CN110257763A - A kind of Ni-Al alloy coating and its method for preparing Ni-Al alloy coating - Google Patents
A kind of Ni-Al alloy coating and its method for preparing Ni-Al alloy coating Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/12—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on oxides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F3/00—Changing the physical structure of non-ferrous metals or alloys by special physical methods, e.g. treatment with neutrons
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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
- C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
- C23C10/28—Solid state diffusion of only metal elements or silicon into metallic material surfaces using solids, e.g. powders, pastes
- C23C10/34—Embedding in a powder mixture, i.e. pack cementation
- C23C10/36—Embedding in a powder mixture, i.e. pack cementation only one element being diffused
- C23C10/48—Aluminising
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Abstract
The invention discloses a kind of Ni-Al alloy coatings, including NiAl phase crystal grain, Ni2Al3Phase crystal grain, AlCr deposit, dislocation tangle, dislocation ring, unauspicious item；The coating is by NiAl phase crystal grain and Ni2Al3Phase crystal grain is constituted；NiAl phase crystal grain, Ni2Al3Dislocation tangle is arranged in phase crystal particle crystal boundary periphery；Intra-die around the NiAl phase is provided with precipitated phase；Multiple precipitated phase peripheries are provided with dislocation ring；There is a large amount of unauspicious item at adjacent NiAl phase grain boundary sites.Ni-Al alloy coating of the invention carries out laser reinforcing processing after using plasma spraying, improves the oxidation-resistance property of Ni-Al alloy coating.
Description
Technical field
The present invention relates to high-temperature alloy protecting coating fields, and in particular to a kind of Ni-Al alloy coating and its prepares the conjunction of nickel aluminium
The method of gold plating.
Background technique
Powder investment is to bury sample to be overlying in powder penetrating agent, carries out heat diffusion treatment before the deadline to obtain
The method of Ni-Al alloy coating.Solid powder investment is also referred to as pack, is to develop a kind of earliest and most widely used aluminium
Compound coating production.Pack aluminizing substantially belongs to chemical gaseous phase aluminising, usually adds 2% in embedding penetration enhancer and arrives
5% activator, activator, which easily resolves into hydrogen halide at high temperature and reacts with Al, generates metal halide, these metals
Halide is in gaseous state and is adsorbed on sample surface layer and releases active Al atom, to generate Ni-Al alloy coating.Solid powder packet
Bury and be impregnated with following some advantages: equipment requirement is simple, easy to operate, is suitable for most of component of machine, the nickel aluminium prepared
Alloy coat quality is preferable, is most widely used method.
In order to further increase the oxidation resistance of Ni-Al alloy coating, only improve alloy surface by common aluminized coating
Coating mass be far from being enough, it is therefore desirable to Ni-Al alloy coating is modified.
Summary of the invention
The technical problem to be solved in the present invention is to provide a kind of Ni-Al alloy coatings, improve the resistant to high temperatures of Ni-Al alloy coating
Oxidability.
In order to solve the above technical problems, the present invention adopts the following technical scheme that: a kind of Ni-Al alloy coating, including NiAl phase
Crystal grain, Ni2Al3Phase crystal grain, AlCr deposit, dislocation tangle, dislocation ring, unauspicious item；The coating by NiAl phase crystal grain,
Ni2Al3Phase crystal grain and AlCr deposit are constituted；NiAl phase crystal grain, Ni2Al3Dislocation tangle is arranged in phase crystal particle crystal boundary periphery；It is described
Intra-die around NiAl phase is provided with precipitated phase；Multiple precipitated phase peripheries are provided with dislocation ring；Adjacent NiAl phase crystal boundary position
There are several unauspicious items at the place of setting.
Further, the partial size of the NiAl phase crystal grain is in 200nm-300nm；Ni2Al3The partial size of phase crystal grain is in 48-
52nm。
A kind of method preparing Ni-Al alloy coating described in claim 1 of the invention, includes the following steps:
(1) aluminizing medium is sufficiently mixed to infiltration that is uniformly rear and needing the nickel-base alloy for carrying out aluminising processing to be co-located in sealing in proportion
In filling, heats under vacuum or under inert gas shielding and carry out aluminising processing；
(2) powder that surface adhesion is washed off with cleaning agent, then polishes to the surface after aluminising, polishing treatment；
(3) alloy its progress handled to step (2) is laser impact intensified.
