CN116900218A - TiAl alloy and forging method thereof - Google Patents
TiAl alloy and forging method thereof Download PDFInfo
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- CN116900218A CN116900218A CN202310781266.3A CN202310781266A CN116900218A CN 116900218 A CN116900218 A CN 116900218A CN 202310781266 A CN202310781266 A CN 202310781266A CN 116900218 A CN116900218 A CN 116900218A
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- 238000005242 forging Methods 0.000 title claims abstract description 157
- 239000000956 alloy Substances 0.000 title claims abstract description 124
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 122
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 99
- 238000000034 method Methods 0.000 title claims abstract description 62
- 238000010438 heat treatment Methods 0.000 claims abstract description 35
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 15
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 15
- 238000003723 Smelting Methods 0.000 claims abstract description 13
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 12
- 238000012545 processing Methods 0.000 claims abstract description 12
- 238000010304 firing Methods 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 230000001186 cumulative effect Effects 0.000 claims description 2
- 229910052727 yttrium Inorganic materials 0.000 claims description 2
- 230000000694 effects Effects 0.000 abstract description 2
- 238000004321 preservation Methods 0.000 description 17
- 238000003825 pressing Methods 0.000 description 13
- 238000005266 casting Methods 0.000 description 9
- 230000006698 induction Effects 0.000 description 7
- 238000002844 melting Methods 0.000 description 7
- 230000008018 melting Effects 0.000 description 7
- 239000000463 material Substances 0.000 description 5
- 230000003647 oxidation Effects 0.000 description 5
- 238000007254 oxidation reaction Methods 0.000 description 5
- 238000010275 isothermal forging Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 229910001182 Mo alloy Inorganic materials 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229920000742 Cotton Polymers 0.000 description 1
- 229910010413 TiO 2 Inorganic materials 0.000 description 1
- 229910001080 W alloy Inorganic materials 0.000 description 1
- 230000002860 competitive effect Effects 0.000 description 1
- 239000004020 conductor Substances 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000000881 depressing effect Effects 0.000 description 1
- 230000000994 depressogenic effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 230000005674 electromagnetic induction Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
- B21J1/003—Selecting material
-
- 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
- B21J5/008—Incremental forging
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Forging (AREA)
Abstract
The invention discloses a TiAl alloy and a forging method thereof, belonging to the technical field of alloy material processing, wherein the method comprises the following steps: smelting to prepare a TiAl alloy ingot, wherein the main system of the TiAl alloy is Ti-Al-Mn-X, and X is at least one of Mo, W and Nb elements; heating and heat-preserving the TiAl alloy cast ingot; and in a non-wrapping and non-isothermal environment, selecting a forging mode according to the length-diameter ratio of the TiAl alloy ingot, and processing the TiAl alloy ingot to a preset size. The invention forges the TiAl alloy under the non-isothermal condition without a sheath, thereby realizing the technical effect of reducing the forging cost of the TiAl alloy.
Description
Technical Field
The invention relates to the technical field of alloy material processing, in particular to a TiAl alloy and a forging method thereof.
Background
Compared with the traditional Fe and Ni-based alloy, the TiAl alloy has the characteristics of low density, high specific strength, high specific modulus, good high-temperature fatigue resistance, creep resistance, corrosion resistance and the like, and is a tip strategic structural material with great competitive power in the engine fields of aerospace, advanced ships, unmanned aerial vehicles, automobiles and the like.
Because TiAl alloy belongs to intermetallic compound, effective hot working window is narrow, and the requirements on deformation temperature and deformation rate in actual hot forging deformation process are very strict, namely special hot forging deformation process such as near isothermal or sheath is generally required, and the problem of high forging cost exists.
Disclosure of Invention
The invention mainly aims to provide a TiAl alloy and a forging method thereof, and aims to solve the problem of high forging cost caused by the fact that the existing TiAl alloy needs to adopt a special hot forging deformation process.
