CN114686797A - Multilayer self-healing ceramic coating and preparation method thereof - Google Patents

Multilayer self-healing ceramic coating and preparation method thereof Download PDF

Info

Publication number
CN114686797A
CN114686797A CN202210363583.9A CN202210363583A CN114686797A CN 114686797 A CN114686797 A CN 114686797A CN 202210363583 A CN202210363583 A CN 202210363583A CN 114686797 A CN114686797 A CN 114686797A
Authority
CN
China
Prior art keywords
self
layer
healing
coating
tic
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
CN202210363583.9A
Other languages
Chinese (zh)
Inventor
李微
余昌科
胡胜男
李聪
黄伟颖
任延杰
周立波
陈荐
陈建林
李磊
张英哲
廖力达
陈安琪
吴泽林
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Changsha University of Science and Technology
Original Assignee
Changsha University of Science and Technology
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Changsha University of Science and Technology filed Critical Changsha University of Science and Technology
Priority to CN202210363583.9A priority Critical patent/CN114686797A/en
Publication of CN114686797A publication Critical patent/CN114686797A/en
Priority to JP2023023135A priority patent/JP7482463B2/en
Withdrawn legal-status Critical Current

Links

Images

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
    • C23C4/12—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
    • 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
    • C23C4/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • 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
    • C23C4/10—Oxides, borides, carbides, nitrides or silicides; Mixtures thereof
    • 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
    • C23C4/18—After-treatment

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Coating By Spraying Or Casting (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)

Abstract

The invention relates to a multilayer self-healing ceramic coating and a preparation method thereof, belonging to the technical field of metal material protection. The coating comprises: spraying a NiCrAlY bonding layer, a TiC self-healing layer and Al on the surface of the metal substrate from inside to outside2O3‑13％TiO2A ceramic environmental barrier layer; heat treatment to obtain; the thickness of the NiCrAlY bonding layer is 50 mu m; the thickness of the TiC self-healing layer is 30-60 mu m; the Al is2O3‑13％TiO2The thickness of the ceramic environmental barrier layer is 100-120 μm. The invention also provides a preparation method of the coating. Hair brushThe prepared ceramic coating has the advantages of low self-healing temperature, high coating bonding strength and no influence on the mechanical property of the base material.