Further, described to carry out laser reinforcing impact in alloy surface, percussion power is 10kw, number of shocks 2-4
Secondary, spot diameter 4mm, overlapping rate 50% uses aluminium foil for protective layer, and 2mm thickness water is restraint layer.
Further, aluminizing medium includes following component in percentage by weight in step (1): Cr 12wt.%, 1.5 Pd
wt.%、Al 24.5wt.%、NH4Cl 3.2wt.%, AlCr alloyed powder 18wt.%, Y2O3 3.8wt.%、Al2O3Surplus.
Beneficial effects of the present invention: by means of the present invention, the oxidation film on Ni-Al alloy coating surface has refining effect,
The speed of growth for facilitating inhibition oxidation film and intrinsic silicon TCP, delays the transformation time of oxide, for improving oxidation film
Adhesion strength has preferable effect, therefore the oxidation-resistance property of Ni-Al alloy coating can be improved in laser-impact.
Detailed description of the invention
It, below will be to needed in the embodiment in order to more clearly illustrate the technical solution in the embodiment of the present invention
Attached drawing is simply introduced, it should be apparent that, the accompanying drawings in the following description is only some embodiments recorded in the present invention, for
For those of ordinary skill in the art, without creative efforts, it can also be obtained according to these attached drawings other
Attached drawing.
Fig. 1 is the surface microstructure of calorized coating deformation and dislocation；
Fig. 2 is calorized coating deformation and dislocation motion surface microstructure；
Fig. 3 is the surface microstructure of calorized coating NiAl phase；
Fig. 4 is the surface microstructure of calorized coating NiAl phase electronic diffraction；
Fig. 5 is the surface microstructure of the unauspicious striped of calorized coating；
Fig. 6 is unauspicious striped electron diffraction diagram.
Fig. 7 is the microstructure of calorized coating dislocation wall, dislocation born of the same parents and dislocation tangle；
Fig. 8 is the microstructure that calorized coating mistake is movement；
Fig. 9 is the microstructure of calorized coating crystal grain refinement；
Figure 10 is the microstructure of calorized coating dislocation permutation；
The calorized coating that Figure 11 is sample a oxidizing dynamics curve at 800 °C -1100 DEG C；
The calorized coating that Figure 12 is sample b oxidizing dynamics curve at 800 °C -1100 DEG C；
Sample a calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 13 is 800 DEG C；
Sample a calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 14 is 900 DEG C；
Sample a calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 15 is 1000 DEG C；
Sample a calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 16 is 1100 DEG C；
Sample b calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 17 is 800 DEG C；
Sample b calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 18 is 900 DEG C；
Sample b calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 19 is 1000 DEG C；
Sample b calorized coating aoxidizes the analysis of 100h Surface Phases when Figure 20 is 1100 DEG C；
Sample a calorized coating aoxidizes 100h surface topography when Figure 21 is 800 DEG C；
Sample a calorized coating aoxidizes 100h surface topography when Figure 22 is 900 DEG C；
Sample a calorized coating aoxidizes 100h surface topography when Figure 23 is 1000 DEG C；
Sample a calorized coating aoxidizes 100h surface topography when Figure 24 is 1100 DEG C；
Sample b calorized coating aoxidizes 100h surface topography when Figure 25 is 800 DEG C；
Sample b calorized coating aoxidizes 100h surface topography when Figure 26 is 900 DEG C；
Sample b calorized coating aoxidizes 100h surface topography when Figure 27 is 1000 DEG C；
Sample b calorized coating aoxidizes 100h surface topography when Figure 28 is 1100 DEG C；
Sample a calorized coating aoxidizes 100h Cross Section Morphology when Figure 29 is 800 DEG C；
Sample a calorized coating aoxidizes 100h Cross Section Morphology when Figure 30 is 900 DEG C；
Sample a calorized coating aoxidizes 100h Cross Section Morphology when Figure 31 is 1000 DEG C；
Sample a calorized coating aoxidizes 100h Cross Section Morphology when Figure 32 is 1100 DEG C；
Sample b calorized coating aoxidizes 100h Cross Section Morphology when Figure 33 is 800 DEG C；
Sample b calorized coating aoxidizes 100h Cross Section Morphology when Figure 34 is 900 DEG C；
Sample b calorized coating aoxidizes 100h Cross Section Morphology when Figure 35 is 1000 DEG C；
Sample b calorized coating aoxidizes 100h Cross Section Morphology when Figure 36 is 1100 DEG C.
