CN101310971A - Ni-base superalloy complex gradient coating and preparation technique thereof - Google Patents
Ni-base superalloy complex gradient coating and preparation technique thereof Download PDFInfo
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- CN101310971A CN101310971A CNA2007100114318A CN200710011431A CN101310971A CN 101310971 A CN101310971 A CN 101310971A CN A2007100114318 A CNA2007100114318 A CN A2007100114318A CN 200710011431 A CN200710011431 A CN 200710011431A CN 101310971 A CN101310971 A CN 101310971A
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- 239000011248 coating agent Substances 0.000 title claims abstract description 115
- 238000000576 coating method Methods 0.000 title claims abstract description 115
- 238000002360 preparation method Methods 0.000 title claims abstract description 22
- 238000000034 method Methods 0.000 title claims abstract description 20
- 229910000601 superalloy Inorganic materials 0.000 title description 3
- 239000002131 composite material Substances 0.000 claims abstract description 15
- 238000007733 ion plating Methods 0.000 claims abstract description 12
- 238000005269 aluminizing Methods 0.000 claims abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- 238000009792 diffusion process Methods 0.000 claims abstract description 7
- 239000000843 powder Substances 0.000 claims description 26
- 238000000151 deposition Methods 0.000 claims description 22
- 239000010410 layer Substances 0.000 claims description 19
- 230000008021 deposition Effects 0.000 claims description 17
- 229910015372 FeAl Inorganic materials 0.000 claims description 15
- 238000005516 engineering process Methods 0.000 claims description 11
- 238000004518 low pressure chemical vapour deposition Methods 0.000 claims description 11
- 238000009413 insulation Methods 0.000 claims description 10
- 238000009826 distribution Methods 0.000 claims description 9
- 238000000137 annealing Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 7
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 6
- 239000011247 coating layer Substances 0.000 claims description 6
- 239000003961 penetration enhancing agent Substances 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 5
- 229910052751 metal Inorganic materials 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 5
- 150000001875 compounds Chemical class 0.000 claims description 4
- 239000000758 substrate Substances 0.000 claims description 4
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 3
- 238000005270 abrasive blasting Methods 0.000 claims description 3
- 239000008367 deionised water Substances 0.000 claims description 3
- 229910021641 deionized water Inorganic materials 0.000 claims description 3
- 239000003599 detergent Substances 0.000 claims description 3
- 239000011521 glass Substances 0.000 claims description 3
- 238000004506 ultrasonic cleaning Methods 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 238000001035 drying Methods 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 238000005275 alloying Methods 0.000 claims 1
- 238000010891 electric arc Methods 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 abstract description 11
- 239000000956 alloy Substances 0.000 abstract description 11
- 238000007254 oxidation reaction Methods 0.000 abstract description 10
- 238000005229 chemical vapour deposition Methods 0.000 abstract description 8
- 230000007797 corrosion Effects 0.000 abstract description 5
- 238000005260 corrosion Methods 0.000 abstract description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 4
- 239000011253 protective coating Substances 0.000 abstract description 2
- 238000004321 preservation Methods 0.000 abstract 1
- 229910000943 NiAl Inorganic materials 0.000 description 21
- 239000012071 phase Substances 0.000 description 17
- 239000000203 mixture Substances 0.000 description 8
- 230000003647 oxidation Effects 0.000 description 8
- 238000003860 storage Methods 0.000 description 6
- 239000012720 thermal barrier coating Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 3
- 230000014759 maintenance of location Effects 0.000 description 3
- 238000004062 sedimentation Methods 0.000 description 3
- 239000004411 aluminium Substances 0.000 description 2
- 230000007850 degeneration Effects 0.000 description 2
- 238000003475 lamination Methods 0.000 description 2
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- 230000002000 scavenging effect Effects 0.000 description 2
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- 230000008023 solidification Effects 0.000 description 2
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- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 description 1
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- 239000012808 vapor phase Substances 0.000 description 1
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Abstract
The invention mainly relates to the coating technique, in particular to a gradient MCrAlY coating used for protecting high-temperature alloy and a preparation method thereof. The invention prepares an MCrAlY composite gradient coating by adopting the method combining the arc ion plating (AIP) and the diffusion aluminizing. The thickness of an aluminum-rich layer on the surface of the MCrAlY composite coating can be controlled by setting the aluminizing temperature and the period of heat preservation and the Al elements are distributed in a gradient way along the depth direction; in addition, the chemical vapor deposition method used for the aluminizing has the advantages of good uniformity on the aluminum-rich layer and being not affected by the size and shape of a sample. Since the method of direct diffusion is adopted without introducing a weak interface, the MCrAlY high-temperature protective coating can increase the content of Al memory phase to the utmost extent under the condition that the mechanical property of the coating is guaranteed, so as to improve the high-temperature oxidization resistance and the heat corrosion resistance of the coating, and can effectively prolong the service life of the coating. The MCrAlY composite gradient coating and the preparation method of the invention can be applied to the protection of Ni-based and Co-based high-temperature alloys.
