EP2547805A1 - Revêtement à base de nial2o4 en structure spinelle - Google Patents

Revêtement à base de nial2o4 en structure spinelle

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Publication number
EP2547805A1
EP2547805A1 EP11711494A EP11711494A EP2547805A1 EP 2547805 A1 EP2547805 A1 EP 2547805A1 EP 11711494 A EP11711494 A EP 11711494A EP 11711494 A EP11711494 A EP 11711494A EP 2547805 A1 EP2547805 A1 EP 2547805A1
Authority
EP
European Patent Office
Prior art keywords
layer
coating
layers
coating according
target
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP11711494A
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German (de)
English (en)
Inventor
Juergen Ramm
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Oerlikon Surface Solutions AG Pfaeffikon
Original Assignee
Oerlikon Trading AG Truebbach
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Oerlikon Trading AG Truebbach filed Critical Oerlikon Trading AG Truebbach
Priority to EP11711494A priority Critical patent/EP2547805A1/fr
Publication of EP2547805A1 publication Critical patent/EP2547805A1/fr
Withdrawn legal-status Critical Current

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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
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
    • C23C14/24—Vacuum evaporation
    • C23C14/32—Vacuum evaporation by explosion; by evaporation and subsequent ionisation of the vapours, e.g. ion-plating
    • C23C14/325—Electric arc evaporation
    • 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
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • C23C14/08—Oxides
    • C23C14/081—Oxides of aluminium, magnesium or beryllium
    • 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
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • C23C14/08—Oxides
    • C23C14/085—Oxides of iron group metals
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
    • H01J37/00—Discharge tubes with provision for introducing objects or material to be exposed to the discharge, e.g. for the purpose of examination or processing thereof
    • H01J37/32—Gas-filled discharge tubes
    • H01J37/34—Gas-filled discharge tubes operating with cathodic sputtering