Specific embodiment
Technical solution of the present invention will be clearly and completely described by specific embodiment below.
Embodiment 1
As shown in Figure 1, being a kind of Ni-Al alloy coating of the invention, including NiAl phase crystal grain, Ni2Al3Phase crystal grain, AlCr deposition
Object, dislocation tangle, dislocation ring, unauspicious item；The coating is by NiAl phase crystal grain, Ni2Al3Phase crystal grain and AlCr deposit are constituted；
NiAl phase crystal grain, Ni2Al3Dislocation tangle is arranged in phase crystal particle crystal boundary periphery；Intra-die around the NiAl phase is provided with precipitation
Phase；Multiple precipitated phase peripheries are provided with dislocation ring；There are several unauspicious items at adjacent NiAl phase grain boundary sites.The NiAl phase crystal grain
Partial size in 200nm-300nm；Ni2Al3The partial size of phase crystal grain is in 48-52nm.
Embodiment 2
A kind of method preparing Ni-Al alloy coating described in claim 1 of the invention, includes the following steps
(1) aluminizing medium is sufficiently mixed to infiltration that is uniformly rear and needing the nickel-base alloy for carrying out aluminising processing to be co-located in sealing in proportion
In filling, segmentally heating carries out aluminising processing under vacuum or under inert gas shielding；First segment is heated to 800 DEG C, keeps the temperature 6h, the
Two sections are heated to 900 DEG C, keep the temperature 1h, then cool to room temperature with the furnace and take out sample；Heating rate in two sections of heating processes is equal
For 7-12 DEG C/min；Aluminizing medium includes following component in percentage by weight: Cr 12wt.%, 1.5 Pd wt.%, Al
24.5wt.%, NH4Cl 3.2wt.%, AlCr alloyed powder 18wt.%, Y2O33.8wt.%, Al2O3 surplus.
(2) powder that surface adhesion is washed off with cleaning agent, then polishes to the surface after aluminising, polishing treatment；
(3) alloy its progress handled to step (2) is laser impact intensified.
The present invention carries out laser reinforcing impact in alloy surface, and percussion power is 10kw, and number of shocks is 2-4 times, hot spot
Diameter 4mm, overlapping rate 50% use aluminium foil for protective layer, and 2mm thickness water is restraint layer.
Ni-Al alloy coating made from the present embodiment, as shown in figures 1 to 6 by transmission electron microscope observing its surface microstructure.
As can be seen from the figure coated grains are substantially all in nanoscale, and NiAl phase crystal grain is in 200nm-300nm, it is also possible to bigger crystalline substance
Grain, Ni2Al3Phase crystallite dimension is about in 50nm or so.Coating surface after laser-impact only has a small amount of crystal grain to produce
Deformation, as shown in Figure 1, discovery has a small amount of dislocation at the crystal boundary edge of deformation.Although NiAl phase is fragile material, deformation is very
It is small, but still can be seen that dislocation through laser in the process of movement wherein, such as Fig. 2, it can be seen from the figure that dislocation motion
Approach there are two: one is to be obstructed when encountering other crystal boundaries along grain boundary and generate long-pending plug；It in addition is exactly in crystal
Portion's movement generates product plug when moving to another side crystal boundary.The dislocation moved from multiple directions, in some position of crystal boundary
Product plug forms dislocation tangle.Obstruction when also found dislocation motion simultaneously by some precipitated phases, forms along precipitated phase
The dislocation on periphery wraps up phenomenon, produces dislocation ring.According to Fig. 4 electronic diffraction calibration shown in, Fig. 3 be NiAl phase, due to by
The influence of plasma stock wave, crystal produce lesser deformation, and there are a small amount of dislocations on crystals and crystal boundary.?
