CN116732460A - Hf (Hf) 6 Ta 2 O 17 Base abradable seal coating and preparation method thereof - Google Patents
Hf (Hf) 6 Ta 2 O 17 Base abradable seal coating and preparation method thereof Download PDFInfo
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- CN116732460A CN116732460A CN202310697906.2A CN202310697906A CN116732460A CN 116732460 A CN116732460 A CN 116732460A CN 202310697906 A CN202310697906 A CN 202310697906A CN 116732460 A CN116732460 A CN 116732460A
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- 238000000576 coating method Methods 0.000 title claims abstract description 97
- 239000011248 coating agent Substances 0.000 title claims abstract description 95
- 238000002360 preparation method Methods 0.000 title claims abstract description 22
- 239000000843 powder Substances 0.000 claims abstract description 144
- 239000000919 ceramic Substances 0.000 claims abstract description 111
- 229910000601 superalloy Inorganic materials 0.000 claims abstract description 62
- 230000007704 transition Effects 0.000 claims abstract description 61
- 238000005507 spraying Methods 0.000 claims abstract description 51
- 239000000758 substrate Substances 0.000 claims abstract description 47
- 238000007750 plasma spraying Methods 0.000 claims abstract description 20
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 17
- 238000005516 engineering process Methods 0.000 claims abstract description 14
- 230000001050 lubricating effect Effects 0.000 claims abstract description 12
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 98
- 229910052759 nickel Inorganic materials 0.000 claims description 49
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 32
- 239000000956 alloy Substances 0.000 claims description 30
- 238000000498 ball milling Methods 0.000 claims description 29
- 229910045601 alloy Inorganic materials 0.000 claims description 27
- 239000011259 mixed solution Substances 0.000 claims description 27
- 239000011812 mixed powder Substances 0.000 claims description 25
- 239000007921 spray Substances 0.000 claims description 24
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 23
- 238000000034 method Methods 0.000 claims description 23
- CJNBYAVZURUTKZ-UHFFFAOYSA-N hafnium(iv) oxide Chemical compound O=[Hf]=O CJNBYAVZURUTKZ-UHFFFAOYSA-N 0.000 claims description 20
- BPUBBGLMJRNUCC-UHFFFAOYSA-N oxygen(2-);tantalum(5+) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[Ta+5].[Ta+5] BPUBBGLMJRNUCC-UHFFFAOYSA-N 0.000 claims description 20
- 230000000630 rising effect Effects 0.000 claims description 20
- 229910001936 tantalum oxide Inorganic materials 0.000 claims description 20
- 239000002994 raw material Substances 0.000 claims description 19
- 239000012071 phase Substances 0.000 claims description 18
- 230000008569 process Effects 0.000 claims description 18
- 239000000463 material Substances 0.000 claims description 17
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 16
- 229910052786 argon Inorganic materials 0.000 claims description 16
- 239000001257 hydrogen Substances 0.000 claims description 16
- 229910052739 hydrogen Inorganic materials 0.000 claims description 16
- 238000001035 drying Methods 0.000 claims description 15
- 150000002148 esters Chemical class 0.000 claims description 13
- 229920006389 polyphenyl polymer Polymers 0.000 claims description 13
- 239000007788 liquid Substances 0.000 claims description 12
- 238000005245 sintering Methods 0.000 claims description 12
- 239000008367 deionised water Substances 0.000 claims description 11
- 229910021641 deionized water Inorganic materials 0.000 claims description 11
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 11
- 238000003756 stirring Methods 0.000 claims description 9
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 8
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 8
- 238000005488 sandblasting Methods 0.000 claims description 8
- 239000000243 solution Substances 0.000 claims description 8
- 239000011230 binding agent Substances 0.000 claims description 7
- 239000004372 Polyvinyl alcohol Substances 0.000 claims description 6
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 6
- 230000002572 peristaltic effect Effects 0.000 claims description 6
- 229920002451 polyvinyl alcohol Polymers 0.000 claims description 6
- 238000004321 preservation Methods 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 229920002472 Starch Polymers 0.000 claims description 4
- DPXJVFZANSGRMM-UHFFFAOYSA-N acetic acid;2,3,4,5,6-pentahydroxyhexanal;sodium Chemical compound [Na].CC(O)=O.OCC(O)C(O)C(O)C(O)C=O DPXJVFZANSGRMM-UHFFFAOYSA-N 0.000 claims description 4
- 239000000440 bentonite Substances 0.000 claims description 4
- 229910000278 bentonite Inorganic materials 0.000 claims description 4
- SVPXDRXYRYOSEX-UHFFFAOYSA-N bentoquatam Chemical compound O.O=[Si]=O.O=[Al]O[Al]=O SVPXDRXYRYOSEX-UHFFFAOYSA-N 0.000 claims description 4
- 239000008107 starch Substances 0.000 claims description 4
- 235000019698 starch Nutrition 0.000 claims description 4
- 125000000816 ethylene group Chemical group [H]C([H])([*:1])C([H])([H])[*:2] 0.000 claims description 3
- 229920000573 polyethylene Polymers 0.000 claims description 3
- 229910052582 BN Inorganic materials 0.000 claims description 2
- 239000001768 carboxy methyl cellulose Substances 0.000 claims description 2
- 238000005461 lubrication Methods 0.000 claims description 2
- 238000002156 mixing Methods 0.000 claims description 2
- 235000019812 sodium carboxymethyl cellulose Nutrition 0.000 claims description 2
- 229920001027 sodium carboxymethylcellulose Polymers 0.000 claims description 2
- 238000005299 abrasion Methods 0.000 abstract description 17
- 238000005336 cracking Methods 0.000 abstract description 7
- 230000035939 shock Effects 0.000 abstract description 6
- 229910001233 yttria-stabilized zirconia Inorganic materials 0.000 description 10
- 238000010438 heat treatment Methods 0.000 description 7
- 238000012876 topography Methods 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000003746 solid phase reaction Methods 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000005219 brazing Methods 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000007789 sealing Methods 0.000 description 3
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 229920003123 carboxymethyl cellulose sodium Polymers 0.000 description 2
- 229940063834 carboxymethylcellulose sodium Drugs 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005524 ceramic coating Methods 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000002270 dispersing agent Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000010285 flame spraying Methods 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000005469 granulation Methods 0.000 description 1
- 230000003179 granulation Effects 0.000 description 1
- 238000000713 high-energy ball milling Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000003760 magnetic stirring Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