Description

Multilayer self-healing ceramic coating and preparation method thereof
Technical Field
The invention relates to the field of metal material protection, in particular to a multilayer self-healing ceramic coating and a preparation method thereof.
Background
Supercritical carbon dioxide (S-CO)2) The Brayton cycle technology has the advantages of high cycle efficiency, compact structure and the like, can reduce the investment cost of a large-scale power station, and is a new way for realizing high-efficiency clean power generation of coal. Compared with Rankine cycle working medium-steam of the traditional thermal power generating unit, the supercritical carbon dioxide of the heat exchange working medium has more stable chemical property and weak corrosivity at 400 ℃, but because of supercritical CO2Brayton cycle for high temperature, high pressure (28MPa/620 ℃ or higher) conditionsCorrosion of the material is still difficult to avoid.
The heat-resistant steel is subjected to S-CO treatment by oxide film falling, surface carbon deposition, internal carburization and the like2The main corrosion problem in (1). CO obtained based on combustion of coal and petrochemical resources2As S-CO2For the Brayton cycle working medium system, the doping water vapor is supercritical CO2Brayton cycle systems are unavoidable. Research shows that water with the content of 0-0.1% can accelerate carbon steel to be in S-CO2Corrosion rate of S-CO containing wet steam2Cause pitting corrosion and oxide film cracking of stainless steel, especially high pressure intake valve and supercritical CO2In the case of direct fluid contact, the valve fails, thereby affecting the service life of the entire system. Thus, the high temperature corrosion resistance of the valve is S-CO2One of the problems that needs to be solved in power generation systems.
The basic idea for improving the carburization resistance of the alloy material is to form a compact and continuous oxide layer with high stability on the surface of the material to prevent the infiltration of carbon. Aluminizing is the most common protection method for high temperature carburization resistance, but because an aluminide coating needs longer time and higher temperature, the mechanical property of a base material is reduced, the bonding property of the coating and a matrix is poor, the aluminized layer is easy to peel off, and Al is enabled to be obtained2O3The protective properties of the coating are not fully developed. The ceramic material has excellent performances of high temperature resistance, corrosion resistance and the like, and the ceramic used as the coating layer has wide application in the technical fields of heat insulation, oxidation resistance, seepage prevention and the like. However, the brittleness of the ceramic material and defects such as pores and cracks in the coating greatly affect the reliability and consistency of the material performance. Thus, the porosity of the ceramic coating and the resistance to cracking at high temperatures can become critical issues affecting its application.
The ceramic coating is added with a self healing agent, and oxides generated by oxidation reaction at high temperature block 'channels' formed by coating cracking, so that the mechanical property of the coating is improved, and the oxygen in the environment is locally inhibited from permeating into the coating too fast, so that the coating is prevented from premature failure in the service process. With respect to the development of self-healing ceramic materials, the focus has been primarily on SiC，TiB2The ceramic is prepared by the following steps of (1) waiting for ceramic, but the healing condition is harsh, the healing temperature is above 1400 ℃, the melting point of the oxide ceramic is close, and the main healing mechanism is similar to that of heavy sintering. Meanwhile, the problem of serious growth of crystal grains exists due to higher healing temperature, so that the performance of the ceramic material is greatly reduced. For example, patent application No. CN201810351184.4, polynary complex phase nano boride, corresponding ultra-high temperature oxidation resistant coating and preparation method thereof, discloses a high temperature self-healing coating, an embedding infiltration method is adopted to prepare a SiC bottom layer, and a low pressure plasma spraying process is adopted to prepare HfB with the particle size of 200-300 mu m2-SiC-TiB2And (6) complex phase surface layer. The self-healing temperature of the composite coating of the component is as high as 1800 ℃, and the composite coating is not suitable for environments with medium and low temperatures. Patent application No. CN201910174390.7 discloses a high-temperature ablation-resistant self-healing coating, a preparation method and application thereof, wherein the high-temperature ablation-resistant self-healing coating is prepared by preparing a SiC transition layer with the thickness of 20-40 mu m by a chemical vapor deposition method, and preparing ZrC-SiC-Gd with the thickness of 100-120 mu m by a vacuum plasma spraying method 203The self-healing phase of the coating is SiC, and the healing temperature is 1000-1500 ℃.
Document "preparation of TiC + (Al) by plasma spraying2O3/TiC)+Al2O3Self-healing coatings (silicate bulletin 2011, 39(11), 1844-2O3After powder is sprayed and granulated, TiC + (Al) is prepared on the surface of metal by adopting an ion spraying method2O3/TiC)+Al2O3The self-healing coating has high spraying porosity, the porosity of TiC can be reduced by more than 90% after the TiC is self-healed at 600 ℃, but the bonding strength is low, and the coating is easy to fall off and lose efficacy in a long-time service process. The patent with the application number of 201410100936.1 discloses the preparation of Al by combining a liquid phase method and a vapor deposition method2O3Method of TiC coating. The method has expensive equipment, complex technology, fussy process and high requirement on technical level, and the prepared Al2O3The coating thickness of the/TiC coating is only 10-30 μm,the long-term operation requirement of key parts of the thermal power generating unit cannot be met.
It is worth noting that the mechanical properties of the material are changed while the corrosion resistance of the material is improved. Generally speaking, the introduction of defects such as pores and cracks into the coating layer can cause overall reduction of mechanical properties such as yield strength, tensile strength and elongation of the material, because the difference of the elastic modulus of the ceramic and the matrix is most likely to form crack sources at a bonding interface, thereby causing difficulty in reaching the use standard of the material. In the research of Microlattice evaluation and Tensile Properties of Ti-Al-V Alloys managed by Plasma Spraying and substrate Vacuum Hot Pressing (Materials transformations, 2006,47(4), 1198 and 1203), the Ti-Al-V alloy coating is prepared on a stainless steel plate by adopting a Plasma Spraying technology, and the Tensile strength of the material is mainly influenced by the infiltration amount of O element in the Spraying process, but the elongation of the material is obviously reduced no matter the O content. In the study of the properties of carbon nano tube reinforced aluminum-silicon alloy (compositions Part A: Applied Science and Manufacturing,2009,40(5), 589-594.), uniaxial Tensile test was performed on the plasma sprayed multi-walled carbon nanotube reinforced aluminum-silicon alloy, and the results showed that the elastic modulus of the material was increased by 78%, the breaking strain was decreased by 46%, and the plasticity was greatly decreased. Therefore, the corrosion resistance of the material is improved, and the mechanical property of the material is guaranteed.