Intra-die discovery around the NiAl phase has a small amount of precipitated phase, in addition scale also has a small amount of about in 20-30nm or so
Deformation and dislocation exist.Discovery has a large amount of unauspicious item at adjacent NiAl phase grain boundary sites, as shown in figure 5, this mainly by
Caused by the overlapping of upper and lower two crystal.The display demarcated according to Fig. 6, there are two sets of spots, wherein between a set of spot
Away from being, this is NiAl phase and Ni twice of another set of spot3Al phase produces coherence.
The present invention carries out transmission electron microscope analysis to the GH202 matrix below coating, as is seen in figs 7-10.It is of the invention in figure
Matrix produces highdensity dislocation, as shown in Figure 7.Matrix of the invention is plastically deformed, and causes dislocation motion in crystalline substance
Boundary's product plug, forms dislocation wall and dislocation tangle.Obstruction during dislocation motion by a certain precipitated phase forms dislocation
Ring.The generation of these crystal defects hinders the movement of dislocation, improves the mechanical property of material.Dislocation inside GH202 is in
The movement tendency being parallel to each other, when dislocation motion to grain boundary sites, produces as shown in figure 8, foring some twins across crystal
Raw accumulation, forms highdensity dislocation tangle, increases the resistance that dislocation further slides.Since the movement of dislocation is different, when
It is interlaced that multiple dislocations move to a certain position from different directions, so that crystal is produced refinement, foring size is about 100nm
The small crystals of left and right, as shown in Figure 9.Crystal grain refinement is particularly evident in such as Figure 10, it has further been found that there is depositing for dislocation array
, in an array between also have highdensity dislocation tangle.The above phenomenon illustrates to close using nickel aluminium prepared by method of the invention
Gold plating realizes the reinforcing to matrix, is conducive to the high temperature oxidation resistance for improving coating and alloy.
Embodiment 3
Sample a and sample b is chosen, sample a uses the Ni-Al alloy coating of conventional method preparation, and sample b uses side of the invention
The Ni-Al alloy coating of method preparation.
The test that sample a and sample b are carried out to constant temperature oxidation performance at 800 DEG C -1100 DEG C, according to sample weight in experiment
Two kinds of samples oxidizing dynamics curve at each temperature is drawn out in the variation of amount.The calorized coating of sample a is in oxidation initial stage, unit
Gain in weight on area is in zooming trend, and as high-temperature oxydation persistently carries out, oxidation weight gain speed gradually slows down, such as
Shown in Figure 11.With the raising of oxidizing temperature, coating oxidation weight gain is consequently increased, and sample weight gain is outstanding under the conditions of 1100 DEG C
It is obvious.From in figure it can be found that at 1000 DEG C and 1100 DEG C sample loss of weight, this is because oxidation film at high temperature
Occur to peel off and cause.Sample b oxidation weight gain situation of change at each temperature is shown in Figure 12, it can be seen that its oxidation weight gain is wanted
Significantly lower than the sample not impacted, and at 1000 C and the phenomenon that weight gain is reduced is found no, and 1100 DEG C of weight gains are slightly dropped
It is low, illustrate the phenomenon that oxide layer deterioration also has occurred after 1100 DEG C of oxidation 100h in sample b, but the degree of its loss of weight will have a competition
Sample a wants small.It can thus be seen that aluminising sample generates Al at oxidation initial stage2O3Oxidation film keeps sample weight increase more significant,
With the lasting progress of oxidation, the continuous and fine and close Al of coating surface2O3Film hinders the further infiltration of oxygen, has preferable
Protective effect.What method of the invention can promote Al element is quickly generated finer and close Al2O3Film, it is more efficient
The infiltration of the anti-block in ground illustrates that method of the invention improves the high-temperature oxidation resistant of calorized coating to keep alloy gain in weight lower
Performance.
