A method for depositing composite coatings

Abstract: A process for producing a wear resistant article (30), such as a cutting tool. Gaseous halides of two or more of aluminum, zirconium, and yttrium with other reactants are passed over a cemented carbide or hard ceramic substrate (12) at 900°-1250°C for the cemented carbide substrate or about 900°-1500°C for the hard ceramic substrate, and 1 torr to about ambient pressure to form a composite ceramic coating (32) on the substrate (12). The coating (32) is a continuous first-phase metal oxide matrix (24) having particles (34) of at least one different metal oxide dispersed therein. In a preferred process, one or more of the metal halides is pulsed into the gaseous mixture containing a different metal halide to control the deposition of the particles.

Description: This invention relates to a method for depositing a wear-resistant coating on a cemented carbide or hard ceramic substrate, and more particularly to the deposition of a two or more phase composite oxide coating on such a substrate. Furthermore this invention relates to a wear resistant article. FR-A-2 393 852, discloses a process for forming a thin wear-resistant coating consisting mainly of Al 2 O 3 wherein approximately 85% of the Al 2 O 3 is in the Kappa phase. In order to promote the formation of the Kappa phase, small amounts of titan, zirconium and/or hafnium can be added. Codeposition processes, as described in this prior art, will always result in a solid solution of two materials, for example, oxides. The prior art is silent on how discrete particles can be achieved. Furthermore, it fails to suggest the effectiveness of discrete particles in a wear-resistant coating. Furthermore the abstract of JP-A-59222570 discloses the formation of a wear-resistant coating consisting of different layers. In contrast to its abstract, JP-A-59222570 only describes the formation of a one-layer coating consisting of Al 2 O 3 , ZrO 2 and/or HfO 2 . while the coating is performed using the plasma CVD-method, the starting materials react with each other, for example, a doping of zirconium oxide or hafnium oxide will take place in the Al 2 O 3 and thereby activating the surface diffusion of Al 3+ in Al 2 O 3 . In the final product - the coating, the starting material will be maintained either in the form of a solid solution or of an appropriate mixture, wherein the different particles are not embedded discontinuously but continuously. Cemented carbide and hard ceramic materials are known and are used extensively in such applications as mining tool bits, metal cutting and boring tools, metal drawing dies, wear-resistant machine parts and the like. Hard ceramic materials, as used herein refers to such compositions as Al 2 O 3 , Si 3 N 4 , silicon aluminum oxynitride and related compounds, as hard and dense monolithic or composite materials. The composites include those containing whiskers and/or particulates of SiC, Si 3 N 4 , other ceramic materials, and metal carbides, nitrides, and carbonitrides such as TiC and TiN. It is also known that the service properties such as wear, high temperature and chemical resistance of such materials may be enhanced by the application of one or more thin coatings of, for example, metal carbides, metal nitrides, or ceramics. Great strides have been made in improved performance of these coated substrates, for example in machining applications, by refinement of the substrate compositions and by applying various combinations of superimposed layers of coating materials. However, increasingly stringent use conditions, for example use at high cutting speeds or in extremely high temperatures and/or corrosive environments, are placing increasing demands upon the performance of such materials. The object of the present application is to provide a process for depositing a wear-resistant composite coating of controlled composition and distribution on a cemented carbide or hard ceramic substrate and to provide an article consisting of this wear-resistant coating and cemented carbide or hard ceramic substrate showing improved abrasion resistance under extreme conditions of use. This object is achieved in respect to the process by the subject matter of claim 1 and in respect to the article by the subject matter of claim 22. An improved process for depositing a wear resistant ceramic coating on a cemented carbide or hard ceramic substrate according to one embodiment of the invention involves passing over the substrate a first gaseous mixture of a first halide vapor selected from the halides of aluminum, yttrium and zirconium, with other