Disclosure of Invention
Therefore, the technical problem to be solved by the invention is to overcome the defects in the prior art, so that the self-healing ceramic coating with the multilayer structure and the preparation method thereof are provided, the process is simple, the high-temperature oxidation resistance is good, the self-healing temperature is low, the bonding strength of the coating and a matrix is high, the microcrack self-healing and self-healing capabilities of the coating are strong, the porosity introduced in the preparation process of the coating can be well reduced, the corrosion resistance of the valve of the supercritical carbon dioxide thermal power unit is excellent, and the service life and the reliability of the coating in the service process are obviously improved.
A multilayer self-healing ceramic coating, comprising: on a metal substrateThe surface is sprayed with NiCrAlY bonding layer, TiC self-healing layer and Al from inside to outside2O3-13％TiO2A ceramic environmental barrier layer; is obtained by heat treatment.
Preferably, the NiCrAlY bond coat has a thickness of 45-55 μm; the thickness of the TiC self-healing layer is 40-60 mu m; the Al is2O3-13％TiO2The thickness of the ceramic environmental barrier layer is 100-120 μm.
Preferably, the metal matrix comprises austenitic stainless steel.
Preferably, the heat treatment temperature is 620-650 ℃.
The invention also provides a preparation method of the multilayer self-healing ceramic coating, which comprises the following steps:
s1, mechanically polishing the surface of the substrate;
s2, performing sand blasting treatment on the surface of the substrate:
carrying out sand blasting treatment on the mechanically polished substrate, wherein the surface roughness Ra of the substrate after sand blasting is 7-8;
s3, surface plasma spraying:
mixing NiCrAlY, TiC and Al2O3-13％TiO2Drying the powder, and screening the powder with the particle size of 15-45 mu m; pre-treated NiCrAlY, TiC and Al2O3-13％TiO2Sequentially forming a 45-55 mu m NiCrAlY bonding layer, a 30-60 mu m TiC self-healing intermediate layer and a 100-120 mu m Al-doped layer on the substrate treated in the step S2 by adopting a plasma spraying mode for the powder2O3-13％TiO2A ceramic environmental barrier layer;
the plasma spraying mode is any one of supersonic plasma spraying, atmospheric plasma spraying, low-pressure plasma spraying or vacuum plasma spraying, and only the porosity of each coating after spraying can be achieved, and the porosity of the NiCrAlY bonding layer is 3% -7%; the porosity of the TiC self-healing layer is 10-15%; the porosity of the AT13 ceramic environmental barrier layer is 5-9%.
The embodiment of the invention adopts supersonic plasma spraying, in particular to a HEBJet supersonic plasma spraying system which is specifically used for sprayingThe number is as follows: a NiCrAlY bonding layer with spraying power of 35-45 kW; the main steam flow is 110-. A TiC layer self-healing layer is sprayed with the spraying power of 40-50 kW; the main steam flow is 110-130L/min, the auxiliary steam flow is 70-90L/min, the powder feeding speed is 30-40g/min, the displacement speed is 400-600mm/s, the spraying distance is 100-140mm, and the single-channel spraying distance is 1-3 mm. Al (Al)2O3-13％TiO2The spraying power of the ceramic environment barrier layer is 45-55 kW; the main steam flow is 110-130L/min, the auxiliary steam flow is 70-90L/min, the powder feeding speed is 30-40g/min, the displacement speed is 400-600mm/s, the spraying distance is 100-140mm, and the single-channel spraying distance is 1-3 mm.
S4, self-healing heat treatment:
for the prepared NiCrAlY/TiC/Al2O3-13％TiO2And (3) carrying out primary heat treatment on the composite coating, putting the sprayed sample into a resistance furnace, heating to 620-650 ℃, carrying out heat preservation treatment, opening the furnace door every 2 hours, putting in external air, and cooling to room temperature along with the furnace after 10-14 hours to obtain the multilayer-structure self-healing ceramic coating.
Preferably, step S1 specifically includes: polishing the matrix by using 80-1200-mesh sand paper until no obvious scratch is visible to naked eyes, then cleaning the matrix in ultrasonic waves for 5-20 min by using acetone, removing oil, ultrasonically cleaning the matrix for 5-20 min by using absolute ethyl alcohol, removing stains, and finally drying the matrix in a drying oven at 80 ℃ for 20-40 min.
Preferably, step S2 specifically includes: and (3) sand blasting the mechanically polished substrate under 0.6-0.9 MPa of high-pressure nitrogen, wherein the abrasive is 12-mesh white corundum particles, the sand blasting time is 10-20 min, the sand blasting distance is 2cm, and the surface roughness Ra after sand blasting is 7-8 of the substrate.
Preferably, in step S3, the drying temperature is 130 ℃.
The self-healing coating with the multilayer structure disclosed by the invention has high bonding strength and can self-heal at the temperature of 620-650 ℃. Therefore, the invention also provides the application of the multilayer self-healing ceramic coating in supercritical CO2Use in a valve in a brayton cycle system.
The technical scheme of the invention has the following advantages:
the invention utilizes supersonic plasma spraying to prepare a self-healing coating with a multilayer structure on the surface of austenitic stainless steel, which comprises an austenitic stainless steel substrate, a NiCrAlY bonding layer with the thickness of 40-60 mu m, a TiC self-healing layer with the thickness of 40-60 mu m and Al with the thickness of 100-120 mu m from inside to outside in sequence2O3-13％TiO2The ceramic environment barrier layer has good surface macroscopic appearance of the coating, good bonding condition between internal layers, bonding strength higher than 27.4Mpa, porosity lower than 10 percent and microhardness of the coating of 329.5-967.9 HV. According to XRD analysis, the phases of the layers are mainly Al2O3、TiO2、Al2TiO5、TiC、Ni3Al and metal elementary phases.
After the coating is self-healing oxidized for 10 hours at the temperature of 620-650 ℃, the porosity of the coating is further reduced to below 1 percent and reduced by over 90 percent, and TiC self-healing phases in the TiC layer are oxidized to generate TiO2Effectively filling pores and cracks in the coating, wherein the TiO2TiO of (TiC) layer2Mostly rutile type TiO2The microhardness is improved to above 828.5HV, and the NiCrAlY layer and TiO are coated on the surface of the substrate2The bonding section of The (TiC) layer becomes tighter, and the adhesive strength is improved to 50.16MPa or more.
On one hand, the multilayer self-healing coating prepared by the invention has lower porosity by preparing the coating by supersonic plasma spraying, and further reduces (especially NiCrAlY layer) after self-healing, thereby overcoming the defects brought by the coating. On the other hand, Ni element in the sprayed NiCrAlY layer is mainly gamma′-Ni3The precipitation of the Al phase in the coating is beneficial to reduce the large difference in elastic modulus between the ceramic layer and the metal substrate. The NiCrAlY coating and the base body are combined, the section is compact and smooth, and therefore the adverse effect of the coating on the yield strength and the elongation of the material is improved.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and other drawings can be obtained by those skilled in the art without creative efforts.
FIG. 1 shows the basic morphology and the combined cross-sectional morphology of the coating in the as-sprayed state and after heat treatment;
wherein (a) - (d) are as-sprayed; (e) after (h) heat treatment;
FIG. 2 is an XRD spectrogram of each coating in a powder state, a spraying state and after self-healing;