X-ray diffraction analysis has been carried out to sample a and sample b, from shown in Figure 13-20, can be seen that calorized coating in figure
The main component that sample aoxidizes rear surface oxidation film at 800 DEG C is α-Al2O3, θ-Al2O3,Since oxide thickness is relatively thin, also examine
Measure NiAl, Ni2Al3And matrix.Compare Figure 13 and 17 liang of figure it is not difficult to find that the NiAl of sample b and the peak value of matrix are than sample a
It is eager to excel, illustrates that coating of the invention oxidation film generated is relatively thin, the growth rate of oxidation film is more slow.Coating exists
After aoxidizing 100 hours at 900 DEG C, surface film oxide is still by α-Al2O3, θ-Al2O3Composition, Ni2Al3Peak almost disappear
It loses, this is because phase transformation has occurred at high temperature for a long time, generates NiAl phase；After 1000 DEG C of oxidation 100h on sample b
It was found that there is a small amount of Cr2O3(shown in Figure 15) illustrates the Al on surface2O3A degree of peeling has occurred in film, and do not impact
Sample is then without discovery Cr2O3Appearance, surface film oxide is mainly by α-Al2O3Composition, with a small amount of θ-Al2O3(Figure 19
It is shown)；Sample a and b has occurred large stretch of peeling phenomenon, produces a large amount of Cr after 1100 DEG C of oxidation 100h2O3With it is few
The TiO of amount2With spinelle NiCr2O4.The peak value of comparative sample a and b, the Cr that sample a is generated2O3It obviously wants more, shows
Coating of the invention helps to inhibit Cr2O3Growth, delay Cr element to external diffusion.
Pass through scanning electron microscopic observation sample a and b surface film oxide pattern.As can be seen from the figure in 800 DEG C of oxidation 100h
It is mainly in acicular θ-Al that oxidation film is very fine and close afterwards2O3With a small amount of block-like α-Al2O3.Comparative sample a and b, are not difficult to send out
Existing sample b surface film oxide is finer and close (as shown in Figure 21,22)；As the temperature rises, sample is in 900 DEG C of oxidation 100h
Afterwards, acicular θ-Al in sample a oxidation film2O3With α-Al2O3It grows up obvious, oxidation film shows slightly more loose, and sample
B surface film oxide still seems comparatively dense, θ-Al2O3With α-Al2O3Scale it is relatively small (as shown in Figure 23,24)；?
After 1000 DEG C of oxidation 100h, falling off for larger area occurs for sample a surface film oxide, and oxidation film forms multiple small pits,
And the Al in the oxidation film of sample b2O3Scale, which has, more significantly grows up, but compares that the former still seems fine and close many
(shown in 25,26 figures)；After aoxidizing 100 hours at 1100 DEG C, there is large stretch of area of spall, oxygen in sample a coating oxidation film
Change Al in film2O3Content is less, and the holding of sample b oxidation film is more complete, only α-Al2O3Particle growth is more obvious, θ-
Al2O3It has been disappeared that, while also found that a small amount of Cr occurs in oxidation film surface2O3And TiO2.Thus illustrate sample b oxidisability
Sample a can be better than, this main method of the invention has a kind of refining effect for aluminising surface film oxide, is able to suppress Al2O3
Growth, delay the transformation time of oxidation film, to play a kind of better protective effect to matrix.
