WO2013052992A1 - Procédé de traitement - Google Patents

Procédé de traitement Download PDF

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Publication number
WO2013052992A1
WO2013052992A1 PCT/AU2012/001209 AU2012001209W WO2013052992A1 WO 2013052992 A1 WO2013052992 A1 WO 2013052992A1 AU 2012001209 W AU2012001209 W AU 2012001209W WO 2013052992 A1 WO2013052992 A1 WO 2013052992A1
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WO
WIPO (PCT)
Prior art keywords
substrate
titanium
coating
aluminium
composition
Prior art date
Application number
PCT/AU2012/001209
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English (en)
Inventor
Mingxing Zhang
Shoumou MIAO
Original Assignee
The University Of Queensland
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from AU2011904192A external-priority patent/AU2011904192A0/en
Application filed by The University Of Queensland filed Critical The University Of Queensland
Publication of WO2013052992A1 publication Critical patent/WO2013052992A1/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • 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
    • C23C10/52—Embedding in a powder mixture, i.e. pack cementation more than one element being diffused in one step

Definitions

  • the present invention relates to the treatment of titanium and titanium alloys to provide increased high temperature oxidation resistance and wear resistance.
  • Titanium and titanium-based alloys are used in a variety of applications that take advantage of their lightness, high strength and excellent corrosion resistance.
  • the aerospace industry in particular may be mentioned here.
  • the present invention seeks to provide an alternative methodology for treating a titanium or titanium alloy substrate in order to achieve enhanced high temperature oxidation resistance and wear resistance.
  • the present invention provides a method of treating a titanium or titanium alloy substrate to provide increased high temperature oxidation resistance and wear resistance, which method comprises: providing on the substrate a composition comprising aluminium powder, another metal powder selected from nickel, copper and zinc powder and an activator; and heating to an elevated temperature until an intermetallic coating forms on the substrate.
  • the present invention provides a method of treating a titanium or titanium alloy substrate to provide increased high temperature oxidation resistance and wear resistance, which method comprises: providing on the substrate a composition comprising aluminium powder, another metal powder selected from nickel, copper and zinc powder and a halide activator; and heating to an elevated temperature until an intermetallic coating forms on the substrate.
  • the present invention also provides a titanium or titanium alloy substrate that has been treated in accordance with the present invention to provide increased high temperature oxidation resistance and wear resistance to a surface of the substrate.
  • Figure 1 is a schematic illustrating implementation of the method of the present invention
  • Figure 2 illustrates certain physical properties of a coating formed in accordance with the present invention
  • Figure 3 is a schematic illustrating an apparatus for implementing the method of the present invention together with a photograph of the same;
  • Figure 4 shows photographs of specimens for use in a bonding force test and a lug shear tester;
  • Figure 5 is a plot of wear resistance of coating produced using the invention compared to plain Ti and Ti6A14V;
  • Figure 6 is a plot of weight gain of coated and uncoated titanium compared to Superni 75 superalloy at 900°C;
  • Figure 7 shows photographs of samples including Ti, Ti6A14V, Al-Ni coating on Ti and Ti6A14V after oxidation at 900°C and 800°C for 24h;
  • Figure 8 includes optical micrographs on the cross-sections of coatings produced using the present invention on pure Ti substrate treated at 650°C for different times: (a) 3 h, (b) 6 h, (c) 9 h, (d) 12 h, (e) 15 hours;
  • Figure 9 is a plot showing the variation of the thickness of coatings produced using the present invention on pure Ti and Ti6A14Vsubstrates with treatment time at 650°C;
  • Figure 10 shows optical micrographs on the cross-sections of coatings produced using the present invention on pure Ti6A14V substrate treated at 650°C for different time: (a) 3 h, (b) 6 h, (c) 9 h, (d) 12 h, (e) 15h
  • Figure 1 1 includes SEM back scattered electron micrographs of the coatings produced on (a) Ti-10Cr-2Fe-3Al and (b) Ti-6554 substrates;
  • Figure 12 includes SEM back-scattered electron micrographs of coatings produced using the present invention on pure Ti substrate produced at 650°C for 15 hours;
  • Figure 13 includes X-ray diffraction patterns on the topmost surface and on the layer that is close the interface of coatings produced using the present invention on pure Ti substrate at 650°C for 15 hours;
  • Figure 14 shows the cyclic oxidation behaviors of the coatings produced using the present invention on pure Ti and Ti6A14Vsubstrate compared with those of pure Ti, Ti6A14V and Superni 75 alloys (oxidation was undertaken at 800°C and 900°C for 24 hours);
  • Figure 15 shows cyclic oxidation behaviors of the coatings produced using the present invention on pure Ti and Ti6A14V substrate compared with those of pure Ti and Ti6Al4V alloys (oxidation was undertaken at 1000°C for 24 hours);