Classifications
-
- 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
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/10—Oxides, borides, carbides, nitrides or silicides; Mixtures thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
- C04B35/486—Fine ceramics
- C04B35/488—Composites
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
-
- 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
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
- C23C4/073—Metallic material containing MCrAl or MCrAlY alloys, where M is nickel, cobalt or iron, with or without non-metal elements
-
- 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
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
- C23C4/08—Metallic material containing only metal elements
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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
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/12—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the method of spraying
- C23C4/134—Plasma spraying
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3251—Niobium oxides, niobates, tantalum oxides, tantalates, or oxide-forming salts thereof
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T50/00—Aeronautics or air transport
- Y02T50/60—Efficient propulsion technologies, e.g. for aircraft
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- Chemical & Material Sciences (AREA)
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- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Composite Materials (AREA)
- Structural Engineering (AREA)
- Inorganic Chemistry (AREA)
- Coating By Spraying Or Casting (AREA)
Abstract
Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are laminated, wherein the ceramic layer comprises Hf 6 Ta 2 O 17 Ceramic powder, pore-forming agent and lubricating phase, and Hf is calculated according to mass ratio 6 Ta 2 O 17 Ceramic powder: pore-forming agent: lubricating phase= (88-92):(3-5): (3-7); the preparation method comprises the following steps: preparing a nickel-base superalloy substrate, namely preparing a transition layer, spraying the ceramic layer on the surface of the transition layer by using a supersonic atmospheric plasma spraying technology to obtain the nickel-base superalloy substrate, namely the transition layer, namely the ceramic layer, until the thickness of the ceramic layer is more than 200 mu m, and finishing Hf 6 Ta 2 O 17 Preparing a base abradable seal coating; the invention has the characteristics of high service temperature, difficult cracking and peeling of the coating, simple preparation process, small abrasion loss and good thermal shock resistance.
Description
Technical Field
The invention relates to the technical field of high-temperature thermal coating, in particular to a Hf (high-temperature) coating 6 Ta 2 O 17 A base abradable seal coating and a method of making the same.
Background
About 2000, metco corporation proposed a high temperature seal ceramic coating of Yttria Stabilized Zirconia (YSZ) +polyphenyl ester, wherein YSZ was used as the host material to withstand high temperatures of 1150 ℃ and polyphenyl ester was used as the pore former to increase the porosity of the YSZ seal coating and improve the abradability of the coating. However, in practical production applications, zirconia particles are found to be substantially completely melted in the plasma sprayed flame stream, a dense ceramic layer structure is formed during the coating formation process, and the polyphenyl esters can only form macro macropores with larger pores, and although the hardness of the coating can be partially reduced, the improvement of the abradability of the coating is limited. When the turbine blade tip contacts the casing, the tip rubs against the dense ceramic layer causing tip wear. In addition, under the condition of service temperature higher than 1150 ℃, the YSZ coating is converted from metastable tetragonal phase to monoclinic phase or cubic phase, and the internal stress of the coating is increased by the phase change accompanied by 4-5% of volume change, so that the risk of cracking and peeling of the coating is increased. In general, most of high-temperature sealing coatings are not mature, and the safety and reliability of the high-temperature sealing coatings are poor.
The high-temperature abradable seal coating is coated on the inner wall of the turbine casing in the aeroengine, so that the effects of protecting blades, reducing oil consumption and improving engine efficiency are achieved. The working temperature of the inlet of a high-pressure turbine of a new generation of aero-engine exceeds 1700 ℃, the service temperature of the abradable seal coating is close to 1350 ℃ and far exceeds the melting point of a metal material, and the conventional metal-based and YSZ ceramic-based abradable seal coating system cannot meet the service requirement.
The service life of the existing YSZ ceramic material is drastically reduced when the service temperature exceeds 1200 ℃, and the service temperature of the high-temperature abradable seal coating is continuously increased along with the continuous increase of the thrust ratio of the aeroengine. Under the condition of higher service temperature, the YSZ coating can be peeled off in a whole piece, and the temperature rise of the aeroengine is seriously restricted.
The method comprises the following steps of (1) preparing a high-temperature brazing material layer by a supersonic flame spraying method in a patent application with publication number of [ CN104561881A ] and named as a preparation method of a high-temperature abradable seal coating; preparing a transition layer on the surface of the high-temperature brazing material layer, wherein the transition layer is prepared by performing high-energy ball milling treatment on a high-temperature brazing material and an MCrAlY spraying material, the total content of which is 50wt% respectively; preserving heat for 12-17 min under vacuum condition at 1000-1150 ℃; preparing an MCrAlY compact layer on the surface of the transition layer; preparing a porous abradable seal coating containing a pore-forming agent on the surface of the compact layer, wherein the raw materials of the porous abradable seal coating containing the pore-forming agent comprise the pore-forming agent and MCrAlY spray coating, and the content of the pore-forming agent is 2-5wt%; removing the pore-forming agent to form a porous abradable seal coating to obtain a high-temperature abradable seal coating; the service temperature is far lower than the actual temperature of the existing engine; because the alloy material has a lower melting point, the actual temperature of the engine far exceeds the highest temperature which can be born by the alloy, and therefore, the alloy material has the defect of insufficient service conditions.
