CN113416879A - Titanium-aluminum alloy and preparation method thereof - Google Patents
Titanium-aluminum alloy and preparation method thereof Download PDFInfo
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- CN113416879A CN113416879A CN202110734489.5A CN202110734489A CN113416879A CN 113416879 A CN113416879 A CN 113416879A CN 202110734489 A CN202110734489 A CN 202110734489A CN 113416879 A CN113416879 A CN 113416879A
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- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 title claims abstract description 26
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title abstract description 13
- 238000005245 sintering Methods 0.000 claims abstract description 25
- 239000000843 powder Substances 0.000 claims abstract description 18
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 8
- 238000002490 spark plasma sintering Methods 0.000 claims abstract description 8
- 239000002994 raw material Substances 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 230000002902 bimodal effect Effects 0.000 claims abstract description 3
- 239000002245 particle Substances 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims 5
- 239000000956 alloy Substances 0.000 abstract description 42
- 230000003647 oxidation Effects 0.000 abstract description 42
- 238000007254 oxidation reaction Methods 0.000 abstract description 42
- 229910045601 alloy Inorganic materials 0.000 abstract description 40
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 11
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract description 6
- 238000002474 experimental method Methods 0.000 abstract description 4
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 abstract description 4
- 239000010936 titanium Substances 0.000 abstract description 3
- 238000005336 cracking Methods 0.000 abstract description 2
- 230000035882 stress Effects 0.000 abstract 1
- 230000008646 thermal stress Effects 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 29
- 230000000052 comparative effect Effects 0.000 description 9
- 238000002156 mixing Methods 0.000 description 8
- 230000004584 weight gain Effects 0.000 description 8
- 235000019786 weight gain Nutrition 0.000 description 8
- 238000005520 cutting process Methods 0.000 description 7
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 6
- DKGAVHZHDRPRBM-UHFFFAOYSA-N Tert-Butanol Chemical group CC(C)(C)O DKGAVHZHDRPRBM-UHFFFAOYSA-N 0.000 description 6
- 239000011651 chromium Substances 0.000 description 6
- 229910052593 corundum Inorganic materials 0.000 description 6
- 229910001845 yogo sapphire Inorganic materials 0.000 description 6
- 238000004140 cleaning Methods 0.000 description 5
- 238000000227 grinding Methods 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 238000000498 ball milling Methods 0.000 description 4
- 238000001035 drying Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000001878 scanning electron micrograph Methods 0.000 description 4
- 230000003068 static effect Effects 0.000 description 4
- 244000137852 Petrea volubilis Species 0.000 description 3
- 229910010038 TiAl Inorganic materials 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 238000012669 compression test Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000001186 cumulative effect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 238000009777 vacuum freeze-drying Methods 0.000 description 2
- 238000005303 weighing Methods 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 229910002064 alloy oxide Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000003556 assay Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000012937 correction Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- UIWYJDYFSGRHKR-UHFFFAOYSA-N gadolinium atom Chemical compound [Gd] UIWYJDYFSGRHKR-UHFFFAOYSA-N 0.000 description 1
- 238000011534 incubation Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 229910002059 quaternary alloy Inorganic materials 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 229910002058 ternary alloy Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
Abstract
The invention discloses a titanium-aluminum alloy, which belongs to the technical field of alloy materials, and comprises the following elements in atomic percent: 46 to 49 percent of Ti, 46 to 49 percent of A1, 1.5 to 2.5 percent of Cr, 1.5 to 2.5 percent of Nb and 0.15 to 0.3 percent of Gd; the invention also discloses a preparation method of the titanium-aluminum alloy, which comprises the steps of taking prealloyed Ti-48Al-2Cr-2Nb and elemental Gd powder as raw materials, and sintering by adopting a plasma sintering method to obtain a bimodal structure with Gd-rich phase distributed at the boundaries of powder particles; spark plasma sintering is preferably employed; according to the invention, by adding a proper amount of Gd and combining a spark plasma sintering process, the room-temperature ultimate compressive strength of the alloy is improved, an alumina film generated by high-temperature oxidation is more compact, the growth of titanium oxide is inhibited, the thickness of the oxide film is reduced, the growth stress and the thermal stress in the oxide film are reduced, and the cracking of the oxide film is prevented; after the alloy is subjected to an isothermal oxidation experiment at 800 ℃ for 500 hours, all Gd-containing alloys are not peeled off or cracked, and the Gd is added to improve the oxidation resistance of the alloy.
Description
Technical Field
The invention relates to the field of alloy materials, in particular to a titanium-aluminum alloy with excellent mechanical property and high-temperature oxidation resistance and a preparation method thereof.
