CN114540739A - Preparation method of coating for enhancing boundary lubrication performance of intermetallic compound - Google Patents
Preparation method of coating for enhancing boundary lubrication performance of intermetallic compound Download PDFInfo
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- 238000000576 coating method Methods 0.000 title claims abstract description 81
- 239000011248 coating agent Substances 0.000 title claims abstract description 79
- 229910000765 intermetallic Inorganic materials 0.000 title claims abstract description 31
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 230000002708 enhancing effect Effects 0.000 title claims abstract description 10
- 238000005461 lubrication Methods 0.000 title abstract description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 64
- 239000000843 powder Substances 0.000 claims abstract description 37
- 238000000034 method Methods 0.000 claims abstract description 28
- 238000007750 plasma spraying Methods 0.000 claims abstract description 18
- 230000037452 priming Effects 0.000 claims abstract description 17
- 239000000758 substrate Substances 0.000 claims abstract description 16
- 239000011812 mixed powder Substances 0.000 claims abstract description 13
- 230000001050 lubricating effect Effects 0.000 claims abstract description 11
- 239000011159 matrix material Substances 0.000 claims abstract description 11
- 238000000498 ball milling Methods 0.000 claims abstract description 9
- 238000002156 mixing Methods 0.000 claims abstract description 7
- 229910001005 Ni3Al Inorganic materials 0.000 claims abstract description 6
- 238000009689 gas atomisation Methods 0.000 claims abstract description 5
- 239000011261 inert gas Substances 0.000 claims abstract description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 3
- 238000005507 spraying Methods 0.000 claims description 34
- 229910052961 molybdenite Inorganic materials 0.000 claims description 16
- 229910052982 molybdenum disulfide Inorganic materials 0.000 claims description 16
- 230000008569 process Effects 0.000 claims description 11
- 239000007921 spray Substances 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 8
- 239000012300 argon atmosphere Substances 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 7
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- 238000005516 engineering process Methods 0.000 claims description 5
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- 238000000889 atomisation Methods 0.000 claims description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N nitrogen Substances N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 claims description 2
- 239000002131 composite material Substances 0.000 abstract description 31
- 239000000314 lubricant Substances 0.000 abstract description 5
- 239000007787 solid Substances 0.000 abstract description 5
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- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 229910052759 nickel Inorganic materials 0.000 description 5
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
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- 229910052782 aluminium Inorganic materials 0.000 description 2
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- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
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- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 1
- 229910002061 Ni-Cr-Al alloy Inorganic materials 0.000 description 1
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- 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
- C23C4/04—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
-
- 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
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- 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)
Abstract
The invention discloses a preparation method of a coating for enhancing the boundary lubricating property of an intermetallic compound, which comprises the steps of mixing nickel powder and aluminum powder by an inert gas atomization method to obtain Ni3An Al intermetallic compound; mixing the mixed powder with MoS having a layered structure2Mechanically ball-milling and mixing the solid lubricant to obtain powder to be sprayed; plasma spraying the powder on the surface of a substrate provided with a NiCrAlY priming coat, and obtaining MoS attached to the surface of the substrate after aging treatment2Reinforced Ni3Al intermetallic compound composite coating. The invention provides Ni with high temperature resistance, wear resistance and low friction coefficient3Preparation of Al-based intermetallic compound composite coatingThe coating obtained by the method has the advantages of excellent boundary lubrication and wear resistance effects, good matching with a matrix and the like.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a preparation method of a coating for enhancing the boundary lubricating property of an intermetallic compound.
Background
Under extreme severe working conditions such as high/low temperature (wide temperature range), special medium, high speed and heavy load, and the like, the key metal friction kinematic pair parts of the equipment are subjected to strong friction and abrasion to reduce the service life of the parts, thereby affecting the reliability and stability of the whole equipment. In general, failure of the kinematic pairs begins at their surface. Therefore, the preparation of coatings on the surfaces of the kinematic pairs to control friction, reduce wear and improve lubrication while maintaining the overall properties inherent in the component base material is considered to be an effective solution to the above problems, which is economical and practical.