Definitions

  • the invention relates to a coating according to the preamble of claim 1.
  • the oxide layer consists mainly of aluminum oxide before ⁇ in the corundum (alpha alumina or CX-Al 2 O 3), which is deposited at temperatures around 1000 ° C on the tools.
  • Cuts are the tensile stresses in the layer passing through the high deposition temperature and the temperature-based Fehlanpas ⁇ solution between layer materials and substrate occur disadvantageous. It comes to cracking in the layer system, sometimes even before the use of the tool.
  • a further disadvantage is that material abrasion may occur at the cutting edge of the tool which promotes uncontrolled edge wear.
  • These deposits are believed to be related to the reactivity of the Ti in the layer. It has been observed that Ti-Al-N layers decompose at temperatures between 800 ° C and 900 ° C at the surface and it comes to a porous surface layer of low mechanical strength. The chemical or oxidative layer resistance of this material system is therefore no longer guaranteed at these temperatures. Experience has shown that such deposits can be drastically reduced if an oxidic layer closes the nitridic layer towards the surface of the layer. This with a CVD
  • the CVD layers are usually composed of TiCN and - ⁇ 2 ⁇ 3 and both materials are inferior in hardness and toughness of a good Al-Ti-N layer. That would presumably result in worse service lives with comparable layer thickness.
  • the CVD layer system is under tensile stress, resulting in early layer failure, at least in interrupted cut applications.
  • a disadvantage of the present state of the art is therefore low productivity in machining of hard machineable material, which is due to the low Zerspanungs ⁇ speed.
  • PVD - coating An interesting way of PVD - coating is the Zerstäu ⁇ ben targets (sputtering). In doing so, ions are accelerated to the target surface and knock small conglomerates out of the target. This possibility is described, for example, in WO 2008/148673. Here is a sputtering process
  • HIPIMS Presented (HIPIMS) g iststarget in which one or more AlMe Le ⁇ atomized (sputtered) is where in accordance with one embodiment, the deposited layer two oxide phases or a mixed oxide of the type (Ali_ x Me x) 2 0 3 or spinel (Me) x Al 2 0 3+ x
  • the object of the invention is to provide a layer which essentially combines the high hardness and toughness of the Ti-Al-N (or Al-Ti-N) with greater thermal stability to chemical reactions or oxidation.
  • a layer material is to be created, which hasradara ⁇ ing mechanical properties, even at elevated temperatures.
  • the coating, layer or layer system according to the invention is deposited on cutting tools in order to reduce the abrasive, chemical and oxidative wear of these cutting tools during the cutting process.
  • This oxide-containing layer is preferably or Schichtsys ⁇ system for tools used, which called for the cutting of so- ⁇ be used "difficult zerpanbaren materials," such as, for example, titanium alloys, high-nickel-containing steel alloys, and some types of stainless steels with special alloys that increase the hardness and chemical wear of the materials.
  • the layer or the layer system can also be used for catalytic purposes.
  • the solid materials constituting the layer have a similar oxide as well as nitride. Liehe crystal structure and crystallize preferably in cubic structure, the oxide preferably at least partially in cubic structure of the spinel.
  • An object of this invention is that the layer is so bronzest ⁇ taltet that in addition to the oxides with spinel structure also shares of other oxides can be introduced, which can be formed from the Feststoffanfeilen of the radioactive target used.
  • These oxides should preferably have a finely crystalline or amorphous structure and thus serve to improve the mechanical layer properties, especially at elevated temperatures. For example, to be achieved, that they increase the breaking strength of the layer and reduce mechanical clamping ⁇ voltages that can entste ⁇ hen through the different expansion coefficients between the functional oxide layer and the support and adhesive layers and the substrate (tool).
  • multilayer layers can be produced which are synthesized substantially in a crystal structure.
  • the layer or the layer system according to the invention in addition to the tools made of high-temperature resistant materials such as cemented carbides, composites (cermets), diamond, ceramics of SiC (silicon carbide), SiN (silicon nitride), c-BN (eubie boron nitride) Even less temperature-resistant materials made of HSS (high speed steel) or other steel alloys and aluminum components can be coated with advantage.
  • high-temperature resistant materials such as cemented carbides, composites (cermets), diamond, ceramics of SiC (silicon carbide), SiN (silicon nitride), c-BN (eubie boron nitride)