Background
Titanium-aluminum-based alloys have excellent mechanical properties such as low density, high specific strength and excellent creep resistance, and have been used in aerospace engineering in recent years to replace nickel-based superalloys as high temperature structural materials. TiAl alloys have been used in 650-750 ℃ structures of new-generation turbine engines, and particularly Ti-48Al-2Cr-2Nb alloys are still widely used as 'classic' titanium-aluminum alloys due to the good comprehensive properties thereof after years of development.
Nevertheless, the application of titanium-aluminum alloys is still limited due to their poor machinability, and in order to improve the plasticity of titanium-aluminum alloys, alloying elements are usually added to form ternary or quaternary alloys, such as chromium and manganese, etc. However, Y.Garip et Al in the description of the cycle oxidation catalyst of the Cr/Mn/Mo alloyed Ti-48Al-based assays prepared by ECAS (Journal of Alloys and Compounds [ J]2019) to point out: due to the doping effect, the addition of Cr having a lower valence than Ti introduces oxygen vacancies, resulting in TiO2The growth rate is increased, which is not favorable for the oxidation resistance of the alloy.
Meanwhile, L.Mentis et al, in the examination of Oxidation behavior and related microstructural changes of two β 0-phase containing TiAl alloys between 600 ℃ and 900 ℃ (correction Science [ J ], 2021): nb is advantageous in high temperature oxidation because it has a positive doping effect, but the effectiveness of 2 at.% Nb is not sufficient to offset the negative effects of chromium. And the weight gain of the GE4822 alloy is very low and can be ignored when the alloy is oxidized at 600 ℃ and 700 ℃ for 100 hours, and the oxidation is very serious when the alloy is oxidized at 800 ℃. This also indicates that the alloy has a very limited application at 800 c.
Similarly, Kai Zhang et Al, studying improvement oxidation resistance of γ -TiAl based alloy by deposing TiAlSiN coating, Effects of silicon (Corrosion Science J, 2021), found that the basic Ti-48Al-2Cr-2Nb alloy started to scale after cyclic oxidation at 900 ℃ for only 5 hours.
Therefore, the improvement of the mechanical property and the high-temperature oxidation resistance of the titanium-aluminum alloy plays a crucial role in the application and development of the titanium-aluminum alloy.
At present, in order to coordinate the strength and the plasticity of the titanium-aluminum alloy, a common method is to add alloy elements, but many alloy elements such as Mn, V, Mo, Cr and Zr can reduce the high-temperature oxidation resistance of the titanium-aluminum alloy, and in order to improve the high-temperature oxidation resistance of the titanium-aluminum alloy, a coating can be generally deposited on the surface of the alloy, but the coating and a substrate cannot be well combined.
Disclosure of Invention
An object of the present invention is to provide a titanium aluminum alloy having excellent mechanical properties and high-temperature oxidation resistance, so as to solve the above problems.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows: a titanium-aluminum alloy comprises the following elements in atomic percent: 46 to 49 percent of Ti, 46 to 49 percent of A1, 1.5 to 2.5 percent of Cr, 1.5 to 2.5 percent of Nb and 0.15 to 0.3 percent of Gd.
Namely, the alloy consists of pre-alloy Ti-48Al-2Cr-2Nb and Gd with the atomic percent of 0.15 to 0.3 percent.
The second purpose of the invention is to provide the preparation method of the titanium-aluminum alloy, which adopts the technical scheme that: prealloyed Ti-48Al-2Cr-2Nb and elemental Gd powder are used as raw materials, and a plasma sintering method is adopted to sinter the raw materials to obtain a bimodal structure with a Gd-rich phase distributed at the boundaries of powder particles.
As a preferred technical scheme: the plasma sintering is spark plasma sintering.
As a further preferable technical scheme: the heating rate of the plasma sintering is 80-120 ℃/min.
As a further preferable technical scheme: the sintering temperature of the plasma sintering is 1150-1250 ℃.
As a further preferable technical scheme: the heat preservation time of the plasma sintering is 3-5 min.
As a further preferable technical scheme: the sintering pressure of the plasma sintering is 40-50 MPa.
The titanium-aluminum alloy prepared by adopting the raw materials and the method is proved by an isothermal oxidation experiment at 800 ℃, and the addition of a proper amount of Gd is combined with a proper preparation method, so that the oxidation rate of the alloy is reduced, the oxidation weight increment of the alloy is reduced, the anti-stripping capability of an oxide film is improved, no crack is generated in the oxide film after 500 hours, and the oxide film is not found to fall off. And room temperature compression tests show that the strength and the plasticity of the gadolinium-containing alloy are improved compared with those of gadolinium-free alloy.