Ni3Al intermetallic compounds have many excellent properties such as high melting point, microhardness, specific strength, good thermal conductivity, wear resistance and oxidation resistance, and have become coating protective materials and high-temperature structural materials with wide application potential. However, Ni3The Al intermetallic compound has the bottleneck problems of room temperature brittleness, small creep resistance and the like, and is an important reason for hindering the wide application of the engineering. Although mechanical alloying can be used to improve Ni3Al intermetallic compounds have problems themselves, but the magnitude of the performance improvement is very limited.
Patent CN103498074A proposes graphene-reinforced Ni3The preparation method of the Al composite coating is spark plasma sintering, and graphene is oxidized at the temperature of more than 350 ℃, so that the tribological performance of the material at high temperature is reduced. Patent CN103233223A provides TiC reinforced Ni3The preparation method of the Al composite coating is laser cladding, and the micron-sized additive phase adopted by the patent has the problems of performance reduction and failure of the coating due to growth of crystal grains under the high-temperature condition. Patent CN112553566A proposesProvides a boron nitride nanosheet enhanced Ni3The preparation method of the Al intermetallic compound composite coating is a plasma spraying technology, and the additive phase adopted by the patent cannot be mixed with Ni3The Al intermetallic compound substrate forms good metallurgical bonding, and the bonding interface strength among particles is low, so that the coating is easy to have the particle peeling phenomenon in the service process.
In the prior art, only Ni is added3The Al intermetallic compound substrate is added with a reinforcing phase or a lubricating phase to improve the tribological property of the coating, the microstructure density of the prepared coating is reduced, and the improvement range of the wear resistance of the coating is limited.
Disclosure of Invention
This section is for the purpose of summarizing some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. In this section, as well as in the abstract and the title of the invention of this application, simplifications or omissions may be made to avoid obscuring the purpose of the section, the abstract and the title, and such simplifications or omissions are not intended to limit the scope of the invention.
The present invention has been made keeping in mind the above and/or other problems occurring in the prior art.
Therefore, the present invention is directed to overcoming the disadvantages of the prior art and providing a method for preparing a coating layer for enhancing the boundary lubrication performance of intermetallic compounds.
In order to solve the technical problems, the invention provides the following technical scheme: a method for preparing a coating for enhancing the boundary lubricating property of an intermetallic compound comprises the following steps,
preparation of Ni by inert gas atomization3An Al intermetallic compound;
mixing Ni3Al intermetallic compound and MoS2Mixing and mechanically ball-milling to obtain spraying mixed powder;
spraying a NiCrAlY priming coat on the surface of the substrate by adopting a plasma spraying technology;
pre-oxidizing the NiCrAlY priming layer in an argon atmosphere to obtain a pre-treated NiCrAlY priming layer;
and spraying the spraying mixed powder on the surface of the pretreated NiCrAlY priming coat to obtain the coating.
As a preferable embodiment of the production method of the present invention, wherein: the Ni3The Al intermetallic compound comprises an Al intermetallic compound, wherein the mass ratio of nickel powder to aluminum powder is 87: 90.
as a preferable embodiment of the production method of the present invention, wherein: the spraying mixed powder comprises the following components: ni3Al powder: 80-90 wt%; MoS2Powder: 10 to 20 wt%.
As a preferable embodiment of the production method of the present invention, wherein: the inert gas atomization method is used for preparing Ni3And Al intermetallic compound, wherein the atomizing medium is nitrogen, the atomizing pressure is 5.5 MPa, after the atomization is finished, powder with the particle size of less than 150 mu m is weighed as the spraying material after being sieved by a 100-mesh sieve.
As a preferable embodiment of the production method of the present invention, wherein: and spraying a NiCrAlY priming coat on the surface of the substrate by adopting a plasma spraying technology, wherein the plasma spraying process parameters are as follows: spraying distance is 110 mm, and plasma gas flow H2The flow rate is 2L/min, the Ar flow rate is 40L/min, the current is 400A, the moving speed of the spray gun is 150 mm/s, and the powder feeding speed is 25 g/min.