wherein, (a) NiCrAlY layer, (b) TiC layer, (c) AT13 layer (i.e. Al)2O3-13％TiO2The same applies below);
FIG. 3 is a graph showing the bond strengths of the self-healing coatings obtained in example 1 and comparative example 1;
FIG. 4 is a porosity curve for different self-healing times;
FIG. 5 is a graph of the porosity analysis of the coating at different self-healing times;
wherein, (a) is in a spray state; (b)1 h; (c)2 h; (d)6 h; (e)10 h; (f)14 h;
FIG. 6 is a microhardness curve of different depths before and after oxidation of the self-healing coating;
FIG. 7 is an engineering stress-engineering strain curve for a tensile test of 3 samples at room temperature;
FIG. 8 is a graph comparing the bond strengths of example 1 and comparative examples 2-3;
FIG. 9 is a macro photograph of tensile test of TiCN/TiC/AT13 coating prepared by comparative example;
FIG. 10 is a macro photograph of tensile test on 3 samples at room temperature;
wherein, (a)321 stainless steel, (b) stainless steel of coating as spraying, (c) stainless steel of coating after heat treatment.
FIG. 11 is a graph comparing the engineering stress versus engineering strain curves for example 1 and comparative examples 2-3 and 321 stainless steel;
wherein, (a) stainless steel of examples 1 and 321, (b) stainless steel of comparative examples 2 and 321, and (c) stainless steel of comparative examples 3 and 321.
Detailed Description
Example 1:
a preparation method of a multilayer self-healing ceramic coating comprises the following steps:
(1) and (3) mechanically polishing the surface: grinding hot rolled sheet austenitic stainless steel samples by abrasive paper with different particle sizes (80# -1200 #) until no obvious scratch is visible to naked eyes, then cleaning for 5-20 min by adopting acetone in ultrasonic waves, removing oil, cleaning for 5-20 min by using absolute ethyl alcohol ultrasonic waves, removing stains, and finally drying for 20-40 min in a drying oven at 80 ℃; (wherein the 321 austenitic stainless steel is a rolled sheet material, the mass fractions of chemical components of the 321 austenitic stainless steel are C0.04%, Si 0.38%, Mn 1.08%, Cr 17.02%, Ni 9.06%, N0.05%, P0.03%, Ti 0.22%, and the balance of Fe.321 stainless steel is mechanical properties at normal temperature, namely tensile strength (sigma b)667MPa, yield strength (sigma 0.2)245MPa, elongation 56.5%, and hardness 175 HV.) the Cr hardness of the matrix metal should be less than 40, and the coating is not bonded with the matrix surface in the spraying process if the hardness is too high.
(2) Sand blasting treatment: in order to increase the adhesion of the coating and the rate of powder deposition, the substrate surface is degreased and sandblasted prior to spraying. Placing the polished sample under 0.6-0.9 MPa high-pressure nitrogen for sand blasting, wherein the grinding material is 12-mesh white corundum particles, the sand blasting time is 10-20 min, the sand blasting distance is 2cm, and the surface roughness after sand blasting is Ra 7-8;
(3) pre-drying powder: NiCrAlY, TiC and Al to be sprayed2O3-13％TiO2Drying the powder in an electric furnace at 130 ℃ for 30 minutes, and then separating out powder with the particle size of 15-45 mu m by using a 325-mesh test sieve;
(4) supersonic plasma spraying: using a HEPPiet supersonic plasma spraying system to spray the NiCrAlY, TiC and Al pretreated in the step (3)2O3-13％TiO2The powder is sequentially sprayed on the substrate which is processed to be thick in the steps (1) and (2) to sequentially form a NiCrAlY bonding layer of 45-55 mu m, a TiC self-healing intermediate layer of 40-60 mu m and Al of 100-120 mu m2O3-13TiO2A ceramic environmental barrier layer. The specific spraying parameters are as follows: NiCrAlY bonding layer, the spraying power is 35-37 kW; the main steam flow is 120L/min, the auxiliary steam flow is 80L/min, the powder feeding speed is 36g/min, and the displacement speed is700mm/s, spraying distance of 120mm and single-channel spraying distance of 2 mm. A TiC layer self-healing layer, and the spraying power is 40-43 kW; the main steam flow is 120L/min, the auxiliary steam flow is 80L/min, the powder feeding speed is 24g/min, the displacement speed is 500mm/s, the spraying distance is 110mm, and the single-channel spraying distance is 2 mm. Al (Al)2O3-13％TiO2The spraying power of the ceramic environment barrier layer is 45-48 kW; the main steam flow is 120L/min, the auxiliary steam flow is 80L/min, the powder feeding speed is 32g/min, the displacement speed is 500mm/s, the spraying distance is 100mm, and the single-channel spraying distance is 2 mm.
As shown in fig. 1(a-d), it is evident under high power microscope that the coating has pores inside, and the porosity of each layer is, NiCrAlY layer: 4.57 percent; a TiC layer: 14.51 percent; AT13 layer 6.45%.
(5) Self-healing heat treatment: for the prepared NiCrAlY/TiC/Al2O3-TiO2And performing primary heat treatment on the composite coating, putting a sprayed sample into a resistance furnace, heating to 620 ℃, performing heat preservation treatment, opening a furnace door every 2 hours, putting external air into the furnace, and cooling the furnace to room temperature after 10 hours. As is apparent from fig. 1(e-h) under high power microscope, the inside of the coating becomes denser, most of the pores have disappeared, and the coating exhibits good self-healing ability, compared with that before the heat treatment. The phase components of different samples are analyzed by a TD 3300X-ray diffractometer, the initial angle is 10 degrees, the final angle is 100 degrees, the step width angle is 0.04, the sampling time is 0.8s, and the scanning speed is 3 degrees/min. XRD analysis of the prepared self-healing coating shows that each layer phase is mainly Al as shown in figure 22O3、TiO2、Al2TiO5、TiC、Ni3Al and metal elementary substance phase.
Example 2:
a preparation method of a self-healing ceramic coating with a multilayer structure comprises the following steps:
(1) and (3) mechanically polishing the surface: grinding hot rolled sheet austenitic stainless steel samples by abrasive paper with different particle sizes (80# -1200 #) until no obvious scratch is visible to naked eyes, then cleaning for 5-20 min by adopting acetone in ultrasonic waves, removing oil, cleaning for 5-20 min by using absolute ethyl alcohol ultrasonic waves, removing stains, and finally drying for 20-40 min in a drying oven at 80 ℃; (wherein the 321 austenitic stainless steel is a rolled sheet material, the mass fractions of chemical components of the 321 austenitic stainless steel are C0.04%, Si 0.38%, Mn 1.08%, Cr 17.02%, Ni 9.06%, N0.05%, P0.03%, Ti 0.22%, and the balance of Fe.321 stainless steel is mechanical properties at normal temperature, namely tensile strength (sigma b)667MPa, yield strength (sigma 0.2)245MPa, elongation 56.5%, and hardness 175 HV.) the Cr hardness of the matrix metal should be less than 40, and the coating is not bonded with the matrix surface in the spraying process if the hardness is too high.
(2) Sand blasting treatment: in order to increase the adhesion of the coating and the rate of powder deposition, the substrate surface is degreased and sandblasted prior to spraying. Placing the polished sample under 0.6-0.9 MPa high-pressure nitrogen for sand blasting, wherein the grinding material is 12-mesh white corundum particles, the sand blasting time is 10-20 min, the sand blasting distance is 2cm, and the surface roughness after sand blasting is Ra is 7-8;
(3) pre-drying powder: NiCrAlY, TiC and Al to be sprayed2O3-13TiO2Drying the powder in an electric furnace at 130 ℃ for 30 minutes, and then separating out powder with the particle size of 15-45 mu m by using a 325-mesh test sieve;