reactant gases, and optionally a carrier gas. The temperature is about 900°-1250°C for cemented carbide substrates, or about 900°-1500°C for hard ceramic substrates, and the pressure between about 1 torr and about ambient pressure. The partial pressure ratios, the flow rate, and the length of time is sufficient to deposit a continuous, fully dense, adherent, wear resistant layer of a material selected from the oxides of aluminum, zirconium, and yttrium about 0.1-20 microns thick on the substrate. At least one additional vapor selected from the halides of aluminum, zirconium, and yttrium is mixed with the first gaseous mixture. The additional metal halide vapor is different from the first halide vapor, and is mixed at a partial pressure selected to form at least one discontinuous additional phase, dispersed as discrete particles within the continuous oxide layer, of at least one material selected from the oxides of aluminum, zirconium and yttrium, to form a wear resistant composite ceramic layer on the substrate. In a preferred process according to the invention, the additional metal halide vapor is mixed with the first mixture by intermittently, during the deposition of the continuous oxide layer, pulsing the additional vapor into the first gaseous mixture to mix therewith. Most preferably, a single-phase oxide portion is deposited before the two or more phase portion and/or the process is controlled to form a stratified composite in which two or more phase portions alternate with single-phase continuous oxide portions. The process according to another preferred embodiment of the invention involves passing a halide vapor such as Cl 2 or HCl, optionally mixed with a carrier gas, over a mixture or alloy of two or more metals selected from aluminum, zirconium, yttrium, and their metal salts at about 250°-1250°C to form a first gaseous mixture comprising halides of two or more of aluminum, zirconium, and yttrium, and optionally the carrier gas. The first gaseous mixture is mixed with other reactant gases to form a second gaseous mixture. The second gaseous mixture is passed over the substrate at a temperature of about 900-1250°C for the cemented carbide substrate, or about 900°-1500°C for the hard ceramic substrate, and a pressure between about 1.33 mbar(1 torr) and about ambient pressure, to deposit a composite layer on the substrate. The other reactant gases, the flow rates of the gases, the surface areas and the ratio of the surface areas of the two or more metals, and the deposition time are selected so that the composite layer comprises an adherent layer about 0.1-20 microns thick of a continuous first phase of an oxide of one of the two or more of aluminum, zirconium, and yttrium, and one or more discontinuous additional phases, dispersed as discrete particle within the first-phase layer, of oxides of the remaining of the two or more of aluminum, zirconium, and yttrium. Another preferred embodiment of the invention involves passing a first gaseous halide, optionally mixed with a first carrier gas, over a first metal selected from the group consisting of aluminum, zirconium, yttrium, and metal salts thereof, at about 250°-1250°C to form a gaseous first metal halide of aluminum, zirconium, or yttrium. A second gaseous halide, which may be the same or different from the first gaseous halide, optionally mixed with a second carrier gas, which may be the same or different from the first carrier gas, is passed over one or more additional metals selected from aluminum, zirconium, and yttrium, and alloys and metal salts thereof, and different from the first metal, at about 250°-1250°C to form additional metal halides of one or more of aluminum, zirconium, and yttrium. A gaseous mixture of the first metal halides and the one or more additional metal halides, optionally the carrier gases, and other reactant gases is passed over the substrate, at a temperature of about 900°-1250°C for the cemented carbide substrate, or about 900°-1500°C for the hard ceramic substrate, and at a pressure between about 1 torr and about ambient pressure, to deposit a composite layer on the substrate. The other reactant gases, the flow rates of the vapors, the surface areas of the first metal and the one or more additional metals, and the deposition time are selected so that the composite layer comprises an adherent layer about 0.1-20 microns thick of a continuous first phase of an oxide of one of aluminum, zirconium, and yttrium, having one or more discontinuous additional phases of discrete particles of oxide(s) of one or more of aluminum, zirconium, and yttrium dispersed therein, the