Ca1−xLixAl1−xSi1+xN3:Eu2+ solid solutions as broadband, color-tunable and thermally robust red phosphors for superior color rendition white light-emitting diodes

Color rendition, luminous efficacy and reliability are three key technical parameters for white light-emitting diodes (wLEDs) that are dominantly determined by down-conversion phosphors. However, there is usually an inevitable trade-off between color rendition and luminescence efficacy because the spectrum of red phosphor (that is, spectral broadness and position) cannot satisfy them simultaneously. In this work, we report a very promising red phosphor that can minimize the aforementioned trade-off via structure and band-gap engineering, achieved by introducing isostructural LiSi2N3 into CaAlSiN3:Eu2+. The solid solution phosphors show both substantial spectra broadening (88→117 nm) and blueshift (652→642 nm), along with a significant improvement in thermal quenching (only a 6% reduction at 150 °C), which are strongly associated with electronic and crystal structure evolutions. The broadband and robust red phosphor thus enables fabrication of super-high color rendering wLEDs (Ra=95 and R9=96) concurrently with the maintenance of a high-luminous efficacy (101 lm W−1), validating its superiority in high-performance solid state lightings over currently used red phosphors.


INTRODUCTION
White light-emitting diodes (wLEDs) are broadly known as one of most efficient and environmental friendly lighting technology, greatly contributing to energy saving and greenhouse gas reduction 1,2 . They are now gradually replacing traditional incandescent bulbs and fluorescence tubes for general lighting, and their luminous efficacy, color rendition and reliability are key factors determining these replacements. For those wLEDs using a single garnet yellow phosphor (Y 3 Al 5 O 12 :Ce 3+ ), the insufficient red component in the spectra leads to a small color rendering index (Rao80), making them unsuitable for high-quality general lighting 3 . A single Eu 2+ -doped oxychloride whitelight phosphor was reported to produce high color rendering wLEDs (Ra = 91, R9 = 90.2), but unfortunately, it cannot be excited by blue LEDs 4 . Recently, Pan discovered a broadband yellow phosphor (Ba 0.93 Eu 0.07 Al 2 O 4 ) with an enhanced red spectral component, which yields a medium color rendition (Ra~85) 5 . However, to achieve much higher color rendering indices, a red phosphor is thus essentially required to enhance the red spectral part [6][7][8] . Currently, several promising red-emitting phosphors have been proven to effectively enhance the color rendition, including (Ca, Sr, Ba) 2 Si 5 N 8 :Eu 2+ (ref. 9), (Sr, Ca)AlSiN 3 :Eu 2+ (refs 10,11), SrLiAl 3 N 4 :Eu 2+ (ref. 12) and K 2 (Si, Ti)F 6 :Mn 4+ (refs 8,13).
In general, multi-phosphor-converted wLEDs have higher color rendition (Ra480) but lower luminous efficacy (~70%) than onephosphor-converted wLEDs 14 . This indicates that there exists a fundamental trade-off relation between color rendering index and luminous efficacy, which means that improvements in one generally coincide with diminishment of the other. Moreover, even for the color rendering index, except for the Ra value (the average of the first eight color rendering indices), the ninth color rendering index (R9, the red content) has received much attention because reds are everywhere: there is much red in the color of human skin and of meat, fruits and vegetables, clothes and so on. The R9 value is always negative for onephosphor-converted wLEDs, and increases largely by complementing a red phosphor 3,7,12 . Kimura 7 combined a phosphor blend of BaSi 2 O 2 N 2 :Eu 2+ , β-sialon:Eu 2+ , Ca-α-sialon:Eu 2+ and CaAlSiN 3 :Eu 2+ with a blue LED and fabricated high-rendition wLEDs with Ra = 95-98, R9 = 89 and a luminous efficacy of 28-35 lm W − 1 .