Disclosure of Invention
In order to overcome the above-mentioned drawbacks of the prior art, an object of the present invention is to provide a Hf 6 Ta 2 O 17 Abradable seal coating and preparation method thereof, and Hf is prepared through high-temperature solid-phase reaction 6 Ta 2 O 17 Spraying the transition layer on the nickel-based superalloy substrate by using the powder and then using a supersonic atmospheric plasma spraying technology to obtain a nickel-based superalloy substrate-transition layer, and finally spraying the ceramic layer on the nickel-based superalloy substrate-transition layer to finish Hf 6 Ta 2 O 17 The preparation of the abradable seal coating has the advantages of high service temperature, difficult cracking and peeling of the coating and preparationSimple process, small abrasion loss and good thermal shock resistance.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows:
hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are laminated, wherein the ceramic layer comprises Hf 6 Ta 2 O 17 Ceramic powder, pore-forming agent and lubricating phase, and Hf is calculated according to mass ratio 6 Ta 2 O 17 Ceramic powder: pore-forming agent: lubricating phase= (88-92): (3-5): (3-7).
The Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: hafnium oxide powder and tantalum oxide powder, wherein the hafnium oxide powder comprises the following components in percentage by mass: tantalum oxide powder = 1: (0.35-1.05).
The pore-forming agent is a material which is easy to remove at high temperature and does not negatively affect the coating performance, and is specifically polyphenyl ester or carbon powder or starch.
The lubricating phase is a high-temperature lubricating material, and is specifically hexagonal boron nitride or bentonite or diatomite.
The material of the transition layer is NiCrAlY powder or PtAl alloy powder.
Hf (Hf) 6 Ta 2 O 17 The preparation method of the base abradable seal coating comprises the following steps:
step 1: ball milling hafnium oxide powder and tantalum oxide powder at the rotation speed of 250-350 r/min for 8-10h to obtain a uniformly mixed powder mixed solution, stirring the uniformly mixed powder mixed solution at the rotation speed of 700-1200 r/min and the temperature of 180-220 ℃ until the powder mixed solution becomes gel, putting the gel into a baking oven, drying at the temperature of 75-100 ℃ for 8-10h to obtain uniformly mixed powder to be sintered, and sintering the powder to be sintered at the temperature of 300 ℃ below room temperature at 8-10 ℃/min, the temperature rising rate of 300-950 ℃ at 6-8 ℃/min, the temperature rising rate of 900-1250 ℃ at 4-6 ℃/min and the temperature rising rate of 1250 ℃ at 1250 ℃ for 8-10h to obtain Hf 6 Ta 2 O 17 Ceramic powder; the hafnium oxide powder comprises the following raw materials in percentage by mass: tantalum oxide powder = 1: (0.35-1.05);
step 2: hf prepared in step 1 6 Ta 2 O 17 Ball milling and mixing the ceramic powder, pore-forming agent, lubricating phase, binder, deionized water and absolute ethyl alcohol, and ball milling for 4-6 hours under the condition of rotating speed of 60-90 r/min, wherein the weight ratio of Hf is calculated 6 Ta 2 O 17 Ceramic powder: pore-forming agent: lubrication phase: and (2) a binder: deionized water: absolute ethanol= (88-92): (3-5): (3-7): (94-104): (15-25): (15-25) to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution to obtain sprayable powder of the ceramic layer;
step 4: spraying a transition layer on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 80-120 mu m, so as to obtain a nickel-based superalloy substrate-transition layer; the spraying power is 30-40kW, the flow of argon used in the spraying process is 65-70slpm, and the flow of hydrogen is 2-5slpm;
step 5: spraying the ceramic layer sprayable powder prepared in the step 3 on the surface of the transition layer of the nickel-based superalloy substrate prepared in the step 4 by using a supersonic atmospheric plasma spraying technology to obtain the nickel-based superalloy substrate, the transition layer and the ceramic layer; the spraying power is 35-45kW, the flow of argon is 65-70slpm, and the flow of hydrogen is 2-5slpm in the spraying process;
step 6: continuously repeating the step 5 until the thickness of the ceramic layer is more than 200 mu m to finish the Hf 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
The pretreated nickel-based superalloy substrate in the step 4 is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide.
The binder in the step 2 is polyvinyl alcohol solution or modified ethylene polymer or sodium carboxymethyl cellulose.
Compared with the prior art, the invention has the beneficial effects that:
1. due to Hf 6 Ta 2 O 17 The phase transition temperature is about 2250 ℃, so that no obvious phase transition point exists at 1350 ℃, no volume change caused by phase transition exists, the service temperature can be 1350 ℃ far exceeding the melting point of the alloy material, and the service temperature is obviously improved compared with the traditional metal-based and YSZ ceramic-based abradable seal coating system.
2. Compared with the existing YSZ ceramic-based abradable seal coating, hf 6 Ta 2 O 17 The abradable seal coating has lower thermal expansion coefficient, thus having obvious advantages in the service environment of 1350 ℃, having no obvious peeling at 1350 ℃ and having the characteristic of good thermal shock resistance.
3. The invention prepares Hf through high-temperature solid phase reaction 6 Ta 2 O 17 The powder can prepare the required Hf by only two raw materials 6 Ta 2 O 17 The powder has the characteristics of simple preparation process and mass production.
5. The invention only needs polyvinyl alcohol as a binder to complete granulation, deionized water and absolute ethyl alcohol are added as dispersing agents, and Hf is prepared by a solid phase sintering method 6 Ta 2 O 17 The ceramic powder has the characteristic of simple preparation process.
In conclusion, the invention prepares Hf through high-temperature solid phase reaction 6 Ta 2 O 17 Spraying the transition layer on the nickel-based superalloy substrate by using the powder and then using a supersonic atmospheric plasma spraying technology to obtain a nickel-based superalloy substrate-transition layer, and finally spraying the ceramic layer on the nickel-based superalloy substrate-transition layer to finish Hf 6 Ta 2 O 17 The abradable seal coating is prepared, so the method has the characteristics of high service temperature, difficult cracking and peeling of the coating, simple preparation process, small abrasion loss and good thermal shock resistance.
Drawings
FIG. 1 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 Base abradable seal coating structureSchematic diagram.