  • Figure 16 shows the coefficient of friction (COF) of a coating produced using the present invention on Ti6A14V substrate measured at different loads for 30 minutes and compared to the Ti6A14V alloy;
  • Figure 17 shows the wear resistance, indicated by the wear volume, of a coating produced using the present invention on Ti6A14V substrate measured at different loads for 30 minutes and compared to the Ti6A14V alloy;
  • Figure 18 includes SEM micrographs showing the morphology on worn surfaces after wear testing at a load of 5 ON: (a) Ti6A14V,(b) coating produced using the invention at 650°C.
  • the present invention relies on forming a coating on a titanium or titanium alloy substrate by heating the substrate in contact with a mixture of aluminium powder, Ni or Zn or Cu powder, and activator/catalyst.
  • the coating comprises intermetallic species and is believed to be formed by a diffusion-based mechanism. Specifically, it is believed that during heating titanium atoms diffuse from the substrate to the powder mixture surrounding the substrate and react with the aluminium in the mixture to form Al-Ti intermetallics. When nickel is present in the powder mixture the aluminium may also react with it to form Al-Ni intermetallics. When copper and zinc are present in the powder mixture, these species are not believed to react with the aluminium (or titanium).
  • Aluminium atoms in the powder mixture are also believed to diffuse from the powder mixture into the substrate, thereby forming Al-Ti intermetallics within surface regions of the substrate. This is believed to lead to the formation of sub-micrometre or even nanometre-scaled structures within the substrate close to the original surface of the substrate.
  • This diffusion-based mechanism leads to the formation of a coating that has very good adhesion to the underlying substrate. As the coating is formed by diffusion there is no hard boundary as such between it and the substrate, and this means that the thermal expansion coefficient varies gradually rather than abruptly. Provision of a coating in accordance with the present invention can provide increased surface hardness (and thus increased wear resistance) and a surprisingly high increase in oxidation resistance at elevated temperature.
  • the present invention may be possible to produce coated titanium and titanium alloys substrates that exhibit high temperature oxidation resistance that is at least comparable to some nickeUbased superalloys.
  • the present invention may therefore increase the range of applications in which titanium and titanium alloys may be used.
  • a composition comprising a mixture of aluminium powder, one of nickel powder, copper powder and zinc powder, and an activator is provided on (the parts of) the substrate to be coated.
  • the present invention must use aluminium powder since formation of Al-Ti intermetallics is important to formation of a coating having desirable properties.
  • the other metal used nickel, copper or zinc is believed to play some beneficial role in allowing/facilitating diffusion of aluminium and titanium atoms as necessary, although the precise details of this are not clearly understood.
  • the composition includes particles aluminium and copper powders or aluminium and zinc powders.
  • the present invention is described with reference to using aluminium in combination with another metal, namely nickel, copper or zinc. It may be possible to employ aluminium in combination with other metals but in this case such (other) metal must not impede or interfere with diffusion of aluminium and titanium atoms and reactions to form Al-Ti intermetallics.
  • the composition should be in intimate contact with the substrate surface and the composition may be consolidated/pressed onto and around the substrate to facilitate this. It is preferred that there minimal no voids and air gaps at the interface between the substrate surface to ensure good contact between the substrate and the composition.
  • the composition should be in dry form.
  • the composition should be provided as a relatively thick layer enough to cover the surface of the substrate, for example at least about 5mm thick.
  • the composition is packed around the substrate in a suitable container. This embodiment may be regarded as a packed powder diffusion coating technique.
  • the packing process includes burying the substrate in the composition in a container, shaking to ensure intimate contact between the substrate and composition and compaction of the composition around the substrate. Then, a layer of a mixture of sand and coke may be provided on top_of the coating composition to prevent ingress of air and to provide a reducing environment
  • the relevant surface(s) of the substrate may be cleaned (e.g. de-greased). It may also be desirable to prepare the surface(s) by machining or grinding as this may enhance coating formation.
  • the present invention has been found to give advantageous results in terms of high temperature oxidation resistance and wear resistance by using a mixture of aluminium powder in combination with nickel powder, copper powder or zinc powder in the composition.
  • the efficacy of combining in the composition aluminium and one or more of these other metals may be assessed by experiment.
  • the average particle size of the aluminium powder used is from 10 to 50 ⁇ .
  • the nickel, copper and zinc are used at an average particle size of from 5 to 15 ⁇ .
  • Useful metal particles are commercially available.
  • the composition contains up to 80% by weight of aluminium particles based on the total weight of the composition.