  • HSS high speed steel
  • HSS high speed steel
  • the object is achieved by layers which comprise at least one iAl 2 0 4 layer in spinel structure.
  • Ge ⁇ Telss a preferred embodiment includes a inventions dung contemporary layer N1AI 2 O 4 in spinel structure as well as aluminum oxide ⁇ in at least one of the phases from the group of X-ray amorphous, corundum, gamma phase, kappa phase or theta phase.
  • the layer according to the invention contains N1Al 2 O 4 in spinel structure and a NiO constituent, which is preferably present in X-ray amorphous phase.
  • a multilayer system is present, containing layers with N1AI 2 O 4 in spinel structure and in addition, metallic oxides and / or nitrides, being different in adjacent layers, the metallic components in percentage. Due to the multi-layer design, the toughness is increased. Thus, there is in Wesentli ⁇ chen no thickness limitation. In addition, the the the
  • the N1AI 2 O 4 alternately contain multi-layer system containing in Spi ⁇ nell founded also one or more additional crystalline and amorphous Oxidpha ⁇ sen, preferably high-temperature phases.
  • gradient layers are realized which include N1AI 2 O 4 in Spi ⁇ nell founded constant lattice constant and varies the proportion of a present amorphous phase within the layer gradually and / or continuously.
  • the layers according to the invention can be produced in an economical manner by means of spark evaporation.
  • spark evaporation so-called droplets are formed.
  • the conglomerates are not oxidized fully or not fully Maschinenwireit ⁇ tured metallic constituents or intermetallic compounds, resulting from the target.
  • the production of layers according to the invention is particularly economical if the filtering of such droplets can be dispensed with.
  • the N1Al 2 O 4 spinel-structured layers include the droplets typical of spark evaporation.
  • layers produced by means of spark evaporation can be produced which comprise N1Al 2 O 4 in spinel structure or cubic structure, the droplets of which have a majority, preferably essentially all, a metal content of less than 50% by% nickel.
  • Fig. 1 a comparison of the XRD spectra of Probenl215 and
  • FIG. 2 shows an SEM cross-section of sample 1216 showing the N1Al 2 O 4 layer with the approximately 150 nm thick chromium adhesion layer;
  • sample 1217 shows a comparison of the XRD spectra of sample 1217 (Ni-Al 2 O 4 ) with the synthesized Ni-Al-N layer (sample 1231, which again shows the agreement of the oxide and nitride peaks in a better resolved 2 ⁇ scale;
  • FIG. 12 shows an enlargement of a region of FIG. 11 between the layers
  • Fig. 13 Reference data for NiAl 2 O 4 (Reference 01-077-1877); Fig. 14: Reference data for Cr (reference 01-089-4055); Fig. 15: Material characteristics sample 1214; Fig. 16: Material characteristics sample 1215; Fig. 17: Material characteristics sample 1216; Fig. 18: Material characteristics sample 1217;
  • Fig. 19 Examples of synthesized layer systems, the NiAl 2 0 4
  • Contain material as the adhesive layer comes ⁇ example, also Cr, CrN, AlCrNN, Ni-Al-N, Ni-CrN, TiN, ZrN or VN in question when backing comes ⁇ example, also TiCN in question.
  • the invention is based on experiments that were made in a spark evaporation plant of the type Innova the company OC Oerlikon Balzers AG.
  • As substrates for the coating indexable inserts made of hard metal (WC based) and composite ⁇ materials (cermets) were used.
  • the spark sources were equipped with Ni-Al targets. In the case described pulverme targets ⁇ tallurgisch prepared were used.
  • targets made in a different manner, containing the combination of Ni and Al in the target can also be used for this process, for example melt metallurgically produced or plasma sprayed targets.
  • a plasma is usually generated in a vacuum chamber in the form of a high-current low-voltage arc discharge on a material source, referred to below as the target.
  • the material to be evaporated is placed in this process as a cathode to the negative pole of a voltage source.
  • the arc melts the cathode at one or more cathode spots where the current transition is concentrated. Essentially, electrons are pulled out of the cathode. In order to maintain the arc, it is therefore necessary to constantly provide for electron supply to the corresponding cathode surface.
  • the arc, or meaning also called Are moves on the cathode surface. It comes to a extremely fast heating of small target surface areas, which locally vaporizes material.
  • Ni-Al target To prepare the oxide layer (functional layer) of the invention compound Ni-Al target were used, the nickel proportions between 10 at% and 80 at% having, preferably ⁇ between 20 at% and 60 at%.
