Red phosphors for solid state lighting

Abstract

A red phosphor composition in combination with a semiconductor light emitting device (e.g., VCSEL, LED, or LD), preferably a GaN based device, that emits light at a bright violet-blue light range, i.e., having a wavelength in the range of 400 nm to 600 nm, which can be further combined with green and blue phosphors. The red phosphor composition in the combination is a vanadate combined with yttrium, gadolinium and/or lanthanum and activated with trivalent Eu3+, Sm3+ and Pr330 , or any combination thereof, with or without Tb3+ as a co-dopant, has the general formula: BixLn1-xVO4:A where x=0 to 1, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Eu3+, Sm3+ and Pr3+, or any combination thereof, with or without Tb3+ as a co-dopant. Novel red phosphor compositions are provided when x is greater than 0 and less than 1, preferably 0.05 to 0.5.

Description

FIELD OF THE INVENTION

The invention is in the field of phosphors for solid state lighting.

BACKGROUND OF THE INVENTION

Recently, solid-state lighting based on GaN semiconductors has made remarkable breakthroughs in efficiency. GaN-based diodes emit bright violet-blue light, which can be used to pump longer wavelength phosphors. The first white light emitting diodes (LEDs) became commercially available in 1997. These white LEDs can be obtained by combining a InGaN blue LED emitting at 465 nm with a broad-band yellow phosphor, e.g. (Y_1-xGd_x)₃(Al_1-yGa_y)₅O₁₂ (YAG:Ce). The variation of x and y can be used to produce a broad emission from 510 nm and 580 nm, leading to a high color rendering index. These white LEDs have efficiencies comparable to incandescent lights and are proving useful in a wide variety of niche lighting applications.

White light can be produced by a variety of other approaches, including color mixing of three LED emissions (e.g., combining discrete blue, green, and red LEDs) or the pumping of phosphors with a deep blue/UV LED or laser diode (LD). Nitride-based vertical cavity surface emitting lasers (VCSELs), coupled with phosphors optimized for violet or near-UV absorption, offer the greatest potential for high-efficiency solid-state lighting [D. A. Steigerwald, et al]. However, the problem lies in the unavailability of suitable RGB phosphors that are optimized for absorbing the near UV or violet emission from the LEDs or lasers. The red, green and blue phosphors that are currently used in conventional fluorescent lighting have been optimized for excitation by the UV emission from a mercury discharge, for which the characteristic wavelengths are 185 and 254 nm [G. Blasse, et al, 1994]. Hence, the challenge for the new generation of lighting based upon GaN lies in the development of novel families of phosphors that are optimized for excitations at longer wavelengths in the near UV (350–400 nm).

The current phosphor materials of choice for the solid-state lighting initiative are Y₂O₂S:Eu³⁺ for red, ZnS:(Cu⁺, Al³⁺) for green, and BaMgAl₁₀O₁₇:Eu²⁺ (BAM) for blue [M. Shinoya, et al]. Unfortunately, the red emission with Y₂O₂S:Eu³⁺ is inadequate in comparison with the green and blue phosphors, both in terms of its efficiency and its stability, so there is an urgent need to make superior red phosphors.

BRIEF SUMMARY OF THE INVENTION

The present invention provides new phosphors absorbing in near UV and emitting in the red by using materials that have broad and intense charge-transfer (C-T) absorption bands in the near UV and are therefore capable of efficiently capturing the emission from a GaN-based LED or LD over a range of wavelengths. Vanadates, combined with selected lanthanides or yttrium, are used, optionally with bismuth, where the oxygen to metal charge-transfer bands are very intense. Following the excitation in the UV, the energy is transferred to an activator ion by a non-radiative mechanism. More particularly, the activator ion is selected from Eu³⁺, Sm³⁺, and Pr³⁺ and any combination thereof, alone or co-doped with Tb³⁺ as an intensifier to enhance transfer. While the red phosphor materials generally should not absorb any of the green or blue emissions, a colored phosphor that converts some of the blue or green to red can have some advantages and are, therefore, not excluded.

