 0.2 ，δ 4 Psi represents room temperature tensile strength, 0.2% yield strength, elongation, and reduction of area respectively. As shown in table 2, the disc of example 1 had a higher tensile strength, a higher 0.2% yield strength, a satisfactory elongation, and a satisfactory reduction of area, as compared to the disc of comparative example 1.
3. Creep performance test
Creep performance test results: the discs of example 1 and comparative example 1 were sampled and inspected at the location of the thinnest thickness cross section in accordance with ASTM E139 test standard. The thinnest thickness is 50mm for example 1 and 30mm for comparative example 1. The detection results are as follows:
comparative example 1:510 ℃/241MPa/35h, creep property epsilon p＝ 0.108％；
Example 1:510 ℃/241MPa/35h, creep property epsilon p＝ 0.074％。
The disc of example 1 has a lower ε than the disc of comparative example 1 p The value, i.e. the better creep properties.
4. Microscopic topography testing
Fig. 4 shows a metallographic photograph of a disc of comparative example 1 sampled at the location of the thinnest thickness section. Fig. 5 shows a metallographic photograph of a position sample of the thinnest thickness section of the disc member of example 1.
As can be seen from a comparison of FIGS. 3 and 4, the disc of comparative example 1 has a primary alpha + beta Rotation Wherein the primary alpha content is about 10% by volume, beta Rotation The precipitated platelets were finer and the disc of example 1 had a primary alpha + beta Rotation Wherein the primary alpha content is about 20%, beta Rotation The precipitated sheet layer is thicker. The advantage of the disc of example 1 over comparative example 1 is that it is ensured that a standard-compliant microstructure and correspondingly better creep performance is obtained at the thinnest cross-section at faster cooling speeds.
Although specific embodiments of the invention have been described in detail, those skilled in the art will appreciate that: many modifications and variations of details may be made to the disclosed embodiments in light of the overall teachings of the invention and remain within its scope. The full scope of the invention is given by the appended claims and any equivalents thereof.
Claims (11)
1. A preparation method of a Ti6242 titanium alloy disc comprises the following steps:
(1) Providing a Ti6242 titanium alloy rod-shaped ingot;
(2) Performing 8-12 times of axial upsetting forging on the rod-shaped cast ingot, wherein the forging temperature of each time is 900-1200 ℃, and the forging ratio is 1.3-1.5;
the axial heading forging includes: upsetting forging and drawing forging are carried out for one time or more times along the axial direction of the forging stock;
(3) Carrying out n-fire-time eight-direction reversing upsetting forging on the product of the last step, wherein n=4-6, and the forging temperature of each fire time is 950-1000 ℃;
(4) Upsetting and forging the product of the previous step for 1-2 times, wherein the forging temperature is 950-1000 ℃ and the forging ratio is 1.3-1.6, so as to obtain cake blanks;
(5) Heating the cake blank to 950-1000 ℃, placing the cake blank into a disc die for die forging, wherein the cavity size of the disc die has the following characteristics: maximum thickness tmax=200-250 mm, minimum thickness tmin=50-80 mm of the cavity region of the corresponding disc body;
(6) Carrying out solid solution and aging treatment on the product of the last step;
wherein the temperature of the solid solution treatment is Tbeta-30 ℃ to Tbeta-20 ℃, the heat preservation time is 1-2 h, the cooling mode is water cooling, and Tbeta is the Ti6242 titanium alloy beta phase transition point temperature;
wherein the temperature of aging treatment is 580-600 ℃, the heat preservation time is 7-9 h, and the cooling mode is air cooling.
2. The method according to claim 1, wherein in the step (1), the titanium alloy rod-shaped ingot has a diameter of 500-1000 mm and a length of 2300-3000mm.
3. The method of claim 1, wherein step (2) comprises performing an axial upsetting forging of the bar ingot 10 firings, the 10 firings of axial upsetting forging comprising:
carrying out A1 fire forging on the rod-shaped cast ingot, wherein the forging temperature is 1150-1200 ℃, the forging mode is one forging and one drawing, and the forging ratio is 1.3-1.5;
forging the product in the previous step by using an A2 fire at the forging temperature of 1100-1150 ℃ in a two-upsetting and two-pulling mode, wherein the forging ratio is 1.3-1.5;
forging the product in the previous step by the A3 fire at 1050-1100 ℃ in a two-upsetting and two-pulling mode with the forging ratio of 1.3-1.5;
forging the product of the last step by A4 fire, wherein the forging temperature is 950-990 ℃, the forging mode is upsetting and pulling, the forging ratio is 1.3-1.5, and chamfering is carried out on the forging stock after the forging is finished;
forging the product in the last step by the A5 fire at 1050-1100 ℃ in a two-upsetting and two-pulling mode with the forging ratio of 1.3-1.5;
forging the product of the previous step by firing A6, A7 and A8 in sequence, wherein the forging temperature is 950-1000 ℃, the forging modes are heading and pulling, and the forging ratio is 1.3-1.5;
and (3) forging the product in the last step by sequentially carrying out A9 and A10 fires, wherein the forging temperature is 950-1000 ℃, the forging mode is drawing, and the deformation of drawing is 35-45%.