Description
Technical field
The present invention relates to the high-temperature protection coating technology, specifically a kind of MCrAlY adds complex gradient high-temperature protection coating and preparation method.
Background technology
As a kind of MCrAlY (M=Ni with good resistance oxidation, hot corrosion resistance, Co or Ni+Co) coating, be widely used in the protection of heat-resistant parts such as aero-engine, gas turbine blades, it both can use separately, also can be used as adhesive linkage (bond coat) and surface ceramic layer (as Y
2O
3Partially stabilized ZrO
2) constitute thermal barrier coating (TBCs, i.e. thermal barrier coatings) system together, improve resistance to high temperature oxidation, the hot corrosion resistance of parts, prolong the service life of parts.The document of related application is as 1. Chinese invention patent, and a kind of detonation flame spraying prepares the method for thermal barrier coating, application number 01133423.1; 2. Chinese invention patent, a kind of oxidation-inhibited thermal barrier coating and preparation method, application number 02133193.6; 3. Chinese invention patent, a kind of preparation method of heat shock resistance thermal barrier coating, application number 03133344.3; 4. Chinese invention patent, a kind of NiCoCrAlYSiB corrosion and heat resistant coating and preparation method thereof, application number 03111363.X; Or the like.
For high temperature alloy and high-temperature protection coating parts, oxidation is one of major reason that causes component failure, and the raising of its antioxygenic property mainly depends on the slowly Al of growth of surface
2O
3Film.At high temperature, the pellumina of even compact, particularly α-Al
2O
3Film has excellent heat endurance, and the element diffusion coefficient of portion within it is very little, so wishes to add the Al element of high level in high temperature alloy or the high-temperature protection coating usually, utilizes the selective oxidation of Al to generate single even Al
2O
3Film does not protect inner base oxidated or reduce oxidation rate, prolongs parts service life.In the Ni base high temperature protection MCrAlY coating between common Al metal element compound Ni is arranged
2Al
3, β-NiAl and γ '-Ni
3Al etc., wherein Ni
2Al
3Compare crisp, γ '-Ni
3Al content is too low and can not keep for a long time and generate single Al among the Al
2O
3Film, and β-NiAl is to have higher Al content and relative good mechanical performance simultaneously as Al storage phase (Al-reservoir) common in the coating.
The element counterdiffusion of high-temperature oxydation and coating and matrix is the major reason that causes coating system to lose efficacy for a long time, is characterized in that the storage of Al element is consumed in a large number, and the Al concentration of final coating inside is not enough to selective oxidation and generates single Al
2O
3Film and no longer have protective value.In order to improve service life under the coating high-temp, can improve the reserves of outer surface Al element by the method that design MCrAlY adds NiAl two-layer compound coating, but this method has increased the multilayer interface in the coating system, can cause the increase of weak link in the coating system.Therefore, how do not changing or guaranteeing that the content that improves Al element in the coating under the prerequisite of coating mechanical property becomes the key issue that prolongs the high-temperature protection coating active time.
Summary of the invention
In order to delay the degeneration of high-temperature protection coating, prolong the active time of coating, the object of the present invention is to provide a kind of MCrAlY of Al element distribution gradient to add complex gradient coating and preparation method.Because Gradient Effect makes coating improve β-NiAl to greatest extent under the prerequisite that guarantees mechanical property and stores phase content, thereby can delay the coating degradation process, improves the protection effect and the military service cycle of coating.