More particularly, the invention provides a novel red phosphor composition as well as its combination with a light emitting semiconductor device (e.g., VCSEL, LED, or LD), preferably a GaN based device, that emits light having a wavelength in the range of 200 nm to 620 nm. The composition can contain at least one non-red phosphor in addition to the red phosphor, preferably green and blue phosphors (such as the ZnS:(Cu⁺, Al³⁺) and BaMgAl₁₀O₁₇:Eu²⁺ phosphors described above). The red phosphor absorbs the light of a wavelength in the range of 240 nm to 550 nm and emits red light at a wavelength in the range of 580 nm to 700 nm, and is a vanadate combined with yttrium, gadolinium and/or lanthanum and activated with trivalent Eu³⁺, Sm³⁺ and Pr³⁺, or any combination thereof, with or without Tb³⁺ as a co-dopant. When combined with a light emitting semiconductor device, the red phosphor composition of this invention has the general formula:Bi_{xl Ln1-x}VO₄:Awhere x=0 to 1, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Eu³⁺, Sm³⁺ and Pr³⁺, or any combination thereof, with or without Tb³⁺ as a co-dopant. Novel red phosphor compositions are provided when x is greater than 0 and less than 1, preferably 0.05 to 0.5.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph showing the powder X-ray diffraction patterns of samples of Bi_xY_1-xVO₄:Eu;

FIG. 2 is a graph showing the photoluminescence spectra of Bi_xY_1-xVO₄:Eu samples (λ_exc=365 nm);

FIG. 3 is a graph showing the excitation spectra of Bi_xY_1-xVO₄:Eu samples for the 614 nm Eu³⁺ emission;

FIG. 4 is a graph showing the excitation spectra of Bi_xGd_1-xVO₄:Eu samples for the 613 nm Eu³⁺ emission;

FIG. 5 is a graph showing the excitation spectra of Bi_xLa_1-xVO₄:Eu samples for the 612 nm Eu³⁺ emission;

FIG. 6 is a graph showing the photoluminescence spectra of Bi_xY_1-xVO₄:Sm samples (λ_exc=363.8 nm); and

FIG. 7 is a graph showing the excitation spectra of Bi_xY_1-xVO₄:Sm samples for the 645 nm Sm³⁺ emission.

DETAILED DESCRIPTION OF THE INVENTION

The light emitting device of the present invention can be any GaN based LED, LD or VCSEL that emits light, preferably monochromatic, at a wavelength in the range of 200 nm to 620 nm. Such devices are well known [M. Shinoya, et al and D. A. Steigerwald, et al], but the red phosphor used in prior devices is inadequate.

In according with the present invention, particularly useful for red phosphors are materials of the general formula:Bi_xLn_1-xVO₄:Awhere x is a number equal to or larger than 0 but smaller than 1, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Eu³⁺, Sm³⁺ and Pr³⁺, or any combination thereof, with or without Tb³⁺ as a co-dopant. In a preferred embodiment, particularly useful are yttrium vanadates containing Eu³⁺ (f⁵), which fluoresces via a ⁵D₀ to ⁷F₂ transition at ˜612 nm when the ion is present in a non-centrosymmetric site. Eu-doped YVO₄, is used as a cathodoluminescent material in color television screens, and is appropriate for the present application, since the C-T band of the vanadate ion is well placed in the UV.

In a preferred embodiment, it is useful to incorporate Bi³⁺ in which 6s²→6s6p excitations in the bismuth ion can also be used to harvest the near-UV light. In the case of the Bi_xLn_1-xVO₄ (Ln=Gd, Eu,) system, for example, structural and spectral studies have shown the existence of two ranges of solid solution [Ghamri, et al., 1990; Ghamri, et al., 1989]. One has a tetragonal structure of the zircon type (0<x<0.64) and the other has a monoclinic structure of the scheelite-related fergusonite type (x>0.93). Coordination of the cations in these oxides is such that V is coordinated to four oxygen atoms forming a tetrahedron and Ln (or Bi) to eight oxygen atoms from different tetrahedra. In the present embodiment we have utilized the luminescence behavior of the solid solutions of Bi_xLn_1-xVO₄:A, where Ln and A are as defined above and 0<x<1, and correlated it with the available structural information. In addition, we have also investigated the effect of co-doping with Tb, e.g., Tb(III)/Pr(III) on the Eu(III) emission in these solid solutions and compare the emission intensities of these samples with the standard red phosphor (Y₂O₂S:Eu³⁺).