Cross Section Morphology is as shown in Figure 29-36 after 800-1100 DEG C of oxidation 100h by sample a and b, after 800 DEG C of oxidation 100h
Section forms three-decker, and a thin layer of continuous oxidation film of densification is formd in superficial layer, main according to XRD analysis
It is Al2O3, it is interior diffusion layer (Inter-diffusion Zone) in the lower section of coating, such as Figure 29 that intermediate one layer, which is NiAl coating,
Shown in 30.With the raising of oxidizing temperature, sample a is still three-decker after 900 DEG C of oxidation 100h, outermost oxidation film
Grown in thickness is more obvious, and the calorized coating oxidation film of sample b is rendered as double-layer structure, outer layer Al2O3Film, internal layer are
Cr2O3Film, outer layer is slightly thick, and internal layer is very fine and close, and dual protective effect is played to matrix.Interior expansion below oxidation film
Scattered region is obviously thickened, and illustrates that method of the invention facilitates the inside diffusion of Al element, as shown in figs. 31 and 32.At 1000 DEG C
The aluminising specimen cross section of sample a has not seen three-decker after oxidation 100h, and oxidation film becomes more loose at this time, with perhaps
The appearance of multiple cracks and the area of spall of bulk, and a degree of internal oxidition has occurred in intrinsic silicon, while with thick
The TCP phase of big strip is precipitated, as shown in figure 33.And also there is loose and peeling phenomenon in the top of sample b its oxidation film, is precipitated
The internal oxidition phenomenon also occurred like acicular TCP phase, below oxidation film, compare the former many of having wanted light, as shown in figure 33.
After 1100 DEG C of oxidation 100h, the peeling of sample a surface film oxide is more serious, and alloy substrate is big along the depth of internal oxidation of crystal boundary
About 50 μm, and the surface film oxide of sample b is thicker, is divided into two layers, outer layer is thin and loose, has stomata, inner-layer thick and it is fine and close,
Still there is certain protective effect to matrix alloy.The degree of internal oxidition, which has, adds play, and TCP is precipitated and becomes more, grows up more obvious.
It can thus be seen that method of the invention has refining effect for the oxidation film on calorized coating surface, help to inhibit oxidation film
With the speed of growth of intrinsic silicon TCP, delay the transformation time of oxide, the adhesion strength for improving oxidation film has preferable
Effect, the oxidation-resistance property of calorized coating can be improved.
Embodiment described above is only that the preferred embodiment of the present invention is described, not to design of the invention
It is defined with range, without departing from the design concept of the invention, ordinary engineering and technical personnel is to this hair in this field
The all variations and modifications that bright technical solution is made should all fall into protection scope of the present invention, claimed skill of the invention
Art content is all documented in technical requirements book.
Claims (5)
1. a kind of Ni-Al alloy coating, it is characterised in that: including NiAl phase crystal grain, Ni2Al3Phase crystal grain, AlCr deposit, dislocation
Entanglement, dislocation ring, unauspicious item；The coating is by NiAl phase crystal grain, Ni2Al3Phase crystal grain and AlCr deposit are constituted；NiAl phase
Crystal grain, Ni2Al3Dislocation tangle is arranged in phase crystal particle crystal boundary periphery；Intra-die around the NiAl phase is provided with precipitated phase；It is more
A precipitated phase periphery is provided with dislocation ring；There are several unauspicious items at adjacent NiAl phase grain boundary sites.
2. a kind of Ni-Al alloy coating according to claim 1, it is characterised in that: the partial size of the NiAl phase crystal grain exists
200nm-300nm；Ni2Al3The partial size of phase crystal grain is in 48-52nm.
3. a kind of method for preparing Ni-Al alloy coating described in claim 1, characterized by the following steps:
(1) aluminizing medium is sufficiently mixed to infiltration that is uniformly rear and needing the nickel-base alloy for carrying out aluminising processing to be co-located in sealing in proportion
In filling, heats under vacuum or under inert gas shielding and carry out aluminising processing；
(2) powder that surface adhesion is washed off with cleaning agent, then polishes to the surface after aluminising, polishing treatment；
Alloy its progress handled to step (2) is laser impact intensified.
4. the method according to claim 3 for preparing Ni-Al alloy coating, it is characterised in that: described to be carried out in alloy surface
Laser reinforcing impact, percussion power is 10kw, and number of shocks is 2-4 times, spot diameter 4mm, overlapping rate 50%, use aluminium foil for
Protective layer, 2mm thickness water are restraint layer.
5. the method according to claim 3 for preparing Ni-Al alloy coating, it is characterised in that: aluminizing medium is pressed in step (1)
Include following component according to weight percent meter: Cr 12wt.%, 1.5 Pd wt.%, Al 24.5wt.%, NH4Cl 3.2wt.%,
AlCr alloyed powder 18wt.%, Y2O33.8wt.%, Al2O3 surplus.
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