Effect of Li⁺ doping on the luminescence performance of a novel KAlSiO₄:Tb³⁺ green-emitting phosphor

Abstract

A new green-emitting phosphor, KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺, was prepared via a high-temperature solid-phase method, and its crystal structure, diffuse reflectance spectrum, and luminescence were studied. The results show that the Li⁺ doping shifts the strongest diffraction peak to a high angle direction, reducing grain size by 11.4%. The entry of Li₂CO₃ improves the luminescence performance of KAlSiO₄:1.5 mol% Tb³⁺. At a Li⁺ concentration of 1.5 mol%, the sample has strong absorption in the ultraviolet light range from 250 to 400 nm. The luminous intensity of the sample at 550 nm approximately quadruples after Li⁺ doping. Additionally, the colour purity of the sample and the internal quantum yield increase to 83.3% and 42%, respectively. The sample changes colour with time when exposed to air without an obvious fading phenomenon. The emission intensity at 200 °C is 95.1% of its value at room temperature, indicating that the phosphor has excellent thermal stability when x = 1.5. These results show the feasibility of using the silicate phosphor for generating the green light component of white light-emitting diodes for solid-state lighting.

Introduction

In recent years, rare earth luminescent materials have been widely used in white light-emitting diodes (w-LEDs) because of their long life and high efficiency¹. In commercial solid-state lighting, phosphor-converted LEDs (pc-WLEDs) offer many advantages including low cost, good colour rendering, high colour purity, and good chemical stability. pc-WLEDs have also attracted the attention of many researchers².

Silicate phosphor luminescent materials for LED lighting are made of cheap raw materials. They offer good thermal stability and have a long life. Muyasier et al. prepared a green Na₈Al₆Si₆O₂₄Cl₂: x mol% Tb³⁺ phosphor and analysed the luminescence spectrum and colour coordinates, and they found that the silicate phosphor has a lifetime of up to 2.8 ms with good thermal stability³. Wan et al. prepared BaAl₂Si₂O₈:Tb³⁺, Ce³⁺ phosphors, studied their photoluminescence characteristics, and found that they can be used as green phosphors⁴. Yu et al. prepared Sr₂SiO₄:Tb³⁺, Ce³⁺ phosphors with a lifetime of up to 2.85 ms. The colour of this phosphor can be changed from green to blue by using the high-temperature solid-phase method⁵. Dilare et al. prepared NaAlSi₃O₈:Tb³⁺ phosphor and obtained a new type of silicate luminescent material with tuneable colours from green to red⁶. KAlSiO₄ has potential applications in luminescent glass and optical devices. In recent years, a few groups have reported on artificially synthesised KAlSiO₄ doped with other rare earths to prepare three-color phosphors suitable for white LEDs.

Since Tb³⁺ has a strong green emission band in the wavelength range of 535 nm–555 nm, rare earth luminescent materials doped with Tb³⁺ can often be used to obtain the green component of an ideal white LED⁷. The actual luminous intensity of Tb³⁺ is generally determined by the crystal field coordination environment in the selected matrix. When different valencies are substituted, Li⁺ can often be used as a charge compensator or a flux to achieve the desired luminous efficiency. Li Zhen et al. reported a new green emitting phosphor Sr₂MgB₂O₆:Tb³⁺, x mol% Li⁺ with good thermal stability and a maximum doping concentration of 9 mol%⁸. Potassium aluminosilicate (KAlSiO₄) has a lattice site suitable for rare earth doping, and the corresponding crystal symmetry is relatively high. The standard card number of this material is 33–0989. In this study, a new type of green-emitting phosphor, KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺, was synthesised by a high-temperature solid-phase method. The crystal structure, photoluminescence characteristics, UV–Vis absorption spectrum, colour coordinates, and colour purity of the samples were systematically studied. The addition of Li⁺ improves the luminescence performance of KAlSiO₄:1.5 mol% Tb³⁺, making it a new type of green silicate phosphor with potential application as the green component of white LEDs.