As mentioned above, the narrow-band or short-wavelength (blueshifted) red phosphors are able to attain high-luminous efficacy but also decrease color rendering indices (typically R9). To eliminate or minimize this trade-off, there is a need for the red phosphor to have both a broadband and blueshifted emission simultaneously. CaAlSiN 3 : Eu 2+ is a deep-red phosphor and superior to its counterparts, such as Sr 2 Si 5 N 8 :Eu 2+ and K 2 SiF 6 :Mn 4+ , in thermal stability, reliability and quantum efficiency 16,17 . The color tuning of CaAlSiN 3 :Eu 2+ can be achieved by Sr → Ca substitution. This leads to a substantial blueshift in emission (650 → 610 nm), but concurrently, an unfortunate dramatic narrowing in the full width at half maximum (FWHM) of the emission spectrum (94 → 75 nm) 11,18 . Recently, Huang and colleagues 19 observed emission spectral broadening in CaAlSiN 3 :Eu 2+ by co-doping with C and Al to form However, the mechanism of the spectral broadening remains elusive.
Structural disorder is often recognized as an origin of the spectral broadening in luminescent materials and can be created by introducing impurities in the crystal lattice 20,21 . CaAlSiN 3 is isostructural with LiSi 2 N 3 , both crystallizing in an orthorhombic Cmc2 1 structure, which makes it possible to introduce LiSi 2 N 3 into CaAlSiN 3 as an 'impurity' 22 . The introduction can also be considered as the double-substitution in CaAlSiN 3 , that is, [Li,Si] 5+ → [Ca,Al] 5+ . Silicon and aluminum randomly and equally reside at the same crystallographic site in the CaAlSiN 3 lattice; thus, the double-substitution will increase the Si/Al ratio and in turn result in an increase in the degree of structural disorder. The broadening of the emission spectrum is therefore anticipated. Moreover, the solid-solution formation between CaAlSiN 3 and LiSi 2 N 3 (Ca 1 − x Li x Al 1 − x Si 1+x N 3 ) will also definitely change the electronic and crystal structure of the host crystals, thus having a great influence on photoluminescence properties, such as the spectral tuning, luminescence efficiency and thermal quenching.
In this work, we report, for the first time, the realization of simultaneous spectral broadening and blueshift in CaAlSiN 3 :Eu 2+ by forming solid solutions via double cationic substitutions. The newly developed broadband red phosphors exhibit a high external quantum efficiency (70-78%) and enhanced thermal stability, enabling them to be superior to the commonly used Ca 1 − x Sr x AlSiN 3 :Eu 2+ in reliability and color rendition. We demonstrate that by using the Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ (x = 0.20) red phosphor, a super-high color rendering index (Ra = 95 and R9 = 96) can be achieved without compromising the luminous efficacy (~101 lm W − 1 ) of wLEDs.

MATERIALS AND METHODS
The phosphor powders of Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ were prepared by using a gas pressure sintering furnace. The x value was varied in the range of 0-0.22. Appropriate amounts of high purity Ca 3 N 2 , Si 3 N 4 , AlN, Li 3 N and EuN powders were mixed in a nitrogen-filled glove box (H 2 Oo1 ppm, O 2 o1 ppm). The powders were put into BN crucibles and fired at 1800°C for 2 h under 1.0 MPa nitrogen gas. The weak reducing atmosphere in the furnace, using graphite heating units, enabled the reduction of Eu 3+ (EuN) into Eu 2+ in the phosphor. After firing, the phosphor powders were pulverized by hand using a silicon nitride mortar and pestle, and further washed in deionized water at 60°C.
The chemical composition was measured by using an inductively coupled plasma-mass spectrometer (ICP-MS, Thermo Fisher Scientific K.K., Yokohama, Japan). The nitrogen and oxygen content was measured via the selective hot-gas extraction method (TC-436, CS-444LS, LECO CO., Tokyo, Japan). The microstructure of powders was imaged using a scanning electron microscope (S-5000; Hitachi Ltd., Tokyo, Japan).
The crystal structure was determined via X-ray powder diffraction (XRD; RINT Ultima-III, Rigaku Co., Tokyo, Japan) with Cu Kα radiation (λ = 1.54056 Å). The current and cathode voltage were 40 mA and 40 kV, respectively. The data of CaAlSiN 3 single crystals were utilized as an initial mode for the Rietveld refinement using the GSAS package.