  • the other metals may each be used in an amount up to 40% by weight based on the total weight of the composition.
  • the activator (catalyst) used is one that promotes formation of the Al-Ti intermetallic coating layer by diffusion of metallic species, and possibly formation of the Al-Ni intermetallics when nickel is used in combination with aluminium.
  • the activator may be a halide activator such as ammonium chloride, aluminum chloride or zinc chloride. Aluminium chloride has been found to work well but can be unstable. The use of ammonium chloride is therefore preferred.
  • the activator (catalyst) is used in an amount of up to 5% by weight based on the total weight of the composition.
  • the composition may also include a small amount of a refractory material, such as alumina (particles), that is inert at the temperature at which heating takes place. It has been found that this kind of material allows the coated substrate to be more readily released from the coating composition after heating has taken place and the coating has been formed as required.
  • a refractory material such as alumina (particles)
  • the refractory material has an average particle size of 10 to 50 ⁇ and is present in an amount of up to 30% by weight based on the total weight of the composition.
  • the composition is formed by intimate blending of the individual components to form a uniform mixture. This is desirable in terms of ensuring formation of a uniform and homogeneous coating on the substrate. Once provided the composition has been provided in intimate contact with the substrate heating is undertaken.
  • the temperature should be sufficiently high to allow the coating to form by diffusion of active metal species. Generally, the temperature will be from 500 to 900°C. Heating is generally carried out for a number of hours, for example up to 15 hours. It has been found that the coating generally develops more rapidly at higher temperatures than at lower temperatures. It may be beneficial to carry out heating in an inert atmosphere.
  • the coating developed in accordance with the present invention should have a thickness of at least 100 ⁇ , for example from 100 to 2000 ⁇ . The thickness depends upon the coating parameters used, primarily on the temperature and time of heating, and these may be manipulated and optimized as necessary. The optimum coating thickness for a given application may also be determined.
  • Coated substrates may be assessed for coating quality and analysed using a variety of techniques, such as optical microscopy, electron microscopy and X-ray diffraction.
  • the present invention may be used to treat a titanium or titanium alloy substrate.
  • Various grades of pure titanium may be used, such as Grade 2.
  • Examples of titanium alloys that may be treated include Ti6A14V, Til 0V2Fe3Al, Ti6Cr5Mo5V4Al, Ti l 100 and IM1834. This list is not exhaustive however and the usefulness of the present invention in relation to other grades of titanium and other titanium alloys may be assessed by experiment.
  • the present invention may be used to coat the entire exterior surface of a substrate or only a part of the exterior surface. Surfaces not to be coated may be masked or otherwise prevented from being in contact with the composition that is used in the method. It is believed that the present invention will enable titanium and titanium alloys to be more widely used in applications where their high temperature oxidation resistance and/or wear resistance might previously have been an impediment to use.
  • Total world titanium mill product shipments in 2006 were over 75,000 tons. Approximately 40% of that titanium demand comes from the aerospace industry. Modem aircraft include many tons of titanium per unit and it is commonly used for structural components as well as in engine components at temperatures less than 550°C. It is also used extensively in military aircraft with titanium contributing a significant percentage of the structural weight per unit.
  • the invention may also be applied to provide wear resistant coatings on titanium machine components such as on drill bits and cutting tools.
  • surface hardening of such components is undertaken by using gas nitriding, chemical/physical vapour deposition, thermal spraying or laser gas alloying in cases where components are subject to sliding forces or friction.
  • the present invention may also find use in providing wear resistant coatings on medical implants.
  • Apure titanium piece was placed in a stainless steel container, and buried in a packed powder mixture.
  • the container was placed in a tube furnace with argon protection and heated to temperatures of between 600 and 900 °C for around 12 hours.
  • the argon pressure was kept at 0.04-0.06 MPa with a gas flow rate of 0.1-0.3 ml/min during the whole process.
  • the arrangement is shown schematically in Figure 1.
  • the figure shows a substrate block (Ti) with dimension of 15 x 15 x 15mm embedded and completely surrounded in a composition comprising aluminium (average size -45 ⁇ , 63.2 wt.%) and nickel ( 1 -5 ⁇ , 15.8 wt.%) powders as metals, ammonium chloride ( 1 wt.%) as catalyst to activate the metallic particles, and alumina (average size -45 ⁇ , 20 wt.%) particles as inert filler to avoid sintering.
  • This powder mixture is thoroughly mixed for 60 minutes in a mechanical powder-mixer before use.
