A coated article

Abstract: A superalloy turbine blade (10) has a bond coating (92) and a thermal barrier coating (94). The bond coating (92) comprises a MCrAlY coating on the metallic substrate (90) of the superalloy turbine blade (10), an aluminide coating on the MCrAlY coating and an alumina interface layer (94) on the aluminide coating. The thermal barrier coating (96) is on the alumina interface layer (94). The aluminide coating on the MCrAlY provides more aluminium to bond the thermal barrier coating (6) onto the metallic substrate (90).

Description: The present invention is concerned with coatings for metallic substrates, and is particularly concerned with ceramic thermal barrier coatings for metallic components for use in gas turbine engines. It is known in the prior art to apply ceramic to a metallic substrate to produce a ceramic thermal barrier coating by the thermal, or plasma, spray process. In this technique the ceramic is applied onto a bond coat, for example a MCrAlY bond coat, which has been applied to the metallic substrate. It is also known in the prior art to apply ceramic to a metallic substrate to produce a ceramic thermal barrier coating by the physical vapour deposition (PVD) process. In this technique the ceramic is applied onto a bond coat, for example a MCrAlY coating with an alumina interface layer, which has been applied to the metallic substrate. The ceramic thermal barrier coatings deposited by the PVD process have benefits over the ceramic thermal barrier coatings deposited by a thermal spray process. The main benefit is improved thermal shock resistance due to the columnar structure of the ceramic thermal barrier coating produced by the PVD process. Other benefits are improved erosion resistance and improved aerothermal performance. The present invention seeks to provide an article which comprises a metallic substrate having a bond coating and thermal barrier coating in which the bond coating provides a better bond between the thermal barrier coating and the metallic substrate. Accordingly the present invention provides an article comprising a metallic substrate, a bond coating on the metallic substrate, the bond coating comprising a MCrAlY coating on the metallic substrate, an aluminide coating on the MCrAlY coating, an interface layer on the aluminide coating, the interface layer comprising alumina, and a thermal barrier coating on the interface layer. The use of a MCrAlY coating provided with an aluminide coating provides more aluminium content to bond the thermal barrier coating onto the substrate. The aluminide coating may be a platinum aluminide coating. The present invention also provides an article comprising a metallic substrate, a bond coating on the metallic substrate, the bond coating comprising an aluminide coating on the metallic substrate, a platinum aluminide coating on the aluminide coating, an interface layer on the platinum aluminide coating, the interface layer comprising alumina, and a thermal barrier coating on the interface layer. The thermal barrier coating may have columnar grains. The columnar grains may have layers with different structures. The thermal barrier coating may comprise zirconia, yttria or a mixture thereof. The metallic substrate may be a superalloy substrate. The present invention also provides a method of manufacturing an article comprising applying a MCrAlY coating to a metallic substrate, forming an aluminide coating on the MCrAlY coating, forming an alumina interface layer on the aluminide coating and depositing a thermal barrier coating on the alumina interface layer. The thermal barrier coating may be deposited by vapour deposition. The thermal barrier coating may be deposited by vapour deposition and plasma assisted vapour deposition. The MCrAlY may be deposited by vapour depositions. The present invention also provides a method of manufacturing an article comprising applying a MCrAlY or an aluminide coating to a metallic substrate, forming a platinum aluminide coating on the MCrAlY or aluminide coating, forming an alumina interface layer on the platinum aluminide coating and depositing a thermal barrier coating on the alumina interface layer. The aluminide coating may be formed by pack aluminising. The platinum aluminide coating may be formed by platinum aluminising. The alumina may be formed by oxidation. The present invention will be more fully described by way of example, with reference to the accompanying drawings in which:- Figure 1 is a perspective view of a gas turbine engine turbine blade according to the present invention. Figure 2 is a sectional view through an article having a thermal barrier coating applied by a first prior art method. Figure 3 is a sectional view through an article having a thermal barrier coating applied by a second prior art method. Figure 4 is a sectional view through an article having a thermal barrier coating. Figure 5 is an enlarged view of a portion of the thermal barrier coating shown in