阅读说明：本技术 经涂覆的硫铝酸盐荧光体颗粒 (Coated thioaluminate phosphor particles ) 是由 A·C·托马斯 Y·谢 J·梅尔曼 R·诺德赛 Y·B·勾 K·巴娄第 E·托马斯 于 2019-05-15 设计创作，主要内容包括：公开了具有包括氮化物或基本上由氮化物组成的涂层的硫铝酸盐荧光体颗粒,以及制备此类荧光体颗粒的方法。荧光体转换的发光二极管可以包括此类经涂覆的荧光体颗粒。与氧化铝涂层相比,硫铝酸盐荧光体颗粒上的氮化物涂层提供了显著改进的防水屏障,并延长了此类荧光体转换的发光二极管的工作寿命。(Thioaluminate phosphor particles having a coating comprising or consisting essentially of a nitride are disclosed, as well as methods of making such phosphor particles. Phosphor converted light emitting diodes may include such coated phosphor particles. The nitride coating on the thioaluminate phosphor particles provides a significantly improved water barrier compared to the alumina coating and extends the operating life of such phosphor converted light emitting diodes.)

1. A light-emitting composition comprising:

particles of a sulfide phosphor material comprising rare earth activator ions; and

a nitride coating on each particle.

2. The luminescent composition of claim 1, wherein the nitride coating layer comprises aluminum nitride.

3. The luminescent composition of claim 1, wherein the nitride coating layer consists essentially of aluminum nitride.

4. The luminescent composition of claim 1, wherein the nitride coating layer comprises gallium nitride.

5. The luminescent composition of claim 1, wherein the nitride coating layer consists essentially of gallium nitride.

6. The luminescent composition of claim 1, wherein the sulfide phosphor material is capable of absorbing blue, violet, or ultraviolet light and responsively emits light having a peak wavelength in the green region of the visible spectrum.

7. The luminescent composition of claim 1, wherein the nitride coating layer is disposed directly on the sulfide phosphor material.

8. The luminescent composition of claim 1, wherein each particle comprises an oxide layer disposed between the sulfide phosphor material and the aluminum nitride coating layer.

9. The luminescent composition of claim 1, wherein each particle comprises at least a second coating layer disposed on the nitride coating layer.

10. The luminescent composition of claim 9, wherein the second coating layer comprises at least one oxide.

11. The luminescent composition of claim 1, wherein the sulfide phosphor material pass through RE_1-wA_wM_xE_yA characterization, wherein:

RE is a rare earth element or a mixture of rare earth elements;

a is selected from the group consisting of magnesium, calcium, strontium, barium and mixtures thereof;

m is selected from the group consisting of aluminum, gallium, boron, indium, scandium, lutetium, yttrium, and mixtures thereof;

e comprises sulfur and is selected from the group consisting of sulfur, selenium, oxygen, tellurium, and mixtures thereof;

0≤w≤1.0；

x is more than or equal to 2 and less than or equal to 4; and

4≤y≤7。

12. the luminescent composition of claim 11, wherein the nitride coating layer comprises aluminum nitride.

13. The luminescent composition of claim 11, wherein the nitride coating layer consists essentially of aluminum nitride.

14. The luminescent composition of claim 13, wherein the nitride coating layer is disposed directly on the sulfide phosphor material.

15. The luminescent composition of claim 13, wherein each particle comprises an oxide layer disposed between the sulfide phosphor material and the aluminum nitride coating layer.

16. A light emitting device comprising:

a light emitting diode emitting a main light; and

particles of a sulfide phosphor material comprising rare earth activator ions;

wherein the sulfide phosphor material is capable of absorbing at least a portion of the primary light and responsively emitting secondary light having a longer wavelength than the primary light, and each particle of the sulfide phosphor material includes a nitride coating layer.

17. The light emitting device of claim 16, wherein the nitride coating layer comprises aluminum nitride.

18. The light emitting device of claim 16, wherein the nitride coating layer consists essentially of aluminum nitride.

19. The light emitting device of claim 16, wherein the nitride coating layer comprises gallium nitride.

20. The light emitting device of claim 16, wherein the nitride coating layer consists essentially of gallium nitride.

21. The light emitting device of claim 16, wherein the secondary light has a peak wavelength in the green region of the visible spectrum.