4. The method of claim 1, wherein in step (3), the n-shot eight-way reverse upsetting forging has the following characteristics:
the eighth direction reversing upsetting forging of the 1 st firing time comprises the following steps: heating the forging stock to the forging temperature of 950-980 ℃, firstly upsetting and deforming along the axial direction, wherein the forging ratio is 1.8-2, then radially drawing the forging stock, wherein the forging ratio is 1.5-1.6, obtaining a square section forging stock, returning to the furnace for heat preservation, radially upsetting the forging stock, wherein the forging ratio is 1.8-2, and then axially drawing the forging stock, wherein the forging ratio is 1.8-2, thus obtaining an octagonal section forging stock;
in the eight-direction forging of the 2 nd to n-1 th heats, the forging of each heat includes: heating the forging stock to the forging temperature of 950-980 ℃, upsetting and deforming the forging stock along the axial direction, wherein the forging ratio is 1.7-1.9, then drawing the forging stock along the radial direction, wherein the forging ratio is 1.6-1.8 to obtain a square section forging stock, returning to the furnace for heat preservation, upsetting the forging stock along the radial direction, wherein the forging ratio is 1.8-2, and drawing the forging stock along the axial direction to obtain an octagon section forging stock, wherein the forging ratio is 1.8-2;
the eighth forging of the nth firing time includes: heating the forging stock to the forging temperature of 950-980 ℃,
firstly upsetting and deforming along the axial direction, wherein the forging ratio is 1.7-1.9, then drawing the forging stock along the radial direction, wherein the forging ratio is 1.6-1.8, obtaining a square section forging stock, returning to the furnace for heat preservation, upsetting the forging stock along the radial direction, wherein the forging ratio is 1.8-2, and then axially rounding, wherein the forging ratio is 1-1.2, thus obtaining the round section forging stock.
5. The method of claim 4, wherein in step (3), n = 5.
6. The method according to claim 3 or 4, wherein in the step (3), the temperature of the tempering heat preservation is 950-1000 ℃ and the time is 180-270 min.
7. The method of claim 1, wherein in the step (4), the size of the biscuit is 400 to 600mm in diameter and 250 to 350mm in thickness.
8. The method of claim 1, wherein step (5) has one or more of the following features:
-the diameter of the disc mould cavity is 600-1000 mm;
the number of times of die forging is 2, and the total deformation of the die forging is 40% -70%;
the disc mold is a preheated disc mold, and the preheating temperature is 250-300 ℃.
9. The method of claim 1, wherein the forging is cooled in an air-cooled manner after the forging of each firing.
10. The method of claim 1, wherein the titanium alloy disc is an aircraft engine compressor disc.
11. A titanium alloy disc, prepared by the method of any one of claims 1-10.
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| CN102418060A (en) * | 2011-12-12 | 2012-04-18 | 西部钛业有限责任公司 | Processing method for TC4 titanium alloy large-sized bar |
| CN106734796A (en) * | 2016-12-14 | 2017-05-31 | 西部超导材料科技股份有限公司 | The engine forging method of high temperature resistant titanium alloy large scale rod bar |
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| CN111235506A (en) * | 2020-03-19 | 2020-06-05 | 中国科学院金属研究所 | Thermal processing technology of TC25G titanium alloy forging |
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| US7008491B2 (en) * | 2002-11-12 | 2006-03-07 | General Electric Company | Method for fabricating an article of an alpha-beta titanium alloy by forging |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102418060A (en) * | 2011-12-12 | 2012-04-18 | 西部钛业有限责任公司 | Processing method for TC4 titanium alloy large-sized bar |
| CN106734796A (en) * | 2016-12-14 | 2017-05-31 | 西部超导材料科技股份有限公司 | The engine forging method of high temperature resistant titanium alloy large scale rod bar |
| CN109622833A (en) * | 2018-12-11 | 2019-04-16 | 陕西宏远航空锻造有限责任公司 | A kind of structural homogeneity control method of big thickness Ti-6Al-2Sn-4Zr-2Mo alloy forged piece |
| CN111235506A (en) * | 2020-03-19 | 2020-06-05 | 中国科学院金属研究所 | Thermal processing technology of TC25G titanium alloy forging |
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