figure 4. Figure 6 is a graph of voltage applied to the substrate against time during the application of the thermal barrier coating. Figure 7 is a sectional view through an apparatus for use in the method of applying the thermal barrier coating according to the present invention. Figure 8 is a graph of thermal conductivity against temperature for several thermal barrier coatings. Figure 9 is a sectional view through an article having an alternative thermal barrier coating applied according to the present invention. Figure 10 is an enlarged view of a portion of the thermal barrier coating in Figure 9. Figure 11 is a graph of voltage applied to the substrate against time during the application of the thermal barrier coating. Figure 12 is a graph of current density against substrate voltage. Figure 13 is a graph of current density against pressure. Figure 14 is a micrograph of a fracture cross-section through an article according to the present invention. A gas turbine engine turbine blade 10 is shown in figure 1. The turbine blade 10 comprises a shaped root portion 12, for attaching the turbine blade 10 to a turbine rotor, a platform portion 14, for defining a portion of the radially inner boundary of the gas flow path through the turbine, and an aerofoil portion 16, which extracts energy from the hot gases passing through the turbine. The platform portion 14, and the aerofoil portion 16, of the turbine blade 10 are provided with a coating system 18 which allows the turbine blade 10 to operate at higher gas temperatures. The coating system 18 comprises a bond coating 22, deposited onto the metallic substrate 20 of the turbine blade 10, and a ceramic thermal barrier coating 24 deposited onto the bond coating 22. A coating system 38 applied by a first prior art (e.g. EP-A-0 366 924) method is shown in figure 2. The coating system 38 comprises a bond coating 42, deposited onto the metallic substrate 40 and a ceramic thermal barrier coating 44 deposited onto the bond coating 42. The bond coating 42 is generally a MCrAlY coating which has been deposited by thermal spraying or by physical vapour deposition (PVD), or the bond coating may be an aluminide coating. The bond coating 42 may additionally have an alumina layer. The ceramic thermal barrier coating 44 is generally zirconia or yttria or a mixture thereof which has been deposited onto the bond coating 42 by physical vapour deposition (PVD). The ceramic thermal barrier coating 44 has a columnar grained microstructure 46 which has a relatively high thermal conductivity, good strain tolerance, good surface finish and good erosion resistance. A coating system 48 applied by a second prior art method is shown in figure 3. The coating system 48 comprises a bond coating 52, deposited onto the metallic substrate 50 and a ceramic thermal barrier coating 54 deposited onto the bond coating 52. The bond coating 52 is generally a MCrAlY coating which has been deposited by thermal spraying or by physical vapour deposition (PVD), or the bond coating may be an aluminide coating. The ceramic thermal barrier coating 54 is generally zirconia or yttria or a mixture thereof which has been deposited onto the bond coating 52 by thermal spraying. The ceramic thermal barrier coating 54 has a "brick wall" microstructure which has poor erosion resistance but has a relatively low thermal conductivity when compared to the thermal conductivity of the ceramic thermal barrier coating applied by the first prior art method mentioned above. The coating system 18 applied by the method of the present invention is shown more clearly in figures 4 and 5. The coating system 18 comprises a bond coating 22, deposited onto the metallic substrate 20 and a ceramic thermal barrier coating 24 deposited onto the bond coating 22. The bond coating 22 is generally a MCrAlY coating which has been deposited by thermal spraying or by physical vapour deposition (PVD). Alternatively the bond coating 22 may be an aluminide coating which has been deposited by pack aluminising or may be a platinum-aluminide coating which has been deposited by platinum aluminising. The ceramic thermal barrier coating 24 is generally zirconia, yttria or a mixture thereof which has been deposited onto the bond coating 22 by physical vapour deposition (PVD). Alternatively the ceramic thermal barrier coating 24 may comprise any other suitable ceramic. The ceramic thermal barrier coating 24 has a columnar grained microstructure 28 which has good strain tolerance, good surface finish and good erosion resistance. The ceramic thermal barrier coating 24 has a relatively low thermal conductivity when compared to the ceramic thermal barrier coating 44 of the coating system 38 in figure 2 and is substantially the same or better than the thermal conductivity of the ceramic thermal barrier coating 54 of the coating system 48 in figure 2. The ceramic thermal barrier coating 24 in figures 4 and 5 has reduced thickness compared to the ceramic thermal barrier