CN114657501B - 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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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 64
- 239000000956 alloy Substances 0.000 title claims abstract description 64
- 230000003647 oxidation Effects 0.000 title claims abstract description 53
- 238000007254 oxidation reaction Methods 0.000 title claims abstract description 53
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 29
- 238000000034 method Methods 0.000 title claims abstract description 29
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Chemical compound [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 claims abstract description 15
- 230000008569 process Effects 0.000 claims abstract description 14
- 238000004140 cleaning Methods 0.000 claims abstract description 9
- 229910052731 fluorine Inorganic materials 0.000 claims abstract description 7
- 239000011737 fluorine Substances 0.000 claims abstract description 7
- 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
- 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
- -1 fluorine ions Chemical class 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
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 8
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 5
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 claims description 4
- 230000015572 biosynthetic process Effects 0.000 claims description 4
- 239000010955 niobium Substances 0.000 claims description 4
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 3
- 238000005242 forging Methods 0.000 claims description 3
- 238000010146 3D printing Methods 0.000 claims description 2
- FKNQFGJONOIPTF-UHFFFAOYSA-N Sodium cation Chemical compound [Na+] FKNQFGJONOIPTF-UHFFFAOYSA-N 0.000 claims description 2
- 238000011065 in-situ storage Methods 0.000 claims description 2
- 239000012528 membrane Substances 0.000 claims description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 2
- 238000005096 rolling process Methods 0.000 claims description 2
- 229910001415 sodium ion Inorganic materials 0.000 claims description 2
- 230000007704 transition Effects 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 abstract description 8
- 239000000243 solution Substances 0.000 abstract description 4
- 238000005516 engineering process Methods 0.000 abstract description 3
- 239000011521 glass Substances 0.000 abstract 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 abstract 1
- 125000004122 cyclic group Chemical group 0.000 description 10
- 229910052782 aluminium Inorganic materials 0.000 description 7
- 239000000463 material Substances 0.000 description 5
- 229910006281 γ-TiAl Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 238000005468 ion implantation Methods 0.000 description 4
- 239000000758 substrate Substances 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 239000003963 antioxidant agent Substances 0.000 description 2
- 230000003078 antioxidant effect Effects 0.000 description 2
- 230000015556 catabolic process Effects 0.000 description 2
- 238000006731 degradation reaction 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
- 239000000203 mixture Substances 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 230000004584 weight gain Effects 0.000 description 2
- 235000019786 weight gain Nutrition 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 239000000306 component Substances 0.000 description 1
- 239000008358 core component Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 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
- 238000005259 measurement 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
- 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
- 238000007740 vapor deposition Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
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)
- Turbine Rotor Nozzle Sealing (AREA)
- Chemical Treatment Of Metals (AREA)
Abstract
A method for improving high-temperature oxidation resistance of high Nb-TiAl alloy belongs to the field of high-temperature oxidation resistance of high Nb-TiAl alloy surfaces. The method is characterized in that the surface of the high Nb-TiAl alloy is treated by sodium fluoride solution, and then the sample is subjected to high-temperature oxidation treatment to form an oxide film on the surface of the sample, so that the long-term oxidation resistance of the high Nb-TiAl alloy is improved. The specific method and the technology are as follows: treating the surface of the high Nb-TiAl alloy for 15s-30s by using a sodium fluoride aqueous solution, wherein the concentration of fluorine ions is 0.08-0.12 mol/L; then cleaning the surface of the glass with deionized water, cleaning the glass with alcohol, and drying; in a heat treatment furnace, the temperature is increased to 900-950 ℃ for oxidation treatment for 3-5 h, so that a compact alumina film is formed 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 high-temperature oxidation resistance of a high-Nb-TiAl alloy surface.
Background
The thrust-to-weight ratio of the engines increases as the weight of the aircraft decreases, and the engines as a core component of the aerospace vehicle directly affect the overall weight of the aircraft, with high thrust-to-weight ratio aircraft engines being sought after by various national engine manufacturers. The gamma-TiAl alloy is an important material for the high thrust-weight ratio aircraft engine blade and the low-pressure turbine blade due to light weight, high-temperature strength, good high-temperature creep and the like, and has important application value in the aerospace field. But the insufficient high-temperature oxidation resistance is one of the main problems which hinder the 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 the gamma-TiAl alloy system, and has more excellent comprehensive performance. For example, compared with common gamma-TiAl, the Ti- (43-45) Al- (8-10 Nb) - (W, B, Y) alloy has a melting point higher than 100 ℃, yield strength higher than 150MPa at 900 ℃, high-temperature creep resistance improved by 2-10 times and oxidation resistance at 750-800 ℃. Therefore, the combined service temperature of the high Nb-TiAl is improved by 100 ℃ compared with that of the common gamma-TiAl alloy. However, the alloy also faces 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 are not fully exerted, and the actual 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 thereof are researched, theoretical references are provided for the design and manufacture of high-performance and high-reliability aeroengine parts, and engineering application of the alloy in the fields of aerospace and the like can be promoted.