additional phase oxide(s) being different from the first-phase oxide. In yet another preferred embodiment of the process according to the invention, at least one intermediate layer about 0.5-10 microns thick selected from the group consisting of the carbides, nitrides, and carbonitrides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Si, and B is deposited between the substrate and the oxide layer. In a process according to yet another embodiment of the invention, the step of passing the first halide over the first metal is a continuous step, producing a steady flow of the first metal halide to pass over the substrate, and the step of passing the second halide over the one or more additional metals is an intermittent, pulsing step, producing pulses of the one or more additional metal halide to pass over the substrate with the first metal halide, the second halide being pulsed at intervals and for times selected to control the size and distribution of the additional phase particles within the continuous first phase. In the most preferred embodiment of the process according to the invention, the step of passing the gaseous mixture over the substrate takes place within a reactor, and at least one of the first metal and the one or more additional metals is disposed within a separate vessel within the reactor. The separate vessel operationally communicates with a source of the associated gaseous halide, and optionally the associated carrier gas, and with the reactor, so that the associated gaseous halide enters the separate vessel, passes over the surfaces of the metal or metals therein to form the metal halide, which flows into the reactor to pass over the substrate as a component of the gaseous mixture. The invention will now be described in detail with reference to the accompanying drawings in which: FIGURES 1 and 2 are schematic cross-sectional illustrations of substrates coated by two different embodiments of processes according to the invention. FIGURE 3 is a bar graph of comparative machining results. The process according to the present invention involves deposition of an adherent two or more phase composite oxide-based coating on a cemented metal carbide substrate, for example, a tungsten carbide-cobalt or related material, or on a hard ceramic material as described above. The deposition of a two or more phase oxide-based composite coating which possesses the properties of adherence to the substrate, wear resistance, high temperature resistance and resistance to chemical attack or breakdown at high temperatures depends on careful control of the process parameters. The outstanding properties of the coating are a result of the achievement of a second phase of discrete particles of an Al 2 O 3 , ZrO 2 or Y 2 O 3 , or a combination of these, within an Al 2 O 3 , ZrO 2 , or Y 2 O 3 matrix. For example, the preferred coatings include ZrO 2 and/or Y 2 O 3 particles within a continuous Al 2 O 3 matrix, Y 2 O 3 particles within a continuous ZrO 2 matrix, ZrO 2 particles within a continuous Y 2 O 3 matrix, or Y 2 O 3 stabilized ZrO 2 particles, i.e., an Y 2 O 3 -ZrO 2 solid solution, in a continuous Al 2 O 3 matrix. The particles may be evenly distributed throughout the matrix, or their distribution may be controlled to achieve, for example, a stratified structure of single-phase oxide matrix portions alternating with two or more phase matrix/particle portions, preferably distributed at controlled intervals throughout the depth of the matrix. Similarly, the deposition may be controlled to deposit a single-phase continuous portion of controlled depth of the matrix material below the two or more phase portion or the alternating single-phase/two or more phase portion of the coating. The process involves the use of a mixture of gases including a mixture of two or more metal halides and other reactant gases under carefully controlled conditions to deposit by chemical vapor deposition (CVD) compounds of the metals on a substrate. The metal halides preferably are produced by passing halide gas or gases over the metals, for example metal particulates. For example, the metals may be combined as a mixture of metals, as a metal alloy, or as metal salts. A single halide gas is passed over the combined metals to form a mixture of metal halides. Alternatively, at least the metal forming the matrix is separate, and separate halide gas streams are passed over the metals to form separate metal halides, which are later combined. Carrier gases, for example Ar, may be combined with the halide gases. Preferred halide gases are Cl 2 and HCl, forming with the metals described