The red phosphors of the present invention are excited by light of 240 to 550 nm and emits light of 580 to 700 nm which peaks at ˜610 to 650 nm. The Bi_xLn_1-xVO₄:A composition is obtained by mixing oxides, carbonate and the like of elements which constitute the phosphor at a desired stoichiometric ratio. The red phosphor can be combined with green and blue phosphors, e.g., respectively, ZnS:(Cu⁺, Al³⁺) and BaMgAl₁₀O₁₇:Eu²⁺ phosphors. The combination of phosphors can be applied as a layer to a light emitting semiconductor device such as a VCSEL, LED or LD. For example the combination can be applied as a layer to a GaN die and encapsulated by a lens typically formed of a transparent epoxy. In operation, electrical power is supplied to the GaN die to activate it, which then emits light that activates the phosphors to emit output light of combined wavelengths and which will vary depending on the spectral distribution and intensities of the light emitted from the phosphors. See, for example, the description of the prior art phosphor LED in Lowery, et al. U.S. Pat. No. 6,351,069, the disclosure of which is incorporated herein by reference. The present invention enables the emitted wavelengths to have a combined spectral distribution such that it appears to be “white” light.

In a preferred embodiment, the combination of a red phosphor of this invention and prior art green and blue phosphors are such that the white light is obtained having a combination of spectral ranges of 500 to 580 nm (green), 400 to 500 nm (blue), and 580 to 700 nm (red).

EXAMPLES 1–9

Syntheses of red phosphors in accordance with this invention were carried out by firing well ground samples of rare earth oxide, bismuth oxide and NH₄VO₃ in an alumina crucible at 600° C. for 24 h. The products were then removed from the furnace, cooled, finely ground and reheated at 800° C. for another 24–48 h to complete the reaction. In some cases, another round of regrinding was needed. The rare-earth vanadate compounds are white powders (yellow or orange when there is unreacted vanadium oxide), which become yellowish with increasing Bi-content. The dopant atoms were Eu³⁺ (added as Eu₂O₃) and Sm³⁺ (added as Sm₂O₃) and the doping concentration was about 5 mol % (of the Ln³⁺+Bi³⁺) in each of the syntheses. The final products were characterized by powder X-ray diffraction, photoluminescence and photoexcitation spectroscopy.

X-ray diffraction studies on Bi_xLn_1-xVO₄ samples doped with Eu³⁺

Structural studies of the system Bi_xGd_1-xVO₄ have shown the existence of two ranges of solid solution, as described above [Ghamri, et al., 1990]. The study of the mixed LnVO₄-BiVO₄ (Ln=Y, Gd, La) samples doped with Eu³⁺ samples shows the expected change in the XRD pattern with increasing bismuth concentration (FIG. 1). Samples with x≦0.65 show a powder pattern corresponding to the tetragonal zircon phase (FIGS. 1a–d), whereas for x>0.65 the powder pattern indicates that these samples contain a mixture of both monoclinic fergusonite and tetragonal zircon phases (FIGS. 1e,f). The pure BiVO₄ doped with Eu³⁺ shows the powder pattern corresponding to the monclinic form (FIG. 1g).

Spectral Properties of Bismuth-Rare-Earth Vanadates Doped with Eu³⁺

In general, the photoluminescence spectra of YVO₄-BiVO₄ doped with Eu³⁺ ions show strong ⁵D₀→⁷F₂ (614, 618 nm) and ⁵D₀→⁷F₁ (593 nm) emission lines on excitation at both 254 nm and 365 nm (FIG. 2). The excitation spectrum for monitoring the ⁵D₀→⁷F₂ emission of Eu³⁺ shows a broad charge-transfer band along with a sharp ⁷F₀→⁵L₆, Eu³⁺ line at 394 nm, the latter being a relatively weak spectral feature when compared to the broad C-T band (FIG. 3). The excitation spectrum in pure YVO₄ doped with Eu³⁺ shows a broad absorption maximum centered around ˜310 nm, and a band edge at 340 nm, however the absorption in the short-wavelength UV (240–275 nm) is very low. In the case of Bi_xY_1-xVO₄:Eu³⁺ the band edge shifts to longer wavelengths with increasing bismuth concentration. For example, the band edge in the excitation spectrum moves from 340 nm (for pure YVO₄, x=0) to ˜420 nm for the x=0.45 bismuth rich sample (FIG. 3). This increase occurs due to extra absorption involving the Bi—O component in addition to the V-O charge-transfer bands. This increase seems to be monotonic only when less than half (x=0.4–0.45 ) of the yttrium ions are substituted by Bi³⁺ ions. For substitutions exceeding more than half (x>0.45) of yttrium by Bi³⁺, the long-wavelength charge-transfer band diminishes in intensity and disappears completely for compositions with x>0.65; however, the absorption in the short-wavelength (240–275 nm) appears to increase gradually (FIG. 3).