The valence state of Eu ions in phosphors was measured by using an X-ray absorption fine structure, and was recorded at the BL37XU beamline of the SPring-8 synchrotron radiation facility (Hyogo, Japan).
The 29 Si-and 7 Li-MAS nuclear magnetic resonance (NMR) spectra were collected using a 14.1-T wide-bore Bruker Advance III spectrometer (Karlsruhe, Germany). A 4-mm MAS probe was used for 29 Si, with the sample spinning at 13.5 kHz, and a 3.2-mm probe was used for 7 Li, with the sample spinning at 10 kHz. The Larmor frequencies for 7 Li and 29 Si were 233.3 and 119.2 MHz, respectively. The excitation pulse was set as 1.7 μs (the π/6-pulse) for 7 Li, and 2.5 μs (the π/4-pulse) for 29 Si. The recycle delay was 2 and 60 s for 7 Li and 29 Si, respectively.
The diffusive reflection spectrum was obtained by using a UV-Vis spectrophotometer with an integrating sphere (JASCO, Ubest V-560, Tokyo, Japan). The Spectralon diffusive white standard was used for calibration. The luminescence spectra were recorded by using a fluorescent spectrophotometer (F-4500, Hitachi Ltd., Tokyo, Japan). A 200 W Xe lamp was used as an excitation source. Quantum efficiencies were measured by using an intensified multichannel spectrometer (MCPD-7000, Otsuka Electronics, Tokyo, Japan) and computed by using the equations proposed in the literature 23 . An ultrahigh vacuum SEM with a Gemini electron gun (Omicron, Bavaria, Germany) equipped with a cathodoluminescence (CL) system was used to measure CL spectra at room temperature 24 . The diameter of the electron beam was in the order of 10 nm. The specimen was irradiated for 1 h under electron beams of 5 kV and 1000 pA before measurements.
Thermal quenching was evaluated using the MCPD-7000 by heating the phosphor up to 250°C at a heating rate of 100°C min − 1 and holding at each temperature for 5 min. The high-temperature quantum efficiency was measured using a quantum yield spectrophotometer (QE-1100, Otsuka Electronics).
The prototype warm wLEDs were fabricated using a Chip-on-Board packaging solution by pumping the red Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ (x = 0 and 0.20) and commercial garnet green (LuAG or GYAG) phosphors using a blue InGaN LED chip (450 nm). Dow Corning@ OE2140 (Tokyo, Japan) was used as the epoxy resin for binding phosphors. The optical properties of these wLEDs were recorded using a spectroradiometer (LHS-1000, Everfine Co., Hangzhou, China). The spatial radiation spectrum was obtained by using a goniophotometer (LED626, Everfine Co., Hangzhou, China). wLEDs were driven at 60 mA and 2.925 V.

Structural evolutions
Measured using inductively coupled-plasma and an oxygen/nitrogen analyzer, the synthesized samples have actual chemical compositions very similar to the nominal ones, except that half of the Li content was evaporated at high temperatures (Supplementary Table S1). Moreover, a small amount of oxygen (equal for all samples) was detected due to the contamination of the raw nitride materials.
The XRD spectra of samples are illustrated in Figure 1. All of the diffraction peaks are identified as the CaAlSiN 3 phase, demonstrating the production of a solid solution between CaAlSiN 3 and LiSi 2 N 3 in all compositions (x = 0-0.22). The XRD peaks shift toward higher angles with increasing x, implying lattice shrinkage owing to the smaller Li + (0.76 Å, CN = 6) and Si 4+ (0.26 Å, CN = 4) ions compared with Ca 2+ (1.00 Å, CN = 6) and Al 3+ (0.39 Å, CN = 4) 25 . Moreover, as seen in Figure 1b, the XRD peaks are significantly split as the LiSi 2 N 3 content increases, indicative of the enhanced degree of structural disorder and lowered symmetry in the solid-solution phase. As we know, the structure of CaAlSiN 3 can be considered a distorted AlN-like wurtzite superstructure, in which Al and Si are randomly distributed and disordered on the 8b site 10,22 . The Si/Al ratio in the lattice becomes larger with the introduction of LiSi 2 N 3 and hence further increases the structural disorder. The decrease in structural symmetry is supported by the lattice energy calculations by Vienna Ab initio simulation package (VASP) 26,27 , which show that the monoclinic Cc structure may be more energetically stable than the orthorhombic structure for x = 0.2 ( Supplementary Fig. S1). In this work, we observed that the structure transition occurs at x ≥ 0.15.