  • reactive gas for the functional layer either pure oxygen was used during the Fun ⁇ kenverdampfung or a mixture of oxygen and nitrogen, both with and without argon admixture.
  • the selection and addition of the gases depends on which chemical to ⁇ composition of the layer to be synthesized is sought: purity nitrogen for a nitride, pure oxygen for an oxide or a mixture of both gases for an oxy nitride.
  • spark currents were varied in large areas. For voting decision of the functional layer was worked with currents of between 60 A and 350 A, with both DC pulsed as Funkenströ ⁇ me were used. The range of preferred spark currents is between 80 A and 200 A.
  • substrate bias Zvi ⁇ rule -20 and -300 V Were coated in a substrate temperature range between 200 ° C to 600 ° C substrates were applied to substrate bias Zvi ⁇ rule -20 and -300 V.
  • substrate bias Zvi ⁇ rule -20 and -300 V Preferably, bipolar pulsed substrate bias has been used, especially during coating with the oxide layers.
  • the substrates are coated with the layers which take place before the actual functional layer deposition.
  • this is a layer which serves as an intermediate or adhesive layer (interface) for the later layer or the later layer package.
  • Typical known materials for this adhesive layer are Al, Ti, Cr, Zr, Nb both in metallic form and as nitrides.
  • these layers may contain Ni and / or Co according to an embodiment of the present invention. Combinations of these materials and their nitrides also lead to improved layer adhesion in many cases.
  • Ni-Cr, Ni-Al, Al-Ni-Cr, Zr and their nitrides may be mentioned, without this enumeration should be ver ⁇ limited.
  • elemental metallic targets consist of the above-mentioned metals or composite targets, which are made of mixtures of two or more elements, for example powder metallurgy or as an alloy or as an intermetallic compound or by plasma spraying.
  • the coating of the substrate coated with adhesive layer and backing layer takes place with the actual functional layer.
  • the transition from the adhesive or support layer to the functional layer can be made fluent or abrupt. Smooth transitions, for example, achieved ⁇ to by the targets that were needed for the adhesive layer or the support layer, for a time be operated together with the targets of the functional layer both and thus will be a mixed layer in transition.
  • Another Possibility to create a mixture or a graded transition exists by ramping the gas flows.
  • a nitride layer sauce ⁇ excreted was the target of the functional layer can be operated at ⁇ fssenlich in nitrogen which then graded or abrupt is replaced, for example, by oxygen, in order of a nitride in an oxynitride and then to pass into the pure oxide.
  • a Ni-Al oxide layer is deposited.
  • Ni-Al mixed targets with a mixture of 30 at% nickel and 70 at% Al were used and the evaporation of the target material takes place in a pure oxygen atmosphere.
  • the oxygen fluxes are selected from the range given above.
  • the targets may in turn have been produced by powder metallurgy or as an alloy or as an intermetallic compound or by plasma spraying. In the present experiment we worked with powder metallurgy targets. It should be remembered here that nickel self ⁇ companies has magnetic. This can lead to unwanted guidance of the spark on the target. In practice, this has not been shown so far, because the addition of oxygen or nitrogen has a stabilizing effect on the spark discharge from ⁇ . In particularly critical cases, pulsed spark operation can further support this stabilization.
  • Figure 1 shows the XRD spectra of Ni-Al oxide films produced with different oxygen fluxes.
  • a logarithmic representation of the intensity of the scattered X-rays was chosen to better distinguish between the substrate and the coated substrates.
  • the XRD spectrum of the uncoated WC substrate (indexable insert ) can be seen as a line with pronounced noise.
  • the XRD spectra of the coated substrates are represented by circular and triangular symbols.
  • the sample points of sample 1215 were shown with open triangular symbols and the samples of sample 1217 with open circular symbols.
  • the XRD database was compared to a N1AI 2 O 4 spectrum
  • the XRD analysis shows that a crystalline layer of Ni-Al 2 O 4 can be synthesized by reactive sputtering, the cubic (Fd-3m) or spiral has nell Modell. This synthesis was carried out in the present example at 550 ° C substrate temperature. This substrate temperature is well below the formation temperature of this compound in thermal equilibrium.
  • FIG. 14 For the chromium, a reference spectrum (01-089-4055, Fig. 14) was again selected from the XRD database, which has an Im-3m (cubic body-centered) structure. As expected, this spectrum explains the additional peaks in the spectrum derived from the chromium adhesion layer.