Compared with the prior art, the invention has the advantages that: for Ti-48Al-2Cr-2Nb alloy, a proper amount of Gd is added, and a proper preparation method is combined, so that the room-temperature mechanical property of the alloy is improved, the ultimate compressive strength of the alloy is improved from 2384MPa to 2750MPa by adding a proper amount of Gd, and the fracture strain is improved from 40.26% to 47.9%; meanwhile, the oxidation resistance of the alloy at 800 ℃ is obviously improved, and the weight gain of the alloy with proper amount of Gd in unit area is 2.64mg/cm after isothermal oxidation for 500 hours2Significantly less than the base alloy (3.36 mg/cm)2) (ii) a And the addition of Gd promotes dense Al2O3Inhibiting the formation of TiO2Promoting the growth of the alloy oxide film inner layer Al2O3The formation of the layer changes the structure of the oxide film, reduces the thickness of the oxide film, is beneficial to relieving the growth stress and the internal stress of the oxide film, and prevents the generation and the expansion of cracks in the oxide film and the falling of the oxide film.
Drawings
FIG. 1 is an oxidation weight gain curve of titanium aluminum alloy containing 0.3 at.% Gd and no Gd after 500 hours of isothermal oxidation at 800 ℃;
FIG. 2 is an SEM image of the cross-section of the oxide film after isothermal oxidation of 0.3 at.% Gd and Gd-free titanium aluminum alloy at 800 ℃ for 500 hours.
Fig. 3 is a graph of room temperature mechanical properties of titanium aluminum alloys with 0.3 at.% Gd and without Gd.
FIG. 4 is an oxidation weight gain curve of titanium aluminum alloy with 0.15 at.% Gd and no Gd after 500 hours of isothermal oxidation at 800 ℃;
FIG. 5 is an SEM image of the cross-section of the oxide film after isothermal oxidation of 0.15 at.% Gd and no Gd in a titanium aluminum alloy for 500 hours at 800 ℃.
Fig. 6 is a graph of room temperature mechanical properties of titanium aluminum alloys with 0.15 at.% Gd and without Gd.
Detailed Description
The present invention will be described in further detail with reference to the following examples and accompanying drawings. It should be understood that the scope of the above-described subject matter is not limited to the following examples, and any techniques implemented based on the disclosure of the present invention are within the scope of the present invention.
Example 1
The experimental scheme adopted by the invention is as follows:
(1) ball milling: weighing Ti48Al2Cr2Nb powder and rare earth Gd powder (0.3 at%) according to the proportion, mixing the materials by using a planetary ball mill, wherein the rotating speed of the ball mill is 300r/min, the ball milling time is 4 hours, wet mixing is adopted in a powder mixing mode, the medium is tert-butyl alcohol, and vacuum freeze drying is carried out for 24 hours after powder mixing;
(2) spark plasma sintering: heating rate is 100 ℃/min, sintering temperature is 1200 ℃, sintering pressure is 40MPa, heat preservation and pressure maintaining time is 5 minutes, and argon is introduced for sintering;
(3) preparation of an oxidized sample: wire-cutting into 4 × 4 × 8mm size3Grinding 6 surfaces of the test sample to 600 meshes by using SiC abrasive paper, ultrasonically cleaning the test sample in alcohol for 15min, and drying the test sample by using a blower;
(4) isothermal oxidation experiment: the test is carried out in a box type resistance furnace, the test medium is static air, and the test temperature is 800 ℃. In order to ensure that each surface of the sample can be in good contact with air, the sample is obliquely placed in an alumina crucible, the sample is taken out after being oxidized for a period of time, air-cooled for 20 minutes and weighed, and then the sample is continuously placed back into the furnace for oxidation for 500 hours;
(5) preparation of a compressed sample: wire-cutting into 5 × 5 × 7mm size3Grinding 6 surfaces of the test sample to 800 meshes by using SiC sand paper, ultrasonically cleaning the test sample in alcohol for 15min, and drying the test sample by using a blower;
(6) room temperature compression test: the test is carried out by using a WDW electronic universal tester, and the strain rate is 0.005s-1；
Use ofPreparing an alloy with nominal components of Ti-48Al-2Cr-2Nb- (0,0.3) Gd by spark plasma sintering of Ti-48Al-2Cr-2Nb powder and elemental Gd powder, and cutting the alloy into 4 multiplied by 8mm in size by wire cutting36 surfaces of the test piece were ground to 600 mesh with SiC sandpaper, and then ultrasonically cleaned in alcohol for 15 min. The test is carried out in a box type resistance furnace, the test medium is static air, and the test temperature is 800 ℃. In order to ensure that all surfaces of the sample can be in good contact with air, the sample is obliquely placed in an alumina crucible, the sample is taken out after being oxidized for a period of time, air is cooled for 20 minutes and weighed, then the sample is continuously placed back into the furnace for oxidation, and the cumulative oxidation time of the sample is 500 hours.