To achieve these goals, technical scheme of the present invention is:
A kind of MCrAlY adds complex gradient coating, compound Al element gradient coating on the MCrAlY coating, and the Al concentration of element is along the depth direction distribution gradient, and top layer Al concentration of element is 20-30wt%, and nexine Al concentration of element is 5-10wt%.
The MCrAlY that the present invention adopts the method for solid-state embedding or low-pressure vapor phase Diffusional aluminizing to prepare the distribution of Al concentration gradient on the conventional MCrAlY coating that deposits with arc ion plating (AIP) method adds composite coating.
Described conventional MCrAlY coating alloy system composition is Co:0～40, Cr:15～40, Al:6～16, Y:0.1～1, Si:0～2, B:0.01～0.03, Hf:0～1.5, Ni: surplus by mass percentage.
The concrete preparation method of described gradient Ni-base superalloy coating is: 1) the conventional MCrAlY coating of arc ion plating (AIP, i.e. Arc IonPlating) preparation; 2) on conventional MCrAlY coating basis, adopt: a.) powder embedding+vacuum diffusion annealing method, b.) low-pressure chemical vapor deposition (CVD) method, the MCrAlY that preparation Al concentration in gradient distributes adds complex gradient coating.
Running parameter is as follows: during arc ion plating, operating room's vacuum is evacuated to 2 * 10 in advance
-3～1 * 10
-2Pa, and sample carried out pre-sputter clean, pulsed bias be-800～-1000V, target-substrate distance 230～250mm, dutycycle 20～40%, time 2～5min; During deposition, arc voltage 20～25V, arc current 50～70A, pulsed bias-150～-300V, dutycycle 20～40%, 300～400 ℃ of depositing temperatures are controlled coating layer thickness according to sedimentation time, and coating layer thickness is 40～60 μ m;
When adopting the aluminising of pressed powder investment on the MCrAlY coating, penetration enhancer is that 95-99wt%FeAl powder (Al content is 48～52wt% mass ratio, powder size 100～300 orders) adds 1～5wt%NH
4Cl (FeAl powder content and NH
4The Cl sum is 100%); 850～1050 ℃ of pack cementation aluminizing temperature, the rate of heat addition are controlled in the 8 ℃/min, and normal pressure is insulation 3～5h down, and air cooling is to room temperature subsequently.The composite coating that obtains is carried out vacuum heat, and vacuum diffusion annealing temperature is 900～1000 ℃, time 4～6h, and heating rate≤8 ℃/min cool to room temperature with the furnace, obtain the MCrAlY that the Al concentration in gradient distributes and add complex gradient coating;
When adopting the aluminising of low-pressure chemical vapor deposition (CVD) method on conventional MCrAlY coating, penetration enhancer adds the NH of 1～5wt% oven dry for dry 95-99wt%FeAl powder (Al content is 48～52wt% mass ratio, powder size 100～300 orders)
4Cl (FeAl powder content and NH
4The Cl sum is 100%); The interior vacuum of furnace chamber is evacuated to 0.1～0.01 atmospheric pressure during the CVD aluminising, temperature is 800～1050 ℃, and heating rate is no more than 8 ℃/min, insulation 3～6h, be quickly cooled to room temperature, obtain Al concentration and add complex gradient coating along the MCrAlY of depth direction distribution gradient.
The gradient coating of the present invention's preparation can satisfy mechanical property and improve the double requirements of Al constituent content, its inner Al element distribution gradient promptly can improve the mark of the storage of Al in coating phase to greatest extent under the condition that does not reduce or seldom reduce the coating mechanical property.In the gradient coating, surface Al concentration height helps forming the Al of protectiveness
2O
3Film and the long-time slowly required Al element of growth of oxide-film that replenishes; The inner Al content of coating is relatively low, and is limited with the Al element that the matrix alloy counterdiffusion is consumed, and therefore this structure can generate Al mutually to greatest extent with the Al storage of inside
2O
3Film becomes effective Al source.In addition, because Al element distribution gradient, coating surface and the inner metal combination that belongs to the continuous transition state that combines, there is not weak interface, and surperficial rich Al layer thickness is limited, and its fragility reduces greatly because of small-size effect, can not bring results of serious failure such as coating stripping.
The present invention has the following advantages:
1. coating longer service life.Owing to improved the content of coating storage inside phase β-NiAl, make the interior Al source of coating can give replenishing of surface film oxide longer time, thereby delayed the degeneration of coating, promptly prolonged the active time of coating.