The photoluminescence spectra of GdVO₄-BiVO₄ doped with Eu³⁺ again show the characteristic spectral lines for Eu³⁺ emission. The excitation spectrum for monitoring the ⁵D₀→⁷F₂ emission of Eu³⁺ shows a small absorption in the short-wavelength region (240–275 nm), a broad charge-transfer band at lower energies, and a sharp but weak ⁷F₀→⁵L₆, Eu³⁺ line at 394 nm (FIG. 4). The excitation spectrum in pure GdVO₄ doped with Eu³⁺ shows a band edge at 350 nm, but in the Bi_xGd_1-xVO₄:Eu³⁺ system the band edge shifts to longer wavelengths with increasing bismuth concentration, moving to ˜425 nm for the x=0.4 sample (FIG. 4). Again, this increase seems to be monotonic only when less than half (x=0.4) of the gadolinium ions are substituted by Bi³⁺ ions. For substitutions exceeding x=0.4, the long-wavelength charge-transfer band again decreases in intensity, as in the yttrium system, though the short-wavelength (240–275 nm) absorption increases gradually.

The photoluminescence spectra of LaVO₄-BiVO₄ doped with Eu³⁺ also show similar trends in luminescence properties with increasing bismuth content to those observed for yttrium-bismuth/gadolinium-bismuth vanadates (FIG. 5).

Spectral Properties of Bismuth-Yttrium Vanadates Doped with Sm³⁺

Sm⁺³ as an activator in YVO₄ is known to have high emission efficiency. There is also considerable similarity in the emission colors of both Sm³⁺ (orange red) and Eu³⁺ (red) in the vanadate lattice. The photoluminescence spectra YVO₄-BiVO₄ doped with Sm³⁺ ions show the main emission lines for Sm⁺³ are 564 (⁴G_5/2–⁶H_5/2), 601 (⁴G_5/2–⁶H_7/2) and 645, 654 nm (⁴G_5/2–⁶H_9/2) on excitation at 363.8 nm (FIG. 6). The excitation spectrum for monitoring the ⁴G_5/2→⁶H_9/2 emission of Sm³⁺ shows a weak absorption band at short wavelengths (240–275 nm), a broad charge-transfer band centered around ˜320 nm, plus the sharp Sm³⁺ lines (FIG. 7). The excitation spectrum in pure YVO₄ doped with Sm³⁺ shows a broad maximum centered around ˜320 nm with a band edge at 350 nm. In the case of Y_1-xBi_xVO₄:Sm³⁺ samples the charge-transfer band and the band edge shift to longer wavelengths with increasing bismuth concentration. As the bismuth concentration increases the band edge in the excitation spectrum moves from 340 nm (for pure YVO₄x=0) to ˜415 nm for (x=0.4) bismuth rich samples. As with the other systems described above, this increase seems to be monotonic only when less than half (x=0.4) of the yttrium ions are substituted by Bi³⁺ ions. For substitutions exceeding x>0.45 of yttrium by Bi³⁺ ions the long-wavelength charge-transfer band decreases drastically in intensity, whereas the absorption at short wavelengths (240–275 nm) increases gradually (FIG. 7).

In Table 1, we list the comparison of emission intensities of the Bi_xY_1-xVO₄:Eu³⁺ ions to that of the standard Y₂O₂S:Eu³⁺ red phosphor on excitation at 400 nm. The samples containing low concentrations of Bi³⁺ show a decreased Eu³⁺ emission when compared to that of the standard red phosphor when excited at 400 nm, whereas the samples containing bismuth x≧0.2 show a much enhanced emission, the highest being in sample containing bismuth x=0.3. The increase in the emission intensity of Eu³⁺ with Bi³⁺ content is due the energy transfer from Bi³⁺ center to Eu³⁺. Increased bismuth content decreases the efficiency of this energy transport from the matrix to Eu³⁺, perhaps by distorting the former. Such distortions may arise from the chemical and electronic nature of Y³⁺ and Bi³⁺ ions.

