CN114657501A - Method for improving high-temperature oxidation resistance of high Nb-TiAl alloy - Google Patents
Method for improving high-temperature oxidation resistance of high Nb-TiAl alloy Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 66
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 64
- 230000003647 oxidation Effects 0.000 title claims abstract description 52
- 238000007254 oxidation reaction Methods 0.000 title claims abstract description 52
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 31
- 238000000034 method Methods 0.000 title claims abstract description 26
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Chemical compound [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 claims abstract description 15
- 235000013024 sodium fluoride Nutrition 0.000 claims abstract description 7
- 239000011775 sodium fluoride Substances 0.000 claims abstract description 7
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims abstract description 5
- 239000007864 aqueous solution Substances 0.000 claims abstract description 5
- 229910052731 fluorine Inorganic materials 0.000 claims abstract description 5
- 239000011737 fluorine Substances 0.000 claims abstract description 5
- 239000008367 deionised water Substances 0.000 claims abstract description 4
- 229910021641 deionized water Inorganic materials 0.000 claims abstract description 4
- 238000001035 drying Methods 0.000 claims abstract description 4
- 230000007774 longterm Effects 0.000 claims abstract description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 4
- 238000004140 cleaning Methods 0.000 claims description 7
- 229910000505 Al2TiO5 Inorganic materials 0.000 claims description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 5
- 229910052593 corundum Inorganic materials 0.000 claims description 5
- 239000010955 niobium Substances 0.000 claims description 5
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 5
- 229910001845 yogo sapphire Inorganic materials 0.000 claims description 5
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 claims description 4
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 238000005242 forging Methods 0.000 claims description 3
- 238000005096 rolling process Methods 0.000 claims description 3
- 238000010146 3D printing Methods 0.000 claims description 2
- 238000011065 in-situ storage Methods 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 2
- 230000007704 transition Effects 0.000 claims description 2
- DGAQECJNVWCQMB-PUAWFVPOSA-M Ilexoside XXIX Chemical compound C[C@@H]1CC[C@@]2(CC[C@@]3(C(=CC[C@H]4[C@]3(CC[C@@H]5[C@@]4(CC[C@@H](C5(C)C)OS(=O)(=O)[O-])C)C)[C@@H]2[C@]1(C)O)C)C(=O)O[C@H]6[C@@H]([C@H]([C@@H]([C@H](O6)CO)O)O)O.[Na+] DGAQECJNVWCQMB-PUAWFVPOSA-M 0.000 claims 1
- 229910052708 sodium Inorganic materials 0.000 claims 1
- 239000011734 sodium Substances 0.000 claims 1
- 230000008569 process Effects 0.000 abstract description 10
- 238000010438 heat treatment Methods 0.000 abstract description 8
- 239000000243 solution Substances 0.000 abstract description 5
- -1 fluorine ions Chemical class 0.000 abstract description 3
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 abstract 2
- 238000005406 washing Methods 0.000 abstract 2
- 125000004122 cyclic group Chemical group 0.000 description 11
- 238000005468 ion implantation Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 229910006281 γ-TiAl Inorganic materials 0.000 description 5
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 239000000306 component Substances 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000000758 substrate Substances 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910052736 halogen Inorganic materials 0.000 description 2
- 150000002367 halogens Chemical class 0.000 description 2
- 238000002513 implantation Methods 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- FKNQFGJONOIPTF-UHFFFAOYSA-N Sodium cation Chemical compound [Na+] FKNQFGJONOIPTF-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000003064 anti-oxidating effect Effects 0.000 description 1
- 239000003963 antioxidant agent Substances 0.000 description 1
- 230000003078 antioxidant effect Effects 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 239000008358 core component Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 238000001755 magnetron sputter deposition Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000011253 protective coating Substances 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000008261 resistance mechanism Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 229910001415 sodium ion Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 239000012720 thermal barrier coating Substances 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
- 230000004584 weight gain Effects 0.000 description 1
- 235000019786 weight gain Nutrition 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/10—Oxidising
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/02—Pretreatment of the material to be coated
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Chemical Treatment Of Metals (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Abstract
A method for improving the high-temperature oxidation resistance of a high Nb-TiAl alloy belongs to the field of high-temperature oxidation resistance of the surface of the high Nb-TiAl alloy. The method is characterized in that a sodium fluoride solution is used for treating the surface of the high Nb-TiAl alloy, and then a sample is subjected to high-temperature oxidation treatment to generate an oxide film on the surface of the high Nb-TiAl alloy, so that the long-term oxidation resistance of the high Nb-TiAl alloy is improved. The specific method and the process are as follows: treating the surface of the high Nb-TiAl alloy for 15-30 s by using an aqueous solution of sodium fluoride, wherein the concentration of fluorine ions is 0.08-0.12 mol/L; then, washing the surface of the product by using deionized water, then washing the product by using alcohol and then drying the product; in a heat treatment furnace, the temperature is raised to 900-950 ℃ for oxidation treatment for 3-5 h, so that a compact aluminum oxide film is generated on the surface of the aluminum oxide film. The invention has simple process and easy engineering application.