(4) supersonic plasma spraying: using a HEPPjet supersonic plasma spraying system to spray the NiCrAlY, TiC and Al pretreated in the step (3)2O3-13％TiO2The powder is sequentially sprayed on the thick substrate treated by the steps (1) and (2) to sequentially form a NiCrAlY bonding layer of 45-55 mu m, a TiC self-healing intermediate layer of 30-35 mu m and Al-doped layer of 100-120 mu m2O3-13％TiO2A ceramic environmental barrier layer. The specific spraying parameters are as follows: a NiCrAlY bonding layer with the spraying power of 37-41 kW; the main steam flow is 110L/min, the auxiliary steam flow is 70L/min, the powder feeding speed is 36g/min, the displacement speed is 600mm/s, the spraying distance is 100mm, and the single-channel spraying distance is 2 mm. A TiC layer self-healing layer, wherein the spraying power is 43-47 kW; the main steam flow is 110L/min, the auxiliary steam flow is 70L/min, the powder feeding speed is 24g/min, the displacement speed is 450mm/s, the spraying distance is 110mm, and the single-channel spraying distance is 2 mm. Al (Al)2O3-13％TiO2The spraying power of the ceramic environment barrier layer is 48-52 kW; the main steam flow is 110L/min, the auxiliary steam flow is 70L/min, and the powder feeding rate is 32g/min, the displacement speed is 450mm/s, the spraying distance is 100mm, and the single-channel spraying distance is 2 mm.
The porosity of each layer is respectively NiCrAlY layer: 5.64 percent; a TiC layer: 12.15 percent; AT13 layer 6.73%.
(5) Self-healing heat treatment: for the prepared NiCrAlY/TiC/Al2O3-TiO2And (3) carrying out primary heat treatment on the composite coating, putting the sprayed sample into a resistance furnace, heating to 650 ℃, carrying out heat preservation treatment, opening a furnace door every 2 hours, putting in external air, and cooling to room temperature along with the furnace after 10 hours. It should be noted that the topography at the high power microscope was substantially the same as in example 1.
Example 3:
a preparation method of a multilayer self-healing ceramic coating comprises the following steps:
(1) and (3) mechanically polishing the surface: polishing austenitic stainless steel samples of the hot rolled plate by abrasive paper with different particle sizes (80-1200 meshes) until no obvious scratch is visible to naked eyes, then cleaning for 5-20 min by adopting acetone in ultrasonic waves, removing oil, cleaning for 5-20 min by using absolute ethyl alcohol in ultrasonic waves, removing stains, and finally drying for 20-40 min in a drying oven at 80 ℃; (wherein the 321 austenitic stainless steel is a rolled sheet material, the mass fractions of chemical components of the 321 austenitic stainless steel are C0.04%, Si 0.38%, Mn 1.08%, Cr 17.02%, Ni 9.06%, N0.05%, P0.03%, Ti 0.22%, and the balance of Fe.321 stainless steel is mechanical properties at normal temperature, namely tensile strength (sigma b)667MPa, yield strength (sigma 0.2)245MPa, elongation 56.5%, and hardness 175 HV.) the Cr hardness of the matrix metal should be less than 40, and the coating is not bonded with the matrix surface in the spraying process if the hardness is too high.
(2) Sand blasting treatment: in order to increase the adhesion of the coating and the rate of powder deposition, the substrate surface is degreased and sandblasted prior to spraying. Placing the polished sample under 0.6-0.9 MPa high-pressure nitrogen for sand blasting, wherein the grinding material is 12-mesh white corundum particles, the sand blasting time is 10-20 min, the sand blasting distance is 2cm, and the surface roughness after sand blasting is Ra is 7-8;
(3) pre-drying powder: NiCrAlY, TiC and Al to be sprayed2O3-13TiO2Drying the powder in an electric furnace at 130 ℃ for 30 minutesThen separating out powder with the particle size of 15-45 mu m by using a 325-mesh test sieve;
(4) supersonic plasma spraying: using a HEPPiet supersonic plasma spraying system to spray the NiCrAlY, TiC and Al pretreated in the step (3)2O3-13TiO2The powder is sequentially sprayed on the thick substrate treated by the steps (1) and (2) to sequentially form a NiCrAlY bonding layer of 45-55 mu m, a TiC self-healing intermediate layer of 40-60 mu m and Al-doped layer of 100-120 mu m2O3-13TiO2A ceramic environmental barrier layer. The specific spraying parameters are as follows: NiCrAlY bonding layer with spraying power of 42-45 kW; the main steam flow is 130L/min, the auxiliary steam flow is 90L/min, the powder feeding speed is 36g/min, the displacement speed is 650mm/s, the spraying distance is 120mm, and the single-channel spraying distance is 2 mm. A TiC layer self-healing layer, wherein the spraying power is 47-50 kW; the main steam flow is 130L/min, the auxiliary steam flow is 90L/min, the powder feeding speed is 24g/min, the displacement speed is 500mm/s, the spraying distance is 110mm, and the single-channel spraying distance is 2 mm. Al (Al)2O3-13％TiO2The spraying power of the ceramic environment barrier layer is 52-55 kW; the main steam flow is 130L/min, the auxiliary steam flow is 90L/min, the powder feeding speed is 32g/min, the displacement speed is 500mm/s, the spraying distance is 100mm, and the single-channel spraying distance is 2 mm.
The porosity of each layer is respectively NiCrAlY layer: 4.77 percent; a TiC layer: 10.81 percent; AT13 layer 6.95%.
(5) Self-healing heat treatment: for the prepared NiCrAlY/TiC/Al2O3-TiO2And (3) carrying out primary heat treatment on the composite coating, putting the sprayed sample into a resistance furnace, heating to 650 ℃, carrying out heat preservation treatment, opening a furnace door every 2 hours, putting in external air, and cooling to room temperature along with the furnace after 12 hours. It should be noted that the topography at the high power microscope was substantially the same as in example 1.
Comparative example 1
According to the literature "Effects of heating temperature and duration on the microstructure and properties of the self-heating coatings [ J ]].Surface&TiC + (Al) prepared by the method described in Coatings Technology, 2011, 206, 1342-2O3/TiC)+Al2O3And (4) coating.
Comparative example 2
A45-55 μm NiCrAlY bondcoat was prepared on an austenitic stainless steel substrate according to the procedure described in example 1. The difference from example 1 is that the coating is only a NiCrAlY bond coat.
Comparative example 3
A45-55 μm NiCrAlY bond coat and a 40-60 μm TiC self-healing interlayer were formed on an austenitic stainless steel substrate according to the method described in example 1. The difference from example 1 is that the coating is only a NiCrAlY bondcoat and a TiC self-healing interlayer.
Comparative example 4
According to the method described in example 1, a TiCN bonding layer of 45-55 μm, a TiC self-healing intermediate layer of 40-60 μm and Al of 100-120 μm are formed on an austenitic stainless steel substrate2O3-13％TiO2A ceramic environmental barrier layer. The difference from example 1 is that the coating is only a component of the adhesive layer.
And (3) performance characterization:
the self-healing coatings proposed by the invention (in a spraying state and before heat treatment) have the bonding strength higher than 27.4Mpa, which is improved by 171.5% compared with that of comparative example 1; the bonding strength of the self-healing coating (after heat treatment) provided by the invention is improved to more than 50.16MPa, compared with TiC + (Al) in comparative example 12O3/TiC)+Al2O3The coating is improved by 340%.
And (3) carrying out SEM observation on the cross section of the sample, selecting 20 fields for observation under the same magnification of each sample, carrying out post-processing analysis by using Image J Image analysis software, calculating the total area of the pores and the total area of the Image, and dividing to obtain the porosity. The porosity of the sample can be obtained by counting the porosity of 20 fields and then averaging. The porosity test of different self-healing time shows that the porosity of the overall coating in the spraying state is lower than 10 percent as shown in figures 4 and 5.