In order to achieve the above object, the present invention provides a forging method of a TiAl alloy, comprising:
smelting to prepare a TiAl alloy ingot, wherein the main system of the TiAl alloy is Ti-Al-Mn-X, and X is at least one of Mo, W and Nb elements;
heating and heat-preserving the TiAl alloy cast ingot;
forging the TiAl alloy cast ingot in a non-wrapping and non-isothermal environment, and processing the TiAl alloy cast ingot to a preset size.
Optionally, the composition of the TiAl alloy ingot comprises 41.0% -46.0% of Al, 1.0% -4.0% of Mn, 0.1% -6.0% of X, 0.1% -0.3% of B, 0.1% -0.3% of C, 0% -0.3% of Si, 0-0.1% of Y, and the balance being Ti.
Optionally, the X is 2.0% -3.5% Nb and/or 0.3% -1.5% Mo and/or 0.1% -1.0% W.
Optionally, the elemental composition of Ti, al, and Mn in the TiAl alloy ingot deviates less than 0.2wt.%, and W, mo and Nb deviate less than 0.1wt.%.
Optionally, impurity elements O, N and H are further included in the TiAl alloy ingot, wherein the content of O element is less than 0.08wt.%, the content of N element is less than 0.0020wt.%, and the content of H element is less than 0.0020wt.%.
Optionally, the step of forging the TiAl alloy ingot comprises:
if the length-diameter ratio of the TiAl alloy cast ingot is larger than 1.5, directly drawing and forging the TiAl alloy cast ingot;
and if the length-diameter ratio of the TiAl alloy cast ingot is smaller than or equal to 1.5, upsetting forging or upsetting and then drawing forging are carried out on the TiAl alloy cast ingot.
Alternatively, the drawing forging and upsetting forging employ a forging press having a pressing speed of 10 to 60mm/s.
Optionally, the forging mode is multi-fire multi-pass forging, and the final forging temperature of each firing is more than 1100 ℃.
Optionally, the forging cumulative deformation of the TiAl alloy ingot is greater than 50%.
In addition, in order to achieve the above purpose, the present invention also provides a TiAl alloy, which is prepared by adopting the forging method of the TiAl alloy as described above.
According to the TiAl alloy and the forging method thereof, provided by the invention, ti-Al-Mn-X is adopted as an alloy main system, wherein X is at least one of Mo, W and Nb, so that the thermal deformation of the TiAl alloy in a high-temperature environment is improved, the thermal processing window of the TiAl alloy is widened, and meanwhile, the good oxidation resistance of the TiAl alloy can be ensured, so that the requirement on forging conditions can be reduced, the alloy forging meeting the use requirement is obtained by adopting a simpler non-wrapping and non-isothermal forging mode, and the forging cost is greatly reduced.
Drawings
FIG. 1 is a schematic flow diagram of one embodiment of a forging method of a TiAl alloy of the present invention;
FIG. 2 is an external view of a cast bar before forging in accordance with example 1 of the present invention;
FIG. 3 is a schematic illustration of a heating scenario for a casting bar according to example 1 of the present invention;
FIG. 4 is a schematic illustration of a first hot forging scenario for a cast rod according to example 1 of the present invention;
FIG. 5 is a schematic illustration of a second hot forging scenario for a cast rod according to example 1 of the present invention;
FIG. 6 is an external view of a cast rod according to example 1 of the present invention after forging;
FIG. 7 is an external view of an ingot before forging in example 2 of the present invention;
FIG. 8 is an external view of a 1/2 ingot in example 2 of the present invention;
FIG. 9 is a schematic illustration of a fifth firing of the ingot of example 2 of the present invention;
fig. 10 is an external view of an ingot after forging in example 2 of the present invention.
The achievement of the objects, functional features and advantages of the present invention will be further described with reference to the accompanying drawings, in conjunction with the embodiments.
Detailed Description
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.