22. The light emitting device of claim 21, wherein the sulfide phosphor material pass RE_1-wA_wM_xE_yA characterization, wherein:

RE is a rare earth element or a mixture of rare earth elements;

a is selected from the group consisting of magnesium, calcium, strontium, barium and mixtures thereof;

m is selected from the group consisting of aluminum, gallium, boron, indium, scandium, lutetium, yttrium, and mixtures thereof;

e comprises sulfur and is selected from the group consisting of sulfur, selenium, oxygen, tellurium, and mixtures thereof;

0≤w≤1.0；

x is more than or equal to 2 and less than or equal to 4; and

4≤y≤7。

23. the light-emitting device of claim 22, wherein RE is europium.

24. The light emitting device of claim 23, wherein the primary light is blue light.

25. The light emitting device of claim 24, wherein the secondary light has a peak wavelength in the green region of the visible spectrum.

Technical Field

The present invention generally relates to coated thioaluminate phosphor particles and methods for coating thioaluminate phosphor particles.

Background

Over the past years, LED lighting has made tremendous progress in energy efficient lighting, while achieving high quality. Another feature of LED lighting is that the useful life of the lighting product is very long, typically L70 (the amount of time a light source will operate before its lumen output drops to 70% of its initial output) is greater than 25,000 hours. In contrast, the L70 of existing light sources for LED replacement is typically 10,000 hours (fluorescent lamps) or catastrophic failure at about 1000 hours (incandescent lamps). This long lifetime depends on all components in the LED light source, especially the blue or violet light emitting diode and the down-converting phosphor material, which absorbs the light emitted by the diode and converts it to other colors to form the visible spectrum. When the diode degrades, the LED becomes less bright but maintains its color balance. However, as the phosphor degrades, the LED typically becomes less bright and also loses its color balance. The LEDs may be non-white in color. Color shift is often more problematic from a user's perspective.

The most common architecture for LED packaging is to disperse a phosphor material in a silicone matrix to form a paste and deposit the paste into a reflective cup area that also includes a light emitting diode. The package has two types of reflective areas: a diffusely reflective surface, typically composed of plastic or ceramic, and a more specularly reflective surface formed by electrical contacts. Typically, the specularly reflective surface is plated with silver to significantly improve reflectivity and increase light extraction from the package.

LED phosphors are typically composed of activator ions (typically divalent europium or trivalent cerium) in a host (host). The activator ions directly absorb the incident light and emit light at longer wavelengths in a process commonly referred to as down-conversion. That is, incident photons are down-converted from higher energy blue photons to lower energy photons (such as cyan, green, yellow, orange, or red). The host helps to tune the absorption and emission wavelengths of the (tune) activator. In addition, the crystallinity of the host around the activator can play an important role in the efficiency of absorption and emission.

Phosphor degradation is generally due to the action of water or oxygen in the presence of heat and light generated by the LED. It is common practice to coat many types of phosphors with a layer to prevent water or oxygen from contacting the phosphor and promoting degradation. Typically, these coatings are inorganic oxides and are deposited on the phosphor by a liquid phase (e.g., sol-gel) reaction or a vapor phase reaction.

Phosphors can generally degrade by three mechanisms. First, oxidation of the activator may eliminate its charge transfer absorption from the 4f orbital to the 5d orbital, thereby making it unable to absorb incident light. Second, the body may be chemically deformed, thereby altering the energy absorbed and emitted by the active agent. Third, the body may physically deform, thereby losing crystallinity around the active agent and reducing the efficiency of absorption and emission by the active agent. Typically, low temperature chemical changes of the host will also result in loss of crystallinity. The overall effect of these degradations depends on the extent to which the host (original or degraded) allows water or oxygen to permeate through the material. For example, cerium-doped yttrium aluminum garnet phosphor materials degrade very slowly relative to europium-doped alkaline earth orthosilicate phosphors.

Unlike oxide and nitride phosphors, which constitute almost all commercially used phosphors, sulfide-based phosphors (e.g., thioaluminate phosphors) add an additional LED failure mechanism. Hydrolysis reactions with water can liberate sulfur from the phosphor, which can degrade performance by, for example, delustering the reflective surface in the LED package. This blackening can greatly reduce the light output of phosphor-converted LEDs. Therefore, the inability to properly coat sulfide phosphors poses a greater problem than the inability to properly coat oxide or nitride phosphors.

The surface chemistry differences between these phosphors and their oxide or nitride analogs hinder the ability to effectively coat sulfide phosphors.