From the engineering application effect, the gamma-TiAl alloy surface film or coating can play an antioxidant function in the service process and ensure the combination property with the base material, so that the protective effect on the TiAl base material can be formed. The German schu tze et al examined the effect of halogen injection on the oxidation properties of TiAl alloys. At the oxide film/substrate interface, the ion implanted halogen element first reacts with Al to form a thermodynamically stable aluminum halide. Although ion implantation is performed at a low temperature, the effect on the substrate is small, degradation is likely to occur at a high temperature where the implantation amount and depth are very limited, while ion implantation is performed at room temperature, the effect on the substrate is small, degradation is likely to occur at a high temperature where the implantation amount and depth are very limited, and ion implantation equipment is expensive and cannot process parts and grooves and parts of complex shapes. The shape of the blade in practical application is complex, and with the improvement of the plasticity and the processing technology of the TiAl alloy, the future TiAl alloy blade is also possible to be subjected to hollow treatment like a nickel-based blade. Conventional coating preparation, ion implantation, and the like have difficulty providing protection both inside and outside such blades. Therefore, there is a need to find a process that can be used on complex blades and hollow blades to provide antioxidant treatment to the blades.
Disclosure of Invention
The invention aims to solve 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 high-temperature oxidation resistance of high Nb-TiAl alloy is characterized by comprising the following steps:
(1) Adopting sodium fluoride aqueous solution with the fluorine ion concentration of 0.08-0.12mol/L to carry out surface treatment on the high Nb-TiAl alloy for 30-60s, cleaning the surface of the Nb-TiAl alloy by deionized water for 5-10min, cleaning the surface by alcohol for 5-10min, and drying by a blower; wherein, the selected alloy components are as follows: the Al content is: (43-46) at%; the Nb content is as follows: (6-10) at%; the microelements (W, B, Y) are as follows: (0.3-1) at%, and the balance being Ti element, wherein the original structure of the alloy is in a casting state, a forging state, a rolling state or a 3D printing state;
(2) The temperature is increased to 900-950 ℃ for oxidation treatment for 3-5 h, so that fluorine ions promote alpha-Al 2 O 3 Formation of continuous film, sodium ion promotion of Al 2 O 3 And TiO 2 Formation of Al 2 TiO 5 The surface of the Nb-TiAl alloy obtains compact Al 2 O 3 A membrane; and during the long-term oxidation process, al 2 O 3 And a transition layer rich in niobium element is generated in situ below the film, so that the bonding performance of the surface oxide film and the high Nb-TiAl alloy is improved.
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, vapor deposition and the like), the sodium fluoride introduced on the alloy surface has low density and low content, the treated alloy has very low weight gain before oxidation, the oxide film generated in the oxidation process can effectively improve the oxidation resistance, the toughness phase at the interface of the oxide and the alloy matrix can effectively improve the combination of the oxide film and the alloy matrix, and the high Nb-TiAl alloy treated by the method reaches the full oxidation resistance grade at 900-950 ℃ according to the oxidation resistance measurement experimental method (national standard 5858-2000) of steel and high-temperature alloy. In addition, the process method is simple and easy to operate, and engineering application is easy to realize. Therefore, the result of the invention has important significance for improving the high-temperature oxidation resistance and the protection of high-Nb-TiAl alloy aeroengine parts (blades and turbine discs).
Drawings
FIG. 1 shows the kinetics of 1000h cycle oxidation of Ti-45 Al-8.5 Nb- (W, B, Y) alloy at 950 ℃.
FIG. 2 shows the surface morphology of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 1000h of cyclic oxidation at 950 ℃.
FIG. 3 shows the cross-sectional morphology of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy for 1000h cycle oxidation at 950 ℃.
FIG. 4 shows XRD results of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 1000h of cyclic oxidation at 950 ℃.
FIG. 5 shows a room temperature tensile fracture of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 1000h of cyclic oxidation at 950 ℃.
FIG. 6 shows XRD results for an isothermal oxidation of Ti-45 Al-8.5 Nb- (W, B, Y) alloy at 900℃for 100 h.
FIG. 7 shows XRD results for isothermal oxidation of Ti-45 Al-8.5 Nb- (W, B, Y) alloy at 950℃for 100 h.
Detailed Description
In order that those skilled in the art will better understand the present invention, a technical solution in the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings in which it is apparent that the described embodiments are only some embodiments of the present invention, not all embodiments. All other embodiments, which can be made by a person of ordinary skill in the art based on the embodiments of the present invention without making any inventive effort, shall fall within the scope of the present invention.