coating 44 in figure 2 for operation at the same temperature. Alternatively the same thickness of ceramic thermal barrier coating 24 may be used to allow operation at higher temperatures. The ceramic thermal barrier coating 24 has alternate layers 25 and 27 which have different structure to create interfaces 26 substantially parallel to the metallic substrate 20/bond coating 22 interface. These interfaces 26 provide paths of increased resistance to heat transfer to emulate the good thermal conductivity properties of thermal sprayed ceramic thermal barrier coatings. The structure in the alternate layers 25,27 of the ceramic thermal barrier coating 24 is columnar 28 to ensure that the strain tolerance of the ceramic thermal barrier coating 24 is not impaired. The columnar grains 28 in the layers 25,27 extend substantially perpendicular to the metallic substrate 20/bond coating 22 interface. The difference in structure in layers 25, 27 are the result of variations in the micro-structure and/or density/coarseness of the columnar grains 28 of the ceramic. It is to be noted that the columnar grains 28 in one of the layers 27 continue to grow into the adjacent layer 25 and that there is no interruption of the columnar grains 28 at the interfaces 26 between the layers 25,27. It may also be considered that the columnar grains 28 in the ceramic thermal barrier coating 24 extend through the full thickness of the coating 24, and that each columnar grain 28 has its structure modulated along its length by the provision of the layers 25,27. The coating system 18 is applied to the metallic substrate 20 by firstly depositing a MCrAlY bond coating 22 onto the metallic substrate 20 by plasma spraying. Alternatively the MCrAlY may be deposited by physical vapour deposition (PVD). A ceramic thermal barrier coating 24 is then deposited onto the MCrAlY bond coating 22. An apparatus used for depositing the ceramic thermal barrier coating 24 onto the MCrAlY bond coating 22 is shown in figure 7. The apparatus 60 comprises a vacuum chamber 62 which has one or more pumps 64 to evacuate the vacuum chamber 62. An electron beam from an electron beam gun 66 is arranged to impinge upon a supply of ceramic vapour 68, i.e zirconia-yttria alloy, such that the ceramic is evaporated when the vacuum chamber 62 is evacuated. The metallic substrate 20 is also connected into an electrical circuit such that it may given a D.C. or R.F. potential 70. The apparatus 60 also includes supplies of argon 74, hydrogen 76 and oxygen 78 which are interconnected to the interior of the vacuum chamber 62 via a pipe 72. Each of the supplies of argon 74, hydrogen 76 and oxygen 78 are provided with valves to control the flow of the gases. In order to deposit the ceramic thermal barrier coating 24 onto the MCrAlY bond coating 22 the metallic substrate 20 with the deposited bond coating 22 is placed into the vacuum chamber 62. The vacuum chamber 62 is evacuated and the electron beam gun 66 directs electrons at the supply of ceramic vapour 68 to evaporate ceramic. The interior of the vacuum chamber 62 is supplied with controlled amounts of an inert gas and oxygen during the evaporation of the supply of ceramic vapour 68. The supply of inert gas, e.g. argon, is to maintain the correct glow discharge, or plasma, conditions and the supply of oxygen is to maintain the composition of the ceramic thermal barrier coating at the stoichiometric ratio. The ceramic vapour deposits onto the MCrAlY bond coating 22. In order to produce the layers 25 and 27 in the ceramic thermal barrier coating 24, the ceramic vapour is deposited alternately, for predetermined periods of time, by the physical vapour deposition process (PVD) and by a plasma assisted physical vapour deposition process (PAPVD). In the plasma assisted physical vapour deposition process (PAPVD) a D.C. or R.F. potential is applied to the metallic substrate 20, this is known as ion plating. The first layer 25 of ceramic deposited onto the bond coating 22 is preferably deposited by plasma assisted physical vapour deposition (PAPVD) such that the ceramic at the interface with the bond coating 22 has a relatively high density and preferably has maximum density. The use of the plasma assisted physical vapour deposition process (PAPVD) is used to control the structure of the ceramic thermal barrier coating 24 all the way through its thickness, by controlling the way that the columnar ceramic grains 28 grow, to tailor the characteristics of the ceramic at particular positions. The plasma assisted physical vapour deposition process (PAPVD) causes the columnar ceramic grains 28 to be packed together more closely. The D.C. or R.F. potential used during the plasma assisted physical vapour deposition process (PAPVD) may be adjusted for deposition of different ceramic layers to control the density of the columnar ceramic grains 28. In order to achieve the maximum difference in thermal conductivity between adjacent layers 25,27, the