2. Al concentration has the advantages that gradient distributes among the present invention, does not increase the combination of weak interface, its mechanical property excellence.This MCrAlY adds the thickness of the rich aluminium lamination in composite coating surface and can control by setting aluminising temperature and temperature retention time, and the Al element is along the depth direction distribution gradient.
3. the present invention adopts the MCrAlY of preparation to add that rich Al layer has the adjustable characteristics of thickness in the complex gradient coating, promptly by regulating the thickness that aluminising temperature and temperature retention time are controlled β-NiAl layer of rich Al.
4. the present invention's MCrAlY adds the protection that complex gradient coating can be applicable to Ni base, Co based high-temperature alloy.
5. the present invention adopts the advantage that the chemical vapour deposition technique aluminising has rich aluminium lamination good uniformity and not influenced by the specimen size shape.Owing to adopt the directly method of diffusion, do not introduce weak interface, this MCrAlY increases temperature protective coating can improve Al storage phase to greatest extent under the condition that guarantees the coating mechanical property content, then improve coating resistance to high temperature oxidation, hot corrosion resistance, and can prolong coating service life effectively.
Description of drawings
Fig. 1 (a)-(b) is (a) and annealing back (b) before 1000 ℃ of annealing, pack aluminizing MCrAlY+ composite coating cross section pattern (backscattered electron image).
Fig. 2 is a MCrAlY+ composite coating XRD diffracting spectrum after deposition attitude MCrAlY coating and the 950 ℃ of aluminisings before the aluminising of low pressure chemical vapor deposition gas phase.
Fig. 3 is the section S EM pattern (backscattered electron image) that MCrAlY adds complex gradient coating behind 950 ℃ of low pressure chemical vapor deposition gas phase aluminising 4h.
Fig. 4 is the section S EM pattern (backscattered electron image) that MCrAlY adds complex gradient coating behind 900 ℃ of low pressure chemical vapor deposition gas phase aluminising 4h.
Fig. 5 is the section S EM pattern (backscattered electron image) that MCrAlY adds complex gradient coating behind 1000 ℃ of low pressure chemical vapor deposition gas phase aluminising 6h.
The specific embodiment
Below by example the present invention is described in further detail.
Embodiment 1
Base material adopts directional solidification nickel-base high-temperature alloy DSM11, its composition following (mass percent): Co:9.5, Cr:14, W:3.8, Mo:1.5, Al:3, Ti:4.8, Ta:2.8, C:0.1, Ni: surplus.On base material, adopt the conventional MCrAlY coating of arc ion plating (AIP) deposition, MCrAlY target composition following (mass percent meter), Co:32; Cr:20; Al:8; Y:0.5; Si:1; B:0.03, Ni: surplus.Concrete operations technology is as follows: before the deposition sample is carried out preliminary treatment, being about to the base material sample polishes to Ra=0.4 μ m, adopt 200 order hollow glass ball wet abrasive blastings to handle, successively adopt metal detergent, deionized water, acetone ultrasonic cleaning 15min immediately, with dry for standby after the alcohol rinsing.Adopt homemade MIP-8-800 type multi-arc ion plating equipment to deposit conventional MCrAlY coating, forvacuum to 7 * 10
-3Pa feeds Ar gas when bombardment and deposition, and vacuum is 2.2 * 10
-1Pa.Sample is carried out pre-sputter bombardment clean, target-substrate distance is 240mm, and pulsed bias is-800V dutycycle 33%, scavenging period 5min; Arc voltage is 20V during deposition, and arc current 62A, pulsed bias be-250V, dutycycle 33%, and 350 ℃ of depositing temperatures, sedimentation time 500min, the conventional MCrAlY coating layer thickness of acquisition is about 60 μ m.
Adopt powder investment Diffusional aluminizing, penetration enhancer adopts the FeAl powder (contain Al and be about 51wt%, powder size is about 250 orders) of 98wt% to add 2wt%NH
4Cl, sample is deposition attitude or the conventional MCrAlY coating of annealed state.Sample is coated in the penetration enhancer, 900 ℃ of insulation 4h in the Muffle furnace under the normal pressure, the rate of heat addition is no more than 8 ℃/min during intensification, and last air cooling is to room temperature.With the aluminising sample that obtains under vacuum condition, 1000 ℃ of annealing 4h, SEM cross section pattern photo is as Fig. 1 (a) with (b) before and after the annealing.