TABLE 1
Comparison of emission intensities of the
Y1–xBixVO4:Eu3+ ions to that of the standard Y2O2S:Eu3+
red phosphor
Example	Composition	Emission Intensity (λexc = 400 nm)
	Y2O2S:Eu (standard)	3.3
1	Y0.95Eu0.05VO4	0.13
2	Y0.90Bi0.05Eu0.05VO4	0.15
3	Y0.85Bi0.10Eu0.05VO4	0.12
4	Y0.75Bi0.20Eu0.05VO4	0.72
5	Y0.70Bi0.25Eu0.05VO4	0.77
6	Y0.65Bi0.30Eu0.05VO4	1.2
7	Y0.60Bi0.35Eu0.05VO4	0.81
8	Y0.55Bi0.40Eu0.05VO4	0.97
9	Y0.50Bi0.45Eu0.05VO4	0.71

The Bi_xY_1-xVO₄ samples codoped with Eu³⁺, Tb³⁺ or Eu³⁺, Pr³⁺ ions also show a similar comparison to the standard red phosphor when their emission intensities were measured at 400 nm. No energy transfer from the Tb³⁺ or Pr³⁺ was observed as expected in the beginning, though the reasons to this effect are still unclear. Further study in this regard is under progress.

Datta, et al. showed that for the YVO₄:Eu, Bi system, increasing amount of Bi³⁺ ions in the lattice, the excitation bands shift to longer wavelengths. The 6s²→6s6p transition of Bi³⁺ ions often contributes to the luminescence of bismuth-doped phosphors [Blasse, et al. 1968]. We believe that the extra absorption and the band shift towards longer wavelengths in the excitation spectrum of LnVO₄-BiVo₄ samples doped with Eu³⁺ or Sm³⁺ involves the absorption due to Bi³⁺ ions. Such extra absorption has also been witnessed in other cases when ns² ions have been introduced in other host lattices absorbing in the UV region, for example, CaWO₄-PbWO₄ [Blasse, et al. 1994], Y₂WO₆-Bi [Blasse, et al. 1968]. The more puzzling observation however, is that the excitation spectra of the Bi_1-xLn_xVO₄ samples doped with Eu³⁺ or Sm³⁺ show a decrease in the long wavelength absorption above a critical bismuth concentration. Literature reports on bismuth, antimony niobates and tantalates have concluded that if ns² ions are in a more favorable asymmetrical coordination, the outer electrons (ns²) tend to be more localized and stabilized, so their influence on the luminescence of the surrounding centers is smaller [Wiegel, et al.]. The excitation spectra of the samples with low bismuth content (x≦0.4) can be explained by the fact that Bi³⁺ ions are present in a more symmetrical (zircon-type) environment, and hence the 6s² electrons are on top of the 2p level of O²⁻ as a result of which the excitation band shifts to longer wavelengths. Beyond a certain limit increasing bismuth content (0.4<x<0.64), we observe a drastic reduction in the long-wavelength absorption in the excitation spectra, even though the samples are still with in the composition regime of the zircon phase (0<x<0.64). The luminescence behavior of the Bi_1-xLn_xVO_v:Eu/Sm samples with 0.4<x<0.64 must stem from distortion of the bismuth environments as more Bi is introduced into the zircon structure.

EXAMPLES 10–19

Syntheses of other red phosphors having the general formula: Bi_xLn_1-xVO₄:A, where x=0 to 1, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Eu³⁺, Sm³⁺ and Pr³⁺, combination thereof, with or without Tb³⁺ as a co-dopant can be synthesized using the procedure of Examples 1–9. Thus, well ground samples of rare earth oxide, bismuth oxide and NH₄VO₃ can be fired in an alumina crucible at 600° C. for 24 h. The products can then be removed from the furnace, cooled, finely ground and reheated at 800° C. for another 24–48 h to complete the reaction, with another round of regrinding if needed. Dopant atoms of Eu³⁺ (as Eu₂O₃), Sm³⁺ (as Sm₂O₃), and/or Pr³⁺ (Pr₂O₃) can be added at a doping concentration of about 5 mol % (of the Ln³⁺+Bi³⁺) in each of the syntheses. To some of the compositions ˜25 to 40 ppm of Tb³⁺ can be added. The final red phosphors, which will have formulas shown in Table 2, can be characterized by powder X-ray diffraction, photoluminescence and photoexcitation spectroscopy.