Description
Technical Field
The invention belongs to the field of intermetallic compound high-temperature structural materials, and particularly relates to a method for improving the high-temperature oxidation resistance of the surface of a high Nb-TiAl alloy.
Background
The thrust-weight ratio of the engine is increased along with the weight reduction of the aircraft, the engine serving as a core component of the aerospace aircraft directly influences the overall weight of the aircraft, and the aircraft engine with high thrust-weight ratio is sought by engine manufacturers in various countries. The gamma-TiAl alloy is an important material for high thrust-weight ratio aircraft engine blades and low-pressure turbine blades due to light weight, high-temperature strength, good high-temperature creep and the like, and has important application value in the field of aerospace. However, its insufficient high-temperature oxidation resistance is one of the major problems that prevent its practical industrial application. The high Nb-TiAl alloy (Nb content is 5-10%, Al content is 43-49%) is used as a new member of a gamma-TiAl alloy system, and has more excellent comprehensive performance. For example, compared with common gamma-TiAl, the Ti- (43-45) Al- (8-10Nb) - (W, B, Y) alloy has the advantages that the melting point is higher by 100 ℃, the yield strength at 900 ℃ is higher by 150MPa, the high-temperature creep resistance is improved by 2-10 times, and the oxidation resistance at 750-800 ℃ is good. Therefore, the service temperature of the high Nb-TiAl alloy is improved by 100 ℃ compared with that of the common gamma-TiAl alloy. However, the alloy also has the problem of insufficient oxidation resistance at the service temperature, so that the actual working temperature of the material is far lower than the target service temperature, the advantages of high-temperature mechanical properties cannot be fully exerted, and the practical engineering application of the alloy in the fields of aerospace and the like is limited. Therefore, the preparation of the high-temperature protective coating on the surface of the high Nb-TiAl alloy and the high-temperature oxidation resistance mechanism of the high Nb-TiAl alloy are researched, theoretical reference is provided for the design and manufacture of high-performance and high-reliability aeroengine parts, and the engineering application of the alloy in the fields of aerospace and the like can be promoted.
From the aspect of engineering application effect, the protective effect can be formed on the TiAl base material as long as the surface film or the coating of the gamma-TiAl alloy can play an anti-oxidation function in the service process and the bonding performance with the base material is ensured. German schau tze et al investigated the effect of halogen element injection on the oxidation behavior of TiAl alloys. At the oxide film/substrate interface, the ion implanted halogen first reacts with Al to form a thermodynamically stable aluminum halide. Although the ion implantation is performed at a low temperature and has a small influence on the substrate, the ion implantation is easily degraded at a high temperature with a very limited implantation amount and depth, and the ion implantation is performed at a room temperature and has a small influence on the substrate, the ion implantation is easily degraded at a high temperature with a very limited implantation amount and depth, and the ion implantation equipment is expensive and cannot process the grooves and the complex-shaped portions of the parts. The blade in practical application has a complex shape, and with the improvement of the plasticity and the processing technology of the TiAl alloy, the TiAl alloy blade is likely to be subjected to hollowing treatment like a nickel-based blade in the future. Conventional coating preparation and ion implantation approaches have difficulty providing protection both inside and outside such blades. Therefore, there is a need to find a process for antioxidant treatment of blades that can be used on both complex blades and hollow blades.
Disclosure of Invention
The invention aims to overcome the problem of insufficient high-temperature oxidation resistance of a high Nb-TiAl alloy and provides a treatment method for improving the oxidation resistance of the high Nb-TiAl alloy at 900-950 ℃.
