Abstract:
New oxide phosphors based on doped gallium oxides, alkaline earth gallates and germanates for electroluminescent display materials. Bright orange red electroluminescence has been obtained in amorphous and crystalline oxides Ga 2  O 3  :Eu for the first time. SrGa 2  O 4  and SrGa 4  O 9  doped with 1-8 mole % of Eu and Tb, CaGa 2  O 4 , Ca 3  Ga 2  O 6  and CaGa 4  O 7  doped with 1-4 mole % of Eu, Tb, Pr and Dy, BaGa 2  O 4  doped with 1-2 mole % of Eu and Tb, have been prepared using RF magnetron sputtering onto ceramic dielectric substrates and annealed at 600° C.-950° C. in air or Ar for 1-2 hours. Bright electroluminescent (EL) emission was obtained with wavelengths covering the visible spectrum from 400 to 700 nm, and infrared emission above 700 nm with spectral peaks characteristic of rare earth transitions. The films of CaGa 2  O 4  with 1 mole % Eu achieved 22 fL (75 cd/m 2 ) at 60 Hz and had a maximum efficiency of 0.2 lm/w for red emission. An amorphous thin film of Ca 3  Ga 2  O 6  with 2 mole % Eu achieved 34 fL in red EL at 60 Hz when annealed at 600° C. SrGa 2  O 4  with 1 mole % Eu and 4 mole % Tb yielded &#34;white&#34; phosphor having red, green and blue emission (13 fL at 60 Hz), and SrGa 2  O 4  with 8 mole % Tb resulted in a blue and green phosphor measuring 30 fL at 60 Hz. Zn 2  Si 0 .5 Ge 0 .5 O 4  containing Mn was sputtered using magnetron RF sputtering onto ceramic dielectric substrates and annealed at 700° C. for 1 hour in air or argon. Bright green (540 nm) emission was obtained in electroluminescence: 110 fL (377 cd/m 2 ) at 60 Hz with a maximum efficiency of 0.9 l/w. Moderately bright red emission (640 nm) was also obtained.

Description:
This application claims the benefits of U.S. Provisional Application 60/000,781, filed Jul. 5, 1996. 
     FIELD OF THE INVENTION 
     The present invention relates to new phosphor materials exhibiting electroluminescence based on gallium oxide and methods for their production. More particularly, the invention relates to rare earth doped amorphous and crystalline alkaline earth gallate phosphors and rare earth doped amorphous and crystalline gallium oxide and methods for making these materials. The present invention also relates to new doped germanium oxide, Zn 2  Si x  Ge 1-x  O 4  :Mn for use as electroluminescent display materials. 
     BACKGROUND OF THE INVENTION 
     Electroluminescence (EL) occurs by the emission of light from a phosphor in response to a sufficiently high electric field developed across the phosphor. Phosphor refers to those materials which emit light in response to the application of a field across the material. Thin film electroluminescent devices have a basic structure comprising a phosphor film or layer sandwiched between two electrodes. EL laminates are typically made by depositing the various layers onto a substrate such as quartz or glass, first a reflective metal layer onto the substrate onto which an insulating dielectric layer is deposited. The phosphor layer is then deposited onto the dielectric layer and then an optically transparent electrode, typically a transparent conducting oxide such as ITO is deposited onto the top surface of the phosphor layer. Application of an effective voltage between the two electrodes produces the electric field strength required to induce electroluminescence in the phosphor. The role of the dielectric layer is to reduce the voltage drop across the phosphor layer to avoid dielectric breakdown of the phosphor. 
     There is strong commercial interest to achieve the full spectral range in electroluminescent phosphors for visible display application and in particular for making colour flat panel displays. Sulphide phosphors are well known as efficient light emitters in electroluminescence as discussed in T. Inoguchi, M. Takeda, Y. Kakihara, Y. Nakata, M. Yoshida, SID&#39;74 Digest, p. 84-85, 1974. These include ZnS:Mn and SrS:Ce. A significant drawback to these phosphors is that they are moisture sensitive and are prone to reacting with oxygen especially when electrically driven. Known electroluminescent materials being studied include materials such as SrS:RE, see W. A. Barrow, R. E. Coovert, C. N. King, Digest 1984 SID International Symposium, Los Angeles, p. 249, SrGa 2  S 4  :RE and CaGa 2  S 4  :RE as disclosed in W. A. Barrow, R. C. Coovert, E. Dickey, C. N. King, C. Laakso, S. S. Sun, R. T Tuenge, R. Wentross, Digest 1993 SID International Symposium, Seattle, p. 761; W. Halverson, T. Parodos, P. Colter, Display Phosphors Conference, San Diego, Nov. 13-16, 1995, p. 115; S. S. Sun, E. Dickey, R. Tuenge, R. Wentross, Display Phosphors Conference, San Diego, Nov. 13-16, 1995, p. 119; T. Yang, M. Chaichimansour, W. Park, B. K. Wagner, C. J. Summers, Display Phosphors Conference, San Diego, Nov. 13-16, 1995, p. 123; and T. S. Moss, D. C. Smith, J. A. Samuels, R. C. Dye, Display Phosphors Conference, San Diego, Nov. 13-16, 1995, p. 127. While these materials do achieve red, green and blue emission, the gallium based sulphides suffer from low brightness, difficulty of preparation and stability problems. 
     It has recently been demonstrated that in the gallate based family of materials, ZnGa 2  O 4  :Mn could achieve bright and stable electroluminescence, see T. Minami, S. Takata, Y. Kuroi, T. Maeno, Digest 1995 SID International Symposium, Orlando, p. 724; and T. Minami, Y. Kuroi, S. Takata, Display Phosphors Conference, San Diego, Nov. 13-16, 1995, p. 91. They obtained good green emission (200 cd/m 2  at 60 Hz at up to 0.9 lm/w) but only obtained 0.5 cd/m 2  blue, and 11.0 cd/m 2  red at a drive frequency of 1000 Hz, which are not practical brightness values for a display by replacing Mn with Ce and Eu, respectively. They annealed these phosphor materials at 1020° C. in argon. 
     More recently, Minami et al. have doped ZnGa 2  O 4  with chromium to generate a better red phosphor, claiming 120 cd/m 2  at 1000 Hz, as disclosed in T. Minami, Y. Kuroi, S. Takata, T. Miyata, presented at Asia Display &#39;95, October 16-18, Hamamatsu. However it is not feasible, to achieve full colour in ZnGa 2  O 4  since rare earths are not compatible with this host lattice due to the size mismatch between Zn or Ga and the rare earth ions. 