  • a layer of sand and coke is provided over the upper surface of the composition to prevent oxidation of metallic powders and titanium substrate by atmospheric oxygen. Heating was undertaken at a rate of 5°C/min to the desired temperature.
  • a modified arrangement was employed to produce coatings on titanium alloys without argon protection. This arrangement is shown in Figure 3.
  • a small amount of pure alumina (average particle size: -45 ⁇ ) was pre-filled, in order to facilitate easy removal of the samples after heating.
  • the container was then filled with a powder mixture to completely cover the specimen substrate.
  • the remaining part of the container was topped up with pure alumina powder to evacuate air in order to reduce oxidation of the packed powder.
  • the container was sealed by a combination of compact mechanical contact and high temperature aluminide-base cement to achieve a strong sealing effect. Heating was carried out in a box furnace (exposure to air directly).
  • Bonding force test Coatings up to 1000 ⁇ thick have been found to have a bonding force stronger than sprayed coatings.
  • the bond strength of the coating can be determined under shear conditions using a lug shear tester (see Figure 4).
  • a coating strip of 10x 10mm 2 with a thickness of 1 mm was produced on a 40 10 10 mm substrate lug, which covers the middle of the substrate as shown in Figure 4.
  • the lug with a coated strip was forced through a steel die with a 10 10 mm square opening and with sharp edges, and the coatings were sheared off.
  • the nominal shear strength was calculated as the peak load divided by the area of the coating/substrate interface.
  • this testing method overcomes the problem associated with the adhesive failing before the coating. Three tests were performed for the coating, and the average bond strength was found to be 50 MPa. This is believed to be higher than the bond strength that can be achieved by spray coating methodologies, such as cold spray.
  • Figure 5 shows a comparison of volume loss for a Al-Ni coated material produced in accordance with the invention compared to plain Ti and Ti6A14V.
  • Two-body abrasive wear tests were conducted on the pin-on-disc TABER® Rotary platform abrasion tester (Model 5135), where the coatings and the comparison titanium alloys slides over SiC abrasive paper (#600) adhered on a rotating disc.
  • the wear testing parameters are: specimen size 10x 10x 10 mm, axial load 5-30 N, and disc rotation speed 60cycles/min. During the tests the surface of SiC paper was cleaned by vacuum.
  • the volume loss of the specimen was utilized to evaluate the wear resistance of materials under two-body abrasive conditions.
  • the coating produced in accordance with the present invention prevented high temperature oxidation of the underlying titanium substrates up to 1000°C. Oxidation is major barrier that prevents the use of titanium in high temperature environments as titanium oxide is brittle. What is also surprising is that at these elevated temperatures the aluminium in the coating should melt. However, the material structure of the coating prevents this from happening.
  • the high temperature resistance of the new, coated material is similar to a superalloy.
  • the coated material can be created at a much lower cost due to the significantly lower nickel content.
  • Figure 6 shows weight gain (a measure of the amount of oxidation) versus time at 900 °C.
  • the uncoated materials show significant oxidation, while the coated Ti6A14V and Ti show comparable performance to the Superni-75 superalloy.
  • the photographs of the corresponding samples after oxidation are given in Figure 7.
  • Example 2
  • Ti alloys plates and rods including pure Ti (Grade 2), Ti-6A1-4V, Ti-l0V-2Fe-3Al and Ti-6Cr-5Mo-5V-4Al, were cut into 10x 10x 10 mm blocks. All faces of the blocks were ground on silicon carbide (SiC) paper up to grade 600, followed by ultrasonic cleaning and drying.
  • SiC silicon carbide
  • the packed powder mixture used was the same as that in Example 1 (Al: -45 ⁇ , 63.2 wt.%; Ni: 1-5 ⁇ , 15.8 wt.%; NH C1: 1 wt.%; A1 2 0 3 : -45 ⁇ , 20 wt.%).
  • An optimized treatment temperature of 650°C was chosen to produce coatings with different thickness on Ti alloys for various heating times of 3-15 hours, followed by air cooling down to room temperature.
  • the thickness of coatings produced on was measured on optical micrographs.
  • the microstructure and chemical compositions of the coatings was also examined using scanning electron microscopy (SEM) together with energy-dispersive spectroscopy (EDS) on JEOL 6460LA.
  • SEM scanning electron microscopy
  • EDS energy-dispersive spectroscopy
  • X-ray diffraction of Cu Ka radiation was used to characterize the phase structures of coatings.
  • thermal cyclic oxidation tests were conducted in static air at temperature ranging from 800 to 1000°C for 24 cycles. Each cycle consisted of one hour immersion in static air in the box furnace, followed by a 30 minutes air cooling down to room temperature.
  • the coated samples were subjected to oxidation together with pure Ti and a commercial Ti-6A1-4V alloy for comparison. These specimens were placed in a quartz tube with both ends closed through a 20 mm hole on the cylinder wall. An electronic balance was used to measure weight change. The sample weights were measured to 0.000 lg.
  • the oxidation kinetics were monitored by measuring the weight gain as a function of oxidation time and also by measuring the total scale thickness after oxidation. Friction and wear tests