Experimental results and discussion

Phase analysis of KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ series samples

Figure 1a shows the X-ray diffraction pattern of the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ (x = 0, 0.5, 1, 1.5, 2) sample. It can be seen from the figure that the diffraction peaks are consistent with the standard JCPDS No. 33–0989. Figure 1b shows an enlarged view of the strongest diffraction peak at 28.66°. The peak appears to gradually shift to a high-angle direction. Both Li⁺ and Tb³⁺ are added to the crystal lattice. It can be inferred that Li₂CO₃ can be used as a charge compensator in the KAlSiO₄ crystal lattice to adjust the valence state of ions to achieve charge balance¹. When CN = 7, Tb³⁺ (r = 0.098 nm) and Li⁺ (r = 0.092 nm) are close to the seven-coordinate K⁺ radius (r = 0.146 nm) in KAlSiO₄, whereas Si⁴⁺(r = 0.026 nm) and Al³⁺ (r = 0.039 nm) have smaller radii. Hence, Tb³⁺ and Li⁺ replace the K⁺ positions. According to the Bragg formula [Eq. (1)]⁶, the interplanar spacing (d) will be reduced after the substitution. Hence, the diffraction peak position moves to a higher angle direction.

$$2d\sin \theta = n\lambda$$

(1)

Figure 1

(a, b) X-ray diffraction pattern of KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺. (c) Crystal structure of KAlSiO₄. (d) Refined XRD image of KAlSiO₄:1.5 mol% Tb³⁺ and (e) KAlSiO₄:1.5 mol% Tb³⁺, 1.5 mol% Li⁺.

where θ is the Bragg angle of X-ray diffraction peak, d is the interplanar spacing, n stands for constant factor, and λ represents the incident X-ray wavelength.

Figure 1c shows the crystal structure of KAlSiO₄. There are many types of KAlSiO₄ space groups. The space group corresponding to KAlSiO₄ synthesised in this study is P212121(19), which is an orthorhombic structure (α = β = γ = 90°) with unit cell parameters a = 0.9057 nm, b = 1.5642 nm, c = 0.8582 nm, and V = 1.2158 nm³. It can be seen from the figure that K⁺ is filled between the [SiO₄] and [AlO₄] tetrahedrons. K⁺ has a 7-coordinated 4a site with higher symmetry and a 10-coordinated 4a site with lower symmetry in KAlSiO₄ crystals. The crystal structure along the z-axis has high symmetry. This is conducive to the narrowband emission of Tb³⁺.

Figure 1d,e show the refined XRD images of KAlSiO₄:1.5 mol% Tb³⁺ and KAlSiO₄:1.5 mol% Tb³⁺, 1.5% Li⁺, respectively. It can be seen from the refined diagram that the XRD refined results of this series of samples are reliable. It was further confirmed that Tb³⁺ and Li⁺ doping had no significant effect on the crystal structure of KAlSiO₄.

Figure 2a shows the variation of the unit cell parameters of KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ for various doping concentrations (x = 0, 0.5, 1, 1.5, 2). The changes in V, a, b, and c can be obtained from the refined XRD results. The relational formula [Eq. (2)]⁹ of the orthorhombic crystal plane spacing d (hkl) and crystal plane group (hkl) is used for the verification.

$$\frac{1}{{d^{2} }} = \frac{{h^{2} }}{{a^{2} }} + \frac{{k^{2} }}{{b^{2} }} + \frac{{l^{2} }}{{c^{2} }}$$

(2)

Figure 2

(a) Variation of the unit cell parameters with doping concentration (x = 0,0.5,1,1.5,2) for KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ (b) The relationship between x, the grain size, and the (202) crystal plane FWHM in KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺.

It can be seen from the figure that as the Li⁺ concentration increases, the values of V, a, b, and c decrease to varying degrees. When Tb³⁺ and Li⁺, which have a small radius, replaces the large radius of K⁺, the volume of the unit cell will shrink, causing the unit cell parameters to gradually show a downward trend.