  • the chrome peaks of the reference are shown as gray bars.
  • the (211) peak of Cr shows no overlap with substrate peaks.
  • the (110) peak can be separated well if the 29 scale is better resolved, as is done in FIG. 4.
  • the chemical composition of the layers made at 300 sccm and 800 sccm oxygen fluxes was analyzed.
  • the analysis was carried out by means of EDX and RBS measurements. Since no significant difference between the EDX and the RBS analysis could be found for the metallic compositions, only the RBS measurements are to be discussed here because they give quantitatively better information about the oxygen content and also qualitatively the depth profile of the metals in the vicinity describe the layer surface.
  • the second surprising conclusion concerns the depen ⁇ dependence of the ratio of the metallic components in the syn ⁇ thetarraen layer. While an Al / Ni ratio of 3.0 was measured for the 300 sccm oxygen flow layers (samples 1214 and 1215) (near the near surface), an Al / Ni ratio is obtained for 800 sccm oxygen flow (samples 1216 and 1217) from 2.5. This means that the oxygen flux can be used to control the concentration of the target components Ni and Al in the layer (with the same target concentrations of the metallic constituents!).
  • the oxygen is mainly consumed for the N1AI 2 O 4 spinel structure and alumina is formed from the "remainder" of the available oxygen.
  • the oxygen flow further sccm to 1200 he was ⁇ höht, it came virtually to the target entspre ⁇ accordingly stoichiometric layer formation, which was in this case IAL 2 0 4th It could not be accurately clarified why there is this influence of the ratio of Targetkompo ⁇ components on the oxygen flow with respect to the layer.
  • ge ⁇ go in the first use of the targets with or without target shutter to avoid a layer structure on the substrate, or to obtain a copy of conditioning (possible nucleation) in the layer structure.
  • the temperature stability of the oxide layer with the NiA ⁇ C ⁇ Spi ⁇ nell structure was verified by these temperature cycles were exposed up to 1100 ° C and the stability of the Rönt ⁇ genspektren was observed under these conditions. There was no significant change in the spectra, which indicated a change in the crystal structure of the spinel. At temperatures above 1000 ° C, only diffusion processes of the WC cemented carbide inserts took place; for example, the diffusion of the co-binder could be observed by RBS analysis. The quality of the coupling of the Ni-Al-oxide layer at the sub ⁇ strat or to the adhesive or backing layer is decided by the ⁇ importance for the performance of the coated tool or component.
  • the X-ray spectrum of the WC substrate is indicated again and the bars again show the iAl 2 0 4 reference spectrum.
  • No reference spectrum could be found in the database for the Ni-Al-N layer, indicating that this compound has not yet been synthesized or investigated.
  • the comparison indicates that some peaks of the oxide and the nitride are in approximately the same positions, namely the (311), (400) and (511) peaks (Oxidrefe ⁇ ence). This is shown more clearly once again in FIG. 10 with a spread 2 ⁇ axis.
  • the measurement result is indicative of similar crystal structures, and suggests that the nitrogen can be replaced gradually by the oxygen and vice ⁇ versa without causing major changes in the crystal structure, which means that Ni-Al-N is present in similar cubic structure as the NiAl 2 0 4 .
  • This measurement result and the material ⁇ similarity leave good coupling behavior between nitride and oxide expect. Accordingly, in the experiments no adhesion problems between the Ni-Al-N and the Ni-Al-0 Schicht and also the Scratch tests, which were carried out for the purpose of quantifying the adhesion, showed above-average adhesion.
  • FIG. 11 shows the SEM cross-sectional image of a layer system consisting of an Al-Ti-N
  • Support layer and a Ni-Al-0 functional layer according to the invention consists.
  • a higher magnification of the area Zvi ⁇ rule the layers demonstrates the transition between nitride and oxide, and shows that there are no abrupt changes in the morphology of the layers, indicating good adhesion.
  • FIG. 11 also shows the typical in the Fun ⁇ kenverdampfung droplets in the submicron range, which occur mainly in the use of multi-component target.
  • the germs of the droplets mainly contain the metal of the high-melting component of the multicomponent target.
  • the picture also shows larger spatters that were generated before the start of the oxide coating and that can be greatly reduced by skillful litigation.
  • the process control allows an uncomplicated and secure production of layers in multi-layer structure.
  • the first method is to operate targets of different materials alternately or spatially offset in the plant.