  • Dry sliding wear tests on the coatings were performed on an Optimol SRVIII oscillating friction and wear tester at room temperature (25°C) in air with a relative humidity of 40- 50%.
  • the machine was equipped with a ball-on-disc contact configuration, which uses WC-Co balls with a hardness of HV- 1750 as the counter friction pair. Prior to testing, all specimens were cut into 3mm thick plates and mechanically polished through a level of #1200 grit paper, followed by ultrasonic cleaning and drying.
  • Ti6A14V alloy which is a typical Ti alloy.
  • the cross-sectional optical micrographs of PPDC coatings on Ti6A14V substrates produced at 650°C for 3-15 hours are shown in Figure 10. Similar to pure Ti, all coatings exhibit a high level of bonding with the substrates without cracks, pore and gaps. However, dense coatings are obtained when the heat treatment is over 6 hours. Variation of the coating thickness with treatment time is also shown in Figure 10. Compared to the coatings on pure Ti, the coatings produced on Ti6A14V substrates are slightly thinner. It is believed that the existence of aluminium in Ti6A14V may suppress aluminium atom diffusion from the source powder into the substrate.
  • coatings were produced on Ti-10Cr-2Fe-3Al and Ti-6Cr-5Mo-5V-4Al alloy substrates. As shown in Figure 1 1, thick and dense coatings were also successfully produced on both Ti alloys. Therefore, it is reasonable to conclude that the newly developed technique can be used on various Ti alloys and the thickness of the coating can be varied from 100 ⁇ to 2000 ⁇ depending on the treatment temperature and time.
  • FIG. 12 shows a typical example of such micrographs, taken from the coating on pure Ti produced at 650°C for 15hours. It can be seen that the coating consists of two different phases, i.e. it is a composite coating. The "white” phase uniformly distributes in the "dark" matrix phase. Subsequent EDS analysis revealed that the "white” phase is an Al-Ni intermetallic compound and the "dark” phase is an Al-T intermetallic compounds. To further identify the phases in the coating, X-ray diffraction analysis was performed on both the topmost surface and on the coating layer close to the interface between the coating and substrate. The latter was explored through mechanical removal of material outer layers from the substrate. The X-ray diffraction spectra are shown in Figure 13. Indexing the spectra indicates that the coating contains AI3N1 and AI3T1 intermetallic compounds and Al solid solution.
  • this composite coating could provide much more volume tolerance avoiding the formation of cracks during heating or cooling.
  • Figure 14 shows the kinetic curves of cyclic oxidation of coatings, pure Ti and Ti6A14V in static air at 800 and 900°C for 24 cycles, respectively. It can be seen that the weight gains of coated samples are much lower than that of pure Ti and Ti6A14V at both temperatures. Compared to a Ni-based superalloy (Superni 75), the coatings show comparable, or even better, oxidation resistance than the Ni-based superalloy. This implies that some Ni-based superalloys could possibly be replaced with coated Ti alloys in industrial applications, significantly reducing the cost.
  • Figure 16 shows the average friction coefficients of the coatings measured at different loads. At each load, the coatings show lower friction coefficient than Ti6A14V substrates. In addition, the coatings also exhibit higher wear resistance under dry sliding conditions, as shown in Figure 17. This is attributed to the hardening effect of AI3T1 in the coating. After the dry sliding tests on both coating and Ti6A14V substrate, examination of the wom surface shows the same abrasive wear, and shallower grooves can be observed on the worn surface of the coating than that on surface of worn T16A14V substrate, as shown in Figure 18.
  • the process uses a powder mixture of commercial Al powder with average particles size ranged from 10 ⁇ to 40 ⁇ , 10 to 40 wt% Ni powder with particle size ranged from 5 ⁇ to 15 ⁇ , and 10 to 30% A1 2 0 3 , together with 0.5 to 4 % NH4CI as catalyst.
  • heat treatment is carried out at temperature between 550°C to 800°C for various times depending on the thickness of the coating required.
  • the optimised parameters of treatment to achieve thick coatings are a coating composition of approx. 60wt%Al, approx. 20wt%Ni, approx. 20wt%Al 2 Oj and approx. 1 wt%NH 4 Cl, treated at 650°C for 1 to 12 hours.
  • the thickness of the coating produced varies from 100 ⁇ to 2000 ⁇ depending on the treatment parameters. Electron microscopy and X-ray diffraction analysis indicates that the coating consists of Al, TiAl 3 and N1AI3 phases forming a composite coating. The hardness of the coating has been found to be 2 to 3 times higher than the substrate with significantly increased wear resistance. More importantly, the oxidation resistance provided by the coating has been found to be comparable to Ni-based superalloys at temperature as high as 1000°C. Raw materials and equipment:
  • Substrate pure Ti, Ti alloys and Ti-based composites. Surface finish as machined or ground.
  • Powders Commercial pure Al powder with average particle size between 10 and 40 ⁇ . Commercial pure Ni powder with average particle size between 1 and 20 ⁇ . Commercial NH4CI as catalyst. (
  • Furnace Any open air heat treatment furnaces.
  • Container stainless steel or ceramic container. Dimension of the container depends on the size of Ti components.
  • Cooling In furnace or in air