interfaces 26 between the adjacent layers 25,27 should be as abrupt as is practical. The abrupt interfaces 26 are preferably achieved by the use of a simple switching action between the physical vapour deposition process and the plasma assisted physical vapour deposition process such that the voltage at the substrate follows a square wave form with time as shown in figure 6. The peak voltages in figure 6 correspond to the time when the layers 25 of ceramic are deposited by plasma assisted physical vapour deposition and the minimum voltages in figure 6 correspond to the time when the layers 27 of ceramic are deposited by physical vapour deposition. The switching points in figure 6 correspond to the time when the interfaces 26 between the layers 25 and 27 are produced. In an experiment four different coating systems were applied to a metallic substrate. The first coating system comprised a plasma sprayed MCrAlY bond coating applied onto a nickel superalloy, N75 a nickel-chromium superalloy, and a purely physical vapour deposited (PVD) ceramic thermal barrier coating applied onto the bond coating. The vacuum chamber was evacuated to a pressure of 0,67 Pa (5 mTorr) and the electron beam gun power was 8KV at 500mA. A total coating thickness of 90 x 10 -6 m was deposited. The thermal conductivity of the ceramic thermal barrier coating was measured at a temperature of 1000 o C and was 1.0 W/m/K. The second coating system comprised a plasma sprayed MCrAlY bond coating applied onto the same nickel superalloy and a purely plasma assisted physical vapour deposited (PAPVD) ceramic thermal barrier coating applied onto the bond coating. The vacuum chamber was evacuated to a pressure of 0,93 Pa (7 mTorr) and the electron beam gun power was 8KV at 500mA. The R.F. power used during the PAPVD process was 500W. A total ceramic coating thickness of 160 x 10 -6 m was deposited. The thermal conductivity of the ceramic thermal barrier coating was measured at a temperature of 1000 o C and was 0.55 W/m/K. The third coating system comprised a plasma sprayed MCrAlY bond coating applied onto the same nickel superalloy and alternate layers of physical vapour deposited (PVD) and plasma assisted physical vapour deposited (PAPVD) ceramic thermal barrier coating applied onto the bond coating. The vacuum chamber was evacuated to a pressure of 0,53 Pa (4 mTorr) and the electron beam gun power was 8KV at 500mA. The R.F. power used during the PAPVD process was 500W. A total of 70 layers of ceramic were deposited. Each of the 35 layers of ceramic deposited by the physical vapour deposition process (PVD) were 2 x 10 -6 m thick and each of the 35 layers of ceramic deposited by the plasma assisted physical vapour deposition process (PAPVD) were also 2 x 10 -6 m thick. The thermal conductivity of the ceramic thermal barrier coating was measured at a temperature of 1000 o C and was 0.3 W/m/K. The fourth coating system comprised a plasma sprayed MCrAlY bond coating applied onto the same nickel superalloy and alternate layers of physical vapour deposited (PVD) and plasma assisted physical vapour deposited (PAPVD) ceramic thermal barrier coating applied onto the bond coating. The vacuum chamber was evacuated to a pressure of 0,53 Pa (4 mTorr) and the electron beam gun power was 8KV at 500mA. The R.F. power used during the PAPVD process was 500 W. A total of 70 layers of ceramic were deposited. Each of the 35 layers of ceramic deposited by the physical vapour deposition process (PVD) were 2 x 10 -6 m thick and each of the 35 layers of ceramic deposited by the plasma assisted physical vapour deposition process (PAPVD) were 1 x 10 -6 m thick. The thermal conductivity of the ceramic thermal barrier coating was measured at a temperature of 1000 o C and was 1.0 W/m/K. Figure 8 shows a graph of thermal conductivity against temperature for each of the four different coating systems. Line A indicates the thermal conductivity of the first coating system with temperature. Line B indicates the thermal conductivity of the second coating system with temperature. Line C indicates the thermal conductivity of the third coating system with temperature and finally line D indicates the thermal conductivity of the fourth coating system with temperature. The thermal conductivity of the third coating system is a third of that of the first coating system. The first coating system is the ceramic thermal barrier coating applied by the prior art method of physical vapour deposition (PVD). The thermal conductivity of the third coating system is also less than that of the second coating system. The second coating system is the ceramic thermal barrier coating applied purely by plasma assisted physical vapour deposition (PAPVD). The thermal conductivity of the fourth coating system is approximately the same as the first coating system. A coating system 88 applied by the method of the present invention is shown more clearly in figures 9 and 10. The coating system 88 comprises a bond