FIG. 2 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 And (3) carrying out a microscopic morphology graph of the granular powder of the abradable seal coating.
FIG. 3 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 Surface micro topography of the abradable seal coating.
FIG. 4 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 Microscopic topography of the mirror cross section of the abradable seal coating.
FIG. 5 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 A microscopic topography map of the wear surface after the abrasion test of the abradable seal coating; wherein FIG. 5 (a) is a view of Hf prepared in the present invention 6 Ta 2 O 17 FIG. 5 (b) is a microscopic topography of the wear surface of the abradable seal coating after abrasion testing, and FIG. 5 (b) is a Hf prepared in accordance with the present invention 6 Ta 2 O 17 And (3) carrying out microscopic topography of the abrasion surface of the abrasion seal coating after abrasion test.
FIG. 6 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 The abradable seal coating outputs a result graph against abrasion after abrasion test.
FIG. 7 is a photograph of Hf prepared in the present invention 6 Ta 2 O 17 Macroscopic graph of abradable seal coating after 30 thermal cycles at 1300 ℃.
Detailed Description
The present invention will be described in detail with reference to the accompanying drawings.
Example 1
Referring to FIG. 1, a Hf 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are arranged in a laminated manner; the transition layer is made of NiCrAlY alloy powder; the ceramic layer comprises the following raw materials: 92g of Hf 6 Ta 2 O 17 Ceramic powder, 3g of polyphenyl ester powder and 5g of hexagonal boron nitride powder; the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: 74g of hafnium oxide powder and 26g of tantalum oxide powder.
Hf (Hf) 6 Ta 2 O 17 Base abradableThe preparation method of the sealing coating comprises the following steps:
step 1: adding 74g of hafnium oxide powder and 26g of tantalum oxide powder into absolute ethyl alcohol serving as a ball milling medium, wherein the absolute ethyl alcohol is added in an amount of completely bypassing the ball milling balls, ball milling is carried out for 8 hours at the rotating speed of 250r/min to obtain uniformly mixed powder mixed liquid, the uniformly mixed powder mixed liquid is magnetically stirred and dried, the stirring rotating speed is 700r/min, the drying temperature is 180 ℃ until the powder mixed liquid becomes gel, the gel is put into a baking oven, the temperature is 75 ℃, the baking is carried out for 10 hours, the uniformly mixed powder to be sintered is obtained, the powder to be sintered is sintered, the sintering temperature is respectively that the temperature rising rate is 10 ℃/min at the room temperature of 300 ℃ and the temperature rising rate is 8 ℃/min at the temperature rising rate of 300-950 ℃, the heat preservation is carried out for 1 hour at the temperature of 950 ℃, the temperature rising rate is 5 ℃/min at the temperature rising rate of 900-1250 ℃ and the heat preservation is carried out for 10 hours at the temperature of 1250 ℃ to obtain Hf 6 Ta 2 O 17 Ceramic powder;
step 2: 92gHf prepared in step 1 6 Ta 2 O 17 Ceramic powder, 3g of polyphenyl ester powder, 5g of hexagonal boron nitride powder, 94g of modified ethylene polymer solution, 25g of deionized water and 25g of absolute ethyl alcohol, and ball milling for 4 hours under the condition that the rotating speed is set to be 60r/min in a roller ball mill to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution by using a spray granulator to obtain the Hf-containing ceramic-based multiphase mixed solution 6 Ta 2 O 17 Is a multi-phase granulated powder; the inlet temperature of the spray granulator is 300 ℃, the outlet temperature is 100 ℃, the rotating speed of a spray head is 35rpm, and the rotating speed of a peristaltic pump is 13rpm;
step 4: spraying NiCrAlY alloy powder on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 80 mu m, so as to obtain a nickel-based superalloy substrate-NiCrAlY alloy transition layer; the spraying power is 30kW, the flow of argon used in the spraying process is divided into 65slpm, and the flow of hydrogen is 2slpm; the pretreated nickel-based superalloy substrate is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide;
step 5: using supersonic atmospheric plasma spraying technology to spray the Hf-containing material prepared in the step 3 6 Ta 2 O 17 The multiphase granulating powder is sprayed on the surface of the transition layer prepared in the step 4 to obtain the nickel-based superalloy substrate, namely the NiCrAlY alloy transition layer, namely Hf 6 Ta 2 O 17 A multiphase ceramic layer; the spraying power is 35kW, the flow of argon used in the spraying process is 68slpm, and the flow of hydrogen is 3slpm;
step 6: step 5 is repeated until Hf 6 Ta 2 O 17 The thickness of the multiphase ceramic layer is 300 mu m, and the Hf is finished 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
Example 2
Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are arranged in a laminated manner; the transition layer is made of NiCrAlY alloy powder; the ceramic layer comprises the following raw materials: 88g of Hf 6 Ta 2 O 17 Ceramic powder, 5g of polyphenyl ester powder and 7g of hexagonal boron nitride powder; the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: 59g of hafnium oxide powder and 41g of tantalum oxide powder.