     In the binary gallium oxide based system, β-Ga 2  O 3  has the θ-alumina type structure with two different Ga sites, one in tetrahedral coordination and the other in octahedral coordination. High temperature heat treated β-Ga 2  O 3  is known to exhibit bright broad-band photoluminescence under 254 nm UV irradiation and cathodoluminescence between 340 and 650 nm as disclosed in W. C. Herbert, H. B. Minnier and J. J. Brown, Jr., J. Electrochem. Soc. vol. 116, pp. 1019-1021 (1969). β-Ga 2  O 3  :Cr, the gallium analog of ruby, has been studied as a potential red to infrared tunable laser material because of the broad-band emission between 650 and 950 nm that is associated with the  4  T 2  - 4  A 2  transition of the Cr 3+  ion in the octahedral site, see for example H. H. Tippins, Phys. Rev. vol. 137, pp. A865-A871 (1965), and D. Vivien, B. Viana, A. Revcolevschi, J. D. Barde, B. Dunn, P. Nelson and O. M. Stafsudd, J. Lum. vol. 39, pp. 29-33 (1987). 
     Even though there exists a significant difference in ionic radii of the rare earth ions and Ga 3+ , Ga 2  O 3  :Dy was reported to be a reasonably efficient photoluminescent phosphor with characteristic narrow Dy 3+  lines in the blue (470-500 nm) and the yellow (570-600 nm) regions, see W. C. Herbert, H. B. Minnier and J. J. Brown, J. Electrochem. Soc. vol. 115, pp. 104-105 (1968). Other common rare earth dopants such as Eu 3+  and Tb 3+ , however, did not show efficient PL emission in β-Ga 2  O 3 , see J. L. Sommerdijk and A. Bril, J. Electrochem. Soc. vol 122, pp. 952-954 (1975). Sommerdijk also disclosed the solubility of Dy 3+  in β-Ga 2  O 3  to be only about 1%. W. C. Herbert, H. B. Minnier and J. J. Brown, J. Electrochem. Soc. vol. 115, pp. 104-105 (1968) disclosed that maximum PL brightness occurred in the range of 5-10% (mole percent) Dy concentration. The mechanism of the rare earth activation is still not clear. 
     Recently it has been demonstrated that Zn 2  SiO 4  :Mn could achieve electroluminescence, see T. Miyata, T. Minami, Y. Honda and S. Takata, SID &#39;91 Digest, p. 286-289, 1991. Thin films were RF magnetron sputtered onto polished BATiO 3  substrates using the method disclosed in T. Minami, T. Miyata, S. Takata, I. Fukuda, SID&#39;92 Digest, p. 162. A good brightness of 200 cd/m 2  was achieved at 60 Hz with an efficiency of 0.8 lm/W. A drawback to these films is that they had to be annealed at 1000° C. for several hours, which severely limits their applicability to practical substrates for displays. 
     As mentioned above, a major drawback to known electroluminescent materials is the need for post fabrication high temperature annealing (in the vicinity of 1000° C.) of the films to produce electroluminescent behaviour. This need for high temperature treatment results in severe restrictions in the choice of substrates with only a limited number being available for use under these conditions. High temperature annealing also increases the cost of producing EL films rapidly on a large scale. Another limitation of many electroluminescent materials is that they are restricted to emitting at particular wavelengths or in a relatively narrow wavelength range, such as yellow ZnS:Mn or blue-green SrS:Ce which are not ideal for color displays that requires emission in the red, green and blue parts of the visible spectrum. Electroluminescent materials based on sulphides inherently suffer from chemical stability problems such as oxide formation (since oxides are generally thermodynamically more stable than sulphides) which changes the electronic properties of the material over time. 
     The classic EL phosphor, ZnS:Mn, is yellow and has a peak wavelength of 580 nm. However, while it may be filtered red and green, most of the light is lost because only ≦10% of the light is passed through the red and green filters. Similarly, a drawback of SrS:Ce, which is green-blue, is that only about 10% of the light is passed through a blue filter. 
     In the rare-earth doped oxides, narrow peaks that are red, green or blue result from dopants Eu +3  or Tb +3  so that little or no light is generated at wavelengths that are positioned in the visible spectrum away from the desired red, green and blue wavelengths. 
     It would therefore be very advantageous to provide a method of producing new electroluminescent materials which can be deposited at temperatures well below 1000° C. thereby avoiding the requirement for high temperature annealing. It would also be advantageous to provide new electroluminescent materials which emit over a broader portion of the visible spectrum than known EL materials. More specifically it would be very advantageous to provide a white phosphor, and phosphors with red, green and blue emission. 
     It would also be advantageous to provide a method of producing new EL materials that are chemically stable and do not react appreciably with water or oxygen and provide stable EL performance in which the brightness is maintained substantially constant during operation. Known color phosphors such as SrS:Ce and other sulphides are not stable in these respects. 
     SUMMARY OF THE INVENTION 
     It is an object of the present invention to provide new electroluminescent materials based on oxides of gallium and germanium which exhibit electroluminescent behaviour over the visible portion of the electromagnetic spectrum useful in color electroluminescent flat panel displays. It is also an object of the present invention to provide a method of producing these new films which does not require post production high temperature annealing of the films in order to achieve electroluminescent behaviour. 
     A significant commercial advantage of the present invention is that several new germanium and gallium oxide based electroluminescent materials have been produced onto substrates at low temperatures and excellent electroluminescent behaviour has been obtained without the need for high temperature annealing as is common in other known systems. As deposited films of Ga 2  O 3  :Eu and films of Ca 3  Ga 2  O 6  :Eu and Zn 2  GeO 4  :Mn annealed at temperatures as low as 600° C. exhibit excellent electroluminescent properties. Therefore a very significant advantage of the present invention is that the new electroluminescent materials can be deposited onto a wide variety of substrates not normally useable as substrates for EL materials with those known oxide EL materials requiring high temperature annealing to produce electroluminescence. 
     Another commercially significant advantage of the present invention is that it provides new electroluminescent materials characterized as green, red and white phosphors which exhibit electroluminescence over the visible spectrum raffler than emissions centred around a specific wavelength region, such as the yellow regions alone. 
     The inventors report for the first time electroluminescence of amorphous and crystalline Eu-doped gallium oxide, Ga 2  O 3  :Eu, and other related systems. In one aspect of the present invention, there is provided films of doped amorphous and crystalline gallium oxides, Ga 2  O 3  :Eu and Ga 2  O 3  :Eu,Cd exhibiting bright orange red electroluminescence. 