coating 92, deposited onto the metallic substrate 90, an interface layer 94 on the bond coating 92 and a ceramic thermal barrier coating 96 deposited onto the interface layer 94. The bond coating 92 is generally a MCrAlY coating which has been deposited by thermal spraying or by physical vapour deposition (PVD). Alternatively the bond coating 92 may be an aluminide coating which has been deposited by pack aluminising or may be a platinum-aluminide coating which has been deposited by platinum aluminising. The bond coating 92 may be a MCrAlY coating with an aluminide top coating or a MCrAlY coating with a platinum aluminide top coating. The interface layer 94 comprises oxides or oxide/metal on the bond coating which improves the adhesion of the ceramic thermal barrier coating 96. The oxide is predominantly alumina which has controlled structure and properties. The metal comprises the metallic elements in the bond coating. The ceramic thermal barrier coating 96 is generally zirconia, yttria or a mixture thereof which has been deposited onto the interface layer 94 by physical vapour deposition (PVD). Alternatively the ceramic thermal barrier coating 96 may comprise any other suitable ceramic. The ceramic thermal barrier coating 96 has a columnar grained microstructure 100 which has good strain tolerance, good surface finish and good erosion resistance. The ceramic thermal barrier coating 96 has a relatively low thermal conductivity when compared to the ceramic thermal barrier coating 44 of the coating system 38 in figure 2 and is substantially the same or better than the thermal conductivity of the ceramic thermal barrier coating 54 of the coating system 48 in figure 3. The ceramic thermal barrier coating 96 in figures 9 and 10 has reduced thickness compared to the ceramic thermal barrier coating 44 in figure 2 for operation at the same temperature. Alternatively the same thickness of ceramic thermal barrier coating 96 may be used to allow operation at higher temperatures. The ceramic thermal barrier coating 96 has alternate layers 97 and 98 which have different structure to create interfaces 99 substantially parallel to the metallic substrate 90/bond coating 92 interface. These interfaces 99 provide paths of increased resistance to heat transfer to emulate the good thermal conductivity properties of thermal sprayed ceramic thermal barrier coatings. The structure in the alternate layers 97,98 of the ceramic thermal barrier coating 96 is columnar 100 to ensure that the strain tolerance of the ceramic thermal barrier coating 96 is not impaired. The columnar grains 100 in the layers 97,98 extend substantially perpendicular to the metallic substrate 90/bond coating 92 interface. The difference in structure in layers 97, 98 are the result of variations in the structure and/or density/coarseness of the columnar grains 100 of the ceramic. The columnar grains 100 in one of the layers 98 continue to grow into the adjacent layer 97 and there are no interruptions of the columnar grains 100 at the interfaces 99 between the layers 97,98. The columnar grains 100 in the ceramic thermal barrier coating 96 extend through the full thickness of the coating 96 and each columnar grain 100 has its structure modulated along its length by the provision of the layers 97,98. The coating system 88 according to the present invention is applied to the metallic substrate 90 by firstly depositing a MCrAlY bond coating 92 onto the metallic substrate 90 by plasma spraying. Alternatively the MCrAlY may be deposited by physical vapour deposition (PVD). The surface of the bond coating 92 is then modified to create an oxide or oxide/metal interface layer 94 which has controlled structure and properties to improve the adhesion of the subsequently deposited ceramic thermal barrier coating 96. A ceramic thermal barrier coating 96 is then deposited onto the interface layer 94. In order to create the interface layer 94 on the surface of the bond coating 92 and to deposit the ceramic thermal barrier coating 96 onto the interface layer 94 the metallic substrate 90 with the deposited bond coating 92 is placed into the vacuum chamber 62. The vacuum chamber 62 is evacuated and an electrical bias, e.g. a D.C. potential or R.F. field, is applied to the metallic substrate 90 prior to the deposition of the columnar grained ceramic thermal barrier coating 96 in order to modify the structure and/or chemistry of the surface of the bond coating 92. Controlled amounts of gases are introduced into the interior of the vacuum chamber 62 during this phase of the process, for example argon-oxygen, argon-hydrogen or argon. The electrical bias produces chemically active glow discharges or plasmas in the case of argon-oxygen and argon-hydrogen, or produces neutral glow discharges or plasmas in the case of argon. The argon plasma may be used to produce argon ions which bombard the surface of the bond coating 92 to clean the surface i.e. to remove undesired oxides and/or any