Hf (Hf) 6 Ta 2 O 17 The preparation method of the base abradable seal coating comprises the following steps:
step 1: adding 59g of hafnium oxide powder and 41g of tantalum oxide powder into absolute ethyl alcohol as a ball milling medium, wherein the absolute ethyl alcohol is added in an amount of completely overflowing the ball milling balls, ball milling is carried out for 9 hours at the rotating speed of 300r/min to obtain uniformly mixed powder mixed liquid, the uniformly mixed powder mixed liquid is magnetically stirred and dried, the stirring rotating speed is 900r/min, the temperature is 200 ℃ until the powder mixed liquid becomes gel, the gel is put into a baking oven, the temperature is 85 ℃ and dried for 9 hours to obtain uniformly mixed powder to be sintered, the powder to be sintered is sintered, the sintering temperature is respectively that the temperature rising rate of the powder to be sintered is 9 ℃/min at the room temperature of 300 ℃ or lower, the temperature rising rate of 300-950 ℃ is 7 ℃/min, the heat preservation is carried out for 1 hour at the temperature of 950 ℃, the temperature rising rate of 900-1250 ℃ is 4 ℃/min, and the sintering temperature is kept at the temperature of 1250 ℃Heating for 9h to obtain Hf 6 Ta 2 O 17 Ceramic powder;
step 2: 88gHf prepared in step 1 6 Ta 2 O 17 Ceramic powder, 5g of polyphenyl ester powder, 7g of hexagonal boron nitride powder, 100g of polyvinyl alcohol solution, 15g of deionized water and 15g of absolute ethyl alcohol, and ball milling for 4 hours under the condition of 75r/min of rotating speed to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution by using a spray granulator to obtain the Hf-containing ceramic-based multiphase mixed solution 6 Ta 2 O 17 Is a multi-phase granulated powder; the inlet temperature of the spray granulator is 300 ℃, the outlet temperature is 100 ℃, the rotating speed of a spray head is 35rpm, and the rotating speed of a peristaltic pump is 13rpm;
step 4: spraying NiCrAlY alloy powder on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 100 mu m; obtaining a nickel-based superalloy substrate-NiCrAlY alloy transition layer; the spraying power is 35kW, the flow of argon used in the spraying process is 68slpm, and the flow of hydrogen is 3slpm; the pretreated nickel-based superalloy substrate is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide;
step 5: using supersonic atmospheric plasma spraying equipment to spray the Hf-containing material prepared in the step 3 6 Ta 2 O 17 The multiphase granulating powder is sprayed on the surface of the transition layer prepared in the step 4 to obtain the nickel-based superalloy substrate, namely the NiCrAlY alloy transition layer, namely Hf 6 Ta 2 O 17 A multiphase ceramic layer; the spraying power is 40kW, the flow of argon is 67slpm, and the flow of hydrogen is 5slpm in the spraying process;
step 6: step 5 is repeated until Hf 6 Ta 2 O 17 The thickness of the multiphase ceramic layer is 500 mu m, and the Hf is finished 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
Example 3
Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are arranged in a laminated manner; the transition layer is made of PtAl alloy powder; the ceramic layer comprises the following raw materials: 91g of Hf 6 Ta 2 O 17 Ceramic powder, 4g of polyphenyl ester powder and 5g of diatomite powder; the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: 49g of hafnium oxide powder and 51g of tantalum oxide powder.
Hf (Hf) 6 Ta 2 O 17 The preparation method of the base abradable seal coating comprises the following steps:
step 1: adding 49g of hafnium oxide powder and 51g of tantalum oxide powder into absolute ethyl alcohol serving as a ball milling medium, wherein the absolute ethyl alcohol is added in an amount of completely bypassing the ball milling balls, ball milling is carried out for 10 hours at the rotating speed of 350r/min to obtain uniformly mixed powder mixed solution, magnetic stirring is carried out on the uniformly mixed powder mixed solution for drying, the stirring rotating speed is 1200r/min, the drying temperature is 220 ℃ until the powder mixed solution becomes gel, the gel is put into a baking oven, the temperature is 100 ℃, the baking is carried out for 8 hours, the uniformly mixed powder to be sintered is obtained, the powder to be sintered is sintered, the sintering temperature is respectively that the heating rate of the powder to be sintered is lower than the room temperature of 300 ℃ and is 8 ℃/min, the heating rate of the powder to be sintered is 6 ℃/min, the sintering temperature is kept at the temperature of 950 ℃ and the heating rate of the powder to be 6 ℃/min, the sintering temperature is kept at the temperature of 900 ℃ to 1250 ℃ and the heating rate of the powder to be kept at the temperature of 1250 ℃ for 8h, and the Hf is obtained 6 Ta 2 O 17 Ceramic powder;
step 2: 91gHf prepared in step 1 6 Ta 2 O 17 Ceramic powder, 4g of polyphenyl ester powder, 5g of diatomite powder, 104g of carboxymethyl cellulose sodium solution, 20g of deionized water and 20g of absolute ethyl alcohol, and ball milling for 6 hours under the condition that the rotating speed is set to 90r/min in a roller ball mill to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution by using a spray granulator to obtain the Hf-containing ceramic-based multiphase mixed solution 6 Ta 2 O 17 Is a multi-phase granulated powder; the inlet temperature of the spray granulator is 300 ℃, the outlet temperature is 100 ℃, the rotating speed of the spray nozzle is 35rpm,the peristaltic pump has a rotational speed of 13rpm;
step 4: spraying PtAl alloy powder on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 100 mu m, so as to obtain a nickel-based superalloy substrate-PtAl alloy transition layer; the spraying power is 40kW, the flow of argon used in the spraying process is 70slpm, and the flow of hydrogen is 5slpm; the pretreated nickel-based superalloy substrate is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide;
step 5: using supersonic atmospheric plasma spraying equipment to spray the Hf-containing material prepared in the step 3 6 Ta 2 O 17 The multiphase granulating powder is sprayed on the surface of the transition layer prepared in the step 4 to obtain the nickel-based superalloy substrate, namely the NiCrAlY alloy transition layer, namely Hf 6 Ta 2 O 17 A multiphase ceramic layer; the spraying power is 45kW, the flow of argon used in the spraying process is 70slpm, and the flow of hydrogen is 2slpm;
step 6: continuously repeating the step 5, hf 6 Ta 2 O 17 The thickness of the multiphase ceramic layer is 1000 mu m, and the Hf is finished 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
Example 4
Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are arranged in a laminated manner; the transition layer is made of PtAl alloy powder; the ceramic layer comprises the following raw materials: 90g of Hf 6 Ta 2 O 17 Ceramic powder, 3g of carbon powder and 7g of diatomite powder; the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: 49g of hafnium oxide powder and 51g of tantalum oxide powder.