     The present invention also provides new gallate based oxides such as CaGa 2  O 4 , SrGa 2  O 4  and BaGa 2  O 4  which have been prepared in such a way as to exhibit superior electroluminescent properties including EL efficiencies and brightnesses. The invention also provides other calcium and strontium gallates such as Ca 3  Ga 2  O 6 , CaGa 4  O 7  and Sr 3  Ga 4  O 9  which are also found to exhibit excellent EL. The structures of SrGa 2  O 4  and BaGa 2  O 4  are stuffed tridymite and that of CaGa 2  O 4  is orthorhombic. The other two calcium gallates, Ca 3  Ga 2  O 6  and CaGa 4  O 7 , crystallize in orthorhombic and monoclinic forms, respectively. Rare earth dopants are generally soluble in Sr, Ca and Ba compounds. 
     The present invention also provides a method for producing new electroluminescent zinc silicate-germanate films at lower annealing temperatures thereby permitting the use of more practical substrates. In this aspect of the invention there is provided a method of producing electroluminescent films at temperatures in the vicinity of 700° C. The process comprises replacing Si by Ge in Zn 2  SiO 4  :Mn films to produce films of Zn 2  Si x  Ge 1-x  O 4  :Mn exhibiting electroluminescent where x is in the range from about 0 to about 1.0. 
     In one aspect of the invention there is provided a new phosphor having the formula Ga 2  O 3  :n%RE, wherein RE is a rare earth dopant selected from the group consisting of Fu and Dy, n % is the mole percent of RE present in Ga 2  O 3  and spans the range in which the rare earth is soluble in Ga 2  O 3 , the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     The invention provides a phosphor having the formula Ga 2  O 3  :n%Eu,Cd, wherein n % is the mole percent of a combined amount of Eu and Cd present in Ga 2  O 3  and spans the range in which the combined amount of Eu and Cd are soluble in Ga 2  O 3 , the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     The invention also provides a phosphor having the formula SrGa 2  O 4  :n%RE wherein RE is a rare earth dopant selected from the group consisting of Eu, Tb and combinations thereof, n % is the mole percent of RE present in SrGa 2  O 4 , and spans the range in which the rare earths are soluble in SrGa 2  O 4 , the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     In another aspect of the invention there is provided a phosphor having the formula CaGa 2  O 4  :n%RE wherein RE is a rare earth dopant selected from the group consisting of Eu, Tb, Pr and combinations thereof, n % is the mole percent of RE present in CaGa 2  O 4 , and spans the range in which the rare earths are soluble in CaGa 2  O 4 , the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     The invention also provides a phosphor having the formula BaGa 2  O 4  :n%RE wherein RE is a rare earth dopant selected from the group consisting of Eu and Tb and combinations thereof, n % is the mole percent of RE present in BaGa 2  O 4 , and spans the range in which the rare earths are soluble in BaGa 2  O 4 , the phosphor characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     The invention also provides a phosphor having the formula Ca 3  Ga 2  O 6  :n%RE wherein RE is a rare earth dopant selected from the group consisting of Eu and Tb and combinations thereof, n % is the mole percent of RE present in Ca 3  Ga 2  O 6 , and spans the range in which these rare earths are soluble in Ca 3  Ga 2  O 6 , the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     In another aspect of the invention there is provided a phosphor having the formula CaGa 4  O 7  :n%RE wherein RE is a rare earth dopant selected from the group consisting of Eu, Dy, Tb and combinations thereof, n % is the mole percent of RE present in CaGa 4  O 2 , and spans the range in which the rare earths are soluble in CaGa 4  O 7 , the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
     In another aspect of the invention there is provided a phosphor having the formula Zn 2  Si x  Ge 1-x  O 4  :n%Mn, wherein n % is the mole percent of Mn and spans the range in which Mn is soluble in Zn 2  Si x  Ge 1-x  O 4 , and x varies in the range from about 0 to about 1.0, the phosphor being characterized by electroluminescence when an effective voltage is applied across the phosphor. 
    
    
     BRIEF DESCRIPTION OF THE DRAWINGS 
     The new phosphor materials exhibiting electroluminescent behaviour forming the present invention will now be described, by way of example only, reference being had to the accompanying drawings, in which: 
     FIG. 1 is a side view of an EL device structure using a commercial barium titanate substrate produced by AVX Corp.; 
     FIG. 2 is a plot of brightness versus applied voltage of several thin films (8000 Å) of Ga 2  O 3  :2% Eu each annealed at the temperature indicated for one hour; 
     FIG. 3 is a plot of the voltage dependancy of the electroluminescence efficiency for the thin film samples of FIG. 2; 
     FIG. 4 illustrates the x-ray diffraction patterns of Ga 2  O 3  :1%Eu thin films deposited on Si and annealed at the different temperatures shown; 
     FIG. 5 compares the electroluminescence spectra of Ga 2  O 3  :2% Eu thin films annealed at the indicated temperatures; 
     FIG. 6 is a plot of the voltage dependence of both the efficiency and brightness of a device fabricated from Ga 2  O 3  :2% Eu sputtered in a gas mixture of 5% O 2  and 5% N 2  in argon (Ar), followed by annealing in Ar at 950° C. for 1 hour; 
     FIG. 7 is a plot the EL spectra for two Ga 2  O 3  :1%Dy films annealed at the indicated temperatures for 1 hour illustrating the presence of deep red emissions similar to the samples of FIG. 5, attributed to to the emission of the β-Ga 2  O 3  host lattice; 
     FIG. 8 shows the X-ray diffraction patterns of thin films sputtered from a CdGa 2  O 4  :0.5%Eu target and annealed at the indicated temperatures for one hour; 
     FIG. 9 shows the electroluminescent brightness and efficiency for Ga 2  O 3  :0.5%Eu,Cd thin films annealed at 800° C. for one hour; 
     FIG. 10 compares the electroluminescent spectra (intensity versus wavelength) for Ga 2  O 3  :0.5%Eu,Cd and Ga 2  O 3  :2%Eu; 
     FIG. 11 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL device formed by sputtering a thin film from Ca 0 .99 Eu 0 .01 Ga 2  O 4  onto an AVX substrate and annealed at 950° C. for one hour in air; 