By Fig. 1 (a)-(b) as can be known, behind the pack cementation aluminizing, the MCrAlY coating surface has formed rich Al district, annealed back coating surface partly changes β-NiAl layer of rich Al into, β-NiAl layer thickness of rich Al is about 20 μ m, and Al content is about 30.4wt%, mainly exists with pure β-NiAl form; Inner inner average A l content is about 14.7wt% for MCrAlY adds β-NiAl phase that disperse distributes, and this MCrAlY adds the characteristics that composite coating has gradient-structure.
Embodiment 2
Base material adopts directional solidification Ni based high-temperature alloy DZ125, its composition following (mass percent), Co:10, Cr:9, W:7, Al:5, Ti:2.5, Ta:3.5, C: trace, Ni: surplus.The composition of conventional MCrAlY coating and depositing operation are with embodiment 1, and the conventional MCrAlY coating layer thickness of acquisition is about 50 μ m.Carrying out the low pressure chemical vapor deposition gas phase should be with NH before oozing Al
4The method of 120 ℃ of normal pressure insulation 12h is adopted in Cl oven dry, present embodiment.NH with 96wt%FeAl powder (Al content is 48wt%, and powder size is about 250 orders) and 4wt% oven dry
4Cl puts into the CVD furnace chamber after fully mixing, and after vacuum was evacuated to 0.1 atmospheric pressure (atm), 950 ℃ of insulation 5h obtained dry FeAl powder with stove cooling back.The MCrAlY sample of deposition attitude or annealed state is hung in the low pressure chemical vapor deposition stove, put into the FeAl powder and the dry NH of 25g of 800g drying
4Cl, vacuum is evacuated to 0.08atm, behind 950 ℃ of insulation 4h, opens the quick air cooling of furnace enclosure to room temperature.The MCrAlY that obtains adds composite coating surface XRD diffracting spectrum as shown in Figure 2, and MCrAlY adds composite coating cross section pattern photo as shown in Figure 3.
As shown in Figure 2, after the low pressure chemical vapor deposition aluminising, amorphous " steamed bun " peak γ/γ '-Ni in the former deposition attitude MCrAlY coating
3Al disappears, and the MCrAlY of acquisition adds the pure β-NiAl phase composition of composite coating top layer by complete crystallization.Fig. 3 shows that the β-NiAl layer thickness of rich Al in the gradient Ni-base superalloy coating that this method obtains is about 17 μ m, and the β of rich Al-NiAl layer Al content is 31.2wt%, and Al mainly exists mutually with β-NiAl; Internal layer adds β-NiAl phase that disperse distributes by MCrAlY, and its average A l content is about 16.3wt%, and Al is with β-NiAl and γ '-Ni
3Al exists mutually, adds in the complex gradient coating at this MCrAlY, and Al content has the feature that gradient distributes along depth direction.
Embodiment 3
Base material adopts Co based high-temperature alloy K40, and its nominal composition is (mass percent): 10.5%Ni, 25.5%Cr, and 7.5%W, 0.45%C, Co surplus, specimen size are 15 * 10 * 1.5mm
3Adopt homemade MIP-8-800 type multi-arc ion plating equipment codeposition MCrAlY+Al (SiY) composite coating.MCrAlY alloy target material composition following (mass percent meter), Co:32; Cr:20; Al:10; Y:0.5; Si:1; B:0.03, Ni: surplus.Before the deposition sample is carried out preliminary treatment, be about to the base material sample and polish, adopt 200 order hollow glass ball wet abrasive blastings to handle, successively adopt metal detergent, deionized water, acetone ultrasonic cleaning 15min immediately, with dry for standby after the alcohol rinsing to Ra=0.4 μ m.Adopt MIP-8-800 type arc ion plating apparatus to deposit conventional MCrAlY coating, forvacuum to 7 * 10
-3Pa feeds Ar gas when bombardment and deposition, and vacuum is 2 * 10
-1Pa.Sample is carried out pre-sputter bombardment clean, target-substrate distance is 240mm, and pulsed bias is-800V dutycycle 33%, scavenging period 5min; Arc voltage is 20V during deposition, and arc current 60～65A, pulsed bias be-250V, dutycycle 33%, and depositing temperature is 350 ℃, and sedimentation time is 500min, and the conventional MCrAlY coating layer thickness of acquisition is about 60 μ m.