contaminants. The argon-hydrogen plasma may be used to provide enhanced cleaning of the surface of the bond coating 92 because the additional hydrogen ions chemically react with the undesired contaminants. When the surface of the bond coating 92 is cleaned of undesired oxides and/or contaminants the argon-oxygen plasma, or argon-hydrogen plasma, provides controlled production of desired bonding oxides in an interface 94 on the surface of the bond coating 92. The interface 94 improves the adhesion of the subsequently deposited ceramic thermal barrier coating 96. The gases used during the modification of the surface of the bond coating 92 to produce the interface layer 94 are then extracted from the vacuum chamber 62. The electron beam gun 66 directs electrons at the supply of ceramic vapour 68 to evaporate ceramic. The interior of the vacuum chamber 62 is supplied with controlled amounts of an inert gas and oxygen during the evaporation of the supply of ceramic vapour 68. The supply of inert gas, e.g. argon, is to maintain the correct glow discharge, or plasma, conditions and the supply of oxygen is to maintain the composition of the ceramic thermal barrier coating at the stoichiometric ratio. The ceramic vapour deposits onto the interface layer 94. In order to produce the layers 97 and 98 in the ceramic thermal barrier coating 96, the ceramic vapour is deposited alternately, for predetermined periods of time, by the physical vapour deposition process (PVD) and by a plasma assisted physical vapour deposition process (PAPVD). In the plasma assisted physical vapour deposition process (PAPVD) a D.C. or R.F. potential is applied to the metallic substrate 90. The first layer 97 of ceramic deposited onto the interface layer 94 is preferably deposited by plasma assisted physical vapour deposition (PAPVD) such that the ceramic at the interface with the interface layer 94 has a relatively high density and preferably has maximum density. The use of the plasma assisted physical vapour deposition process (PAPVD) is used to control the structure of the ceramic thermal barrier coating 96 all the way through its thickness, by controlling the way that the columnar ceramic grains 100 grow, to tailor the characteristics of the ceramic at particular positions. The plasma assisted physical vapour deposition process (PAPVD) causes the columnar ceramic grains 100 to be packed together more closely. The D.C. or R.F. potential used during the plasma assisted physical vapour deposition process (PAPVD) may be adjusted for deposition of different ceramic layers to control the density of the columnar ceramic grains 100. In region A of figure 11 an initial large voltage is applied to the metallic substrate 90 to modify the structure and/or chemistry of the surface of the bond coating 92. The magnitude of the initial large voltage is determined by the need to remove contaminants or undesirable oxides from the bond coating 92 prior to establishing the desired oxide structure-composition to achieve satisfactory adhesion of the thermal barrier coating 96. The desired oxide may be grown thermally or in the presence of a glow discharge. In order to achieve the maximum difference in thermal conductivity between adjacent layers 97,98 the interfaces 99 between the adjacent layers 97,98 are kept as abrupt as is practical. The abrupt interfaces 99 are preferably achieved by the use of a simple switching action as shown in region B of figure 11 between the physical vapour deposition process such that the voltage at the substrate follows a square wave form with time. The peak voltage in region B of figure 11 correspond to the time when the layers 97 of ceramic are deposited by PAPVD and the minimum voltages in region B of figure 11 correspond to the time when the layers 98 of ceramic are deposited by PVD. The switching points correspond to the time when the interfaces 99 are produced. The current drawn in the circuit as a function of substrate voltage is shown in figure 12, more current is drawn as the voltage increases. In order to sustain a glow discharge for the plasma assisted physical vapour deposition process, in this configuration for electron beam evaporation, the minimum voltages are of the order of three hundred volts as shown in figure 13 (with 10 mtorr = 1,33 Pa), and the current densities are typically greater than 0.1 mA/sq cm. This increases at any given pressure with applied substrate voltage. In another experiment the structurally modulated thermal barrier coating was produced by switching between a DC applied substrate bias, having a peak voltage of 2000 volts (negative), and ground. The time interval was 1 minute at each of the voltage levels and the pressure was 1,33 Pa (10 mtorr). Figure 14 is a scanning electron micrograph of a fracture cross-section through the thermal barrier coating. The continuous columnar grains can be seen extending through the full thickness of the thermal barrier coating and the modulated structure of the