The refined crystal structure data for samples with x = 0, 0.2 are given in Supplementary Fig. S2 and Supplementary Tables S2 and S3. The structural refinement of the samples reveals that the crystal structure of the solid-solution phases remains unchanged, but the lattice constants and the lattice volume linearly decrease as the solubility of LiSi 2 N 3 increases (Figure 2a and 2b). The shrinkage of a (1.32%) is much larger than that of the b (0.18%) and c (0.60%) constants. This leads to a total shrinkage of 2.33% of the cell volume. Furthermore, the ratio of a/b = 1.708 and c/(b/√3) = 1.542 for x = 0.20 implies that the sample has a structure that is remarkably distorted from the ideal wurtzite structure (a/b = 1.732, c H /a H = 1.633). Conversely, the average Ca(Eu)-N distance unusually increases with increasing LiSi 2 N 3 content to 2.6035 and 2.6179 Å for x = 0 and 0.2, respectively (Figure 2c). It thus leads to an expanded (Ca, Li, Eu)N 5 polyhedron that may influence the photoluminescence of the solid solution phosphors, as schematically shown in Figure 3d. The increased bond length of Ca(Eu)-N may be ascribed to the substitution of larger Ca 2+ ions by smaller Li + ones.
Interestingly, the (Si,Al)-N distances reduce linearly with the substitution, which is ascribed to the increased Si/Al ratio (1.0 for x = 0 and 1.5 for x = 0.2) as the LiSi 2 N 3 content increases (Figure 2d). Moreover, the Ca-(Si,Al) distance also becomes slightly smaller after the substitution.

Structural characterizations
Solid state NMR spectroscopy provides a very precise characterization of the local arrangement around atoms. As shown in Figure 4a, the 29 Si isotropic chemical shifts for both compositions are found to lie in a very narrow range, from δ Si = − 49 to δ Si = − 50.5 ppm, indicating that the silicon environments in all solid solution phases are electronically similar and that Si is tetrahedrally coordinated with N 29 . Moreover, the composition of x = 0.2 exhibits a resonance signal with a reduced intensity, broadened spectrum and negatively shifted peak, suggesting the enhanced Si-Al structural disorder.
The 7 Li-MAS NMR spectra of both samples (x = 0.1, 0.2) consist of a single intensified line at 1.08 ppm with a wide sideband pattern. The 7 Li chemical shift has been reported as 1.3 ppm for LiSi 2 N 3 (ref. 30). The small chemical shift difference between Ca 1 − x Li x Al 1 − x Si 1+x N 3 and LiSi 2 N 3 suggests that the local environments of Li + are geometrically similar. The presence of 7 Li signals also evidences the dissolution of LiSi 2 N 3 into CaAlSiN 3 .
The valence state of europium was investigated by analyzing the Eu L 3 XANES spectra of solid solution phosphors. EuCl 2 and Eu 2 O 3 were used as reference samples for labeling the position of Eu 2+ (6973.6 eV) and Eu 3+ (6982.1 eV), respectively. As seen in Supplementary Fig. S3, all of the spectra show a dominant Eu 2+ peak at~6973.0 eV and a Eu 3+ shoulder at~6981 eV, indicating the coexistence of Eu 2+ and Eu 3+ in all samples 31 . The Eu 2+ /Eu 3+ ratio, however, slightly increases as LiSi 2 N 3 is accommodated into CaAlSiN 3 . This increment may have a positive influence on the photoluminescence and thermal stability of phosphors, as reported for Sr 2 Si 5 N 8 :Eu 2+ by Yeh et al 32 .