As a preferable embodiment of the production method of the present invention, wherein: and the pre-oxidation treatment is carried out in an argon atmosphere, the temperature is raised to 1000 ℃ along with the furnace, the temperature is kept for 4 h, then the temperature is raised to 1080 ℃, the temperature is kept for 4 h, and then the temperature is cooled to room temperature along with the furnace.
As a preferable embodiment of the production method of the present invention, wherein: and spraying the spraying mixed powder on the surface of the pretreated NiCrAlY priming coat, wherein the spraying is a plasma spraying process.
As a preferable embodiment of the production method of the present invention, wherein: the plasma spraying process parameters are as follows: spraying distance of 150 mm, plasma gas flow H2The flow rate is 5L/min, the Ar flow rate is 50L/min, the current is 500A, the moving speed of the spray gun is 200 mm/s, the powder feeding rate is 50 g/min, and the spraying is repeated for 3 times.
As a preferable embodiment of the production method of the present invention, wherein: the matrix comprises a nickel-base superalloy matrix MGA1400 DS.
The invention has the beneficial effects that:
(1) the method adopts the step of carrying out graded heat treatment on the NiCrAlY priming coat prepared by plasma spraying in the argon atmosphere environment, and can form uniform alpha-Al on the surface of the NiCrAlY priming coat2O3The oxide is thermally grown, so that the interface bonding strength between the coating and the substrate is obviously improved.
(2) The invention skillfully utilizes MoS2And Ni3Self-propagating reaction of Al under high temperature conditions and based on MoS2Layered crystal structure, improved Ni prepared3The uniformity of the microstructure of the Al-based self-lubricating coating effectively improves the bonding state between coating layers.
(3) MoS utilizing a layered structure as proposed by the present invention2Solid lubricant enhanced Ni3Method of Al intermetallic compound due to MoS2The solid lubricant can generate a uniform boundary lubricating film on the friction surface under the boundary lubricating condition, and is beneficial to improving the boundary lubricating state of the coating, compared with Ni3The wear resistance of the Al self-lubricating coating is obviously improved.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the description of the embodiments will be briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without inventive exercise. Wherein:
FIG. 1 is a schematic diagram of the principle of forming a plasma sprayed coating according to the present invention, in which 1 is a spray gun, 2 is a powder feeding tube, 3 is molten particles, 4 is a coating layer, and 5 is a base material;
FIG. 2 is a graph comparing the bonding strength of coatings prepared in example 1 of the present invention;
FIG. 3 is a graph of the "boundary lubrication-dry friction" coefficient of friction in example 1 of the present invention.
Detailed Description
In order to make the aforementioned objects, features and advantages of the present invention more comprehensible, specific embodiments thereof are described in detail below with reference to examples of the specification.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, but the present invention may be practiced in other ways than those specifically described and will be readily apparent to those of ordinary skill in the art without departing from the spirit of the present invention, and therefore the present invention is not limited to the specific embodiments disclosed below.
Furthermore, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic described in connection with the embodiment is included in at least one implementation of the invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
The preparation method of the coating for enhancing the boundary lubricating property of the intermetallic compound improves the uniformity of the microstructure of the coating and effectively overcomes the defect of pure Ni3The Al intermetallic compound has the problems of room temperature brittleness, small creep resistance and the like, and the boundary lubrication tribology performance of the composite coating is obviously improved.
The plasma spraying principle diagram adopted by the invention is shown in figure 1: the spray gun 1 and the powder feeding pipe 2 adopt a radial powder feeding mode to feed the composite powder into a flame flow center; the heat source generated by the flame flow of the plasma arc heats the composite powder to form molten particles 3, and the composite coating 4 is deposited on the surface of the substrate 5.
The powder, apparatus and the like used in the present invention are commercially available or can be prepared by a conventional method.