Hf (Hf) 6 Ta 2 O 17 The preparation method of the base abradable seal coating comprises the following steps:
step 1: 49g of hafnium oxide powder and 51g of tantalum oxide powder are added with absolute ethyl alcohol as a ball milling medium, the absolute ethyl alcohol is added in an amount of completely bypassing the ball milling balls, and the rotating speed is 350r/min, ball milling for 10 hours to obtain a uniformly mixed powder mixed solution, magnetically stirring the uniformly mixed powder mixed solution for drying, wherein the stirring speed is 1200r/min, the stirring temperature is 220 ℃, the powder mixed solution is stirred until the powder mixed solution becomes gel, the powder is put into a baking oven, the temperature is 100 ℃, the baking is carried out for 8 hours to obtain a uniformly mixed powder to be sintered, the powder to be sintered is sintered, the sintering temperature is respectively that the temperature rising rate is 8 ℃ below the room temperature of 300 ℃, the temperature rising rate is 6 ℃/min, the temperature keeping temperature is 1.5 hours at 950 ℃, the temperature rising rate is 6 ℃/min, and the temperature keeping temperature is 1250 ℃ for 8 hours, thereby obtaining Hf 6 Ta 2 O 17 Ceramic powder;
step 2: 90gHf prepared in step 1 6 Ta 2 O 17 Ceramic powder, 3g of carbon powder, 7g of diatomite powder, 100g of carboxymethyl cellulose sodium solution, 25g of deionized water and 20g of absolute ethyl alcohol, and ball milling for 6 hours under the condition that the rotating speed is set to 90r/min in a roller ball mill to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution by using a spray granulator to obtain the Hf-containing ceramic-based multiphase mixed solution 6 Ta 2 O 17 Is a multi-phase granulated powder; the inlet temperature of the spray granulator is 300 ℃, the outlet temperature is 100 ℃, the rotating speed of a spray head is 35rpm, and the rotating speed of a peristaltic pump is 13rpm;
step 4: spraying PtAl alloy powder on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 100 mu m, so as to obtain a nickel-based superalloy substrate-PtAl alloy transition layer; the spraying power is 35kW, the flow of argon used in the spraying process is 70slpm, and the flow of hydrogen is 5slpm; the pretreated nickel-based superalloy substrate is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide;
step 5: using supersonic atmospheric plasma spraying equipment to spray the Hf-containing material prepared in the step 3 6 Ta 2 O 17 The multiphase granulating powder is sprayed on the surface of the transition layer prepared in the step 4 to obtain the nickel-based superalloy substrate-NiCrAlY alloy transitionLayer- - -Hf 6 Ta 2 O 17 A multiphase ceramic layer; the spraying power is 45kW, the flow of argon used in the spraying process is 68slpm, and the flow of hydrogen is 3slpm;
step 6: continuously repeating the step 5, hf 6 Ta 2 O 17 The thickness of the multiphase ceramic layer is 900 mu m, and the Hf is finished 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
Example 5
Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are arranged in a laminated manner; the transition layer is made of NiCrAlY alloy powder; the ceramic layer comprises the following raw materials: 91g of Hf 6 Ta 2 O 17 Ceramic powder, 4g of starch and 5g of bentonite powder; the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: 70g of hafnium oxide powder and 30g of tantalum oxide powder.
Hf (Hf) 6 Ta 2 O 17 The preparation method of the base abradable seal coating comprises the following steps:
step 1: adding absolute ethyl alcohol serving as a ball milling medium into 70g of hafnium oxide powder and 30g of tantalum oxide powder, wherein the absolute ethyl alcohol is added in an amount of completely bypassing the ball milling balls, ball milling is carried out for 10 hours at the rotating speed of 350r/min to obtain uniformly mixed powder mixed liquid, the uniformly mixed powder mixed liquid is magnetically stirred and dried, the stirring rotating speed is 1200r/min, the drying temperature is 210 ℃ until the powder mixed liquid becomes gel, the gel is put into a baking oven, the temperature is 90 ℃ and dried for 8 hours to obtain uniformly mixed powder to be sintered, the powder to be sintered is sintered, the sintering temperature is respectively that the heating rate of the powder to be sintered is 10 ℃/min at the room temperature of 300 ℃ and the heating rate of the powder to be sintered is 7 ℃/min at the temperature of 300-950 ℃, the heating rate of the powder to be sintered is 6 ℃/min at the temperature of 900-1250 ℃ and the temperature of the powder to be sintered for 8 hours at the temperature of 1250 ℃ to obtain Hf 6 Ta 2 O 17 Ceramic powder;
step 2: 91gHf prepared in step 1 6 Ta 2 O 17 Ceramic powder, 4g of starch, 5g of bentonite powder, 104g of polyvinyl alcohol solution, 20g of deionized water and25g of absolute ethyl alcohol is ball-milled for 6 hours under the condition that the rotating speed is set to 90r/min in a roller ball mill, and Hf is obtained 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution by using a spray granulator to obtain the Hf-containing ceramic-based multiphase mixed solution 6 Ta 2 O 17 Is a multi-phase granulated powder; the inlet temperature of the spray granulator is 300 ℃, the outlet temperature is 100 ℃, the rotating speed of a spray head is 35rpm, and the rotating speed of a peristaltic pump is 13rpm;
step 4: spraying PtAl alloy powder on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 100 mu m, so as to obtain a nickel-based superalloy substrate-PtAl alloy transition layer; the spraying power is 40kW, the flow of argon used in the spraying process is 65slpm, and the flow of hydrogen is 3slpm; the pretreated nickel-based superalloy substrate is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide;
step 5: using supersonic atmospheric plasma spraying equipment to spray the Hf-containing material prepared in the step 3 6 Ta 2 O 17 The multiphase granulating powder is sprayed on the surface of the transition layer prepared in the step 4 to obtain the nickel-based superalloy substrate, namely the NiCrAlY alloy transition layer, namely Hf 6 Ta 2 O 17 A multiphase ceramic layer; the spraying power is 45kW, the flow of argon used in the spraying process is 70slpm, and the flow of hydrogen is 2slpm;
step 6: continuously repeating the step 5, hf 6 Ta 2 O 17 The thickness of the multiphase ceramic layer is 500 mu m, and the Hf is finished 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
FIG. 2 shows Hf prepared in accordance with the present invention 6 Ta 2 O 17 Microscopic morphology of granulated powder of abradable seal coating, as can be seen, hf 6 Ta 2 O 17 The granulated powder of the abradable seal coating is mixed powder with good sphere shape, so the granulated powder can be used as good spraying powder.