  • the reactive gas can still be varied, ie, at ⁇ play, the oxygen or nitrogen flow or its pressure.
  • Another interesting method of multilayer fabrication is to use targets that are made of the same me- consist of metallic components (here Ni-Al), but with respect to this different composition. Of course, these can also be operated alternately or simultaneously with different reactive gases. The result is multilayer coatings in the same material system, but with changing ratio of the target components (Ni / Al ratio) and corresponding reactive gas components in the layer. Or a multi-layer design, which in addition to the changing ratio of the target components is additionally generated and superimposed by different reactive gases.
  • targets that are made of the same me- consist of metallic components (here Ni-Al), but with respect to this different composition.
  • Ni-Al metallic components
  • these can also be operated alternately or simultaneously with different reactive gases.
  • the result is multilayer coatings in the same material system, but with changing ratio of the target components (Ni / Al ratio) and corresponding reactive gas components in the layer.
  • a multi-layer design which in addition to the changing ratio of the target components is additionally generated and superimposed by different reactive gases.
  • Novel is the production of multi-layer structures by using the same targets, which are operated only with a variation of the oxygen flow and for the production of which in principle no substrate rotation requires, although this can take place naturally.
  • the oxygen flux also changes the Ni / Al ratio, which is the cause of the multilayer structure.
  • the elastic penetration module is higher in comparison to other PVD oxide layers and is even ty- for some nitrides based on Al-Ti.
  • Adhesive layer 0.05 ym to 2 ym
  • the outer longitudinal turning tests were carried out on well mariffe ⁇ NEN inserts with smooth surfaces and was compared between uncoated, coated by default by the manufacturer (Al-Ti-N-based) and coated with the inventive film inserts.
  • Al-Ti-N-based uncoated, coated by default by the manufacturer
  • inventive film inserts As an example, here on a supporting layer of Tio. 34 Alo.66N with the N1AI 2 O 4 functional layer.
  • Coatings were prepared on 3 ym layer thickness (2 ym support layer 1 ym functional layer) compared to the free surface and the termination criterion for the life comparison of the coated inserts was chosen wear at 300 nm if it came to the failure of the tool press ⁇ ges not before.
  • the tool according to the invention with the layer facing ⁇ te about 50% greater life than the uncoated tool at 30 m / min and 20% longer life than the ⁇ be coated tool at 60 m / min. There was also at 90 m / min a significant difference in quality compared to the wear of the manufacturer coated tool, which is based on a stabilization of the cutting edge by the Close the inventive layer. In this area, the uncoated tool failed completely.
  • Ni-Al 0 ceramics for example, gel technology can be made with the sol, it is known that they have catalytic activity, eg greenhouse gas unMd ⁇ Lich. Therefore, nickel is typically embedded in an alumina ⁇ matrix by nickel is applied to aluminum and heated in air. It is therefore advantageous for a Kataly ⁇ sator, the inventive N1AI 2 O 4 layer to be used with alumina, the ratio can be adjusted. This is possible for the first time on a coating method that can produce ⁇ without high-temperature step both materials and that in one process step.
  • the invention allows the production of layers (by reactive spark evaporation), the cubic N1AI 2 O 4 in spinel structure (with submicron splashes).
  • the layer may have other proportions of aluminum oxide ⁇ , which consist of at least one of the Hochtemperaturmodi ⁇ fications of the alumina and that of alumina of the alpha, gamma, theta, kappa structure.
  • the layer can also be synthesized in such a way that, in addition to the cubic N1Al 2 O 4 in spinel layer portion, it contains proportions of ku ⁇ bischem Ni-0 in different crystallite size. Before ⁇ preferably, the layer may consist essentially only of the cubic N1AI 2 O 4 in spinel component.
  • the layer is characterized by high temperature stable egg ⁇ properties, which means that it has the typically high for the spinel curing, the loose less quickly than the size of the nitrides is the case.
  • the cubic N1Al 2 O 4 Spi ⁇ nell structure of the layer according to the invention is maintained even at temperatures above 1000 ° C.
  • the cubic N1AI 2 O 4 layer ensures especially in combination ⁇ nation cubic underlayers stable layer transitions, especially with TiN, Ti-Al-N and TiCN, ZrN, Zr-Al-N, ZrCN, which contributes to excellent adhesion.