above AlCl 3 , ZrCl 4 , and/or YCl 3 . These are combined with suitable other gases such as H 2 and CO 2 or other volatile oxidizing gases such as H 2 O. One or more of the metals may be advantageously contained in a separate vessel within the CVD reactor. The gas enters the reactor via the separate vessel, the halide gas being converted by contact with the metal therein to the desired metal halide, which then enters the reactor to pass over the substrate. This method presents the advantage of utilizing the temperature gradient within the reactor, which can be accurately controlled in a multiple zone furnace or by way of location within the reactor, to control the temperature of the halide-metal reaction. Thus different metals in separate vessels may be disposed at different zones or positions within the reactor to control the reaction temperature for each. In order to achieve a first-phase matrix containing discrete particles of a second phase or phases, it is important to control the relative deposition by controlling such parameters as gas flow rates to produce the desired deposition of first and second phase materials. Further control over the deposition process may be achieved by pulsing the metal halide gas forming the second phase or phases while maintaining continuous flow of the metal halide gas forming the matrix. This pulsing method may also be used to control the distribution of the second phase within the matrix, for example to achieve either an even distribution or a stratified distribution as described above. Likewise, a single metal halide gas may be allowed to flow, with the other reactant gases, for a period of time sufficient to deposit a continuous single-phase portion of the material comprising the matrix, before the two-phase portion or alternating single-phase/two or more phase portion of the coating is deposited. Some examples of composite coatings according to the invention are: Al 2 O 3 matrix/ZrO 2 particles, ZrO 2 matrix/Y 2 O 3 particles, Y 2 O 3 matrix/ZrO 2 particles, Al 2 O 3 matrix/Y 2 O 3 stabilized ZrO 2 particles, Al 2 O 3 matrix/Y 2 O 3 particles, and Al 2 O 3 matrix/ZrO 2 particles and Y 2 O 3 particles. The terms second phase and two-phase as used herein refer to composites comprising a first phase, continuous oxide matrix compound and one or more additional or second phases which may be a single compound or more than one compound, in the form of discrete particles. The particles may be oxides of a single metal or a solid solution of oxides of more than one metal, and the individual particles maybe of the same or different compounds. The particles disclosed herein may be regularly shaped, as spheres, rods, whiskers, etc., or irregularly shaped. The composite coatings according to the invention are fully dense, adherent, and make it possible to combine the wear resistant properties of two or more components without the problems associated with differences in expansion coefficients and adhesion presented by layering of continuous coatings of the materials. Further improvement in the adhesion of the coating to the substrate may be achieved by depositing between the composite coating and the substrate a thin intermediate layer of TiC, TiN, or other carbide, nitride or carbonitride of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Si or B. Such deposition may be achieved in known manner as a preliminary part of the same coating process or in a separate, prior coating process. Similarly, for special applications, for example friction, cosmetic, wear or thermal purposes, a thin outer layer such as TiN may be applied in known manner over the composite coating. Figures 1 and 2, not drawn to scale, schematically illustrate typical articles 10 and 30 coated according to the invention. As shown in Figure 1, substrate 12 is a shaped cemented WC material, and may be a cutting tool or other article requiring wear resistance under the extreme conditions described above. A thin layer 14 of TiC covers the substrate, at least in the area subjected to wear. Composite layer 16 is deposited over TiC layer 14, and is made up of single-phase matrix portions 18 and 20 of Al 2 O 3 , and two-phase portions 22 of an Al 2 O 3 matrix 24 and discrete particles 26 of ZrO 2 . As shown in Figure 1, there is no separation between the Al 2 O 3 of matrix 24 of two-phase portions 22 and that of single-phase matrix portions 18 and 20. The Al 2 O 3 of the composite coating is a single continuous matrix having a second phase of controlled composition and distribution dispersed therein. An outer layer 28 of TiN is deposited over the composite