Example 1:
a preparation method of a coating for enhancing the boundary lubricating property of an intermetallic compound comprises the following steps:
(1) the mixed powder for spraying comprises the following components in percentage by mass: ni3Al powder: 80 percent; MoS2Powder: 20 percent.
(2) Weighing Ni according to the component proportion of the composite coating3Al alloy and MoS2Pouring the solid lubricant powder into a canning container, ball-milling for 3 hours at the ball-milling parameter of the rotating speed of 500 r/min, and drying for 2 hours at the temperature of 100 ℃ after the ball-milling is finished.
(3) And ultrasonically cleaning the surface of the matrix (the nickel-based superalloy matrix MGA1400 DS) by using acetone to remove impurities such as oil stains and rust stains, and immediately drying to prevent rusting after cleaning.
(4) The surface of a substrate to be sprayed is subjected to sand blasting coarsening treatment by brown corundum with the granularity of 24 meshes so as to improve the bonding strength between the coating and the substrate, and the coarsened surface roughness is required to be not less than Ra 7.0.
(5) Preparation of NiCrAlY base coat: the mass ratio of each element in the NiCrAlY powder is Cr: 22.59%, Al: 11.23%, Y: 1.83%, Ni: the balance; plasma spraying process parameters: spraying distance is 110 mm, and plasma gas flow H2The flow rate is 2L/min, the Ar flow rate is 40L/min, the current is 400A, and the powder feeding rate is 25 g/min.
(6) And (5) pre-oxidizing the surface of the priming layer. The method is carried out in the argon atmosphere, the temperature is raised to 1000 ℃ along with the furnace, the heat preservation is carried out for 4 h, then the temperature is raised to 1080 ℃, the heat preservation is carried out for 4 h, and then the temperature is cooled to the room temperature along with the furnace.
(7) And pouring the dried mixed powder into a powder feeder, and adjusting the powder feeding airflow to ensure that the powder is just fed into the center of the plasma flame flow. The technological parameters of plasma spraying are as follows: the spraying distance was 150 mm, the flow of plasma gas H2 was 5L/min, the flow of Ar was 50L/min, the current was 500A, the moving speed of the spray gun was 200 mm/s, each time 3 mm downward, and the spraying was repeated 4 times. Finally, the composite coating with the thickness of about 350-.
(8) Through detection, the prepared composite coating has compact tissue and porosity of 2 percent which is far lower than that of Ni315% of the Al alloy coating; ni3The bonding strength of the Al alloy coating is 18 MPa and is far lower than that of Ni3Al-MoS2The bonding strength (46 MPa) of the composite coating is shown in FIG. 2, wherein A is spray Ni3Bonding strength of Al alloy coating, B is spray Ni3Al-MoS2The bonding strength of the composite coating.
(9) The prepared coating was subjected to a ball-and-disc friction wear test, as a control, and a friction test was performed simultaneously under the same conditions.
Wherein the dual ball is made of Si with a diameter of 5 mm3N4Ball, load 10N, frequency 4 Hz, wear scar length 5 mm.
The results show that sprayed Ni3The friction coefficient of boundary lubrication-dry friction of the Al alloy coating is 0.7 and is far higher than that of Ni3Al-MoS2The "boundary lubrication-dry friction" coefficient of friction of the composite coating (0.4);
as shown in FIG. 3, curve A is sprayed with Ni3The friction coefficient curve of boundary lubrication-dry friction of the Al alloy coating, and the curve B of the sprayed Ni3Al-MoS2Composite coating "boundary lubrication-dry friction" coefficient of friction curve. At the same time, Ni3Al-MoS2The transition time of the boundary lubrication-dry friction curve of the composite coating is 6 h, which is much longer than that of Ni3Transition time (4 h) of boundary lubrication curve of Al alloy coating.
Example 2:
the difference from example 1 is that: the additive phase in the step (2) is soft metal Ag.