Because TiAl alloy belongs to intermetallic compound, effective hot working window is narrow, and the requirement on deformation temperature and deformation rate in actual hot forging deformation process is very harsh, namely, special hot forging deformation process such as near isothermal or sheath is generally required. As a processing method suitable for hot forging deformation of Ti-48Al-2Cr-2Nb alloy, the double conditions of Q235 sheath with the thickness of 5mm and near isothermal temperature are simultaneously satisfied, and the strain rate of the hot forging deformation is only 0.3mm/s. The hot forging deformation method has high requirements on forging equipment conditions, and has the problems of complicated working procedures, low efficiency, high cost and the like, so that the commercial application process of the TiAl alloy deformation piece is limited to a great extent.
In order to reduce the manufacturing cost of the TiAl alloy parts, development of a process method capable of realizing low-cost hot forging deformation of the TiAl alloy is needed. Around the theme, a method for carrying out hot forging deformation on the TiAl alloy under the non-wrapping condition appears, so that the forging deformation cost of the TiAl alloy is reduced to a certain extent, but the problems of complicated working procedures, low deformation efficiency and the like still exist in the forging deformation of the TiAl alloy to a great extent due to the fact that blank preheating treatment is required to be added to the TiAl alloy, glass lubricating powder with the thickness of 2-3 mm is rolled and coated on the alloy after the pretreatment, and working procedures such as a heat preservation cotton layer are required.
The invention aims to provide a simple, quick and universal low-cost forging method for the TiAl alloy, namely a forging deformation method without blank pretreatment and isothermal sheath, which can exert a powerful promotion effect on large-scale application of the TiAl alloy.
The embodiment of the invention provides a forging method of TiAl alloy, and referring to FIG. 1, FIG. 1 is a schematic flow chart of one embodiment of the forging method of TiAl alloy.
In this embodiment, the forging method of the TiAl alloy includes:
s10, smelting to prepare a TiAl alloy cast ingot, wherein a main system of the TiAl alloy is Ti-Al-Mn-X, wherein X is at least one of Mo, W and Nb elements;
the TiAl alloy cast ingot can be smelted by adopting a primary vacuum induction or a vacuum induction and vacuum self-consumption process. Vacuum induction refers to a metallurgical method for smelting by generating vortex heating furnace burden in a metal conductor by electromagnetic induction under a vacuum condition, and alloy components can be accurately controlled. The vacuum consumable smelting refers to a smelting method that under vacuum, a material to be melted is used as one electrode, a water-cooled copper crucible is used as the other electrode, an arc is started between the two electrodes, the material to be melted is melted by the electric arc at high temperature and is dripped into the crucible, and the material is melted gradually and condensed gradually to form an ingot. The smelting method is suitable for smelting TiAl alloy ingots.
In some possible embodiments, the composition of the TiAl alloy ingot comprises, in atomic percent, 41.0% -46.0% Al, 1.0% -4.0% Mn, 0.1% -6.0% X, 0.1% -0.3% B, 0.1% -0.3% C, 0% -0.3% Si, 0-0.1% Y, the balance being Ti. X may be 2.0% -3.5% Nb and/or 0.3% -1.5% Mo and/or 0.1% -1.0% W, i.e., any one or a combination of several of the above elements.
In the case where the main system is Ti-Al-Mn-X, X may be any one or a combination of several of Mo, W and Nb elements. Mn is a beta-phase stabilizing element, which is favorable for forging deformation of TiAl alloy under conventional conditions, however, mn can oxidize as same as Ti and Al under high-temperature oxidation environment, so that the oxidation corrosion of a matrix is caused. So Mo, W or Nb element is added to promote the diffusion of Al in the matrix and inhibit TiO 2 Can improve the high-temperature oxidation resistance of the alloy. In the case where X is a different element, the proportion of X in the alloy is slightly different. In spite of Mo, W or Nb elementsThe diffusion of Al in the matrix can be promoted, but too high an addition amount may have some influence. For example, when the content of Nb element is high, brittle ω phase (Ti 4 Al 3 Nb), and the high Nb content TiAl alloy has poor hot workability, and even if high temperature hot working can be achieved, it is often required to perform the working under severe conditions of sheath or isothermal, and the working process is complicated. Therefore, the composition of the X element needs to be controlled within a proper range, so that the hot workability of the TiAl alloy is ensured.