layer, giving article 10 a distinctive identifying color. Figure 2 illustrates an alternate embodiment of the article coated according to the invention. Like features in the two figures are identified by the same reference numerals. In Figure 2, substrate 12 is overlaid with thin TiC layer 14 in the same manner as shown in Figure 1. Composite layer 32 is deposited over TiC layer 14, and is made up of Al 2 O 3 matrix 24 with particles 34 of Y 2 O 3 stabilized ZrO 2 evenly distributed throughout matrix 24. Outer layer 28 of TiN is deposited over the composite layer. EXAMPLES 1-6 After rinsing of all gas lines with their respective gases for 0.5-1 hr, samples of cutting tool inserts of a cemented carbide material, steel cutting grade C-5, were coated with a layer of TiC about 3 microns thick by known techniques in a CVD reactor. An excess of preweighed zirconium metal chips was placed in a separate vessel disposed in the reactor. An excess of aluminum chips was placed in a vessel outside the reactor. The reactor was evacuated to about 13.3 mbar(10 torr), then heated under low pressure, while being flushed with flowing hydrogen, to increase the outgassing before deposition. Following the deposition procedure, the reactor was cooled, at the deposition pressure and while being flushed with hydrogen, to about 300°C, then under ambient pressure and flowing nitrogen to room temperature. The deposition reaction conditions for Examples 1-6 are given in Table I, below. For all of these Examples the halide gas was Cl 2 , the carrier gas for the Al and Zr reactions was Ar, and the other reactant gas was CO 2 with H 2 as a carrier. The Cl 2 flow rates were adjusted to give the metal chloride flow rates shown in Table I. The deposition pressure for Examples 1-6 was 66.5 mbar(50 torr); the temperature, 1040°C. For each of these Examples, a period of Al 2 O 3 deposition (single-phase) ranging from 0.5 to 2.5 hrs was carried out before the two-phase Al 2 O 3 /ZrO 2 deposition was begun. During the single-phase deposition Ar gas was allowed to flow over the Zr, but the Cl 2 gas flow was shut off. The results of Examples 1-6 are shown in Table II. The thickness of the coatings was measured by the abrasive ball method (Calotest). The chemical composition of the coating was determined by x-ray diffraction analysis. The coating was deposited on the TiC underlayer as a stratified composite of alternating alumina and alumina/zirconia portions over a single-phase alumina portion, similar to that illustrated in Figure 1, but without the TiN layer over the oxide coating. The oxide coating and the TiC underlayer show satisfactory thickness and good adherence. Example Oxides thickness, microns X-Ray Diffraction 1 --- α - Al 2 O 3 + ZrO 2 2 1.8 α - Al 2 O 3 + ZrO 2 3 5 α - Al 2 O 3 + ZrO 2 4 0.5-2 α - Al 2 O 3 + ZrO 2 5 0.7-1.5 α - Al 2 O 3 + ZrO 2 6 1.5 α - Al 2 O 3 + ZrO 2 Machining tests were performed on the coated cemented carbide cutting tool insert samples of Example 6 (A) and, for comparison, on a ceramic based insert (B), and on two different commercial grades of TiC based inserts coated with Al 2 O 3 (C and D). Inserts A, B, C and D were tested by turning a 4340 steel workpiece under dry conditions at 213 surface meter per minute (700 sfm), 0.254 min per revolution (0.01 ipr), 0.5 in DOC. For each insert, 458.9 cm 3 (28 cu. in.) of metal were removed in 6.7 min cutting time. The results are illustrated in Fig. 3, showing the average nose and flank wear for each type of insert. The inserts coated by the method according to the invention compared favorably with the materials in current commercial use. EXAMPLES 7-8 The process of Examples 1-6 was repeated for Examples 7 and 8, to coat the same type of TiC coated cemented carbide cutting tool inserts, except that both AlCl 3 and ZrCl 4 were flowing during the entire deposition period. The deposition pressure and temperature were 66.5 mbar(50 torr) and 1040°C respectively. The remaining reaction conditions are given in Table III below. The resulting composite coatings were similar to that illustrated in Figure 2, except that no TiN layer was deposited over the oxide coating. The coating was a continuous ZrO 2 matrix with Y 2 O 3 particles distributed therein. No single phase portion was deposited below the two phase portion of the oxide layer. Ex. Flow Rate ccpm Total/Reactant Volume percents Time hrs. H 2 CO 2 AlCl 2 ZrCl 4 7 1420/1020 65.7 29.3 2.5 2.5 2.8 8 1100/800 88 7 2.5 2.5 3 The processes described in Examples 1-8 are also useful for applying similar coatings to hard ceramic substrates to produce similar cutting inserts.