Microhardness testing, using an HVT-1000A microhardness tester. The specific test method comprises the following steps: (1) 13 measurement points are selected on the cross section of the coating along the direction vertical to the surface, and each 2 measurementsThe dot spacing was 25um, and in the hardness test, the test loading force was 300N and the load dwell time was 15 s. And 5 parallel measurement points are taken from each measurement point, and the average value is taken after the measurement so as to obtain a reliable statistical value. The results are shown in FIG. 6. The microhardness of the coating in a spraying state is 329.5-967.9HV, and the microhardness of the self-healing coating after heat treatment is improved to be more than 828.5Hv, because TiC self-healing phases in the TiC layer are oxidized to form TiO2Effectively filling pores and cracks in the coating, wherein the TiO2TiO of (TiC) layer2Is mostly rutile type TiO2。
The as-sprayed and heat treated NiCrAlY/TiC/Al prepared in example 12O3-TiO2Performing a tensile test with an austenitic stainless steel matrix, wherein the tensile test is performed on an RDL05 electronic creep fatigue testing machine according to GBT228.1-2010 metal material tensile test Standard, the gauge length section dimension of a high-temperature tensile sample is 4mm multiplied by 8mm, the gauge length is 25mm, the loading mode of the sample is controlled by a strain rate, and the strain rate is 10-4The experimental temperature was 25 ℃ and the results are shown in FIG. 7. As can be seen from fig. 7, the tensile test occurs in the classical four stages: an elastic phase, a yield phase, a reinforcement phase and a necking phase. From the engineering stress-strain curve, 10-4Tensile strength sigma at room temperature for three samples at a tensile rate of/sb642MPa, 618MPa and 579MPa (original 321, as sprayed and after heat treatment), respectively, yield strength sigma0.2246MPa, 267MPa and 286MPa (original 321, as-sprayed and after heat treatment), respectively, and 68.0%, 72.0% and 70.0% elongation (original 321, as-sprayed and after heat treatment), respectively. The tensile strength of the stainless steel is reduced due to partial defects introduced by the coating, and the yield strength and the elongation are improved possibly with a precipitation strengthening phase (Ni) introduced by the NiCrAlY coating3Al). Generally, the introduction of defects such as porosity and cracks into the coating results in an overall reduction in the mechanical properties such as yield strength, tensile strength, elongation, etc. of the material, since the difference in the elastic modulus of the ceramic and the matrix is most likely to form crack origins at the bonding interface. However, the self-healing coating with the multilayer structure prepared by the invention utilizes supersonic plasma spraying on one handThe prepared coating has lower porosity, and the porosity is further reduced after self-healing (especially the NiCrAlY layer), so that the defects caused by the coating are overcome. On the other hand, Ni element in the sprayed NiCrAlY layer is mainly gamma′-Ni3The Al phase precipitates in the coating and is beneficial to reduce the large difference in elastic modulus between the ceramic layer and the metal substrate. The NiCrAlY coating and the base body are combined, the section is compact and smooth, and therefore the adverse effect of the coating on the yield strength and the elongation of the material is improved.
Example 1 and comparative examples 2 to 3 were subjected to the adhesion strength test, and the results are shown in fig. 8. The bonding strength test of the substrate/NiCrAlY coating is that the epoxy resin is partially cracked, which shows that the bonding strength of the NiCrAlY and the substrate exceeds the strength of the epoxy resin per se, and the bonding strength is 51.26 MPa. The bonding strength between the matrix and the NiCrAlY/TiC coating is 27.84MPa, which shows that the addition of the TiC coating reduces the bonding strength between the matrix and the NiCrAlY/TiC coating. And the substrate and NiCrAlY/TiC/Al2O3-TiO2The bonding strength of the coating is slightly increased and is 28.52MPa, which indicates that Al2O3-TiO2The addition of the coating has little influence on the bonding strength of the matrix and the NiCrAlY/TiC coating. Therefore, the bonding interface of the TiC and the NiCrAlY coating and the TiC coating are main factors influencing the bonding strength of the matrix and the NiCrAlY/TiC coating, which is consistent with the result of microscopic morphology observation and is caused by the pores of the TiC layer and the weak bonding force of the TiC layer and the NiCrAlY layer. In order to reduce the influence of coating porosity defects, the method is used for reducing the influence of the coating porosity defects on a matrix/NiCrAlY/TiC/Al2O3-TiO2Carrying out self-healing heat treatment, and finding that the substrate and NiCrAlY/TiC/Al are subjected to the self-healing heat treatment for 12 hours2O3-TiO2The bonding strength of the self-healing coating is obviously improved (49.59 Mpa), and the self-healing treatment improves the bonding strength between the TiC layer and the NiCrAlY layer to 73.9 percent. In a word, the self-healing treatment can improve the internal pore condition of the TiC layer and the TiC/NiCrAlY interface combination condition, and effectively improves the bonding strength of the self-healing coating.
FIG. 9 shows the matrix/TiCN/TiC/Al prepared in example 42O3-TiO2Stretching and compacting of coatingExamining the macroscopic morphology, the bonding layer of the coating was TiCN. It can be seen that in the early stages of the tensile test, the entire coating flaked off directly. On one hand, the coating has high hardness and large brittleness and is easy to crack: on the other hand, the overall bond strength of the coating is not high. Resulting in the coating flaking off and poor mechanical properties.
FIG. 11 is a graph comparing the engineering stress versus engineering strain curves for 321 stainless steel, example 1, and comparative examples 2-3 and 321 stainless steel. As can be seen from the figure, under the condition of only spraying the NiCrAlY layer and the NiCrAlY/TiC layer, the yield strength and the elongation rate of 321 stainless steel are obviously reduced, which indicates that the conventional plasma spraying can prevent the environment from contacting with the material, but the defects introduced by the coating can cause the mechanical property of the base material to be reduced, so that the mechanical requirements of relevant standards under the working environment cannot be met. The self-healing coating prepared in example 1 has a certain repairing effect on the mechanical properties of the sample after heat treatment, so that the yield strength and the elongation of the sample are slightly improved compared with those of 321 stainless steel.
It should be noted that, in the embodiments of the present invention, only austenitic stainless steel is used as the substrate, but the coating and the preparation method according to the present invention can be implemented not only on austenitic stainless steel, but also on martensitic stainless steel, other stainless steel, or other metal substrates.
It should be understood that the above examples are only for clarity of illustration and are not intended to limit the embodiments. Other variations and modifications will be apparent to persons skilled in the art in light of the above description. And are neither required nor exhaustive of all embodiments. And obvious variations or modifications therefrom are within the scope of the invention.