     FIG. 12 shows the EL emission spectra for two phosphor films, both sputtered from Ca 0 .99 Eu 0 .01 Ga 2  O 4  with each annealed according to the indicated conditions; 
     FIG. 13 is a plot of brightness and efficiency versus voltage at 60 Hz for EL phosphor films sputtered from Ca 0 .96 Tb 0 .04 Ga 2  O 4  on an AVX substrate with each film annealed under the indicated conditions; 
     FIG. 14 shows the EL emission spectra for the films of FIG. 13; 
     FIG. 15 shows the EL emission spectra for a phosphor film sputtered from Ca 0 .96 Tb 0 .02 Pr 0 .02 Ga 2  O 4  onto an AVX substrate annealed as indicated; 
     FIG. 16 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Ca 0 .98 Tb 0 .01 Eu 0 .01 Ga 2  O 4  onto an AVX substrate annealed under the indicated condition; 
     FIG. 17 shows the EL emission spectrum for the thin film of FIG. 16; 
     FIG. 18 shows the EL emission spectrum for an EL phosphor film sputtered from Sr 0 .99 Eu 0 .01 Ga 2  O 4  under the indicated annealing condition; 
     FIG. 19 is a plot of brightness and efficiency versus voltage at 60 Hz for EL phosphor films sputtered from Sr 0 .92 Tb 0 .06 Ga 2  O 4  and Sr 0 .96 Tb 0 .04 Ga 2  O 4  on AVX substrates annealed under the indicated conditions; 
     FIG. 20 shows the EL emission spectra for a phosphor film sputtered from Sr 0 .96 Tb 0 .04 Ga 2  O 4  and annealed under the given conditions; 
     FIG. 21 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Sr 0 .95 Tb 0 .04 Eu 0 .01 Ga 2  O 4  onto an AVX substrate annealed under the indicated condition; 
     FIG. 22 shows the EL emission spectrum for the phosphor film of FIG. 21; 
     FIG. 23 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Ba 0 .99 Eu 0 .01 Ga 2  O 4  onto an AVX substrate annealed under the indicated condition; 
     FIG. 24 shows the EL emission spectrum for the phosphor film of FIG. 23; 
     FIG. 25 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Ba 0 .98 Tb 0 .02 Ga 2  O 4  onto an AVX substrate annealed under the indicated condition; 
     FIG. 26 shows the EL emission spectrum for the thin film of FIG. 25; 
     FIG. 27 is a plot of brightness and efficiency versus voltage at 60 Hz for EL phosphor films sputtered from Ca 2 .94 Eu 0 .06 Ga 2  O 6  onto AVX substrates and annealed under the indicated conditions; 
     FIG. 28 shows the EL emission spectra for the phosphor films of FIG. 27; 
     FIG. 29 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Ca 0 .99 Eu 0 .01 Ga 4  O 7  onto an AVX substrate and annealed under the indicated condition; 
     FIG. 30 shows the EL emission spectrum for the phosphor film of FIG. 29; 
     FIG. 31 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Ca 0 .99 Tb 0 .01 Ga 4  O 7  onto an AVX substrate and annealed under the indicated condition; 
     FIG. 32 shows the EL emission spectrum for the phosphor film of FIG. 31; 
     FIG. 33 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Ca 0 .985 Dy 0 .015 Ga 4  O 7  onto an AVX substrate and annealed under the indicated condition; 
     FIG. 34 shows the EL emission spectrum for the phosphor film of FIG. 33; 
     FIG. 35 is a plot of brightness and efficiency versus voltage at 60 Hz for an EL phosphor film sputtered from Sr 2 .68 T 0 .12 Ga 4  O 9  and annealed under the given condition; 
     FIG. 36 shows the EL emission spectrum of the phosphor film of FIG. 35; 
     FIG. 37 compares the x-ray diffraction patterns for EL phosphor films sputtered from Ca 0 .99 Eu 0 .01 Ga 2  O 4  onto AVX substrates and annealed at 700° C., 850° C. and 950° C. for 1 hour; 
     FIG. 38 compares the x-ray diffraction patterns for thin films sputtered from Sr 0 .99 Eu 0 .01 Ga 2  O 4  onto BaTiO 3  and annealed at 700° C., 800° C. and 950° C. for 1 hour; 
     FIG. 39 compares the x-ray diffraction patterns for thin films sputtered from Ca 2 .94 Eu 0 .06 Ga 2  O 8  onto AVX substrates and annealed at 700° C., 750° C., 800° C. and 950° C. for 1 hour; 
     FIG. 40 compares the x-ray diffraction patterns for films sputtered from Ca 0 .99 Eu 0 .01 Ga 4  O 7  onto AVX substrates and annealed at various temperatures for 1 hour, indicating the crystallization temperature for the compound is between 800° C. and 850° C.; 
     FIG. 41 is a plot of brightness and efficiency versus applied voltage at 60 Hz for a green emitting EL phosphor film sputtered from Zn 1 .96 Mn 0 .04 Si 0 .5 Ge 0 .5 O 4  onto a Sherritt substrate and annealed under the given condition; 
     FIG. 42 is a plot of brightness versus applied voltage at 60 Hz for a red emitting EL phosphor film sputtered from Zn 1 .96 Mn 0 .04 Si 0 .5 Ge 0 .5 O 4  with no annealing; 
     FIG. 43 compares the emission spectra of two EL films sputtered from Zn 1 .96 Mn 0 .04 Si 0 .5 Ge 0 .5 O 4 , one of the films being annealed and the other not annealed; 
     FIG. 44 is a plot of brightness and EL efficiency versus applied voltage at 60 Hz for an EL phosphor film sputtered from Zn 1 .96 Mn 0 .04 GeO 4  onto a Sherritt substrate and annealed under the indicated condition; and 
     FIG. 45 is a plot of operating voltage necessary to maintain a brightness of 12 fL in Ga 2  O 3  :2%Eu as a function of time, and the brightness as a function of operating time at 60 Hz and 400 Hz drive for an EL phosphor film sputtered from Sr 0 .96 Tb 0 .002 Ga 2  O 4  onto an AVX substrate with fixed voltages as shown. 
    
    
     DETAILED DESCRIPTION OF THE INVENTION 
     As used herein, the term phosphor refers to substances which exhibit electroluminescence when a suitable or effective electric field is developed across the phosphor. The various elements used in the production of the new EL oxide based materials disclosed herein include gallium (Ga), germanium (Ge), silicon (Si), manganese (Mn), zinc (Zn), europium (Eu), terbium (Tb), cerium (Ce), dysprosium (Dy), cadmium (Cd), strontium (Sr), barium (Ba), calcium (Ca) and praseodymium (Pr). 
     A) NEW DOPED GALLIUM OXIDES EXHIBITING ELECTROLUMINESCENT BEHAVIOUR 
     Film Preparation 
     Target materials were intimate mixtures of Ga 2  O 3  (Alfa Aesar, 99.999%) and appropriate amounts of rare earth (RE) oxide dopants. For the Ga 2  O 3  :(0.01 to 15% RE) where RE is Eu, Dy or mixtures thereof, powder mixtures of the Ga 2  O 3  with the appropriate dopant oxide(s) in the desired ratio were ground together in a mortar. Thin films were deposited on polished AVX BaTiO 3  substrates by RF magnetron sputtering using the mixed powder targets. All substrates are a BaTiO 3  -based ferroelectric ceramic made by green sheet processing (AVX Corp). 