Referring to FIG. 3, the present inventionExplicitly prepared Hf 6 Ta 2 O 17 The abradable seal coating is composed of more molten granulating powder, is in a flat shape, has partially molten granules and better porosity, and has the characteristics of higher deposition efficiency and mass production.
Referring to FIG. 4, hf prepared in the present invention 6 Ta 2 O 17 The thickness of the transition layer of the abradable seal coating is 100 mu m, and the thickness of the ceramic layer is about 400 mu m, so that the abradable seal coating has controllable thickness and has the characteristic of simple preparation process.
Referring to FIG. 5, FIG. (a) is a view of Hf prepared in the present invention 6 Ta 2 O 17 Microscopic topography of the abradable seal coating after abrasion, an enlarged partial view of the abraded area of FIG. (b), from which it can be seen that the abraded area exhibits primarily plow marks, illustrating the Hf prepared in accordance with the present invention 6 Ta 2 O 17 The abradable seal coating has the characteristics of small abrasion loss and difficult cracking and peeling of the coating.
Referring to FIG. 6, hf prepared in the present invention 6 Ta 2 O 17 The abrasion output result graph of the abradable seal coating shows that the abradable seal coating has the characteristics of small abrasion loss and difficult cracking and peeling of the coating, and in the abradable experiment, hf 6 Ta 2 O 17 The base seal coating has smaller abrasion loss after abrasion, and the problems of coating adhesion, blade tip damage and the like do not occur.
Referring to FIG. 7, the Hf prepared in the present invention 6 Ta 2 O 17 The thermal cycle macroscopic graph of the base seal coating is thermally cycled for 30 times at 1350 ℃, so that the defect that peeling does not occur can be seen, a plurality of closed-loop cracks appear on the surface of the coating, the stress is released, the peeling of the coating is delayed, and the Hf prepared by the invention is illustrated 6 Ta 2 O 17 The abradable seal coating has the characteristics of good thermal shock resistance and high service temperature, and can be used as an abradable coating of a high-temperature stator of a turbine part of an aeroengine.
As can be seen from the examples, compared with the prior art, the present invention adopts high temperature solid phase reaction to prepare Hf 6 Ta 2 O 17 Powder and then the transition layer is formed by utilizing the ultrasonic atmospheric plasma spraying technologySpraying on the nickel-based superalloy substrate to obtain a nickel-based superalloy substrate-transition layer, and finally spraying a ceramic layer on the nickel-based superalloy substrate-transition layer to complete Hf 6 Ta 2 O 17 The abradable seal coating is prepared, so the method has the characteristics of high service temperature, difficult cracking and peeling of the coating, simple preparation process, small abrasion loss and good thermal shock resistance.
Claims (9)
1. Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are laminated, and is characterized in that the ceramic layer comprises Hf as raw materials 6 Ta 2 O 17 Ceramic powder, pore-forming agent and lubricating phase, and Hf is calculated according to mass ratio 6 Ta 2 O 17 Ceramic powder: pore-forming agent: lubricating phase= (88-92): (3-5): (3-7).
2. A kind of Hf according to claim 1 6 Ta 2 O 17 A base abradable seal coating characterized by the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: hafnium oxide powder and tantalum oxide powder, wherein the hafnium oxide powder comprises the following components in percentage by mass: tantalum oxide powder=1 (0.35-1.05).
3. A kind of Hf according to claim 1 6 Ta 2 O 17 The base abradable seal coating is characterized in that the pore-forming agent is a material which is easy to remove at high temperature and does not negatively affect the performance of the coating, and is specifically polyphenyl ester or carbon powder or starch.
4. A kind of Hf according to claim 1 6 Ta 2 O 17 The base abradable seal coating is characterized in that the lubricating phase is a high-temperature lubricating material, in particular hexagonal boron nitride or bentonite or diatomite.
5. A kind of Hf according to claim 1 6 Ta 2 O 17 The base abradable seal coating is characterized in that the material of the transition layer is NiCrAlY powder or PtAl alloy powder.
6. Hf according to any one of claims 1 to 5 6 Ta 2 O 17 The preparation method of the base abradable seal coating is characterized by comprising the following steps:
step 1: ball milling hafnium oxide powder and tantalum oxide powder at the rotation speed of 250-350 r/min for 8-10h to obtain a uniformly mixed powder mixed solution, stirring the uniformly mixed powder mixed solution at the rotation speed of 700-1200 r/min and the temperature of 180-220 ℃ until the powder mixed solution becomes gel, putting the gel into a baking oven, drying at the temperature of 75-100 ℃ for 8-10h to obtain uniformly mixed powder to be sintered, and sintering the powder to be sintered at the temperature of 300 ℃ below room temperature at 8-10 ℃/min, the temperature rising rate of 300-950 ℃ at 6-8 ℃/min, the temperature rising rate of 900-1250 ℃ at 4-6 ℃/min and the temperature rising rate of 1250 ℃ at 1250 ℃ for 8-10h to obtain Hf 6 Ta 2 O 17 Ceramic powder; the hafnium oxide powder comprises the following raw materials in percentage by mass: tantalum oxide powder = 1: (0.35-1.05);
step 2: hf prepared in step 1 6 Ta 2 O 17 Ball milling and mixing the ceramic powder, pore-forming agent, lubricating phase, binder, deionized water and absolute ethyl alcohol, and ball milling for 4-6 hours under the condition of rotating speed of 60-90 r/min, wherein the weight ratio of Hf is calculated 6 Ta 2 O 17 Ceramic powder: pore-forming agent: lubrication phase: and (2) a binder: deionized water: absolute ethanol= (88-92): (3-5): (3-7): (94-104): (15-25): (15-25) to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution to obtain sprayable powder of the ceramic layer;
step 4: spraying a transition layer on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 80-120 mu m, so as to obtain a nickel-based superalloy substrate-transition layer; the spraying power is 30-40kW, the flow of argon used in the spraying process is 65-70slpm, and the flow of hydrogen is 2-5slpm;
step 5: spraying the ceramic layer sprayable powder prepared in the step 3 on the surface of the transition layer of the nickel-based superalloy substrate prepared in the step 4 by using a supersonic atmospheric plasma spraying technology to obtain the nickel-based superalloy substrate, the transition layer and the ceramic layer; the spraying power is 35-45kW, the flow of argon is 65-70slpm, and the flow of hydrogen is 2-5slpm in the spraying process;
step 6: continuously repeating the step 5 until the thickness of the ceramic layer is more than 200 mu m to finish the Hf 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
7. A kind of Hf as claimed in claim 6 6 Ta 2 O 17 The preparation method of the base abradable seal coating is characterized in that the pretreated nickel-base superalloy substrate in the step 4 is a nickel-base superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide.