TABLE 2
Compositions of Examples 10–19
Example Composition
10      Y0.95Sm0.05VO4
11      Y0.95Pr0.05VO4
12      Y0.90Bi0.05Sm0.05VO4
13      Y0.85Bi0.10Pr0.05VO4
14      Y0.75Bi0.20Eu0.03Sm0.02VO4
15      Y0.70Bi0.25Eu0.02Pr0.03VO4
16      Y0.65Bi0.30Eu0.04999Tb0.00001VO4
17      Y0.60Bi0.35Eu0.025Pr0.02499Tb0.00001VO4
18      Y0.55Bi0.40Eu0.025Sm0.02499Tb0.00001VO4
19      Y0.50Bi0.45Eu0.025Sm0.01Pr0.01499Tb0.00001VO4

REFERENCES

• Blasse, G. and A. Bril, J. Chem. Phys. 1968 48(1) 217.
• Blasse, G., and B. C. Grabmeier, Luminescent Materials, (Springer-Verlag, Berlin, 1994).
• Datta, R. K., J. Electrochem. Soc. 1967, 114(10) 1057.
• Ghamri, J., H. Baussart, M. Lebras and J. M. Leroy, J. Phys. Chem. Solids, 1989, 50, 1237.
• Ghamri, J., H. Baussart, M. Lebras and J. M. Leroy, Ann. Chim-Sci Mat. 1990 15(3) 111.
• Shinoya, M., and W. M. Yen, Phosphor HandBook, (CRC Press, 1999)
• Steigerwald, D. A., J. C. Bhat, D. Collins, R. M. Fletcher, M. O. Holcomb, M. J. Ludowise, P. S. Martin and S. L. Rudaz, IEEE. J. Sel. Top. Quant. 2002, 8(2) 310.
• Wiegel, M., W. Middel and G. Blasse, J. Mater. Chem. 1995, 5(7) 981.

Claims

1. A light emitting GaN based device, comprising: a semiconductor device capable of emitting light having a wavelength in the range of 200 nm to 620 nm; a blue phosphor; and a red phosphor having the formula: BixLn1-xVO4:Awhere X is 0.05 to 0.5, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Eu3+, Sm3+ and Pr3+, or any combination thereof.

2. The device of claim 1 in which the red phosphor is capable of absorbing light of a wavelength in the range of 240 nm to 550 nm and capable of emitting red light at a wavelength in the range of 580 nm to 700 nm.

3. The device of claim 1 in which the semiconductor device comprises a vertical cavity surface emitting laser, a light emitting diode, or a laser diode.

4. A light emitting GaN based device of claim 1, further comprising Tb3+ as a co-dopant.

5. A light emitting device, comprising: a semiconductor device capable of emitting light having a wavelength in the range of 200 nm to 620 nm; anda red phosphor having a formula of BixLn1-xVO4:A

6. The device of claim 5 in which x is greater than 0 and less than 1.

7. The device of claim 6 in which x is 0.05 to 0.5.

8. A white light emitting phosphor combination, comprising: a red phosphor having the formula of: BixLn1-xVO4:Awhere x is 0.05 to 0.5, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Eu3+, Sm3+ and Pr3+, or any combination thereof,a green phosphor; anda blue phosphor.

9. A white light emitting phosphor combination of claim 8, further comprising Tb3+ as a co-dopant.

10. A light emitting GaN based device, comprising: a semiconductor device capable of emitting light having a wavelength in the range of 200 nm to 620 nm; a blue phosphor; and a red phosphor having the formula: BixLn1-xVO4:Awhere x is greater than zero and less than 1, Ln is an element selected from the group consisting of Y, La and Gd, and A is an activator selected from Sm3+ and Pr3+, or any combination thereof.

11. A light emitting GaN based device of claim 10, further comprising further comprising Tb3+ as a co-dopant.