columns is evident. The outer portion of the coating was deposited purely in the PVD mode. The voltage applied to the substrate during the plasma assisted physical vapour depositions part of the process is sufficient to cause densification of the thermal barrier coating but is not sufficient to cause renucleation/grain growth within the structure with subsequent loss of the major, through thickness, columnar boundaries. The physical vapour deposition process described uses electron beam evaporation, however, other physical vapour deposition processes may be used for example sputtering or arc evaporation. Although the description has referred to physical vapour deposition to deposit the ceramic thermal barrier coating it may be equally possible to deposit the ceramic thermal barrier coating by chemical vapour deposition. The alternate layers may then be deposited using chemical vapour deposition and plasma assisted chemical vapour deposition. The thermal barrier coatings described in the examples are ceramic materials, however the thermal barrier coating may be any suitable material of low thermal conductivity. Materials suitable for use as thermal barrier coatings are generally oxides, for example zirconia, yttria, hafnia, ceria or combinations of any two or more thereof. The different layers in the thermal barrier coating are intended to have substantially the same composition, however the process of applying the thermal barrier coating may result in some compositional differences between the different layers. There appears to be an optimum spacing between the layers of ceramic for improved thermal conductivity when comparing the results of the third and fourth coating systems to the first coating system.

Claims: An article comprising a metallic substrate (90), a bond coating (92) on the metallic substrate (90), the bond coating (92) comprising a MCrAlY coating on the metallic substrate (90) and an interface layer (94), the interface layer (94) comprising alumina, a thermal barrier coating (96) on the interface layer (94), characterised in that the bond coating (92) includes an aluminide coating on the MCrAlY coating and the interface (94) is on the aluminide coating. An article as claimed in claim 1 characterised in that the aluminide coating is a platinum aluminide coating. An article comprising a metallic substrate (90), a bond coating (92) on the metallic substrate (90), the bond coating (92) comprising an aluminide coating on the metallic substrate (90) and an interface layer (94), the interface layer (94) comprising alumina, a thermal barrier coating (96) on the interface layer (94), characterised in that the bond coating (92) includes a platinum aluminide coating on the aluminide coating of the bond coating (92), and the interface layer (94) is on the platinum aluminide coating. An article as claimed in claim 1, claim 2 or claim 3 characterised in that the thermal barrier coating (96) has columnar grains (100). An article as claimed in claim 4 characterised in that columnar grains (100) have layers (97,98) with different structures. An article as claimed in any of claims 1 to 5 characterised in that the thermal barrier coating (96) comprises zirconia, yttria or a mixture thereof. An article as claimed in any of claims 1 to 6 characterised in that the metallic substrate (90) is a superalloy substrate. A method of manufacturing an article comprising applying a MCrAlY coating (92) to a metallic substrate (90), characterised by forming an aluminide coating on the MCrAlY coating (92), oxidising the aluminide coating to form an alumina interface layer (94) and depositing a thermal barrier coating (96) on the alumina interface layer (94). A method of manufacturing an article comprising applying a MCrAlY or an aluminide coating (92) to a metallic substrate (90), characterised by forming a platinum aluminide coating on the MCrAlY or aluminide coating (92), oxidising the platinum aluminide coating to form an alumina interface layer (94) and depositing a thermal barrier coating (96) on the alumina interface layer (94). An method as claimed in claim 8 or claim 9 characterised by depositing the thermal barrier coating (96) by vapour deposition. A method as claimed in claim 10 characterised by depositing the thermal barrier coating (96) by vapour deposition and plasma assisted vapour deposition. A method as claimed in any of claims 8 to 11 characterised by depositing the MCrAlY by vapour deposition. An method as claimed in claim 8 characterised by forming the aluminide coating by pack aluminising. A method as claimed in claim 9 characterised by forming the platinum aluminide coating by platinum aluminising. A method as claimed in any of claims 8 to 14 characterised by the metallic substrate being a superalloy substrate.

Inventors: RICKERBY DAVID STAFFORD, RICKERBY, DAVID STAFFORD
Applicants: ROLLS ROYCE PLC, ROLLS-ROYCE PLC
Application year: 1993
Main classification: C23C14
IPC codes: C23C14, C23C28, F01D5, C23C10