Example 1:
(1) Selecting casting Ti-45 Al-8.5 Nb- (W, B, Y) alloy according to national standard size of 20 x 10 x 1.5mm 3 Cutting a sample, grinding, polishing, ultrasonic alcohol cleaning and blowing by a blower.
(2) The fluorine treatment method comprises the following steps: weighing sodium fluoride salt by an electronic balance (accurate to 0.0001), preparing into an aqueous solution with fluoride ion concentration of 0.1mol/L, placing the alloy sample prepared in the previous step into the aqueous solution for 60s, taking out the sample, placing the sample into a deionized water beaker, ultrasonically vibrating and cleaning for 10min, taking out the sample, placing the sample into alcohol, ultrasonically vibrating and cleaning for 10min, and then taking out the sample, and drying by 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) process. FIG. 1 is a graph showing oxidation kinetics for 950 ℃ cyclic oxidation of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy for 1000 hours, with an oxidation weight gain of about 0.5mg/cm 2 According to national standards, the oxidation resistance reaches the full oxidation resistance level; FIG. 2 shows the surface morphology of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 1000 hours of 950 ℃ cyclic oxidation, the surface being predominantly Al 2 O 3 The method comprises the steps of carrying out a first treatment on the surface of the FIG. 3 shows the cross-sectional morphology of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 950 ℃ cyclic oxidation for 1000 hours, showing that there are no holes, cracks, etc. between the oxide cross-section and the alloy matrix. FIG. 4 shows XRD results of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy subjected to 950 ℃ cyclic oxidation for 1000 hours, and Al can be detected 2 O 3 、TiO 2 Al and Al 2 TiO 5 . FIG. 5 shows a room temperature tensile fracture of Ti-45 Al-8.5 Nb- (W, B, Y) alloy after 950 ℃ cyclic oxidation for 1000 hours, from which it can be seen that the oxide layer is detached and peeled, indicating good bonding property of the oxide layer to the alloy substrate.
Example 2:
(1) The alloy composition is selected to be Ti-45 Al-8.5 Nb- (W, B, Y), and the original structure is in a forging state. The other steps are the same as in example 1.
(2) The fluorine treatment method comprises the following steps: as in example 1, the sodium fluoride solution concentration was 0.12mol/L.
(3) The heat treatment process comprises the following steps: the heat treatment temperature was 950℃for 5 hours in the same manner as in example 1; good oxidation resistance and bonding performance are obtained in the subsequent oxidation (100 h) process. FIG. 6 shows a diagram of a wrought form of Ti-45 Al-8.5 Nb-XRD results of the alloy of W, B and Y) after 100h of 950 ℃ cyclic oxidation can detect that the oxide is Al 2 O 3 、TiO 2 Al and Al 2 TiO 5 。
Example 3:
(1) The alloy composition is selected to be Ti-45 Al-8.5 Nb- (W, B, Y), and the original structure is in a rolled state. The other steps are the same as in example 1.
(2) The fluorine treatment method comprises the following steps: as in example 1, the sodium fluoride solution concentration was 0.08mol/L.
(3) The heat treatment process comprises the following steps: the heat treatment temperature was 900℃for 5 hours in the same manner as in example 1; good oxidation resistance and bonding performance are obtained in the subsequent oxidation (100 h) process. FIG. 7 shows XRD results of a Ti-45 Al-8.5 Nb- (W, B, Y) alloy subjected to 950 ℃ cyclic oxidation for 100 hours, and Al can be detected 2 O 3 、TiO 2 Al and Al 2 TiO 5 。
Claims (1)
1. A method for improving high-temperature oxidation resistance of 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 by deionized water for 5-10min, cleaning the surface by alcohol for 5-10min, and drying by a blower; the alloy comprises the following components: the Al content is: (43-46) at%; the Nb content is as follows: (6-10) at%; the W content is as follows: (0.3-1) at%; the content of B is as follows: (0.3-1) at%; the content of Y is as follows: (0.3-1) at%, and the balance being Ti element, wherein the original structure of the alloy is in a casting state, a forging state, a rolling state or a 3D printing state;
(2) The temperature is increased to 900-950 ℃ for oxidation treatment for 3-5 h, so that fluorine ions promote alpha-Al 2 O 3 Formation of continuous film, sodium ion promotion of Al 2 O 3 And TiO 2 Formation of Al 2 TiO 5 The surface of the Nb-TiAl alloy obtains compact Al 2 O 3 A membrane; and during the long-term oxidation process, al 2 O 3 And a transition layer rich in niobium element is generated in situ below the film, so that the bonding performance of the surface oxide film and the high Nb-TiAl alloy is improved.
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