Claims (8)

1. A multilayer self-healing ceramic coating, comprising: NiCrAlY bonding layer, TiC self-healing layer and Al sprayed on surface of metal substrate from inside to outside2O3-13％TiO2A ceramic environmental barrier layer; is obtained by heat treatment.
2. A multi-layer structured self-healing ceramic coating according to claim 1, wherein said NiCrAlY bonding layer has a thickness of 45-55 μm; the thickness of the TiC self-healing layer is 30-60 mu m; the Al is2O3-13％TiO2The thickness of the ceramic environmental barrier layer is 100-120 μm.
3. A multi-layer structural self-healing ceramic coating according to claim 1, wherein said metal matrix comprises austenitic stainless steel.
4. A multi-layer self-healing ceramic coating according to claim 1, wherein the heat treatment temperature is 650 ℃, and the heat treatment time is 10-14 h.
5. The method for preparing a multi-layer self-healing ceramic coating according to any of claims 1 to 4, comprising the following steps:
s1, mechanically polishing the surface of the substrate;
s2, performing sand blasting treatment on the surface of the substrate:
carrying out sand blasting treatment on the mechanically polished substrate, wherein the surface roughness Ra of the substrate after sand blasting is 7-8;
s3, surface plasma spraying:
mixing NiCrAlY, TiC and Al2O3-13％TiO2Drying the powder, and screening the powder with the particle size of 15-45 mu m; pre-treated NiCrAlY, TiC and Al2O3-13％TiO2Sequentially forming a 45-55 mu m NiCrAlY bonding layer, a 30-60 mu m TiC self-healing intermediate layer and a 100-120 mu m Al-doped layer on the substrate treated in the step S2 by adopting a plasma spraying mode for the powder2O3-13％TiO2A ceramic environmental barrier layer;
s4, self-healing heat treatment:
for the prepared NiCrAlY/TiC/Al2O3-13％TiO2Performing primary heat treatment on the composite coating, putting the sprayed sample into a resistance furnace, heating to 620-650 ℃, and performing heat preservation treatment every other timeAnd opening the furnace door for 2 hours, putting in external air, and cooling to room temperature along with the furnace after 10-14 hours to obtain the multilayer self-healing ceramic coating.
6. The method for preparing a self-healing ceramic coating with a multi-layer structure according to claim 5, wherein step S1 specifically includes: polishing the matrix by using 80-1200-mesh sand paper until no obvious scratch is visible to naked eyes, then cleaning the matrix in ultrasonic waves for 5-20 min by using acetone, removing oil, ultrasonically cleaning the matrix for 5-20 min by using absolute ethyl alcohol, removing stains, and finally drying the matrix in a drying oven at 80 ℃ for 20-40 min.
7. The method for preparing a self-healing ceramic coating with a multi-layer structure according to claim 5, wherein step S2 specifically includes: and (3) sand blasting the mechanically polished substrate under 0.6-0.9 MPa of high-pressure nitrogen, wherein the abrasive is 12-mesh white corundum particles, the sand blasting time is 10-20 min, the sand blasting distance is 2cm, and the surface roughness Ra after sand blasting is 7-8 of the substrate.
8. The method for preparing a multi-layer self-healing ceramic coating according to claim 5, wherein the drying temperature in step S3 is 130 ℃.
CN202210363583.9A 2022-04-08 2022-04-08 Multilayer self-healing ceramic coating and preparation method thereof Withdrawn CN114686797A (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
CN202210363583.9A CN114686797A (en) 2022-04-08 2022-04-08 Multilayer self-healing ceramic coating and preparation method thereof
JP2023023135A JP7482463B2 (en) 2022-04-08 2023-02-17 Multi-layer self-healing ceramic coating and method for its manufacture