The oxidation weight gain curve is shown in FIG. 1. from FIG. 1, it can be seen that the Ti-48Al-2Cr-2Nb-0.3Gd alloy exhibits excellent oxidation resistance with a smaller oxidation rate and an oxidation weight gain at 500 hours (2.64 mg/cm)2) Less than Gd-free alloy (3.36 mg/cm)2)；
The SEM image of the cross section of the oxide film is shown in FIG. 2, and it can be seen from FIG. 2 that the addition of 0.3% Gd element causes Al2O3The layer is denser and the TiO is made2Layer and Al2O3+TiO2The mixed layer is thinned, and the growth stress and TiO brought by the rapid growth of an oxide film are reduced2The compressive stress existing in the outer layer improves the anti-cracking capability of the oxide film;
the room temperature mechanical properties are shown in FIG. 3, and it can be seen that after 0.3% Gd is added, the ultimate compressive strength of the alloy is increased from 2384MPa to 2598MPa, and the fracture strain is increased from 40.26% to 43.2%.
Example 2
The experimental scheme adopted by the invention is as follows:
(1) ball milling: weighing Ti48Al2Cr2Nb powder and rare earth Gd powder (0.15 at%) according to the proportion, mixing the materials by using a planetary ball mill, wherein the rotating speed of the ball mill is 300r/min, the ball milling time is 4 hours, wet mixing is adopted in a powder mixing mode, the medium is tert-butyl alcohol, and vacuum freeze drying is carried out for 24 hours after powder mixing;
(2) spark plasma sintering: heating rate is 100 ℃/min, sintering temperature is 1200 ℃, sintering pressure is 40MPa, heat preservation and pressure maintaining time is 5 minutes, and argon is introduced for sintering;
(3) preparation of an oxidized sample: wire-cutting into 4 × 4 × 8mm size3Grinding 6 surfaces of the test sample to 600 meshes by using SiC abrasive paper, ultrasonically cleaning the test sample in alcohol for 15min, and drying the test sample by using a blower;
(4) isothermal oxidation experiment: the test is carried out in a box type resistance furnace, the test medium is static air, and the test temperature is 800 ℃. In order to ensure that each surface of the sample can be in good contact with air, the sample is obliquely placed in an alumina crucible, the sample is taken out after being oxidized for a period of time, air-cooled for 20 minutes and weighed, and then the sample is continuously placed back into the furnace for oxidation for 500 hours;
(5) preparation of a compressed sample: wire-cutting into 5 × 5 × 7mm size3Grinding 6 surfaces of the test sample to 800 meshes by using SiC sand paper, ultrasonically cleaning the test sample in alcohol for 15min, and drying the test sample by using a blower;
(6) room temperature compression test: the test is carried out by using a WDW electronic universal tester, and the strain rate is 0.005s-1；
Preparing an alloy with a nominal composition of Ti-48Al-2Cr-2Nb- (0,0.15) Gd by spark plasma sintering of Ti-48Al-2Cr-2Nb powder and elemental Gd powder, and wire-cutting into 4 x 8mm in size3Grinding 6 surfaces of the test sample to 600 meshes by using SiC sand paper, and then ultrasonically cleaning the test sample in alcohol for 15 min; the test is carried out in a box type resistance furnace, the test medium is static air, and the test temperature is 800 ℃. In order to ensure that all surfaces of the sample can be in good contact with air, the sample is obliquely placed in an alumina crucible, the sample is taken out after being oxidized for a period of time, air is cooled for 20 minutes and weighed, then the sample is continuously placed back into the furnace for oxidation, and the cumulative oxidation time of the sample is 500 hours.
The oxidation weight gain curve is shown in FIG. 4. from FIG. 4, it can be seen that the Ti-48Al-2Cr-2Nb-0.15Gd alloy exhibits better oxidation resistance with a lower oxidation rate and an oxidation weight gain at 500 hours (3.02 mg/cm)2) Less than Gd-free alloy (3.36 mg/cm)2)；
The SEM image of the cross section of the oxide film is shown in FIG. 5, and it can be seen from FIG. 5 that the addition of 0.15% Gd element causes Al2O3The layer is denser and the TiO is made2Layer and Al2O3+TiO2The mixed layer is thinned and a new layer of Al is formed at the internal mixed oxide layer/matrix interface2O3Layer, further hindering diffusion of atoms, reducing growth stress due to rapid growth of oxide film and TiO2The compressive stress in the outer layer improves the crack resistance of the oxide film.