Figure 2b shows the relationship between x in KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ (x = 0, 0.5, 1, 1.5, 2), the grain size and the (202) full width at half maximum (FWHM) of the crystal plane. The grain size (D) is calculated using Eq. (3)^{10, 11}.

$$D = \frac{K\lambda }{{W\cos \theta }}$$

(3)

Here, λ = 0.15406 nm and K = 0.89. W is the FWHM corresponding to the strongest diffraction peak, and θ is the angle of the strongest diffraction peak. With the increase in x, the grain size of the sample decreased by 11.4%, further confirming the shift of the XRD diffraction peak to the high-angle direction.

Luminescence characteristics of KAlSiO₄: x mol%Tb³⁺ series samples

Figure 3 shows the excitation and emission spectra of the representative sample KAlSiO₄: 1.5 mol% Tb³⁺. The inset is an enlarged view of the excitation spectrum in the range from 325 to 425 nm. Under the excitation of the characteristic excitation wavelength of Tb³⁺ at 378 nm, it can be seen from the figure that the strongest emission peak of the phosphor is at 550 nm, which belongs to the narrow-band green light emission. The phenomenon of spectral splitting occurs at 540 nm. This is because the 7 coordination of Tb³⁺ is substituted. K⁺ has a low symmetry position (Fig. 1c), which is affected by the crystal field environment. Compared with¹², the strongest emission peak has a blue shift of 5 nm. Under 550 nm monitoring, a charge transfer band appeared in the range from 200 to 300 nm. There are different excitation bands from 200–500 nm, indicating that the sample can be effectively excited by ultraviolet light. The charge transfer band (CTB) of Tb³⁺ ions at 249 nm is attributed to the 4f.-5d transition of Tb³⁺ ion^{7, 13}. Owing to the strong symmetry of potassium aluminosilicate belonging to the frame silicate series, the incorporated Tb³⁺ ions are less affected by the crystal field environment, and there is no obvious spectral split at 249 nm and 378 nm. When the sample was excited at 378 nm, it was found that the electrons in the ⁷F₆ ground state of Tb³⁺ in the sample were excited to the ⁵D_J (J = 2, 3, 4) excited state. These electrons then relaxed to the ⁵D₄ energy level by non-radiative transition, while some of the electrons undergo ⁵D₄ to ⁷F_J (J = 6, 5, 4, 3) radiative transition¹⁴.

Figure 3

Excitation and emission spectra of KAlSiO₄:1.5 mol% Tb³⁺ (the inset is an enlarged view of the excitation spectrum from 325–425 nm).

Figure 4 is a diagram of the concentration quenching mechanism of KAlSiO₄:x mol% Tb³⁺(x = 0.5, 1, 1.5, 2). It can be seen that when x = 1.5, the absorption intensity at 378 nm in the excitation spectrum is the strongest, resulting in the strongest emission intensity. The luminous intensity of the sample reaches its maximum, and concentration quenching occurs. When the concentration was increased beyond 1.5 mol%, the absorption intensity of each peak began to decrease slightly. The critical distance is calculated using Eq. (4)¹⁵:

$$R_{c} = 2\left( {\frac{3V}{{4\pi X_{e} N}}} \right)^{\frac{1}{3}}$$

(4)

R_c is the critical distance of concentration quenching, X_e is the critical concentration of Tb³⁺, V is the unit cell volume, and N is the number of unit cells. In this series of samples, V = 1.2158 nm³, X_e = 0.015, and N = 12. It is concluded that R_c = 2.35 nm, which is greater than 0.5 nm. (‘0.5 nm’ is an index that distinguishes exchange interaction and electrical multi-level interaction. When R_c > 0.5 nm, the concentration quenching mechanism is due to a multi-level interaction.) When a single activator is incorporated into the matrix, the relationship between the luminous intensity of the sample and the concentration of the activator x is as follows:

$$\lg ({I \mathord{\left/ {\vphantom {I x}} \right. \kern-\nulldelimiterspace} x}) = c - ({\theta \mathord{\left/ {\vphantom {\theta 3}} \right. \kern-\nulldelimiterspace} 3})lgx$$