In some possible embodiments, the elemental composition of Ti, al, and Mn in the TiAl alloy ingot varies by less than 0.2wt.%, the elemental composition of W, mo and Nb varies by less than 0.1wt.%; impurity elements O, N and H are also included in the TiAl alloy cast ingot, wherein the content of O element is less than 0.08wt.%, the content of N element is less than 0.0020wt.%, and the content of H element is less than 0.0020wt.%.
The component deviation of elements can be controlled in the smelting process by regulating and controlling the process and parameters. So that the proportion of alloy components to theoretical design is as close as possible. For example, the melting speed of the furnace burden in the smelting furnace can be gradually increased, the heating power is gradually increased, the smooth melting and full degassing of the furnace burden are ensured, the heating power can be properly increased in the middle and later period of melting, the melting speed is increased, and the melting time is shortened. As another example, the late melting and early refining phases allow the charge to boil sufficiently to deoxidize, denitrify, dehydrogenate, and remove inclusions.
Step S20, heating and heat-preserving the TiAl alloy cast ingot;
the microstructure can be regulated and controlled by the heating and heat preservation treatment after smelting. The temperature of the heating and heat preserving treatment can be selected to be the temperature of an alpha+beta two-phase region, and the heat preserving time is 10-60 minutes at 1300-1380 ℃. The temperature is based on the temperature of the cross section of the cast ingot reaching 1300-1380 ℃ uniformly. The set heat preservation temperature and heat preservation time of the cast ingots with different sizes are different. Because the length-diameter ratio of the cast ingot is different, the time required for uniform heating is different under the condition of the same heat preservation temperature, so that the temperature and the time can be set according to the length-diameter ratio of the cast ingot.
And step S30, forging the TiAl alloy cast ingot in a non-isothermal environment without a sheath, and processing the TiAl alloy cast ingot to a preset size.
Sheath processing refers to a process of processing metal within a shaped sheath, often in combination with a hot isostatic pressing process. Isothermal forging is forging in which the mold is at substantially the same temperature as the process of the forming member, with a mold heating and temperature control device. The forging in this example can be performed in an atmospheric environment without using the above-described process. The forging in this embodiment may be performed using a forging press, with the ingot placed in the working position of the forging press, and with the forging hammer depressed to press the ingot to a certain size. The pressing speed of the forging press may be 10-60mm/s. In the forging process, the microstructure inside the cast ingot also changes on a microscopic scale, the depressing speed is controlled within a proper range, the alloy performance can be improved, and the problems of cracking and the like are avoided.
In some possible embodiments, if the aspect ratio of the TiAl alloy ingot is greater than 1.5, then directly drawing the TiAl alloy ingot; if the length-diameter ratio of the TiAl alloy cast ingot is less than or equal to 1.5, upsetting forging or upsetting and then drawing forging are carried out on the TiAl alloy cast ingot. The TiAl alloy ingots can be prepared in shapes of different aspect ratios. The aspect ratio refers to the ratio between the lengthwise dimension of the ingot and the radial dimension perpendicular to the lengthwise direction. The large aspect ratio ingot may take the shape of a cast rod, which is relatively slender. Under the condition that the length-diameter ratio of the cast ingot is larger than 1.5, the length of the cast rod is further increased by using an elongation forging process, and the bar TiAl alloy is produced. Under the condition that the length-diameter ratio of the cast ingot is less than or equal to 1.5, the cast ingot can be directly processed into a plate through upsetting forging, or the cast ingot can be firstly subjected to upsetting forging and then processed to a preset size through drawing forging. The preset size refers to the size of the finished material piece, and can be determined according to actual requirements. The upsetting forging can crush columnar crystals in the alloy, optimize microstructure and improve the performance of the alloy.