  • Ni-Al-0 layer in addition to the Ni-Al-0 layer according to the invention, a further novel Ni-Al-N layer system was synthesized for the first time using reactive spark plating, which has a cubic structure with the spinel of very similar lattice constants according to the measured XRD spectrum.
  • This fact allows both the "material-matched” and “lattice-constant matched” bonding of the Ni-Al-N and Ni-Al-0 layers to each other.
  • the inventive layer of Ni-Al-0 has a high hardness, which is higher than Hv 2300, Hv preferably about 2500, more preferably about Hv before ⁇ 2700th
  • the mechanical strength of the Ni-Al-0 spinel layer can be further improved by the incorporation of Aluminiumoxi ⁇ the high-temperature structures or Ni-0, in particular with respect to toughness.
  • the second oxide introduced into the layer in addition to the NiAl 2 O 4 preferably has very different crystallite sizes, preferably smaller than those of the spinel and more preferably X-ray-amorphous structure.
  • the transition from nitride to oxide can be driven in the same target material.
  • the process according to the invention allows the production of a Ni-Al-containing multi-layer layer in a continuous cubic structure by varying the nitrogen-oxygen flux.
  • the inventive method allows the production of N1AI 2 O 4 layers, in particular in spinel structure, wherein the content of alumina and nickel oxide can be controlled via the oxygen flow.
  • the process according to the invention starting from a plasma-sprayed single-phase Ni-Al target, leads to a target whose surface has a plurality of intermetallic compounds or mixed crystals of the following type: Al 3 N 1 , Al 3 N 1 2 , AlNi, Al 3 N 1 5 , AlN 3 , It is important to assume the condition of the condition of the target. In particular, it is possible to condition the target behind a shutter by means of Various ⁇ ner oxygen fluxes. This, for example, to avoid Schichtinhomogenticianen.
  • wear protective coating on cutting tools insbeson ⁇ wider particularly advantageous to toilet and cermet, ceramics, Di ⁇ amant and substrates, Cr, such as HSS and also for applications in hard machinable material.
  • a cubic CrN layer can be provided as a support layer.
  • the layers according to the invention can be used in internal combustion engines and exhaust gas systems or in turbine blades.
  • the layers according to the invention are harder than corundum and at least in the multilayer version more elastic than ordinary PVD oxides, that lattice matching is possible and, for example, the embedding of a cubic N 1 Al 2 O 4 structure in high-temperature aluminum oxide structures is performed can.
  • a coating has been presented which comprises at least one compound of oxygen and / or nitrogen with at least two metallic materials, characterized in that the compound is present at least partially in spinel structure.
  • the coating may have an intrinsic compressive stress of the compound having components between 0.2 GPa and 5 GPa. In this way, the stability of the Beschich ⁇ tion is increased.
  • one of at least two metallic mate rials ⁇ nickel and / or aluminum.
  • the XRD spectrum may show the 311, 400 reflections, and preferably also the 511 reflex.
  • the compound may be N1Al 2 O 3 and other components of the coating may be in X-ray amorphous phase.
  • the X-ray amorphous phase present in other components of aluminum oxide and / or nickel oxide umfas ⁇ sen, wherein optionally the alumina preferably is in the corundum and / or gamma phase.
  • Such a coating may comprise a plurality of superposed layers and the layers may have substantially identical metallic chemical elements but with different metallic proportions. In particular, the layers may even have substantially identical chemical elements.
  • the coating may include the droplets that are typical for spark evaporation.
  • It may be a cubic support layer comprises, preferably from the group Al-Ti-N, Ti-C-N, Ti-N, Cr-N or mixtures thereof.
  • a process has been disclosed for coating substrates by means of spark evaporation, which is characterized in that the target used is an alloy target which has between 10 at.% And 80 at.%, Preferably between 20 at.% And 60 at.% Nickel and which as reactive gas Oxygen and / or nitrogen is used.
  • the alloy target may comprise aluminum.
  • the Al / Ni ratio can be varied currency ⁇ rend of the coating according to the invention.
  • coated substrates in particular tools or components, which are characterized in that the surface of the substrate on which the coating comes to rest comprises a steel, in particular Cr-containing steel, such as HSS.
  • the coated substrate may be an indexable insert.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Analytical Chemistry (AREA)
  • Physical Vapour Deposition (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)