Disclosure of Invention

In one aspect of the invention, the thioaluminate phosphor particles have a coating comprising, consisting essentially of, or consisting of a nitride. For example, the nitride coating may include or consist essentially of aluminum nitride, gallium nitride, or mixtures thereof. The nitride coating on the thioaluminate phosphor particles provides a significantly improved water barrier (barrier) compared to the alumina coating. This improvement may be due to the fact that the nitride coating precursor (precursor) does not react with the volatile gas from the surface of the unstable sulfide phosphor.

In another aspect of the invention, a method of making such nitride coated thioaluminate phosphor particles is disclosed.

In yet another aspect of the invention, a phosphor converted LED includes such nitride coated thioaluminate phosphor particles.

These and other embodiments, features and advantages of the present invention will become more readily apparent to those skilled in the art when taken with the following more detailed description of the invention taken in conjunction with the accompanying drawings that are first briefly described.

Drawings

Fig. 1 shows a schematic diagram of an example fluidized bed reactor for chemical vapor deposition on phosphor particles.

Fig. 2 shows the X-ray photoelectron spectra in the sulfur 2p region for two coated phosphor samples.

Fig. 3 shows exemplary thermogravimetric-mass spectral data of an uncoated calcium sulfoaluminate phosphor sample.

FIG. 4A shows coating with Al₂O₃In AgNO₃Microscope images after testing.

FIG. 4B shows AlN coated ZnS sample in AgNO₃Microscope images after testing.

FIG. 4C shows coating with Al₂O₃The calcium sulfoaluminate phosphor particles are in AgNO₃Microscope images after testing.

FIG. 4D shows AlN coated calcium sulfoaluminate phosphor particles in AgNO₃Microscope images after testing.

Detailed Description

The following detailed description should be read with reference to the drawings, which depict selected embodiments and are not intended to limit the scope of the invention. The present detailed description illustrates by way of example, and not by way of limitation, the principles of the invention. This description will clearly enable one skilled in the art to make and use the invention, and describes several embodiments, adaptations, variations, alternatives and uses of the invention, including what is presently believed to be the best mode of carrying out the invention. As used in this specification and the appended claims, the singular forms "a", "an", and "the" include plural referents unless the context clearly dictates otherwise.

Sulfide phosphors can have very attractive spectral properties. In particular, the emission spectra of many sulfide phosphors can be very narrow, characterized by a full width at half maximum (FWHM) of less than 50nm, and sometimes as little as 25 to 30 nm. This spectral narrowness can be very attractive in display backlighting and general lighting applications.

Divalent rare earth activated sulfide phosphors of interest include RE_1-wA_wM_xE_yWhere RE can be one or more rare earth elements (e.g., Eu or Gd), A can be one or more elements selected from the group Mg, Ca, Sr, or Ba, M can be one or more elements selected from the group Al, Ga, B, In, Sc, Lu, or Y, E includes sulfur and can be one or more elements selected from the group S, Se, O, and Te, w is greater than or equal to zero and less than or equal to about 0.99 or less than or equal to 1.0, 2 ≦ x ≦ 4, and 4 ≦ Y ≦ 7. Such phosphors may be referred to herein as thioaluminatesAcid salt or calcium sulfoaluminate phosphor. Generally, they are capable of absorbing blue or ultraviolet light and responsively emitting light having a peak wavelength in the green region of the visible spectrum.

These thioaluminate phosphors can react with water to release H₂S, and converting part of the sulfide main body into oxide. This change affects the optical properties of the phosphor, generally shifting absorption to higher energies due to reduced crystallinity around the center of the activator, and reducing absorption and emission intensity.

Free sulfide (such as can be hydrolyzed from sulfide phosphor to H)₂Free sulfide released upon S or similar substances) can disrupt the encapsulation at several levels. At high concentrations, it may inhibit curing of the silicone used for encapsulation. This inhibition of curing means that the phosphor can move within the package, thereby shifting the color point of the LED, and that the wire bonds from the contacts to the chip are unprotected, thereby making the LED more susceptible to catastrophic failure due to the electrical connection breaking. At lower concentrations, the sulfides react over time, corroding and blackening the silver of the electrical contact pads and the gold of the wire bonds from the contacts to the chip. If a cationic sulfur source is present (such as SO)₂) The latter degradation mechanism may also play a role and the presence of an electrochemical potential may accelerate the latter degradation mechanism when a current is flowing through the package.