     Referring to FIG. 1, a multi-layer thick film stack was manufactured to incorporate a BaTiO 3  underlayer 12, a screen-printed metal electrode 14 and finally a BaTiO 3  layer 16, 40 μm thick on the surface of electrode 14. Impurities that are commonly incorporated in the BaTiO 3  in industry allow the substrates to have the desired dielectric constant (ε r  =9000), temperature dependence and other properties. The phosphor layer 18 was deposited by sputtering which was effected with a 2&#34; US gun at a substrate temperature between 200°-250° C. in an atmosphere of 10% O 2  in argon and a pressure of 10 mTorr unless otherwise noted. The substrate holder was rotated in a planetary motion and the film thickness variation was less than 10%. Typical phosphor film thickness was 4000-8000 Å. The sputter deposited thin films were either annealed in air at 600° C. to 950° C. for one hour or not annealed. A transparent indium tin oxide (ITO) top electrode layer 20 of 2000 Å was also deposited by sputtering. The EL brightness was measured with a Minolta LS-100 luminance meter. EL efficiencies were measured by the Sawyer-Tower method. Emission spectra were taken with a computer-controlled SPEX 340E spectrometer. 
     Results 
     1. Ga 2  O 3  :Eu 
     Bright orange red electroluminescence (EL) characteristic of the Eu 3+  emission was obtained. Brightness-Voltage (B-V) curves of devices made from thin films with nominal compositions Ga 2  O 3  :2%Eu at a thickness of 8000 Å are shown in FIG. 2. The corresponding efficiencies for these films are shown in FIG. 3. The results clearly indicate that the threshold voltage, V th , increases with increasing annealing temperature. Except for the as-deposited thin films, the brightness and efficiency increase with decreasing annealing temperature as well. The optimum annealing temperature appears to be lower than 700° C. 
     X-ray diffraction patterns of Ga 2  O 3  :1%Eu thin films deposited on Si and annealed at various temperatures are shown in FIG. 4. Even with 800° C. annealing the thin film was still poorly crystallized. Below 700° C. the thin film was essentially amorphous. It was not well crystallized until annealed at about 1000° C. These results suggest that there is no obvious correlation between the EL properties and the crystallinity of the thin films. 
     The EL spectra of Ga 2  O 3  :2%Eu thin films annealed at various temperatures are compared in FIG. 5. There is very little difference in the line shape as well as the line width, indicating again that the emission of Eu 3+  is very much independent of the host lattice. To the inventors&#39; knowledge this surprising behavior has never been reported before. ZnS:Tb is a well-known example of an efficient EL (green) phosphor with a size-mismatched dopant, but good crystallinity is known to be important in the generation of EL in ZnS-related phosphors. 
     The notable increase in the emission intensity above 700 nm at annealing temperatures higher than 700° C. appears to be correlated to the crystallinity of the thin film of host material Ga 2  O 3 . As will be shown later, this emission is due to the β-Ga 2  O 3  host alone. 
     The B-V curves in FIG. 2 show that devices with as-deposited and low temperature annealed thin phosphor films have large clamp voltages, or slow rise in brightness near the threshold. As shown in FIG. 6, a device with Ga 2  O 3  :1%Eu thin film sputtered in a gas mixture of 5% O 2  and 5% N 2  in argon, followed by annealing in argon at 950° C. for 1 hour, appears to have a sharper turn-on. The use of a ZnGa 2  O 4  buffer layer (˜1000 Å) between the BaTiO 3  substrate and the phosphor layer appears to increase the sharpness of the B-V curve as well, data not shown. 
     2. Ga 2  O 3  :M (M=Cr, Ce, Dy) 
     Even though Cr 3+  is an ideal dopant for the β-Ga 2  O 3  host in terms of charge and size, there is essentially no EL emission observed due to Cr 3+ . The EL spectrum of Ga 2  O 3  :1%Cr is the same as that of Ga 2  O 3  :1%Ce, which was sputtered in an atmosphere of 5% N 2  and 5% O 2  in argon and annealed at 950° C. in argon. A deep red and near infrared emission in both cases has also been observed for Ga 2  O 3  :Eu as well as in Ga 2  O 3  :1%Dy, see FIG. 7, and is thus clearly due to the emission of the β-Ga 2  O 3  host lattice. It is worth noting that a similar red emission in the room temperature photoluminescence spectrum of Ga 2  O 3  :Cr was attributed to the  4  T 2  - 4  A 2  transition of the Cr 3+ . However, characteristic Cr 3+  emission, especially the sharp R1 (690 nm) and R2 (697 nm) lines reported in the fluorescence spectrum of Ga 2  O 3  :Cr (see L. P. Sosman, T. Abritta, O. Nakamura and M. M. F. D&#39;Aguiar Neto, J. Mater. Sci. Lett., Vol. 14, pp. 19-20, (1995)) was absent in the EL spectrum. The lack of Ce 3+  emission was very likely due to the existence of stable Ce 4+  instead of the desired Ce 3+ . The Dy 3+  emission appeared as two broad bands at ˜490 and 580 nm, in contrast with its photoluminescent emission spectrum of powder specimens where complicated fine structures have been observed even at room temperature. 
     The EL of Ga 2  O 3  :Dy is much weaker than Ga 2  O 3  :Eu. It is interesting to note that, even with a small concentration (0.5% mole percent) of codoping with europium, a sharp threshold behaviour can be observed which was absent in all devices without europium. In fact, efficient EL has been obtained only in Eu-doped Ga 2  O 3 . These results suggest that europium is playing a very significant role in the charge injection of these EL devices, probably through the ionization of Eu 2+ , which could exist partially in Ga 2  O 3  :Eu. 
     3. Ga 2  O 3  :Eu,Cd 
     X-ray diffraction patterns of thin films sputtered from a CdGa 2  O 4  :Eu target and annealed at various temperatures are shown in FIG. 8. The thin films were also amorphous when annealed below 700° C. in air. No spinel CdGa 2  O 4  phase was observed in the high temperature-annealed thin films. The only phase that could be detected was β-Ga 2  O 3 . Thus cadmium existed in the thin film only as a dopant, very likely due to the decomposition of CdO. The XRD patterns in FIG. 8 strongly suggest that the Cd-doped Ga 2  O 3  :0.5%Eu,Cd thin films crystallize more easily than Ga 2  O 3  :1%Eu when compared with those in FIG. 4. 
     Bright EL was also obtained with Ga 2  O 3  :0.5%Eu,Cd thin films. The brightness and efficiency data for Ga 2  O 3  :0.5%Eu,Cd thin films annealed at 800° C. for one hour in air are shown in FIG. 9. There exists an obvious difference in the EL spectra of Ga 2  O 3  :0.5%Eu,Cd and Ga 2  O 3  :2%Eu as shown in FIG. 10. The relative intensities of peaks at about 580, 655 and 700 nm were substantially weaker for Ga 2  O 3  :0.5%Eu,Cd. These results strongly suggest the existence of cadmium in the thin films although the amount of Cd is not known. 