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  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Engineering & Computer Science (AREA)
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  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)

Abstract

L'invention porte sur un procédé de traitement d'un substrat en titane ou en alliage de titane pour lui conférer une résistance à l'oxydation à haute température et une résistance à l'usure accrues, lequel procédé comprend : l'apport sur le substrat d'une composition comprenant des particules d'aluminium, une autre poudre métallique choisie parmi des poudres de nickel, de cuivre et de zinc et un activateur ; et le chauffage à une température élevée jusqu'à ce qu'un revêtement intermétallique se forme sur le substrat.
PCT/AU2012/001209 2011-10-14 2012-10-05 Procédé de traitement WO2013052992A1 (fr)

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Cited By (2)

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Publication number Priority date Publication date Assignee Title
CN109136828A (zh) * 2018-09-27 2019-01-04 中国人民解放军陆军装甲兵学院 一种Zn-Al-Ni防腐功能渗层制备方法
CN113046683A (zh) * 2021-03-19 2021-06-29 昆明理工大学 一种基于TiB晶须的钛或钛合金的梯度渗层及其制备方法

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WO2010135144A1 (fr) * 2009-05-18 2010-11-25 Sifco Industries, Inc. Formation de revêtements en aluminure modifié par élément réactif ayant une faible teneur en élément réactif et utilisant des techniques de diffusion en phase vapeur
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CN109136828A (zh) * 2018-09-27 2019-01-04 中国人民解放军陆军装甲兵学院 一种Zn-Al-Ni防腐功能渗层制备方法
CN113046683A (zh) * 2021-03-19 2021-06-29 昆明理工大学 一种基于TiB晶须的钛或钛合金的梯度渗层及其制备方法
CN113046683B (zh) * 2021-03-19 2022-03-01 昆明理工大学 一种基于TiB晶须的钛或钛合金的梯度渗层及其制备方法

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