Electronic and band structures
The band gaps of the Ca 1 − x Li x Al 1 − x Si 1+x N 3 samples were determined from their diffuse reflection spectra. As shown in Supplementary  Fig. S4, the band gap is~4.91 eV for the x = 0 sample and increases up to 5.08 eV for x = 0.22. This indicates that the introduction of LiSi 2 N 3 widens the band gap of CaAlSiN 3 progressively, which follows The band structure of the phosphors was calculated via firstprinciples using VASP 26,27 . As illustrated in Figure 5a, the band structure of the x = 0. 2 sample shows an indirect band gap of 3.42 eV.

Simultaneous spectral broadening and blueshift
In Supplementary Fig. S5, it is obvious that the emission of phosphors changes from deep red for x = 0 to orange for x = 0.22 under 365 nm excitation, indicating a significant blueshift in the emission spectra associated with the accommodation of LiSi 2 N 3 . Both external and internal quantum efficiencies of the samples slightly decrease as the LiSi 2 N 3 content increases. As shown in Supplementary Fig. S6, the  29 Si Chemical shift (ppm) 7 Li Chemical shift (ppm) Intensity (a.u.) Intensity (a.u.)  The emission spectra, measured under 450 nm excitation, demonstrate an obvious spectral broadening (Figure 6a and Supplementary  Fig. S7). The spectrum broadens as the left wing is enhanced and blueshifted, whereas the right wing remains almost unchanged. As shown in Figure 6b, the FWHM increases monotonically from 88 nm (x = 0) to 117 nm (x = 0.20). The large band width achieved at high LiSi 2 N 3 concentrations is very exceptional for a single Eu 2+ center. It is usually~90 nm in most hosts and even remarkably narrowed when Eu 2+ resides at a highly symmetric site (for example, SrLiAl 3 N 4 :Eu 2+~5 0 nm; β-sialon:Eu 2+~5 5 nm) 12,35 . The spectral width is exclusively dependent on the local environment surrounding Eu 2+ , including the site symmetry, coordination number, structural disorder and composition fluctuation. The anomalous spectral broadening of Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ can be attributed to (i) reduced structure symmetry, (ii) enhanced structural disorder and (iii) statistical composition fluctuation caused by the random distribution of Al and Si at the same crystallographic site.
Effects of both structural disorder and compositional fluctuation on the spectral broadening are also evidenced by measuring the CL spectrum of Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ . As seen in Figure 6c, the CL spectrum becomes inhomogeneous and again broadens with increasing LiSi 2 N 3 content. The FWHM is significantly increased from 91 nm (x = 0) to 141 nm (x = 0.2). Because the nitrogen concentration is almost unchanged in all samples, the variation of the Si/Al ratio hence plays a crucial role in the change of the spectral shape, as well as the spectral width. Analyzed via Gaussian fitting, the CL spectrum was divided into two sub-bands peaking at 590 nm (Eu I ) and 650 nm (Eu II ), respectively ( Supplementary Fig. S8). Eu I is believed to reside at a Si-rich site with a longer Eu I -Si distance, whereas Eu II resides at an Al-rich site with a shorter Eu II -Al distance because Si 4+ has a smaller ionic size than Al 3+ . The luminescence intensity ratio of Eu I /Eu II for compositions with x = 0, 0.05, 0.10, 0.15 and 0.20 is, respectively, 0.19, 0.45, 0.73, 1.27 and 1.80, which is in a good agreement with the enhanced left wing and broadened spectra.
In addition to the spectral broadening, the blueshift of both emission and excitation spectra is also an interesting feature of the solid solution phosphors (Figure 6a and Supplementary Fig. S7). The peak emission is blueshifted by 10 nm, moving from 652 nm (x = 0) to 642 nm (x = 0.20). It is already known that both lattice parameters and the cell volume reduce after the introduction of LiSi 2 N 3 and that the lattice shrinkage usually yields large crystal field splitting, which may redshift the photoluminescence spectra. However, this is not the case in this work. Besides the influence of the overall lattice volume, the luminescence of Eu 2+ is much more affected by the local environment and band-gap structure. The unexpected blueshift is therefore attributed to (i) an enlarged Ca(Eu)N 5 polyhedron that actually decreases the crystal field strength, (ii) an expanded band gap that lifts up the lowest position of the Eu 2+ 5d state and (iii) an enhanced Eu I emission intensity that increases the left wing of the emission band.