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202210363583.9A CN114686797A (en) 2022-04-08 2022-04-08 Multilayer self-healing ceramic coating and preparation method thereof

Publications (1)

Publication Number Publication Date
CN114686797A true CN114686797A (en) 2022-07-01

Family

ID=82142719

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202210363583.9A Withdrawn CN114686797A (en) 2022-04-08 2022-04-08 Multilayer self-healing ceramic coating and preparation method thereof

Country Status (2)

Country Link
JP (1) JP7482463B2 (en)
CN (1) CN114686797A (en)

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4045697B2 (en) 1999-08-20 2008-02-13 株式会社Ｉｈｉ Oxidation resistant thermal insulation film and method for forming the same
US20110217568A1 (en) 2010-03-05 2011-09-08 Vinod Kumar Pareek Layered article
JP5905336B2 (en) 2012-05-30 2016-04-20 三菱日立パワーシステムズ株式会社 Gas turbine blade for power generation, gas turbine for power generation
JP2014141699A (en) 2013-01-23 2014-08-07 Nippon Electric Glass Co Ltd Anticorrosive coating film, heat transfer pipe and production method thereof
CN109023205A (en) 2018-08-30 2018-12-18 昆明理工大学 A kind of preparation method of thermal spraying thermal barrier coating
CN109778102A (en) 2019-02-27 2019-05-21 中国科学院上海硅酸盐研究所 A kind of multilayered structure selfreparing thermal barrier coating and preparation method thereof

Also Published As

Publication number Publication date
JP2023155160A (en) 2023-10-20
JP7482463B2 (en) 2024-05-14

Similar Documents

Publication Publication Date Title
Shi et al. Effect of spraying powder characteristics on mechanical and thermal shock properties of plasma-sprayed YSZ thermal barrier coating
CN109666911B (en) High-entropy alloy coating resistant to high-temperature corrosion on surface of nuclear zirconium alloy cladding and preparation method thereof
US9109279B2 (en) Method for coating a blade and blade of a gas turbine
CN107130212B (en) High-hardness wear-resistant thermal-shock-resistant thick tantalum coating and preparation method thereof
US20100028711A1 (en) Thermal barrier coatings and methods of producing same
JP2008544127A (en) COATING SYSTEM HAVING INSULATION LAYER AND METAL EROSION PROTECTION LAYER FOR COMPONENT, METHOD FOR PRODUCING THE COATING SYSTEM, AND METHOD FOR OPERATING STEAM TURBINE
Baig et al. Properties and residual stress distribution of plasma sprayed magnesia stabilized zirconia thermal barrier coatings
Song et al. Long lifespan thermal barrier coatings overview: Materials, manufacturing, failure mechanisms, and multiscale structural design
Bahamirian et al. Thermal durability of YSZ/nanostructured Gd2Zr2O7 TBC undergoing thermal cycling
CN109852943A (en) The preparation method and product of nuclear-used zirconium alloy surface C rN coating
CN113278909B (en) Thermal-environmental barrier coating and preparation method and application thereof
CN101310969B (en) Aluminum/aluminum oxide/Ni-base superalloy composite coating for titanium-aluminum alloy and preparation method thereof
CN101294284A (en) Ablation-resistant fatigue-resistant plasma surface recombination reinforcing method
JP2019507828A (en) Adhesion promoting layer for bonding a high temperature protective layer on a substrate and method for producing the same
CN113981366B (en) Preparation method of thermal barrier coating, thermal barrier coating and turbine rotor blade
Ke et al. Study on thermal barrier coatings deposited by detonation gun spraying
Hu et al. Thermal shock behaviour and failure mechanism of two-kind Cr coatings on non-planar structure
CN109457208A (en) A kind of gas turbine turbine blade thermal barrier coating and preparation method thereof
US20080187773A1 (en) Method for the Protection of Titanium Alloys Against High Temperatures and Material Produced
GB2159838A (en) Surface strengthening of overlay coatings
CN114686797A (en) Multilayer self-healing ceramic coating and preparation method thereof
CN114657500A (en) Self-healing coating for improving surface quality and preparation method thereof
Zaini et al. Thermal barrier coating (TBC) of 8 yttria stabilized zirconia and mullite on medium carbon steel
Gao et al. Tritium permeation barrier based on self-healing composite materials
CN115198271B (en) High-heat-matching-property thermal barrier coating and preparation method and application thereof

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
WW01 Invention patent application withdrawn after publication

Application publication date: 20220701

WW01 Invention patent application withdrawn after publication