8. A kind of Hf as claimed in claim 6 6 Ta 2 O 17 The preparation method of the base abradable seal coating is characterized in that the binder in the step 2 is polyvinyl alcohol solution or modified ethylene polymer or sodium carboxymethyl cellulose.
9. Hf (Hf) 6 Ta 2 O 17 The base abradable seal coating comprises a nickel-base superalloy substrate, a transition layer and a ceramic layer which are arranged in a laminated manner, and is characterized in that the transition layer is made of NiCrAlY alloy powder; the ceramic layer comprises the following raw materials: 88g of Hf 6 Ta 2 O 17 Ceramic powder, 5g of polyphenyl ester powder and 7g of hexagonal boron nitride powder; the Hf 6 Ta 2 O 17 The ceramic powder comprises the following raw materials: 59g of hafnium oxide powder and 41g of tantalum oxide powder;
the one kind of Hf 6 Ta 2 O 17 The preparation method of the base abradable seal coating comprises the following steps:
step 1: adding 59g of hafnium oxide powder and 41g of tantalum oxide powder into absolute ethyl alcohol as a ball milling medium, wherein the absolute ethyl alcohol is added in an amount of completely overflowing the ball milling balls, ball milling is carried out for 9 hours at the rotating speed of 300r/min to obtain uniformly mixed powder mixed liquid, the uniformly mixed powder mixed liquid is magnetically stirred and dried, the rotating speed of 900r/min and the temperature of 200 ℃ are stirred until the powder mixed liquid becomes gel, the gel is put into a baking oven, the temperature is 85 ℃ and is dried for 9 hours to obtain uniformly mixed powder to be sintered, the powder to be sintered is sintered, the sintering temperature is respectively that the temperature rising rate of the powder to be sintered is lower than the room temperature of 300 ℃ and is 9 ℃/min, the temperature rising rate of 300-950 ℃ is 7 ℃/min, the heat preservation is carried out for 1 hour at the temperature of 950 ℃, the temperature rising rate of 900-1250 ℃ is 4 ℃/min, and the heat preservation is carried out for 9 hours at the temperature of 1250 ℃ to obtain Hf 6 Ta 2 O 17 Ceramic powder;
step 2: 88gHf prepared in step 1 6 Ta 2 O 17 Ceramic powder, 5g of polyphenyl ester powder, 7g of hexagonal boron nitride powder, 100g of polyvinyl alcohol solution, 15g of deionized water and 15g of absolute ethyl alcohol, and ball milling for 4 hours under the condition of 75r/min of rotating speed to obtain Hf 6 Ta 2 O 17 Ceramic-based multiphase mixed liquor;
step 3: hf prepared in step 2 6 Ta 2 O 17 Granulating and drying the ceramic-based multiphase mixed solution by using a spray granulator to obtain the Hf-containing ceramic-based multiphase mixed solution 6 Ta 2 O 17 Is a multi-phase granulated powder; the inlet temperature of the spray granulator is 300 ℃, the outlet temperature is 100 ℃, the rotating speed of a spray head is 35rpm, and the rotating speed of a peristaltic pump is 13rpm;
step 4: spraying NiCrAlY alloy powder on the pretreated nickel-based superalloy substrate by using a supersonic atmospheric plasma spraying technology until the thickness of the transition layer is 100 mu m; obtaining a nickel-based superalloy substrate-NiCrAlY alloy transition layer; the spraying power is 35kW, the flow of argon used in the spraying process is 68slpm, and the flow of hydrogen is 3slpm; the pretreated nickel-based superalloy substrate is a nickel-based superalloy substrate with certain roughness obtained by sand blasting of aluminum oxide;
step 5: using supersonic atmospheric plasma spraying equipment to spray the Hf-containing material prepared in the step 3 6 Ta 2 O 17 The multiphase granulating powder is sprayed on the surface of the transition layer prepared in the step 4 to obtain the nickel-based superalloy substrate, namely the NiCrAlY alloy transition layer, namely Hf 6 Ta 2 O 17 A multiphase ceramic layer; the spraying power is 40kW, the flow of argon is 67slpm, and the flow of hydrogen is 5slpm in the spraying process;
step 6: step 5 is repeated until Hf 6 Ta 2 O 17 The thickness of the multiphase ceramic layer is 500 mu m, and the Hf is finished 6 Ta 2 O 17 And (3) preparing the base abradable seal coating.
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| CN202310697906.2A CN116732460A (en) | 2023-06-13 | 2023-06-13 | Hf (Hf) 6 Ta 2 O 17 Base abradable seal coating and preparation method thereof |
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| CN202310697906.2A CN116732460A (en) | 2023-06-13 | 2023-06-13 | Hf (Hf) 6 Ta 2 O 17 Base abradable seal coating and preparation method thereof |
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| CN (1) | CN116732460A (en) |
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