The blueshift of the deep-red CaAlSiN 3 :Eu 2+ is desired for achieving high-luminous efficacy because the emission spectrum will be much closer to the eye sensitivity curves. Its emission band can be dramatically blueshifted via the Sr substitution for Ca, but the band width is significantly narrowed simultanously 11 . As a result, the color rendering indices are sacrificed to obtain higher luminous efficacy when using (Sr,Ca)AlSiN 3 :Eu 2+ . To avoid such a loss in color rendition, spectral broadening is simultaneously requested to compensate the reduction of the red spectral component. Interestingly and fortunately, Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ shows both spectral broadening and blueshifting of the emission band, thus enabling it to be a very promising red phosphor for realizing high-luminous efficacy without sacrificing the color rendition.

Substantial enhancement in thermal quenching
The heat generated in LED chips, sometimes higher than 100°C, will definitely induce luminescence quenching or even degrade phosphors; thus, the phosphors must have small thermal quenching to sustain the long lifetime of LED devices. The temperature-dependent luminescence shown in Figure 7a indicates that thermal quenching is progressively reduced with increasing LiSi 2 N 3 content. At 150°C (~423 K), the emission intensity is reduced by 12% for x = 0 but only by 6% for x = 0.20. The difference in thermal stability is more pronounced at higher temperatures, showing a decline of 29% for x = 0 and 18% for x = 0.20 at 250°C (~523 K). The emission intensity was fitted according to the Arrhenius equation I T /I 0 = [1+A × exp(− E a /kT)] −1 , where I 0 and I T are, respectively, the intensities at absolute zero and temperatures of 25-250°C (298-523 K), A is a constant, and E a is the energy barrier for thermal quenching 36 . E a is shown to increase from 0.21 eV (x = 0) to 0.24 eV (x = 0.20), indicating a higher thermal barrier for luminescence quenching after the LiSi 2 N 3 substitution (Figure 7b). Such an improvement in thermal stability was also observed by Wang and colleagues 37 .
Moreover, the temperature-dependent quantum efficiency also has a similar tendency, showing a smaller thermally-induced reduction for the solid solution phosphors (Figure 7c). Although the introduction of LiSi 2 N 3 reduces the efficiency slightly at room temperature (that is,  Thermal quenching of a phosphor greatly depends on the electronic and band structures of host crystals, that is, on the crystallographic site where Eu 2+ resides and the position where the 5d state of Eu 2+ is in between the band gap. As mentioned, the band gap widens due to the substitution of [Li,Si] 5+ for [Ca,Al] 5+ in CaAlSiN 3 . This enlargement separates the distance (ΔE) between the highest position of the 5d state of Eu 2+ and the bottom of the conduction band to a larger degree, leading to an increased activation energy for thermal quenching and therefore minimizing the photoionization (Figure 7b). Moreover, as addressed by Liu and colleagues 17 , the second coordination sphere also yields an effect on the luminescence quenching. With LiSi 2 N 3 dissolving in the CaAlSiN 3 lattice, the second coordination sphere (that is, Eu[Si/Al] n polyhedron) is constrained with an increasing Si 4+ /Al 3+ ratio (from 1.0 to 1.5), counteracting the expansion of the first coordination sphere. This will result in a decrease of the nonradiative losses in the luminescence process and hence higher quenching temperatures. Wang and colleagues 37 proposed a remote control effect to interpret the enhanced thermal quenching as Li partially substitutes Ca in CaAlSiN 3 .