     The ionic radii of Cd 2+  and Eu 3+  are both too great for a simple substitution of the Ga 3+  ion. The significant change in the emission spectra with Cd 2+  codoping probably suggest a very complex association of the Eu 3+  ion with the host lattice that is sensitive to the existence of other impurities like cadmium. Referring to FIG. 9, it is worth noting that the luminescence levels of the best Ga 2  O 3  :0.5%Eu,Cd films are comparable with those of Ga 2  O 3  :2%Eu even though the Eu 3+  concentration is much lower in the former. The effects of cadmium doping and the activator (Eu 3+ ) concentration on the EL properties are worthy of further investigations. 
     B) NEW DOPED ALKALINE EARTH GALLATE PHOSPHORS EXHIBITING ELECTROLUMINESCENCE 
     Film Preparation 
     Commercial high purity SrCO 3  (99%), BaCO 3  (99.95%), Ga 2  O 3  (99.999%) (from Alfa-Aesar), CaO (99.9%) (Aldrich), Tb 4  O 7  (99.99%), Eu 2  O 3  (99.9%), Pr 8  O 11  (99.99%) and Dy 2  O 3  (99.99%) from Rhone-Poulenc, powders were mixed in appropriate ratios and fired at 1000° C. to 1300° C. in air for 12 to 24 hours to form the desired phosphor powder. The compositions of the typical phosphor compounds and their firing conditions are listed in Table 1. The phosphor powders were then pressed and placed in a 2-inch RF magnetron gun (US gun). 
     An AVX ceramic substrate, as shown in FIG. 1, was placed 4 cm above the gun. Sputtering was carried out at a gas pressure of 20 mtorr to grow thin films measuring 4000 Å to 9000 Å in thickness. Except otherwise indicated, the sputtering atmosphere usually consists of 5% O 2  and 95% Ar. It is worth noting that 5-10% N 2  gas has also been used when sputtering some Tb-doped phosphors, where nitrogen acts as an effective charge compensator and significantly improves the EL brightness of the resulting film. The thin films were annealed at between 600° C. and 950° C. for 1 hour in air or Ar depending on the phosphors, and a layer of ITO (indium tin oxide) of ˜2000 Å was grown by RF magnetron sputtering to form a transparent top electrode. The completed device structures are shown in FIG. 1. 
     1) CaGa 2  O 4  :RE Phosphors 
     The Eu doped materials were prepared with about 1% Eu and were sputtered in a mixture of 5% O 2  in Ar. The EL brightness and efficiency versus voltage curves at 60 Hz for Ca 0 .99 Eu 0 .01 Ga 2  O 4  phosphor post-annealed at 950° C. for one hour in air is shown in FIG. 11 and the EL emission spectra for two films post annealed at 950° C. and 700° C. are shown in FIG. 12. 
     Tb doped materials were prepared with between about 0.1% to about 4% Tb. The EL performance at 60 Hz for Ca 0 .96 Tb 0 .04 Ga 2  O 4  sputtered in 5% O 2 , 10% N 2  and 85% Ar atmosphere and post-annealed at 950° C. for 1 hour in air or Ar, are shown in FIG. 13 and the corresponding EL emission spectra are shown in FIG. 14. It is worth noting that post-annealing in Ar significantly improves the EL brightness as well as the relative intensity of the blue peak situated at 490 nm ( 5  D 3  → 7  F 1 ,0 and  5  D 4  → 7  F 6  transitions), which makes the overall emission look bluer. 
     The Tb and Pr doped materials were prepared with about 4% (Tb+Pr) and were sputtered in a mixture comprising Ar:N 2  :O 2  in the ratio of 17:2:1 or Ar:O 2  in the ratio of 19:1. The EL emission spectrum for Ca 0 .96 Tb 0 .02 Pr 0 .02 Ga 2  O 4  post-annealed at 850° C. for 1 hour in air is shown in FIG. 15. 
     The Tb and Eu doped materials were prepared with about 2% (Tb+Eu) and were sputtered in a mixture comprising Ar:N 2  :O 2  in the ratio of 17:2:1. The EL performance and emission spectrum for Ca 0 .96 Tb 0 .01 Eu 0 .01 Ga 2  O 4  sputtered in 5% O 2 , 10% N 2  and 85% Ar atmosphere and post-annealed at 950° C. for 1 hour in Ar are shown in FIGS. 16 and 17 respectively. It is to be noted that red, green and blue peaks appear in the spectrum so that this new material is considered a white phosphor. 
     2) SrGa 2  O 4  :RE Phosphors 
     The Eu doped materials were prepared with about 1% Eu and were sputtered in an Ar:O 2  mixture of 19:1. For Sr 0 .99 Eu 0 .01 Ga 2  O 4  annealed at 950° C. for 1 hour in air the EL emission spectrum is shown in FIG. 18. 
     The Tb doped materials were prepared with about 2% to 12% Tb and were sputtered in pure argon (Ar). The brightness and efficiency data for Sr 0 .92 Tb 0 .08 Ga 2  O 4  and Sr 0 .96 Tb 0 .04 Ga 2  O 4  are shown in FIG. 19. The EL spectra for Sr 0 .96 Tb 0 .04 Ga 2  O 4  post-annealed in Ar are shown in FIG. 20. It is worth noting that higher annealing temperature significantly enhances the emission peaks at 490 nm ( 5  D 3  → 7  F 1 ,0 and  5  D 4  → 7  F 6  transitions), 438 nm ( 5  D 3  → F   4  transition), 441 nm ( 5  D 3  → 7  F 4  transition) and 418 nm ( 5  D 3  → 7  F 5 ), which makes the overall emission colour look bluer as shown in FIG. 20. 
     The Tb and Eu doped materials were prepared with about 5% (Eu+Tb) and were sputtered in an Ar:O 2  mixture of 19:1. The EL performance and emission spectrum for Sr 0 .95 Tb 0 .04 Eu 0 .01 Ga 2  O 4  post-annealed at 950° for 1 hour in air are shown in FIGS. 21 and 22 respectively. It is to be noted that this provides a white phosphor containing red, green and blue peaks. 
     3) BaGa 2  O 4  :RE Phosphors 
     The films were produced by sputtering in an Ar:O 2  mixture of 19:1 and annealing in the range of 700° C. to 950° C. in air. The EL performance at 60 Hz for Ba 0 .99 Eu 0 .01 Ga 2  O 4  post-annealed at 850° C. for 1 hour is shown in FIG. 23. The corresponding EL emission spectrum is shown in FIG. 24. 