The equipment used for drawing forging and upsetting forging can be a forging press, and the pressing speed of the forging press in the forging process is 10-60mm/s. The forging mode is multi-fire multi-pass forging, and the final forging temperature of each firing is more than 1100 ℃. After the ingot is forged by one fire, the ingot is returned to the furnace and heated to 1300-1380 ℃, the temperature is kept for 5-20 minutes, the subsequent forging is carried out according to the forging parameters same as the previous fire until the forging reaches the designed finished product size, and the total deformation of the forging after the deformation of multiple passes is more than 50%. During forging, a fire refers to heating once, and a pass refers to the number of times an ingot is processed. The forging is a process of processing a large-volume cast ingot into a small-volume forging, in the embodiment, under the conditions that the temperature is enough and the deformation of the forging meets the requirements, multi-pass forging can be performed every time of fire, the heating temperature is fully utilized, and the heating times are reduced. Generally, one-fire multi-pass forging can be performed in the early stage of forging, and one-fire one-pass forging can also be performed when the temperature loss is large in the subsequent processing.
In the embodiment, ti-Al-Mn-X is adopted as an alloy main system, wherein X is at least one of Mo, W and Nb, so that the thermal deformation of the TiAl alloy in a high-temperature environment is improved, the thermal processing window of the TiAl alloy is widened, and meanwhile, the good oxidation resistance of the TiAl alloy can be ensured, therefore, the requirement on forging conditions can be reduced, the alloy forging meeting the use requirement is obtained after forging by adopting a simpler non-sheath and non-isothermal forging mode, and the forging cost is greatly reduced.
Example 1
Smelting by using a vacuum induction furnace21kg of heavy alloy cast bars. FIG. 2 is an external view of a casting bar before forging, in which an open shrinkage cavity in the upper portion of the casting bar is cut, and the length of the casting bar after cutting the shrinkage cavity is 980mm, as shown in FIG. 2. The alloy system is Ti-43Al-2Mn-0.5Mo (at.%), the impurity content O in the alloy is 0.062wt.%, N is 0.0018wt.%, and H is 0.0010wt.%.
The resulting cast rod was placed in an induction furnace, brought to 1350 ℃ in one hour and held for 30 minutes, and then the heated alloy cast rod was forged using a hydraulic rapid forging machine.
First firing: original dimensionsAnd (5) casting a rod. FIG. 3 is a schematic view of a scene of heating a casting rod, as shown in FIG. 3, in which one end of the rod is placed into an induction heating furnace in the heating process, and the temperature is quickly raised to 1350 ℃ and maintained for 20 minutes. FIG. 4 is a schematic view of a first forging scene of a casting rod, as shown in FIG. 4, a heated as-cast Ti-Al-Mn-Mo alloy rod is placed on a 60t hydraulic forging machine, a 4Cr5MoSiV1 alloy hammer head is used for forging from a heating end for a plurality of times with small deformation, the center of the kneaded rod is loose, the pressing speed is 50mm/s, a square ingot with the size of 68mm multiplied by 65mm is forged, the length of 670mm is obtained after forging, the heated as-cast Ti-Al-Mn-Mo alloy rod is cut off, and then the heated and heat-preserved for 10 minutes after being quickly returned to a furnace.
Second firing: FIG. 5 is a schematic view of a second-pass forging scene of a cast rod, as shown in FIG. 5, a square ingot with the thickness of 68mm multiplied by 65mm is continuously forged after heat preservation at 1350 ℃ for 10 minutes, the pressing speed is 50mm/s, the square ingot with the thickness of 43mm multiplied by 46mm is forged after multiple pressing, the length is 1500mm, and then the cast rod is cut into three sections of bars with the length of about 500mm, the three sections of bars are quickly returned to a furnace for heating, and the temperature is raised to the forging temperature and kept for 10 minutes.
Third firing: and (3) continuously forging square ingots with the speed of 50mm/s and the length of 640mm at the temperature of 1350 ℃ for 10 minutes, forging square ingots with the speed of 43mm multiplied by 46mm until the square ingots with the speed of 37mm multiplied by 42mm are obtained, then quickly returning to the furnace for heating, heating to the forging temperature, and preserving the heat for 5 minutes.
Fourth forging: the square bar with the thickness of 37mm multiplied by 42mm after heat preservation is forged and angled, and finally the square bar with the thickness of approximately 40mm multiplied by 40mm is obtained, as shown in figure 6.