To ensure the soft metals Ag and Ni3The Al alloy was mixed uniformly, and the powder was mixed in the step (2) in example 1.
In step (8), the porosity of the composite coating is 5%, which is much lower than that of Ni315% of Al alloy coating; the bonding strength of the composite coating is 36 MPa and is much higher than that of Ni3Bonding strength of Al alloy coating (18 MPa).
In step (9), sprayed Ni3The friction coefficient of the Al alloy coating is 0.7 and is far higher than that of Ni3The friction coefficient of the Al-Ag composite coating is 0.6.
At the same time, Ni3The transition time of the boundary lubrication-dry friction curve of the Al-Ag composite coating is 5 h, which is much longer than that of Ni3Transition time (4 h) of "boundary lubrication-dry friction" curve of Al alloy coating.
Example 3:
the difference from example 1 is that: the additive phase in the step (2) is soft metal Mo.
To ensure the soft metals Mo and Ni3The Al alloy was mixed uniformly, and the powder was mixed in the step (2) in example 1.
In step (8), the porosity of the composite coating is 8%, which is much lower than that of Ni315% of Al alloy coating; the bonding strength of the composite coating is 31 MPa and is much higher than that of Ni3Bonding strength of Al alloy coating (18 MPa).
In step (9), sprayed Ni3The friction coefficient of the Al alloy coating is 0.7 and is far higher than that of Ni3The friction coefficient of the Al-Mo composite coating is 0.5.
At the same time, Ni3The transition time of the boundary lubrication-dry friction curve of the Al-Mo composite coating is 4.5 h, which is much longer than that of Ni3Transition time (4 h) of "boundary lubrication-dry friction" curve of Al alloy coating.
Example 4:
the difference from example 1 is that: the additive phase in the step (2) is Ni-coated graphite.
To ensure that Ni wraps graphite and Ni3The Al alloy was mixed uniformly, and the powder was mixed in the step (2) in example 1.
In the step (8), the porosity of the composite coating is 11% or less than that of Ni315% of the Al alloy coating; the bonding strength of the composite coating is 28 MPa and is higher than that (18 MPa) of the Ni3Al alloy coating.
In step (9), sprayed Ni3The friction coefficient of the Al alloy coating is 0.7 and is higher than that of Ni3The friction coefficient of the Al-Ni coated graphite composite coating is 0.6.
At the same time, Ni3The transition time of the boundary lubrication-dry friction curve of the Al-Ni coated graphite composite coating is 5.5 h which is much longer than that of Ni3Transition time (4 h) of "boundary lubrication-dry friction" curve of Al alloy coating.
Example 5:
the pre-oxidation treatment parameters in step (6) were adjusted under the process conditions of example 1, and the experimental conditions are shown in table 1.
TABLE 1
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Test 3 | |
|
|
| First stage temperature (. degree. C.) | 1000 | 870 | 750 | 650 | 1150 |
| First stage treatment time (h) | 4 | 4 | 4 | 4 | 4 |
| Second stage temperature (. degree. C.) | 1080 | 950 | 800 | 750 | 1240 |
| First stage treatment time (h) | 4 | 4 | 4 | 4 | 4 |
| Curve transition time (h) | 6 | 5 | 4.5 | 5.5 | 4 |
When the temperature is increased to 1000 ℃, the content of the gamma ' phase is gradually reduced, the content of the gamma phase is gradually increased, after the temperature is continuously increased to 1080 ℃, the gamma ' phase is separated from the temperature range of the mother phase, and the gamma ' phase precipitated from the Ni-Cr-Al alloy is fine and dispersed and keeps a coherent relationship with the matrix, so that the alloy matrix can be strengthened;
when the temperature exceeds 1100 ℃, the content of the gamma' phase in the bonding layer is obviously reduced, the thermal growth substance has a layering phenomenon, and the uniformity is obviously reduced.