Claims: A process for depositing a wear resistant ceramic coating on a cemented carbide or hard ceramic substrate using thermal vapor desposition comprising the steps of: passing over the substrate a first gaseous mixture of a first halide vapor selected from the group consisting of halides of aluminum, yttrium and zirconium, with other reactant gases, and optionally a carrier gas, at a temperature of about 900°-1250°C for the cemented carbide substrate, or about 900°-1500°C for the hard ceramic substrate, at a pressure between about 1.33 mbar (1 Torr) and about ambient pressure, and at partial pressure ratios, at a flow rate, and for a time sufficient to deposite a continuous, fully dense, adherent, wear resistant layer of a material selected from the group consisting of oxides of aluminum, zirconium, and yttrium about 0.1-20 microns thick on the substrate; which additionally comprises the step of: mixing with the first gaseous mixture at least one additional vapor selected from the halides of aluminum, zirconium, and yttrium; wherein the additional vapor is different from the first halide vapor, and is mixed at a partial pressure selected to form at least one discontinuous additional phase, dispersed as discrete particles within the continuous oxide layer, of at least one material selected from the group consisting of oxides of aluminum, zirconium, and yttrium, to form a wear resistant composite ceramic layer on the substrate. A process according to claim 1 further comprising the step of depositing between the substrate and the composite ceramic layer at least one intermediate layer about 0.5-10 microns thick selected from the group consisting of carbides, nitrides, and carbonitrides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Si and B. A process according to claim 1, wherein the additional vapor is pulsed into the first gaseous mixture, to mix therewith, during the deposition of the continuous oxide layer, and where the additional vapor is selected from the halide of aluminum, zirconium and yttrium, optionally mixed with a carrier gas. A process according to claim 3 further comprising the step of controlling the size and distribution within the oxide layer of the additional phase particles by controlling the partial pressure, the time intervals, and the lengths of time at which the at least one additional vapor is pulsed into the first gaseous mixture. A process according to claim 4 wherein the step of deposition of the continuous oxide layer is carried out for a sufficient time before the pulsing step is begun to form a single-phase, continuous oxide portion separating the substrate and the two or more phase portion of the composite ceramic coating. A process according to claim 4 wherein the intermittent pulsing step occurs at time intervals and for times selected to form a stratified composite ceramic layer in which two or more phase portions alternate with single- phase, continuous oxide portions. A process according to claim 3 further comprising the step of depositing between the substrate and the composite ceramic layer at least one intermediate layer about 0.5-10 microns thick selected from the group consisting of carbides, nitrides, and carbonitrides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Si and B. A process according to claim 3 further comprising the step of depositing between the substrate and the composite ceramic layer an intermediate layer of TiC or TiN about 2-5 microns thick; and wherein the first gaseous mixture consists essentially of 2.5-21 volume % CO 2 , 47-64 volume % hydrogen, and 1.5-30 volume % AlCl 3 , the remainder being argon, passing over the substrate at a temperature of 1000-1100°C, a pressure of 66.5-133 mbar (50-100 torr), and a flow rate of 1100-1500 cm 3 /min for 2.5 to 5 hr; and the at least one additional vapor is 0.5-2.5 volume % ZrCl 4 pulsed for about 1-10 min at intervals of about 2-6 times the pulse time, to deposit a composite ceramic layer consisting of a first, continuous phase of Al 2 O 3 and a discontinuous additional phase of discrete grains of ZrO 2 dispersed within the Al 2 O 3 first phase. A process according to claim 8 wherein the intermediate layer is TiC about 3.0-3.5 microns thick; the first gaseous mixture consists essentially of about 7 volume % CO 2 , 88 volume % hydrogen, 2.5 volume % AlCl 3 , the remainder being argon, passing over the substrate at a temperature of about 1040°C, a pressure of about 66.5 mbar (50 torr), and a flow rate of about 1420 cm 3 /min for about 3.5 hrs; and about 2.5 volume % ZrCl 4 is pulsed for about 8 min of each 22 min during the last 2.5 hrs. A process according to claim 1 further comprising the steps of: passing a halide vapor, optionally mixed with a carrier gas, over a mixture or alloy of two or more metals selected from the group consisting of aluminum, zirconium, yttrium and their metal salts, at about 250°-1250°C, to form a first halide mixture comprising halides of two or more of aluminum, zirconium, and yttrium, and optionally the carrier gas; and mixing the first halide mixture with other reactant gases to