The elongation properties of the non-jacketed TiAl alloy forged bars prepared in example 1 range from: tensile Strength R at room temperature m =900 to 950MPa, yield strength R p0.2 700-800 MPa, elongation a=1-2%; tensile Strength R at 800 ℃ m 550-600 MPa, yield strength R p0.2 300-350 MPa, and elongation a=10-15%.
Example 2
FIG. 7 is an external view of the ingot before forging, as shown in FIG. 7, the vacuum induction melting of a 5kg heavy Ti-42Al-3.5Mn-0.8W-0.2B-0.1Y alloy ingot. The impurity element contents in the ingot were 0.0570wt.% O, 0.0016wt.% N, and 0.0010wt.% H, respectively, and the alloy ingot was cut in half, and the lower half ingot (1/2 ingot) was left for forging, as shown in fig. 8.
The resulting ingot was placed in a muffle furnace, brought to 1310 ℃ in one hour and kept warm for 10 minutes, and then the heated alloy ingot was forged using a hydraulic rapid forging machine.
First firing: original dimensionsAnd (3) reversely conical 1/2 ingot casting, placing the heated Ti-Al-Mn-W alloy ingot casting on a 60t hydraulic forging machine, performing drawing forging by using a 4Cr5MoSiV1 alloy hammer head, forging into square ingots with the size of 75mm multiplied by 65mm multiplied by 150mm at the pressing speed of 50mm/s, and then quickly returning to a furnace for heating and preserving heat for 10 minutes.
Second firing: upsetting and forging the square ingot with the thickness of 75mm multiplied by 65mm multiplied by 150mm after 10 minutes of heat preservation at 1310 ℃, wherein the pressing speed is 50mm/s, forging to square ingot with the thickness of 90mm multiplied by 100mm multiplied by 80mm, then placing the square ingot into a heating furnace for rapid heating, and heating to the forging temperature for 10 minutes.
Third firing: upsetting and forging 90mm multiplied by 100mm multiplied by 80mm square ingots subjected to heat preservation at 1310 ℃ for 10 minutes after drawing, wherein the pressing speed is 50mm/s, upsetting the square ingots with the dimensions of 90mm multiplied by 75mm multiplied by 95mm, and then returning to a furnace for rapid heating, and heating to the forging temperature for 10 minutes.
Fourth forging: drawing and forging 90mm multiplied by 100mm multiplied by 80mm square ingots after 10 minutes of heat preservation at 1310 ℃, wherein the pressing speed is 50mm/s, forging to 130mm multiplied by 90mm multiplied by 60mm square ingots, then returning to a furnace for rapid temperature rise, and heating to the forging temperature for heat preservation for 5 minutes.
Fifth firing: drawing and forging the square ingot with the thickness of 130mm multiplied by 90mm multiplied by 60mm after heat preservation at 1310 ℃ for 5 minutes, wherein the pressing speed is 50mm/s, and after forging to the square ingot with the thickness of 190mm multiplied by 100mm multiplied by 40mm, returning to a furnace for quickly heating, and heating to the forging temperature for heat preservation for 5 minutes as shown in fig. 9.
Sixth forging: and (3) performing drawing forging on a square ingot with the temperature of 190mm multiplied by 100mm multiplied by 40mm after heat preservation for 5 minutes at 1310 ℃, forging to a plate with the pressure reduction speed of 240mm multiplied by 105mm multiplied by 30mm, returning to a furnace, quickly heating, and heating to the forging temperature for heat preservation for 5 minutes.
Seventh forging: drawing and forging the 240mm multiplied by 105mm multiplied by 30mm plate after heat preservation for 5 minutes at 1310 ℃, wherein the pressing speed is 50mm/s, forging to 285mm multiplied by 110mm multiplied by (20-27) mm plate, then returning to the furnace and rapidly heating, and heating to the forging temperature and preserving heat for 5 minutes.
Eighth forging: the plate was drawn and forged to a plate of 285mm×110mm× (20-27) mm after heat preservation at 1310℃for 5 minutes at a pressing speed of 50mm/s, and forged to a plate of 310mm×110mm× (20-15).