The temperature rise process disclosed by the invention is divided into two sections (namely, the temperature rises to 1000 ℃ along with the furnace, the heat preservation is carried out for 4 hours, then the temperature rises to 1080 ℃, the heat preservation is carried out for 4 hours), and continuous, uniform-thickness and single component (Al) can be generated at the interface coating of the bonding layer and the coating2O3) Thermal growth substance (TGO) of (1), Al of single composition2O3The layer effectively blocks the formation of other non-protective oxides, no delamination occurs in the TGO, and Al remains2O3Mainly, the thickness is still relatively uniform, and the TGO can be in a stable oxidation stage.
Example 6:
a preparation method of a coating for enhancing the boundary lubricating property of an intermetallic compound comprises the following steps:
(1) the mixed powder for spraying comprises the following components in percentage by mass: ni3Al powder: 70 percent; MoS2Powder: 30 percent.
(2) Weighing Ni according to the component proportion of the composite coating3Al alloy and MoS2Pouring the solid lubricant powder into a canning container, ball-milling for 3 hours at the ball-milling parameter of the rotating speed of 500 r/min, and drying for 2 hours at the temperature of 100 ℃ after the ball-milling is finished.
(3) And ultrasonically cleaning the surface of the matrix (the nickel-based superalloy matrix MGA1400 DS) by using acetone to remove impurities such as oil stains and rust stains, and immediately drying to prevent rusting after cleaning.
(4) The surface of a substrate to be sprayed is subjected to sand blasting coarsening treatment by brown corundum with the granularity of 24 meshes so as to improve the bonding strength between the coating and the substrate, and the coarsened surface roughness is required to be not less than Ra 7.0.
(5) Preparation of NiCrAlY base coat: the mass ratio of each element in the NiCrAlY powder is Cr: 22.59%, Al: 11.23%, Y: 1.83%, Ni: the balance; plasma spraying process parameters: spraying distance is 110 mm, and plasma gas flow H2The flow rate is 2L/min, the Ar flow rate is 40L/min, the current is 400A, and the powder feeding rate is 25 g/min.
(6) And (5) pre-oxidizing the surface of the priming layer. The method is carried out in the argon atmosphere, the temperature is raised to 1000 ℃ along with the furnace, the heat preservation is carried out for 4 h, then the temperature is raised to 1080 ℃, the heat preservation is carried out for 4 h, and then the temperature is cooled to the room temperature along with the furnace.
(7) And pouring the dried mixed powder into a powder feeder, and adjusting the powder feeding airflow to ensure that the powder is just fed into the center of the plasma flame flow. The technological parameters of plasma spraying are as follows: the spraying distance was 150 mm, the flow of plasma gas H2 was 5L/min, the flow of Ar was 50L/min, the current was 500A, the moving speed of the spray gun was 200 mm/s, each time 3 mm downward, and the spraying was repeated 4 times. Finally, depositing a thick composite coating on the surface of the nickel-based high-temperature alloy substrate subjected to sand blasting.
(8) Through detection, the prepared coating has compact tissue and porosity of 6 percent, which is higher than that of the coating in example 1 (2 percent); the bond strength of the coating was 32 MPa, which is lower than that of example 1 (46 MPa). The results of the tribology performance tests show that the coefficient of friction of the sprayed layer, boundary lubrication-dry friction, is 0.6, which is higher than that of example 1 (0.4); the coating "boundary lubrication-dry friction" curve transition time was 5 h, shorter than that of example 1 (6).
It should be noted that the above-mentioned embodiments are only for illustrating the technical solutions of the present invention and not for limiting, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, which should be covered by the claims of the present invention.
Claims (9)
1. A preparation method of a coating for enhancing the boundary lubricating property of an intermetallic compound is characterized by comprising the following steps: comprises the steps of (a) preparing a substrate,
preparation of Ni by inert gas atomization3An Al intermetallic compound;
mixing Ni3Al intermetallic compound and MoS2Mixing and mechanically ball-milling to obtain spraying mixed powder;
spraying a NiCrAlY priming coat on the surface of the substrate by adopting a plasma spraying technology;
pre-oxidizing the NiCrAlY priming layer in an argon atmosphere to obtain a pre-treated NiCrAlY priming layer;
and spraying the spraying mixed powder on the surface of the pretreated NiCrAlY priming coat to obtain the coating.