A method for improving the high-temperature oxidation resistance of a high Nb-TiAl alloy is characterized by comprising the following steps:
(1) performing surface treatment on the high Nb-TiAl alloy by adopting a sodium fluoride aqueous solution with the fluorine ion concentration of 0.08-0.12mol/L for 30-60s, cleaning the surface of the Nb-TiAl alloy by using deionized water for 5-10min, cleaning by using alcohol for 5-10min, and drying by using a blower; wherein the selected alloy components are as follows: the Al content is: (43-46) at.%; the Nb content is: (6-10) at.%; the trace elements (W, B, Y) are: (0.3-1) at.%, and the balance Ti, wherein the original structure of the alloy is in a casting state, a forging state, a rolling state or a 3D printing state;
(2) raising the temperature to 900-950 ℃ for oxidation treatment for 3-5 h to promote alpha-Al by fluoride ions2O3Formation of continuous film, sodium ion promoted Al2O3And TiO2Formation of Al2TiO5Obtaining compact Al on the surface of Nb-TiAl alloy2O3A film; and during long-term oxidation, Al2O3A transition layer rich in niobium is generated in situ under the film, thereby improving the bonding performance of the surface oxide film and the high Nb-TiAl alloy.
Compared with the prior art, the invention has the following beneficial effects:
compared with the existing coating technology (thermal spraying, thermal barrier coating, laser surface cladding, magnetron sputtering, anodic oxidation, evaporation and the like), the method has the advantages that the sodium fluoride introduced into the alloy surface has low density and low content, the weight of the treated alloy is increased very low before oxidation, the oxidation resistance of an oxide film generated in the oxidation process can be effectively improved, the bonding property of the oxide and the toughness phase at the interface of an alloy matrix can be effectively improved, and according to an oxidation resistance determination experiment method (national standard 5858-2000) of steel and high-temperature alloy, the high-Nb-TiAl alloy treated by the method reaches the level of complete oxidation resistance at 900-950 ℃. In addition, the process method is simple, easy to operate and easy to realize engineering application. Therefore, the result of the invention has important significance for improving the high-temperature oxidation resistance and protection of high-Nb-TiAl alloy aeroengine parts (blades and turbine discs).
Drawings
FIG. 1 is a graph showing the kinetics of cyclic oxidation of Ti-45 Al-8.5 Nb- (W, B, Y) alloy at 950 ℃ for 1000 hours.
FIG. 2 shows the surface morphology of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 1000 h.
FIG. 3 shows the cross-sectional morphology of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 1000h cyclic oxidation at 950 ℃.
FIG. 4 shows XRD results of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 1000 h.
FIG. 5 shows the room temperature tensile fracture of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 1000 h.
FIG. 6 shows XRD results of isothermal oxidation of Ti-45 Al-8.5 Nb- (W, B, Y) alloy at 900 ℃ for 100 h.
FIG. 7 shows XRD results of 950 ℃ isothermal oxidation for 100h of Ti-45 Al-8.5 Nb- (W, B, Y) alloy.
Detailed Description
In order to make the technical solutions of the present invention better understood, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1:
(1) selecting and casting Ti-45 Al-8.5 Nb- (W, B, Y) alloy according to the national standard size of 20 x 10 x 1.5mm3Cutting a sample, and then grinding, polishing, ultrasonic alcohol cleaning and drying by a blower.
(2) The fluorine treatment method comprises the following steps: weighing sodium fluoride salt by using an electronic balance (accurate to 0.0001) to prepare an aqueous solution with the concentration of fluoride ions of 0.1mol/L, placing the alloy sample prepared in the previous step in the aqueous solution for waiting for 60s, then taking out the sample to place in a deionized water beaker, carrying out ultrasonic vibration cleaning for 10min, then taking out the sample to place in alcohol, carrying out ultrasonic vibration cleaning for 10min, and then taking out the sample to blow dry by using a blower.