All of these mechanisms shorten the life of phosphor converted LED light sources.

As described above, it is known that coating phosphor particles can inhibit water from entering the phosphor and prevent degradation thereof. Common coating methods are the formation of a silicon dioxide layer by a sol-gel process or the formation of an aluminum oxide layer by a chemical vapor deposition method.

In the sol-gel process, phosphor particles are suspended in a solvent. The solvent contains a coating precursor and initiates a reaction to form the precursor into a continuous coating on the phosphor particles. Depending on the system, the precursor may be initiated in the presence of the phosphor, or it may be initiated prior to introduction of the phosphor. For example, the phosphor may be stirred in an aqueous or alcoholic solution of Tetraethoxysilane (TEOS). The coating process can then be initiated by adding an ammonia solution to change the pH and accelerate the hydrolysis rate of the silane to form a silica coating on the phosphor. Other types of precursors are known, such as titanium isopropoxide ethanolate and aqueous aluminum nitrate solutions. Many other sol-gel chemistry methods are known and may be utilized.

The chemical vapor deposition process is typically performed on particles that have been fluidized in a fluidized bed. The creation of a fluidized bed typically requires placing the phosphor powder in a column with a gas permeable, but powder impermeable film or frit (frit) at the bottom. The powder is suspended by the upward force of the gas, which counteracts the downward force of gravity. This fluidization enables access to all surfaces of the phosphor particles that might otherwise not be exposed to the solid powder or even to the agitated solution. The second gas flow can carry a second precursor of the coating and can deliver it near the middle of the fluidization region. An example fluidized particle coating system is depicted in fig. 1.

One such fluidization system arrangement uses argon as the fluidizing gas, and argon is bubbled through the water, then up through the frit and through the Trimethylaluminum (TMA), then into the middle of the fluidization zone in two separate streams. The reactants are mixed in a fluidization zone and the zone is heated to a temperature of from 100 ℃ to 300 ℃. Hydrolysis of TMA is then performed to form an amorphous alumina coating on the phosphor particles. In addition to argon, other inert carrier gases may be used, such as nitrogen.

The alumina coating may also be deposited in a layer by layer (layer) process, sometimes referred to as Atomic Layer Deposition (ALD), in which the phosphor particles are treated with a small concentration (small concentration) of water to form a water/hydroxide layer on the surface of the particles, the reaction chamber is evacuated to remove all the water, and then filled with a small concentration of TMA which reacts with the surface hydroxyl groups left behind by the water to form an alumina layer. The chamber is again evacuated and filled with a small concentration of water and the steps are repeated until the desired number of layers has been deposited.

The exact thickness of the coating will be determined, in part, by the method used; ALD will form the thinnest coating layer, CVD will form a thicker coating layer, and sol-gels will typically form much thicker coatings.

Attempts to coat thioaluminate phosphor materials by various sol-gel methods have resulted in significant reductions in the absorption and emission properties of the phosphor materials due to the chemical reactivity of the phosphor.

Attempts to form coatings of alumina or alumina plus other metal oxides on thioaluminate phosphor materials by CVD/fluidized bed processes or ALD processes with trimethylaluminum and water were more successful because the materials did not show complete degradation during the coating process. However, these coating methods do not form a barrier that enables the phosphor material to withstand normal LED reliability tests.

Typically, phosphors are tested as part of packaged LEDs by observing their lumen maintenance and color shift over time under different conditions. A typical test would be a High Temperature Operating Life (HTOL) test in which the LEDs are energized in a test oven at elevated temperatures. Typical temperatures for HTOL testing are 85 ℃ and 125 ℃, and typical durations are 1008 hours and 6000 hours. Another typical test is the Wet High Temperature Operating Life (WHTOL) test, in which the LEDs may be energized at all times, or may be energized periodically at regular intervals in a test oven at elevated temperature and elevated controlled humidity. Typical conditions for the WHTOL test are 60 ℃/90% relative humidity (60/90) and 85 ℃/85% relative humidity (85/85), with a typical duration of 1008 hours. The success criteria may depend on who is performing (administer) the test, but after 1008 hours of the WHTOL test, typically the lumen maintenance should be at least greater than 80%. That is, the final luminance should be at least 80% of the initial luminance, and the color shift measured by Δ u 'v' (the color coordinate change measured in CIE 1976 color space from the beginning of the test period to the end of the test period) should be at least less than 0.007.