The conventional MCrAlY deposition attitude coating that obtains is carried out vacuum heat, and heating rate is controlled at 8 ℃/min, is incubated after 4 hours to cool off with stove, obtains annealed state MCrAlY coating.Annealed state MCrAlY coating is put into the low pressure gas phase deposition stove, and vacuum is evacuated to 0.01atm, adds the FeAl powder and the NH of oven dry according to embodiment 2 prescriptions
4Cl is warming up to 900 ℃ with the speed of 8 ℃/min, is quickly cooled to room temperature behind the insulation 4h, and the cross section pattern that the MCrAlY of acquisition adds gradient coating as shown in Figure 4; Heating rate with 8 ℃/min is heated to 1000 ℃ equally, and insulation 6h is quickly cooled to room temperature, and the cross section pattern that the MCrAlY of acquisition adds complex gradient coating as shown in Figure 5.
As shown in Figure 4, rich Al layer thickness is thinner in this complex gradient coating, is about 10 μ m, and coated inside adds that by MCrAlY β-NiAl that disperse distributes constitutes mutually; As shown in Figure 5, β-NiAl layer thickness of the rich Al in this complex gradient coating top layer is thicker, has surpassed 20 μ m, and has had Interim.The MCrAlY that obtains under two kinds of gas phase aluminising temperature adds composite coating, and the β of its rich Al-NiAl top layer Al content is respectively 30.4wt% (900 ℃) and 29.6wt% (1000 ℃), and Al element wherein mainly exists mutually with β-NiAl; Internal layer adds β-NiAl phase that disperse distributes by MCrAlY, and its average A l content is about 18wt%, and Al is with β-NiAl phase and γ '-Ni
3Al exists mutually; Hence one can see that, and the chemical vapour deposition (CVD) aluminising can come the thickness of the rich Al layer of control surface according to aluminising temperature and temperature retention time, and this MCrAlY adds complex gradient coating and has the adjustable characteristics of thickness.
Claims (8)
1. a MCrAlY adds complex gradient coating, it is characterized in that: compound Al element gradient coating on the MCrAlY coating, the Al concentration of element is along the depth direction distribution gradient, and this complex gradient coating top layer Al concentration of element is 20-30wt%, and nexine Al concentration of element is 5-10wt%.
2. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 1, it is characterized in that:
Method by arc ion plating and Diffusional aluminizing prepares MCrAlY and adds complex gradient coating, and described Diffusional aluminizing adopts pressed powder investment or Low Pressure Chemical Vapor Deposition.
3. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 2, it is characterized in that:
Need before the electric arc ion-plating deposition sample is carried out preliminary treatment, the base material sample is polished to Ra=0.4 μ m, adopt 60～220 order hollow glass ball wet abrasive blastings to handle, successively adopt metal detergent, deionized water, acetone ultrasonic cleaning 15min immediately, with drying after the alcohol rinsing.
4. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 2, it is characterized in that:
Adopt arc ion plating (aip) to deposit conventional MCrAlY coating, deposition parameter is: the base vacuum of vacuum chamber is evacuated to 2 * 10
-3～1 * 10
-2Pa; Feed Ar gas, make pressure in vacuum tank rise to 5 * 10
-2～3 * 10
-1Pa; Target-substrate distance is 230～250mm, bombardment bias voltage-800～-1000V, dutycycle 20～40%, 2～5 minutes sputter clean time; During deposition MCrAlY coating, arc current 50～70A, arc voltage 20～25V, pulsed bias-150～-300V, dutycycle 20～40%, 300～400 ℃ of depositing temperatures, coating layer thickness 40～60 μ m of preparation.
5. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 4, it is characterized in that:
MCrAlY target alloying component, by mass percentage, Co is 0～40%, and Cr is 15～40%, and Al is 6～16%, and Y is 0.1～1%, and Si is 0～2%, and B is 0.01～0.03%, and Hf is 0.05～0.2%, Ni is a surplus.
6. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 2, it is characterized in that:
Adopt the aluminising of pressed powder investment on conventional MCrAlY coating, penetration enhancer adds 1～5wt%NH for the 95-99wt%FeAl powder
4Cl, FeAl powder content and NH
4The Cl sum is 100%, and the Al content of FeAl powder is 48～52wt% mass ratio, powder size 100～300 orders; Heating rate≤8 ℃/min, 850～1050 ℃ of insulation 3～5h under the normal pressure, air cooling is to room temperature subsequently.
7. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 6, it is characterized in that:
The composite coating that obtains is carried out vacuum heat, and subsequently with sample 900～1000 ℃ of diffusion annealing 4～6h under vacuum condition, heating rate≤8 ℃/min cool to room temperature with the furnace, obtain the MCrAlY that the Al concentration in gradient distributes and add complex gradient coating.
8. add the preparation technology of complex gradient coating according to the described MCrAlY of claim 2, it is characterized in that:
Adopt the aluminising of low pressure chemical vapor deposition method on conventional MCrAlY coating, penetration enhancer adds the NH of 1～5wt% oven dry for dry 95-99wt%FeAl powder
4Cl, FeAl powder content and NH
4The Cl sum is 100%, and the Al content of FeAl powder is 48～52wt% mass ratio, powder size 100～300 orders; The interior vacuum of furnace chamber is evacuated to 0.1～0.01 atmospheric pressure during the CVD aluminising, temperature is 800～1050 ℃, and heating rate is no more than 8 ℃/min, insulation 3～6h, be quickly cooled to room temperature, obtain Al concentration and add complex gradient coating along the MCrAlY of depth direction distribution gradient.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2007100114318A CN101310971B (en) | 2007-05-25 | 2007-05-25 | Ni-base superalloy complex gradient coating and preparation technique thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2007100114318A CN101310971B (en) | 2007-05-25 | 2007-05-25 | Ni-base superalloy complex gradient coating and preparation technique thereof |
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|---|---|
| CN101310971A true CN101310971A (en) | 2008-11-26 |
| CN101310971B CN101310971B (en) | 2012-01-04 |
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| CN2007100114318A Expired - Fee Related CN101310971B (en) | 2007-05-25 | 2007-05-25 | Ni-base superalloy complex gradient coating and preparation technique thereof |
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| CN103590002A (en) * | 2012-08-17 | 2014-02-19 | 中国科学院金属研究所 | Preparation method for Al-Cr coating on nickel-based superalloy |
| CN103590003A (en) * | 2013-11-13 | 2014-02-19 | 东北大学 | Method for preparing hard damping coating on surface of rotating machinery blade through PVD (physical vapor deposition) |
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| CN108950489A (en) * | 2018-08-21 | 2018-12-07 | 中国科学院金属研究所 | A kind of gradient Al coating and its preparation process that Pt and Y is modified |
| EP2551381B1 (en) * | 2010-03-25 | 2019-09-11 | IHI Corporation | Method for forming oxidation resistant coating layer |
| CN110295383A (en) * | 2019-07-19 | 2019-10-01 | 中国科学院金属研究所 | A kind of Cr modified aluminide coating and preparation method thereof |
| CN111575645A (en) * | 2020-06-30 | 2020-08-25 | 中国航发动力股份有限公司 | Oxidation-resistant coating containing aluminum storage layer and preparation method thereof |
| CN112575296A (en) * | 2020-11-12 | 2021-03-30 | 中国航发沈阳黎明航空发动机有限责任公司 | Turbine blade high-temperature protective coating and preparation method thereof |
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Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4933239A (en) * | 1989-03-06 | 1990-06-12 | United Technologies Corporation | Aluminide coating for superalloys |
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2007
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| CN102774089A (en) * | 2012-08-10 | 2012-11-14 | 昆山乔锐金属制品有限公司 | Novel gradient thermal barrier coating |
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| CN105349936A (en) * | 2015-11-11 | 2016-02-24 | 厦门理工学院 | Metal tungsten surface WAl4-AlN-Al2O3 high-temperature insulation coating and preparation method thereof |
| CN108130515A (en) * | 2017-12-08 | 2018-06-08 | 中国航发动力股份有限公司 | A kind of preparation method of long-life thermal barrier coating |
| CN108048805A (en) * | 2017-12-08 | 2018-05-18 | 中国航发动力股份有限公司 | A kind of turbo blade composite coating and preparation method thereof |
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