(3) The heat treatment process comprises the following steps: firstly, raising the temperature of a heat treatment furnace to 950 ℃, and placing the sample treated in the previous step into the heat treatment furnace for oxidation treatment for 3 hours to obtain an oxide layer on the surface of the sample; good oxidation resistance and bonding performance are obtained in the subsequent long-term oxidation (1000 h). FIG. 1 is a graph showing the oxidation kinetics curves of Ti-45 Al-8.5 Nb- (W, B, Y) alloy at 950 ℃ cyclic oxidation for 1000h, and the oxidation weight gain is about 0.5mg/cm2The oxidation resistance of the product can reach the complete oxidation resistance level according to the national standard; FIG. 2 shows the surface morphology of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 1000h, which indicates that the surface is mainly Al2O3(ii) a FIG. 3 shows the cross-sectional morphology of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 1000h, and it can be seen that there are no holes, cracks, etc. between the oxide cross-section and the alloy matrix. FIG. 4 shows XRD results of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 1000h, and Al can be detected2O3、TiO2And Al2TiO5. FIG. 5 shows tensile fracture at room temperature after Ti-45 Al-8.5 Nb- (W, B, Y) alloy is cyclically oxidized at 950 ℃ for 1000h, and the separation and peeling of the oxide layer can be seen from the fracture, which shows that the bonding performance of the oxide layer and the alloy matrix is good.
Example 2:
(1) the alloy component is Ti-45 Al-8.5 Nb- (W, B, Y), and the original structure is in a forging state. The rest is the same as in example 1.
(2) The fluorine treatment method comprises the following steps: as in example 1, the concentration of the sodium fluoride solution was 0.12 mol/L.
(3) The heat treatment process comprises the following steps: the heat treatment temperature was 950 ℃ for 5 hours as in example 1; good oxidation resistance and bonding performance are obtained in the subsequent oxidation (100 h). FIG. 6 shows XRD results of Ti-45 Al-8.5 Nb- (W, B, Y) alloy in forged state after cyclic oxidation at 950 ℃ for 100h, and Al as an oxide can be detected2O3、TiO2And Al2TiO5。
Example 3:
(1) the alloy component is Ti-45 Al-8.5 Nb- (W, B, Y), and the original structure is in a rolling state. The rest is the same as in example 1.
(2) The fluorine treatment method comprises the following steps: the concentration of the sodium fluoride solution was 0.08mol/L as in example 1.
(3) The heat treatment process comprises the following steps: the heat treatment temperature was 900 ℃ for 5 hours as in example 1; good oxidation resistance and bonding performance are obtained in the subsequent oxidation (100 h). FIG. 7 shows XRD results of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after cyclic oxidation at 950 ℃ for 100h, and Al can be detected2O3、TiO2And Al2TiO5。
Claims (1)
1. A method for improving the high-temperature oxidation resistance of a high Nb-TiAl alloy is characterized by comprising the following steps:
carrying out fluorine treatment on the high Nb-TiAl alloy for 30-60s by adopting a sodium fluoride aqueous solution with the fluorine ion concentration of 0.08-0.12mol/L, cleaning the surface of the high Nb-TiAl alloy for 5-10min by using deionized water, cleaning for 5-10min by using alcohol, and drying by using a blower; the alloy comprises the following components: the Al content is: (43-46) at.%; the Nb content is: (6-10) at.%; the content of W is: (0.3-1) at.%; the content of B is: (0.3-1) at.%; the content of Y is as follows: (0.3-1) at.%, and the balance Ti, wherein the original structure of the alloy is in a casting state, a forging state, a rolling state or a 3D printing state;
(2) raising the temperature to 900-950 ℃ for oxidation treatment for 3-5 h to promote alpha-Al by fluoride ions2O3Form a continuous film, and form sodium ionsPromotion of Al2O3And TiO2Formation of Al2TiO5Obtaining compact Al on the surface of Nb-TiAl alloy2O3A film; and during long-term oxidation, Al2O3A transition layer rich in niobium is generated in situ under the film, thereby improving the bonding performance of the surface oxide film and the high Nb-TiAl alloy.
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| WO2007134596A1 (en) * | 2006-05-24 | 2007-11-29 | Dechema Gesellschaft Für Chemische Technik Und Biotechnologie E.V. | Method for treating surfaces of titanium-aluminum alloys with fluoride or fluoride compounds |
| EP2428591A2 (en) * | 2010-09-09 | 2012-03-14 | DECHEMA Gesellschaft für Chemische Technik und Biotechnologie e.V. | Method for treating the surfaces of a substrate comprising a TiAl alloy for improved oxidation resistance |
| CN104532061A (en) * | 2014-12-26 | 2015-04-22 | 北京科技大学 | High-temperature-resistant aluminum titanium oxide alloy and preparation method thereof |
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