In addition, the coated sulfide phosphor can be tested by subjecting the phosphor powder to a silver nitrate solution to obtain the effectiveness of the seal of the coating to sulfur. The silver ions in the solution will react with any silver ions not already protected by the coatingSulfide reacts and black Ag is formed₂And S. This black precipitate is readily visible once formed, and its time of occurrence can be used as a measure of the effectiveness of the coating (gauge).

For example, some samples of alumina coated europium doped strontium thiogallate (a well studied phosphor) did not blacken for about 336 hours in silver nitrate solution and retained 80% of their original brightness after 1008 hours of 60/90 testing.

In contrast, some of the more robust alumina coated europium doped calcium sulfoaluminate samples darkened after about 20 minutes in silver nitrate solution and failed to maintain 80% of their original brightness after only 168 hours of testing.

As shown in fig. 2, analysis of alumina coated Strontium Thiogallate (STG) phosphor and alumina coated calcium sulfoaluminate phosphor by XPS in the sulfur 2p region showed negligible signal, if any, for STG, but very significant intensity between 160 and 172eV (about 3 atomic%) for the calcium sulfoaluminate phosphor. This sulfur is expected to react with moisture and promote phosphor failure as determined by various test methods (silver nitrate solution and encapsulated LED testing). It is presumed that the thioaluminate phosphor volatilizes sulfides during the coating process, and then the sulfides are continuously redeposited with the outer layer of the coating.

To help test the speculation about sulfur in the coating of thioaluminates, several uncoated calcium thioaluminate phosphors were analyzed by thermogravimetric analysis coupled with mass spectrometry (TGA-MS). In this technique, a sample is heated under a flowing gas, the mass of which is monitored, and the exiting gas is analyzed by mass spectrometry. Specifically, calcium sulfoaluminate phosphors subjected to several different post-treatment (work-up) protocols were heated under inert gas (argon) and exhibited reactivity with H at temperatures up to about 300 ℃₂S corresponds to the mass number 34 as the primary mass loss. An example data set is shown in fig. 3. Also shown in fig. 3: mass number 44 and CO₂Or CH₂CHO corresponds to SO or CH with a mass of 48₃The SH is corresponding to the basic oxygen in the reaction,mass 64 and SO₂Corresponding to mass 66 and H₂S₂And correspondingly.

These analyses indicate the incompatibility of the thioaluminate phosphor surface with the chemistry used to deposit the oxide-based coating. This incompatibility occurs when the coating chemistry volatilizes some sulfur from the surface and redeposits it as part of the coating layer, forming a continuous reactive pathway for water to penetrate into the coating and react with/degrade the phosphor material.

As a result of the defects found when attempting to apply an oxide coating to a calcium sulphoaluminate phosphor, it is apparent to the inventors that significant changes to the coating process must be made. The inventors then developed an improved coating method that includes coating the thioaluminate phosphor material with a nitride layer rather than with an aluminum oxide layer. For example, aluminum nitride, gallium nitride, and mixtures of the two may be suitable for such coatings. In this process pure ammonia or ammonia with an inert gas is used as fluidizing gas and trimethylaluminum may be used as aluminum source to deposit the aluminum nitride layer. Alternatively, a gallium nitride layer may be deposited instead of an aluminum nitride layer with trimethyl gallium instead of trimethyl aluminum. In this process, both trimethylaluminum and trimethylgallium may be used to deposit mixed aluminum nitride and gallium nitride layers.

Another coating layer (such as, for example, alumina, silica, or alumina and silica) may optionally be added over the aluminum nitride layer by, for example, one of the coating methods described above. In some variations, there may be an oxide layer under the aluminum nitride coating, which is formed during cleaning of the phosphor particles prior to deposition of the nitride coating. Thus, in some variations, there may be oxide or other layers above and below the nitride layer.

Table 1 below presents data for a series of coating runs (run), all of which were run with the same phosphor batch. For each coating experiment, these data are reference values, the amount of phosphor charged to the reactor, the amount of phosphor recovered, the temperature at which the reactor was maintained during the coating cycle, the duration of the coating cycle, the flow rate of argon through the trimethylaluminum bubbler and into the reactor (L/min), the flow rate of anhydrous ammonia into the reactor (L/min), the weight ratio of nitrogen to aluminum precursor used, and the theoretical amount of aluminum nitride formed relative to the amount of phosphor in the reactor.