High efficiency and color rendering white LEDs (Sr,Ca)AlSiN 3 :Eu 2+ is an excellent short-wavelength red phosphor commonly used in highly efficient wLEDs, but its narrow emission band leads to a medium color rendering index Ra and a very low R9 index. The solid solution phosphors Ca 1 − x Li x Al 1 − x Si 1+x N 3 :Eu 2+ developed in this work exhibit both broadened and blueshifted emission spectra, enabling the simultaneous achievement of highluminous efficacy and color rendition wLEDs. To verify this, two compositions, with x = 0 (RD1, λ em = 652 nm, FWHM = 88 nm) and x = 0.20 (RD2, λ em = 642 nm, FWHM = 117 nm), were chosen as red phosphor to fabricate wLEDs and compared with a commercial (Sr, Ca)AlSiN 3 :Eu 2+ phosphor (RD3, λ em = 630 nm, FWHM = 84 nm). RD1 and RD2 were obtained by annealing the as-synthesized phosphors at 1800°C for 4 h; their particle morphologies are given in Supplementary Fig. S9. Both samples show an identical primary particle size of~5 μm. The external quantum efficiency of RD1 and RD2 is, respectively, increased to 78 and 70%, both being still smaller than 82% for RD3.
The type I white LEDs (samples A and B) were prepared by combining RD1/RD2 with a green (Ga,Y) 3 Al 5 O 12 :Ce 3+ (G1, λ em = 535 nm) and a blue BaSi 2 O 2 N 2 :Eu 2+ (B1, λ em = 490 nm) phosphor. As shown in Figure 8 and Table 1, white LEDs using RD2 generally have higher color rendering indices (for example, Ra and R9) than those using RD1. This indicates that the color rendition is not sacrificed due to the spectral blueshift in RD2 but compensated greatly by the spectral broadening. The luminous efficacy of the device using 400    Broadband and robust red-emitting nitride phosphor L Wang et al RD2 is 7% lower than that using RD1, which is attributable to the smaller quantum efficiency of RD2 (8% lower). It is believed that the luminous efficacy will be the same even if the processing conditions of RD2 are further optimized. For comparison with the commercial red phosphor (RD3), Type II wLEDs (samples C and D) were fabricated by combining RD2/RD3 with a green phosphor (G1). As shown, the color rendering index using RD3 (Ra = 84 and R9 = 21) is remarkably lowered, typically the R9 index, due to its narrowed and blueshifted emission band. This again demonstrates the trade-off between color rendering index and luminous efficacy by using common red phosphors. However, a higher color rendering index (Ra = 92, R9 = 69) can be maintained without compromising too much luminous efficacy when using RD2. The relatively low luminous efficacy (103 vs 123 lm W − 1 ) is actually again due to the low quantum efficiency of RD2. Much higher color rendering indices of Ra = 95 and R9 = 96, as well as a high luminous efficacy of 101 lm W − 1 , are obtained by combining RD2 with a shortwavelength Lu 3 Al 5 O 12 :Ce 3+ green phosphor (G2, λ em = 525 nm). This highlights the point that a good balance between the luminous efficacy and color rendition occurs when utilizing the broadband and blueshifted red phosphor discovered in the current work.

CONCLUSIONS
Spectral tuning of phosphors is of great importance to control or optimize the optical properties of solid state lighting devices. In this work, by applying the structure and band-gap engineering strategies, we have developed a promising Ca 1-x Li x Al 1-x Si 1+x N 3 :Eu 2+ solid solution red phosphor with simultaneous spectral broadening and blueshift and solved the essential trade-off between luminous efficacy and color rendition. High-performance wLEDs with super-high color rendering indices of Ra = 96 and R9 = 95 and a preserved luminous efficacy of 101 lm W − 1 have been attained by using the broadband red phosphor. Due to the constrained second coordination sphere and widened band gap, a substantial improvement in thermal quenching has also been obtained after LiSi 2 N 3 substitution. This new broadband red phosphor is superior in color quality and thermal stability to red phosphors, such as (Ca 1 − x Sr x )AlSiN 3 :Eu 2+ and K 2 SiF 6 :Mn 4+ , currently used for general lighting.