form a first gaseous mixture. A method according to claim 10 wherein the mixture or alloy of two or more metals consists essentially of a mixture or alloy of aluminum and zirconium or a mixture or alloy of zirconium and yttrium; the other reactant gases comprise CO 2 with hydrogen as a carrier; and the composite layer comprises a continuous Al 2 O 3 first phase having discrete particles of ZrO 2 dispersed therein, or a continuous ZrO 2 first phase having discrete particles of Y 2 O 3 dispersed therein, or a continuous Y 2 O 3 first phase having discrete particles of ZrO 2 dispersed therein. A process according to claim 10 further comprising the step of depositing between the substrate and the composite ceramic layer at least one intermediate layer about 0.5-10 microns thick selected from the group consisting of the carbides, nitrides, and carbonitrides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Si, and B. A process according to claim 1 further comprising the steps of: first passing a first gaseous halide, optionally mixed with a first carrier gas, over a first metal selected from the group consisting of aluminum, zirconium, yttrium, and metal salts thereof, at 250°-1250°C, to form a gaseous first metal halide of aluminum, zirconium, or yttrium; and passing a second gaseous halide, which may be the same or different from the first gaseous halide, optionally mixed with a second carrier gas, which may be the same or different from the first carrier gas, over one or more additional metals selected from the group consisting of aluminum, zirconium, yttrium, and alloys and metal salts thereof, and different from the first metal, at about 250°-1250°C, to form one or more additional metal halides of one or more of aluminum, zirconium, and yttrium. A process according to claim 13 further comprsing the step of depositing between the substrate and the oxide layer at least one intermediate layer about 0.5-10 microns thick selected from the group consisting of the carbides, nitrides, and carbonitrides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Si, and B. A process according to claim 14 wherein the first metal is aluminum, the additional metal is zirconium, the first and second halides are both Cl 2 or HCl, and the intermediate layer is TiC. A process according to claim 15 wherein the step of passing the first halide over the first metal is a continuous step, producing a steady flow of the first metal halide to pass over the substrate; and the step of passing the second halide over the one or more additional metals is an intermittent, pulsing step, producing pulses of the one or more additional metal halides to pass over the substrate with the first metal halide, wherein the second halide is pulsed at intervals and for times selected to control the size and distribution of the additional phase particles within the continuous first phase. A process according to claim 13 wherein the first metal halide and the other reactant gases are passed over the substrate for a sufficient time before the flow of the second halide is begun to deposit a single-phase, continuous portion of the composite layer separating the substrate and the two or more phase portion of the composite layer. A process according to claim 13 wherein the step of passing the gaseous mixture over the substrate takes place within a reactor; and at least one of the first metal and the one or more additional metals is disposed within a separate vessel within the reactor, the separate vessel operationally communicating with a source of the associated gaseous halide, and optionally the associated carrier gas, and with the reactor, so that the associated gaseous halide enters the separate vessel, and passes over the metal(s) therein to form the metal halide(s), which flows into the reactor to pass over the substrate as a component of the gaseous mixture. A process according to claim 18 wherein the first metal is aluminum or a metal salt thereof; and the one or more additional metals is zirconium or yttrium, or a metal salt thereof, or a mixture or alloy thereof, and is disposed within a separate vessel within the reactor. A process according to claim 13 wherein the additional metal is aluminum, zirconium, yttrium or a metal salt thereof, and is different from the first metal; and further comprising the step of passing a third gaseous halide, which may be the same or different from the first and second gaseous halides, optionally mixed with a third carrier gas, which may be the same or different from the first and second carrier gases, over a third metal selected from the group consisting of aluminum, zirconium, yttrium, and metal salts thereof, and different from the first and additional metals, at about 250°-1250°C, to form a third metal halide of aluminum, zirconium, or yttrium; and wherein the gaseous mixture passing over the substrate further comprises the third metal halide, and the discontinuous additional phase further comprises discrete particles of oxides of two of aluminum, zirconium, and yttrium dispersed therein. A process according to claim 20 wherein the