Table 2 below presents spectral data for the phosphor samples before coating and after each coating run. In addition, another batch of phosphors was coated with ALD and spectral data of the samples before and after coating was presented.

Coated aluminum nitride or Al was tested by subjecting the phosphor powder to the silver nitrate solution test described above₂O₃The thioaluminate sample of (1). In these tests, several milligrams of coated phosphor were placed in a vial. Several milliliters of 0.01M AgNO₃(_aq)(AgNO₃(_{Aqueous solution}) Added to the vial, and the recorded time to a predetermined degree of darkening due to the formation of silver sulfide was observed by the naked eye. The time recorded is the Time To Failure (TTF) and gives a relative measure of the effectiveness of the coating. Table 3 below reports the best Al₂O₃Coated samples, samples deposited with AlN coating by ALD, and AgNO of two samples with CVD AlN coating₃Time to failure. After 19 minutes, optimum Al was observed₂O₃The coating turned black. By 40 minutes, AlN samples by ALD turned black. After 3 hours, blackening was observed in the earlier AlN by CVD (NBG20180326) sample, and after 4.5 hours, blackening was observed in the later AlN by CVD (NBG20180327) sample.

These test results (e.g., for NBG20180327) indicate that a reaction temperature of 300 ℃ is sufficient to provide a barrier coating of aluminum nitride on the thioaluminate phosphor particles that is more effective than the optimal alumina coating prepared for this study. Scanning Electron Microscopy (SEM) and transmission electron microscopy of the cross-section NBG20180327 phosphor particles showed that the aluminum nitride barrier coating was polycrystalline and had a thickness of 50-60 nm. Aluminum nitride is identified by EDS. Scanning Electron Microscopy (SEM) and transmission electron microscopy of the thioaluminate phosphor particles coated with an optimized alumina coating across the cross section showed that the alumina coating thickness was greater than 200 nm.

In a further test, the sample was attached to a slide with double-sided tape, immersed in a silver nitrate solution, and observed over the course of several hours. Four samples were compared: as shown in fig. 4A, coated with Al₂O₃Zinc sulfide of (a); as shown in fig. 4B, zinc sulfide coated with AlN; as shown in fig. 4C, thioaluminate phosphor sample NBG20180301 coated with the previously identified optimal alumina coating; and as shown in fig. 4D, a sample of the same phosphor batch coated with AlN (example NBG 20180327). After about 8 hours, the samples were compared. Zinc sulfide with an alumina coating showed no blackening, while zinc sulfide coated with aluminum nitride showed some blackening. The alumina coated phosphor sample retained some green phosphor particles, but it almost completely blackened (fig. 4C), while the aluminum nitride coated sample appeared less than half blackened (fig. 4D).

The nitride coated thioaluminate phosphors of the present invention may be optically coupled to an excitation source in any conventional manner. A more common approach is to combine a green emitting phosphor, such as the nitride coated thioaluminate phosphors disclosed herein, with a red phosphor and optionally blue and/or yellow phosphors. The phosphors may be combined together and then added to an encapsulant, such as silicone, epoxy, or some other polymer, or the phosphors may be combined during the addition of the phosphors to the encapsulant. The phosphor-loaded encapsulant can then be placed in the optical path of an excitation source, such as an LED or laser diode that emits ultraviolet, violet, or blue light. One common approach is to deposit a slurry of one or more phosphors into an LED (light emitting diode) package containing an LED chip. The slurry is then cured to form a sealed LED package. Other methods include: the encapsulant is formed into a shape or coated onto a substrate that may already have a particular shape or may be subsequently formed into a particular shape. In addition, the phosphor-containing encapsulant can be disposed on or near an in-coupling region of the light guide (e.g., coated on the in-coupling region of the light guide), or on an out-coupling region of the light guide, such as a light guide intended for use in a display. Alternatively, the phosphor composition may be deposited as a thin film on an LED chip or on another substrate, and subsequently optically coupled to a light source. The combination of the excitation source and phosphor of the present invention can be used in general lighting, niche (niche) lighting applications, display backlighting, or other lighting applications.

TABLE 1 coating run data

Table 2 spectral data:

TABLE 3 AgNO₃Resistance test data:

the present disclosure is to be considered as illustrative and not restrictive. Further modifications will be apparent to persons skilled in the art in view of this disclosure, and are intended to fall within the scope of the appended claims.