The elongation properties of the non-jacketed TiAl alloy forging plate prepared in example 2 were in the range of: (1) Transverse tensile test specimen, tensile Strength R at room temperature m =820 to 850MPa, yield strength R p0.2 770-800 MPa, elongation a=0.8-1.5%; tensile Strength R at 800 ℃ m 550-600 MPa, yield strength R p0.2 300-350 MPa, and elongation a=20-30%. (2) Tensile strength R of longitudinal tensile sample at room temperature m =950 to 1000MPa, yield strength R p0.2 870-900 MPa, elongation a=1-1.5%; tensile Strength R at 800 ℃ m 600-650 MPa, yield strength R p0.2 =350 to 400MPa, elongation a=10 to 15%.
The same process is adopted for the remaining two ingots to obtain a finished forging plate, as shown in fig. 10.
It should be noted that, in this document, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or system that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or system. Without further limitation, an element defined by the phrase "comprising one … …" does not exclude the presence of other like elements in a process, method, article, or system that comprises the element.
The foregoing embodiment numbers of the present invention are merely for the purpose of description, and do not represent the advantages or disadvantages of the embodiments.
The foregoing description is only of the preferred embodiments of the present invention, and is not intended to limit the scope of the invention, but rather is intended to cover any equivalents of the structures or equivalent processes disclosed herein or in the alternative, which may be employed directly or indirectly in other related arts.
Claims (10)
1. A forging method of a TiAl alloy, characterized in that the forging method of the TiAl alloy comprises the steps of:
smelting to prepare a TiAl alloy ingot, wherein the main system of the TiAl alloy is Ti-Al-Mn-X, and X is at least one of Mo, W and Nb elements;
heating and heat-preserving the TiAl alloy cast ingot;
forging the TiAl alloy cast ingot in a non-wrapping and non-isothermal environment, and processing the TiAl alloy cast ingot to a preset size.
2. The forging method of a TiAl alloy according to claim 1, wherein the composition of the TiAl alloy ingot comprises, in atomic percent, 41.0% -46.0% Al, 1.0% -4.0% Mn, 0.1% -6.0% X, 0.1% -0.3% B, 0.1% -0.3% C, 0% -0.3% Si, 0-0.1% Y, the balance being Ti.
3. A forging method of a TiAl alloy according to claim 2, wherein X is 2.0% -3.5% Nb and/or 0.3% -1.5% Mo and/or 0.1% -1.0% W.
4. A forging method of a TiAl alloy according to claim 2, wherein the elemental composition deviation of Ti, al and Mn in the TiAl alloy ingot is less than 0.2wt.%, and the elemental composition deviation of W, mo and Nb is less than 0.1wt.%.
5. The forging method of a TiAl alloy according to claim 4, wherein the TiAl alloy ingot further comprises impurity elements O, N and H, wherein the O element content is less than 0.08wt.%, the N element content is less than 0.0020wt.%, and the H element content is less than 0.0020wt.%.
6. The method of forging a TiAl alloy of claim 1, wherein the step of forging the TiAl alloy ingot comprises:
if the length-diameter ratio of the TiAl alloy cast ingot is larger than 1.5, directly drawing and forging the TiAl alloy cast ingot;
and if the length-diameter ratio of the TiAl alloy cast ingot is smaller than or equal to 1.5, upsetting forging or upsetting and then drawing forging are carried out on the TiAl alloy cast ingot.
7. A forging method of a TiAl alloy according to claim 6, wherein the drawing forging and upsetting forging employ a forging press having a reduction speed of 10 to 60mm/s.
8. The forging method of a TiAl alloy according to claim 6, wherein the forging mode is multi-firing multi-pass forging, and the final forging temperature per firing is greater than 1100 ℃.
9. A forging method for a TiAl alloy according to any one of claims 1 to 8, wherein the forging cumulative deformation of the TiAl alloy ingot is greater than 50%.
10. A TiAl alloy prepared by a forging method according to any one of claims 1 to 9.
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