     The EL performance and emission spectrum for Ba 0 .96 Tb 0 .02 Ga 2  O 4  sputtered in 5% O 2 , 5% N 2  and 90% Ar atmosphere and post-annealed at 950° C. for 1 hour in Ar are shown in FIGS. 25 and 26 respectively. 
     4) Ca 3  Ga 2  O 6  :RE Phosphors 
     The Eu doped materials were prepared with about 2% Eu and were sputtered in an Ar:O 2  mixture of 19:1. The EL performances at 60 Hz for Ca 2 .94 Eu 0 .06 Ga 2  O 6  post-annealed at 600° C., 750° C. and 850° C. for 1 hour in air are shown in FIG. 27. The corresponding EL emission spectra are shown in FIG. 28. It is worth noting that the EL performance is the best for the amorphous Ca 2 .94 Eu 0 .06 Ga 2  O 6  thin film, which is annealed at 600° C. in air for one hour. 
     The Tb doped materials were prepared about 2% Tb and were sputtered in an Ar:O 2  mixture of 19:1. The EL of Ca 2 .94 Tb 0 .06 Ga 2  O 6  was weak with a maximum brightness of 3 fL. at 60 Hz. 
     5) CaGa 4  O 7  :RE Phosphors 
     The Eu doped materials were prepared with about 1% Eu and were sputtered in an Ar:O 2  mixture of 9:1. The EL performance at 60 Hz for the specified Ca 0 .99 Eu 0 .01 Ga 4  O 7  film sputtered in 10% O 2  --90% Ar and post-annealed at 950° C. for 1 hour in air is shown in FIG. 29 and the EL emission spectrum is shown in FIG. 30. 
     The Tb doped materials were prepared with about 1% Tb. The EL performance and emission spectrum for the specified Ca 0 .99 Tb 0 .01 Ga 4  O 7  film sputtered in 5% N 2  --10% O 2  --85% Ar and post-annealed at 950° C. for 1 hour in air are shown in FIGS. 31 and 32, respectively. 
     The Dy doped materials were prepared with about 1.5% Dy and were sputtered in an Ar:O 2  mixture of 9:1. The EL performance and emission spectrum for the Ca 0 .985 Dy 0 .015 Ga 4  O 7  film sputtered in 10% O 2  --90% Ar and post-annealed at 850° C. in air are shown in FIGS. 33 and 34, respectively. 
     6) Sr 3  Ga 4  O 9  :Tb Phosphors 
     The Tb doped materials were prepared with about 4% Tb and were sputtered in Ar. The EL performance for the Sr 2 .88 Tb 0 .12 Ga 4  O 9  film sputtered in pure Ar and post-annealed at 850° C. for 1 hour in Ar is shown in FIG. 35. Thus, Sr 2 .88 Tb 0 .12 Ga 4  O 9  is quite efficient as an EL material. It is also quite notable that this material exhibits significant EL behavior as deposited without post fabrication annealing (19 fL at 60 Hz, data not shown). The EL emission spectrum for the film is shown in FIG. 36. 
     Phase confirmation by X-ray diffraction 
     The x-ray diffraction patterns for Ca 0 .99 Eu 0 .01 Ga 2  O 4  thin films grown on AVX substrate and annealed at 700° C., 850° C. and 950° C. for 1 hour are shown in FIG. 37. The patterns suggest that CaGa 2  O 4  :Eu thin film is well-crystallized in orthorhombic form when annealed at above 850° C. The x-ray diffraction patterns for the SrGa 2  O 4  thin films grown on BaTiO 3  and annealed at 700° C., 800° C. and 950° C. for 1 hour are shown in FIG. 38, which confirms that the SrGa 2  O 4  thin film is crystallized when annealed at 950° C. but exhibits a strong preferred orientation. The x-ray diffraction patterns for Ca 3  Ga 2  O 6  thin films annealed at various temperatures are shown in FIG. 39, indicating the crystallization temperature for the compound is between 700° C. and 750° C. FIG. 40 shows the x-ray diffraction patterns for CaGa 4  O 7  thin films annealed at various temperatures, indicating the crystallization temperature for the compound is between 800° C. and 850° C. 
     C) NEW Zn 2  Si x  Ge 1-x  O 4  :Mn PHOSPHORS EXHIBITING ELECTROLUMINESCENCE BEHAVIOUR 
     Film Preparation 
     Sylvania phosphor 2282 which is a powder of Zn 2  SiO 4  :Mn was mixed with 99.998% pure GeO 2  powder, 99.9% pure ZnO powder and 99.9% pure MnO powder in a ratio appropriate for Zn 1 .96 Mn 0 .04 Si 0 .5 Ge 0 .5 O 4 . The mixed powder was ground together using a mortar and pestle and placed in a 2 inch RF magnetron gun (US gun). The films were deposited by sputtering from the powder mixture. A ceramic dielectric substrate (also referred to herein as the Sherritt substrate, described in P. Bailey, D. Carkner and X. Wu, SID&#39;95 Digest, p. 484; and U.S. Pat. No. 5,432,015) was placed 4 cm above the gun and sputtering was carried out in a 5-10 mtorr atmosphere of 5-20% O 2  in argon for about 1 hour. The substrate temperature was about 240° C. and sputtering power was 100 watts. The samples were then either annealed in vacuum or in air at between 650° C. and 700° C. for 1 hour or not annealed. For EL measurements, an indium tin oxide layer was subsequently sputter deposited onto the surface of the film. 
     Results 
     The completed device is similar to that shown in FIG. 1, except that the composition of the ceramic layers 12 and 16 (FIG. 1) is not BaTiO 3  in the case of Sherritt substrates. Electroluminescence was observed and FIG. 41 shows the characteristic brightness and efficiency data of a green-emitting Zn 1 .96 Mn 0 .04 Si 0 .5 Ge 0 .5 O 4  EL device, and FIG. 42 shows the data of a red-emitting EL device. The red-emitting phosphor is amorphous by x-ray diffraction and is stable in air up to 600° C. The emission spectra are shown in FIG. 43. 
     These results are commercially very useful as brightnesses of 50 cd/m 2  (or 15 fL) or more are useful for flat panel displays. These brightnesses compare favourably with brightnesses obtained in the best ZnS green electroluminescent devices reported to date as disclosed in H. Ohnishi, SID&#39;94 Digest, p. 129, 1994. 