step of passing the gaseous mixture over the substrate takes place within a reactor; and at least one of the first metal, the additional metal, and the third metal is disposed within a separate vessel within the reactor, the separate vessel operationally communicating with a source of the associated gaseous halide and optionally the associated carrier gas, and with the reactor, so that the associated gaseous halide enters the separate vessel, and passes over the metal therein to form the metal halide, which flows into the reactor to pass over the substrate as a component of the gaseous mixture. A wear resistant article comprising: a cemented carbide or hard ceramic substrate body, and a fully dense, adherent, wear resistant, composite ceramic coating having at least two phases on the substrate comprising: a continous oxide layer about 0.1-20 microns thick of a material selected from the group consisting of the oxides of aluminium, zirconium, and yttrium; and at least one discontinous additional phase dispersed as disrete particles within the oxide layer, of at least one material selected from the group consisting of oxides of aluminium, zirconium, and yttrium, the least one material being different from that of the oxide layer; characterized in that the composite ceramic layer is a stratified layer in which portions having at least two phases alternate with single phase continous oxide portions. An article according to claim 22, wherein the substrate body is a Si 3 N 4 -based composite, the continous oxide layer is Al 2 O 3 and the additional phase is ZrO 2 particles dispersed within the Al 2 O 3 to form two-phase Al 2 O 3 / ZrO 2 portions alternating with single-phase continous Al 2 O 3 portions, and further comprising, between the substrate body and the composite ceramic layer, an intermediate layer of TiC about 2 - 5 microns thick. A wear resistant article comprising: a cemented carbide or hard ceramic substrate body, and a fully dense, adherent, wear resistant, composite ceramic coating having at least two phases on the substrate comprising: a continous oxide layer about 0.1 - 20 microns thick of a material selected from the group consisting of the oxides of aluminium, zirconium, and yttrium; and at least one discontinous additional phase dispersed as disrete particles within the oxide layer, of at least one material selected from the group consisting of oxides of aluminium, zirconium, and yttrium, the least one material being different from that of the oxide layer; characterized in that the continous oxide layer is ZrO 2 and the additional phase is Y 2 O 3 . A wear resistant article comprising: a cemented carbide or hard ceramic substrate body, and a fully dense, adherent, wear resistant, composite ceramic coating having at least two phases on the substrate comprising: a continous oxide layer about 0.1-20 microns thick of a material selected from the group consisting of the oxides of aluminium, zirconium, and yttrium; and at least one discontinous additional phase dispersed as disrete particles within the oxide layer, of at least one material selected from the group consisting of oxides of aluminium, zirconium, and yttrium, the least one material being different from that of the oxide layer; characterized in that the continous oxide layer is Y 2 O 3 and the additional phase is ZrO 2 . A wear resistant article comprising: a cemented carbide or hard ceramic substrate body, and a fully dense, adherent, wear resistant, composite ceramic coating having at least two phases on the substrate comprising: a continous oxide layer about 0.1 - 20 microns thick of a material selected from the group consisting of the oxides of aluminium, zirconium, and yttrium; and at least one discontinous additional phase dispersed as disrete particles within the oxide layer, of at least one material selected from the group consisting of oxides of aluminium, zirconium, and yttrium, the least one material being different from that of the oxide layer; characterized in that the continous oxide layer is Al 2 O 3 and the additional phase is Y 2 O 3 stabilized ZrO 2 . A wear resistant article comprising: a cemented carbide or hard ceramic substrate body, and a fully dense, adherent, wear resistant, composite ceramic coating having at least two phases on the substrate comprising: a continous oxide layer about 0.1 - 20 microns thick of a material selected from the group consisting of the oxides of aluminium, zirconium, and yttrium; and at least one discontinous additional phase dispersed as disrete particles within the oxide layer, of at least one material selected from the group consisting of oxides of aluminium, zirconium, and yttrium, the least one material being different from that of the oxide layer; characterized in that the continous oxide layer is Al 2 O 3 and the additional phases are Y 2 O 3 and ZrO 2 particles.

Inventors: GINDRAUX GILBERT, HINTERMANN HANS ERICH, SARIN VINOD K, GINDRAUX, GILBERT, HINTERMANN, HANS ERICH, SARIN, VINOD K.
Applicants: VALENITE INC, VALENITE INC.
Application year: 1988
Main classification: C23C16
IPC codes: C23C16, C04B41