Abstract

L'invention concerne un revêtement qui comprend au moins un composé de l'oxygène et/ou de l'azote avec au moins deux matériaux métalliques, le composé présentant au moins en partie une structure spinelle. L'invention concerne également un procédé de revêtement et un substrat pourvu dudit revêtement.
EP11711494A 2010-03-18 2011-03-18 Revêtement à base de nial2o4 en structure spinelle Withdrawn EP2547805A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP11711494A EP2547805A1 (fr) 2010-03-18 2011-03-18 Revêtement à base de nial2o4 en structure spinelle

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
US31510610P 2010-03-18 2010-03-18
EP10173410.1A EP2369031B1 (fr) 2010-03-18 2010-08-19 Revêtement à base de nial2o4 dans une structure de spinelle
PCT/EP2011/054110 WO2011113927A1 (fr) 2010-03-18 2011-03-18 Revêtement à base de nial2o4 en structure spinelle
EP11711494A EP2547805A1 (fr) 2010-03-18 2011-03-18 Revêtement à base de nial2o4 en structure spinelle

Publications (1)

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EP2547805A1 true EP2547805A1 (fr) 2013-01-23

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EP10173410.1A Active EP2369031B1 (fr) 2010-03-18 2010-08-19 Revêtement à base de nial2o4 dans une structure de spinelle
EP11711494A Withdrawn EP2547805A1 (fr) 2010-03-18 2011-03-18 Revêtement à base de nial2o4 en structure spinelle

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US (1) US9428826B2 (fr)
EP (2) EP2369031B1 (fr)
JP (1) JP5771884B2 (fr)
CN (1) CN103189541B (fr)
WO (1) WO2011113927A1 (fr)

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DE102012200378A1 (de) * 2012-01-12 2013-07-18 Federal-Mogul Burscheid Gmbh Kolbenring
MX2016005564A (es) 2013-11-03 2016-12-09 Oerlikon Surface Solutions Ag Pfäffikon Capa de carrera contra oxidacion.
EP3056587B1 (fr) * 2015-02-13 2020-11-18 Walter AG Fraise à queue VHM dotée d'un revêtement en TiAlN-ZrN
JP6533818B2 (ja) 2017-10-20 2019-06-19 株式会社リケン 摺動部材およびピストンリング
US11167375B2 (en) 2018-08-10 2021-11-09 The Research Foundation For The State University Of New York Additive manufacturing processes and additively manufactured products
CN115058697B (zh) * 2022-06-27 2023-10-13 成都工具研究所有限公司 稳态刚玉结构钛铝铬铌氧化物涂层及其制备方法

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See also references of WO2011113927A1 *

Also Published As

Publication number Publication date
CN103189541B (zh) 2015-09-23
CN103189541A (zh) 2013-07-03
EP2369031B1 (fr) 2016-05-04
US9428826B2 (en) 2016-08-30
WO2011113927A1 (fr) 2011-09-22
US20130036942A1 (en) 2013-02-14
EP2369031A9 (fr) 2012-07-18
JP5771884B2 (ja) 2015-09-02
JP2013522058A (ja) 2013-06-13
EP2369031A1 (fr) 2011-09-28

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