The room temperature mechanical properties are shown in FIG. 6, and it can be seen that after 0.15 at% Gd is added, the ultimate compressive strength of the alloy is increased from 2384MPa to 2750MPa, and the fracture strain is increased from 40.26% to 47.9%.
Example 3
The following examples and comparative examples are based on example 2, but the relevant preparation process parameters differ, the specific parameters are shown in Table 1
TABLE 1 preparation conditions for examples 3-7 and comparative examples 1-6
| Rate of temperature rise (. degree. C./min) | Sintering temperature (. degree. C.) | Incubation time (min) | Gd(at％) | |
| Example 3 | 80 | 1200 | 5 | 0.15 |
| Example 4 | 120 | 1200 | 5 | 0.15 |
| Example 5 | 100 | 1150 | 5 | 0.15 |
| Example 6 | 100 | 1250 | 5 | 0.15 |
| Example 7 | 100 | 1200 | 3 | 0.15 |
| Comparative example 1 | 70 | 1200 | 5 | 0.15 |
| Comparative example 2 | 130 | 1200 | 5 | 0.15 |
| Comparative example 3 | 100 | 1100 | 5 | 0.15 |
| Comparative example 4 | 100 | 1300 | 5 | 0.15 |
| Comparative example 5 | 100 | 1200 | 5 | 0.20 |
| Comparative example 6 | 100 | 1200 | 5 | 0.35 |
The above examples and comparative examples were conducted in the same manner as in example 2, and the results are shown in Table 2:
TABLE 2 correlation of performance test results
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the invention, and any modifications, equivalents and improvements made within the spirit and principle of the present invention are intended to be included within the scope of the present invention.
Claims (7)
1. The titanium-aluminum alloy is characterized in that the atomic percentages of elements in the raw materials are as follows: 46 to 49 percent of Ti, 46 to 49 percent of A1, 1.5 to 2.5 percent of Cr, 1.5 to 2.5 percent of Nb and 0.15 to 0.3 percent of Gd.
2. The method for producing a titanium-aluminum alloy according to claim 1, characterized in that: prealloyed Ti-48Al-2Cr-2Nb and elemental Gd powder are used as raw materials, and a plasma sintering method is adopted to sinter the raw materials to obtain a bimodal structure with a Gd-rich phase distributed at the boundaries of powder particles.
3. The method of claim 2, wherein: the plasma sintering is spark plasma sintering.
4. The production method according to claim 3, characterized in that: the heating rate of the plasma sintering is 80-120 ℃/min.
5. The production method according to claim 3, characterized in that: the sintering temperature of the plasma sintering is 1150-1250 ℃.
6. The production method according to claim 3, characterized in that: the heat preservation time of the plasma sintering is 3-5 min.
7. The production method according to claim 3, characterized in that: the sintering pressure of the plasma sintering is 40-50 MPa.
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| CN117363930A (en) * | 2023-12-08 | 2024-01-09 | 成都飞机工业（集团）有限责任公司 | Wear-resistant titanium-aluminum alloy and preparation method thereof |
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| CN103320670A (en) * | 2013-07-01 | 2013-09-25 | 昆山乔锐金属制品有限公司 | High-temperature high-strength titanium-aluminum alloy |
| CN108480651A (en) * | 2018-04-23 | 2018-09-04 | 安徽哈特三维科技有限公司 | A kind of preparation method and application of Ti-48Al-2Cr-2Nb alloy powders |
| CN112063885A (en) * | 2020-08-03 | 2020-12-11 | 西北工业大学 | Ruthenium-containing multi-component TiAl alloy suitable for 800 DEG C |
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| CN103320670A (en) * | 2013-07-01 | 2013-09-25 | 昆山乔锐金属制品有限公司 | High-temperature high-strength titanium-aluminum alloy |
| CN108480651A (en) * | 2018-04-23 | 2018-09-04 | 安徽哈特三维科技有限公司 | A kind of preparation method and application of Ti-48Al-2Cr-2Nb alloy powders |
| CN112063885A (en) * | 2020-08-03 | 2020-12-11 | 西北工业大学 | Ruthenium-containing multi-component TiAl alloy suitable for 800 DEG C |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117363930A (en) * | 2023-12-08 | 2024-01-09 | 成都飞机工业（集团）有限责任公司 | Wear-resistant titanium-aluminum alloy and preparation method thereof |
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