2. The method of claim 1, wherein: the Ni3The Al intermetallic compound comprises an Al intermetallic compound, wherein the mass ratio of nickel powder to aluminum powder is 87: 90.
3. the method of claim 2, wherein: the spraying mixed powder comprises the following components: ni3Al powder: 80-90 wt%; MoS2Powder: 10 to 20 wt%.
4. As claimed in claim1, the preparation method is characterized in that: the inert gas atomization method is used for preparing Ni3And Al intermetallic compound, wherein the atomizing medium is nitrogen, the atomizing pressure is 5.5 MPa, after the atomization is finished, powder with the particle size of less than 150 mu m is weighed as the spraying material after being sieved by a 100-mesh sieve.
5. The method of claim 1, wherein: and spraying a NiCrAlY priming coat on the surface of the substrate by adopting a plasma spraying technology, wherein the plasma spraying process parameters are as follows: spraying distance of 110 mm, plasma gas flow H2The flow rate is 2L/min, the Ar flow rate is 40L/min, the current is 400A, the moving speed of the spray gun is 150 mm/s, and the powder feeding speed is 25 g/min.
6. The method of claim 1, wherein: and the pre-oxidation treatment is carried out in an argon atmosphere, the temperature is raised to 1000 ℃ along with the furnace, the temperature is kept for 4 h, then the temperature is raised to 1080 ℃, the temperature is kept for 4 h, and then the temperature is cooled to room temperature along with the furnace.
7. The method of claim 1, wherein: and spraying the spraying mixed powder on the surface of the pretreated NiCrAlY priming coat, wherein the spraying is a plasma spraying process.
8. The method of claim 7, wherein: the plasma spraying process parameters are as follows: spraying distance of 150 mm, plasma gas flow H2The flow rate is 5L/min, the Ar flow rate is 50L/min, the current is 500A, the moving speed of the spray gun is 200 mm/s, the powder feeding rate is 50 g/min, and the spraying is repeated for 3 times.
9. The method according to any one of claims 1 to 8, wherein: the matrix comprises a nickel-base superalloy matrix MGA1400 DS.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA909606A (en) * | 1970-06-11 | 1972-09-12 | Zeliznak Richard | Coating process |
| CN108950455A (en) * | 2018-07-18 | 2018-12-07 | 合肥市新开创不锈钢设备有限公司 | A method of improving austenitic stainless steel wearability and self-lubrication |
| CN109930102A (en) * | 2019-04-25 | 2019-06-25 | 清华大学无锡应用技术研究院 | A kind of novel thermal barrier coating preparation process |
| CN110983234A (en) * | 2019-12-25 | 2020-04-10 | 陕西科技大学 | NiAl-based bimetal oxide high-temperature lubricating wear-resistant composite coating and preparation method thereof |
-
2022
- 2022-03-23 CN CN202210290519.2A patent/CN114540739A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA909606A (en) * | 1970-06-11 | 1972-09-12 | Zeliznak Richard | Coating process |
| CN108950455A (en) * | 2018-07-18 | 2018-12-07 | 合肥市新开创不锈钢设备有限公司 | A method of improving austenitic stainless steel wearability and self-lubrication |
| CN109930102A (en) * | 2019-04-25 | 2019-06-25 | 清华大学无锡应用技术研究院 | A kind of novel thermal barrier coating preparation process |
| CN110983234A (en) * | 2019-12-25 | 2020-04-10 | 陕西科技大学 | NiAl-based bimetal oxide high-temperature lubricating wear-resistant composite coating and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 李文生;范祥娟;杨军;朱圣宇;胡伟;孙洋;: "Ni_3Al基高温自润滑复合涂层的制备和摩擦学性能", 摩擦学学报, no. 06, pages 11 - 19 * |
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