     Devices were also made on Sherritt substrates using Zn 2  GeO 4  :Mn with the same procedures. The Mn doped materials were prepared with between about 1% to 6% Mn and were sputtered in a gas mixture comprising Ar with O 2  in the range of between 5 to 20% onto substrates heated to between 200° C. to 600° C. The films were annealed in either vacuum or air. Typical brightness and efficiency data are shown in FIG. 44 for a 2% Mn doping. The brightness and efficiency values are smaller than those of the mixed Si--Ge compounds. Annealing temperatures were also 700° C., but could be dropped to 650° C. for Zn 2  GeO 4  :Mn if a longer annealing time was used. 
     It is to be understood that the nomenclature or notation used herein to identify the new phoshor materials is not to be interpreted as limiting in any way. For example, the percentage doping notation has been used in association with the doped gallium oxide compounds since it is not necessarily the case that the rare earth dopants substitute for gallium in the host lattice, while in other compounds the inventors believe substitution occurs and the stoichiometric formulas have been used. 
     It will also be understood by those skilled in the art that the allowable ranges of concentration of dopants in the different new phoshpor materials disclosed herein will depend on the solubility limit of the dopant in the oxides, For example, a series of five targets comprising SrGa 2  O 4  :n%Tb were prepared in which n % was 2%, 4%, 8%, 12% and 16%. Films were prepared by sputtering from these targets and annealed as disclosed above. The sputtered films with dopant levels up to 12% were observed to be homogeneous, single phase films exhibiting EL behaviour while film sputtered from the target with 16% Tb was inhomogeneous with clearly visible precipitates which did not exhibit EL behaviour. Hence in this case a solubility limit of about 15% Tb in the host gallium oxide lattice is estimated. The inventors reasonably contemplate that EL behavior is exhibited in all new phosphors disclosed herein in the range of dopant concentration corresponding to the solubility range of the dopant(s) in the host. 
     Those skilled in the art will understand that the EL characteristics of the phosphors may vary within the solubility range of the dopant(s) in the host lattice. Electronic interactions between dopant ions may determine the prefered concentration of dopant ions for maximum brightness and efficiency. This phenomenon, known as concentration quenching, results in decreasing brightness and efficiency for doping concentrations so that within the solubility limit there will be preferred dopant concentrations which give optimum EL properties. 
     In the case when the dopant in a host lattice comprises more than one element, the criteria for doping ranges involve the above considerations as well as the possibility of energy transfer between dopants of different chemical elements. Notwithstanding this, however, it will be understood by those skilled in the art that more than one chemically distinct dopant element may be simultaneously introduced into a host lattice that EL may be obtained from each distinct dopant simultaneously so as to produce a spectrum of intensity versus wavelength which is a superposition of the spectra obtained from each dopant species separately introduced into the host lattice. 
     It will be appreciated that sputtering has been disclosed herein as the best mode for producing the phosphor films. During sputtering, the composition of the sputtered film will deviate from the composition of the source material forming the sputtering target. This occurs due to a difference in sticking coefficients between the different elements being sputtered; a difference in the sputtering yields between the elements of the target; and incorporation of chemical elements (such as nitrogen) in the sputtering gas into the thin film that are not initially present in the sputtering target. It will be understood however that these deviations are limited in magnitude such that the grown films do crystallize in those crystal structures, when annealed appropriately, expected from the target composition. 
     It will be appreciated by those skilled in the art that while the fabrication of the new electroluminescent phosphors disclosed herein has been described using sputtering as the film preparation method, other methods known to those in the art may be used. Other methods of fabrication include electron beam deposition, laser ablation, chemical vapour deposition, vacuum evaporation, molecular beam epitaxy, sol gel deposition and plasma enhanced vacuum evaporation to mention a few. 
     Various thin film dielectrics used in electroluminescent applications include SiO 2 , SiON, Al 2  O 3 , BaTiO 3 , BaTa 2  O 6 , SrTiO 3 , PbTiO 3 , PbNb 2  O 6 , Sm 2  O 3 , Ta 2  O 5 , TiO 2 , Y 2  O 3 , Si 3  N 4 , SiAlON. These may be used as substrates in the present invention by depositing onto glass, silicon or quartz substrates, to mention just a few. 
     Thick film on ceramic substrates may also be used. While many of the results dislcosed herein were obtained using BaTiO 3  thick film dielectrics, other thick films on ceramic substrates may also be used. The ceramic substrate may be alumina (Al 2  O 3 ) or the same ceramic as the thick film itself. Thick dielectric films of BaTiO 3 , SrTiO 3 , PbZrO 3 , PbTiO 3 , to mention just a few, may also be used. 
     Variations of the EL laminate device configuration will be readily apparent to those skilled in the art. An alumina substrate may be used onto which the lower conductive electrode is deposited followed by the high dielectric constant material, the phosphor and then the outer transparent electrode. Alternatively, a conductive electrode contact may be deposited onto the back of a thick, rigid dielectric substrate material onto the front of which the phosphor layer is deposited followed by the outer conductive electrode. 
     
                                           TABLE 1__________________________________________________________________________TYPICAL PHOSPHOR COMPOSITIONS AND FIRING CONDITIONSFOR PREPARATION OF DOPED GALLATESCaO   BaCO.sub.3  SrCO.sub.3      Ga.sub.2 O.sub.3          Tb.sub.4 O.sub.7              Eu.sub.2 O.sub.3                  Firing                        Compound(g)   (g) (g) (g) (g  (g) conditions                        formed__________________________________________________________________________-- --  4.163      5.563          0.222              0.052                  1100° C./24                        Sr.sub.0.96 Tb.sub.0.04 Eu.sub.0.01 Ga.sub.2                        O.sub.4                  hr-- --  4.308      5.581          0.111              --  1100° C./24                        Sr.sub.0.98 Tb.sub.0.02 Ga.sub.2 O.sub.4                  hr-- --  4.358      5.589          --  0.053                  1100° C./24                        Sr.sub.0.99 Eu.sub.0.01 Ga.sub.2 O.sub.4                  hr2.164   --  --  7.535          0.301              --  1100° C./2                        Ca.sub.0.96 Tb.sub.0.04 Ga.sub.2 O.sub.4                  hr2.269   --  --  7.659          --  0.072                  1100° C./2                        Ca.sub.0.99 Eu.sub.0.01 Ga.sub.2 O.sub.4                  hr-- 5.080  --  4.874          --  0.046                  1200° C./12                        Ba.sub.0.99 Eu.sub.0.01 Ga.sub.2 O.sub.4                  hr-- 5.029  --  4.874          --  0.097                  1200° C./24                        Ba.sub.0.96 Tb.sub.0.02 Ga.sub.2 O.sub.4                  hr4.544   --  --  5.165          --  0.291                  1000° C./12                        Ca.sub.2.94 Eu.sub.0.06 Ga.sub.2 O.sub.6                  hr__________________________________________________________________________