(5)

θ is a multilevel interaction function, and c is a constant. n = 6, 8, and 10 represent dipole–dipole, dipole–quadrupole, and quadrupole–quadrupole interactions, respectively¹⁶. The sample is excited by near-ultraviolet light at 378 nm with x = 0.005, 0.01, 0.015, 0.02. The relationship between lg(I/x) and lg(x) at 550 nm is shown in Fig. 4. It was found that the fitting slope is -θ/3≈-3.62. Hence, θ≈10, which corresponds to the electric four-level interaction.

Figure 4

Concentration quenching mechanism diagram for KAlSiO₄: x mol% Tb³⁺ (x = 0.5, 1, 1.5, 2).

Luminescence characteristics of KAlSiO₄: 1.5 mol%Tb³⁺, x mol% Li⁺ series samples

Figure 5a shows the UV–Vis absorption spectrum of the KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ (x = 1, 1.5, 2) series samples. It can be seen from the figure that this series of samples absorbs UV light well in the 250–400 nm range. The strongest absorption peak at 249 nm is attributed to the charge transfer band transition (CTB) of Tb³⁺. The absorption peak at 283 nm is due to the 4f⁸ → 4f⁷5d¹ transition¹⁷. Weak absorption peaks appear at 352, 360, and 378 nm, respectively. The characteristics of the absorption spectrum are consistent with those of the excitation spectrum of the KAlSiO₄: 1.5 mol% Tb³⁺ sample. When x = 1, 1.5, and 2, three absorption peaks are obtained in the wavelength range from 300–400 nm, all of which are typical 4f.-4f. electronic transitions of Tb³⁺. When x = 1.5, the tangent of the absorption peak has the steepest slope. It shows that the KAlSiO₄:1.5 mol% Tb³⁺, 1.5 mol% Li⁺ sample shows the strongest absorption of ultraviolet light in the wavelength range from 250–800 nm. The excitation light of a commercial ultraviolet LED chip can effectively excite the sample. The strong absorption at 378 nm corresponds to the⁷F₆ → ⁵G₆ transition, and the other two weak absorptions at 352 nm and 360 nm originate from the⁷F₆ → ⁵D₂ and⁷F₆ → ⁵L₁₀ transitions, respectively. The results of UV–visible absorption spectroscopy showed that Tb³⁺ activator ions and Li⁺ were successfully incorporated into KAlSiO₄. This result is consistent with the XRD results.

Figure 5

(a) UV–Vis absorption spectrum and (b) UV–Vis-NIR diffuse reflectance spectrum of KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ (x = 1,1.5,2) series samples.

Figure 5b shows the UV–Vis-NIR diffuse reflectance spectrum of the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ (x = 1, 1.5, 2) series samples. It can be seen from the figure that the sample has strong absorption in the wavelength range from 250–400 nm, and the sample with x = 1.5 has the strongest absorption of ultraviolet and near-ultraviolet light. This result is consistent with the results of Figs. 3 and 5a. This further proves that this series of samples is suitable for excitation by white light LED chips. The strongest absorption peak at 249 nm is attributed to the 4f-5d charge transfer band transition of Tb³⁺ ion¹⁴. The absorption of the 4f-4f transition is weaker than that of the CTB transition.

Figure 6a,b shows the excitation spectrum and emission spectrum of the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ series samples. The excitation spectrum of this series of samples is obtained by monitoring with Tb³⁺ at 550 nm (⁵D₄ → ⁷F₅). There are a series of excitation bands in the range of 300-450 nm, the main peaks are respectively 318, 352, 359, 378 nm, of which the strongest peak is at 378 nm. It confirms that it can be excited by ultraviolet light, near ultraviolet light and blue light.

Figure 6

(a) Excitation spectrum and (b) emission spectrum of KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ series samples.

It can be seen that as x increases, the intensity of the strongest emission peak at 550 nm (when excited with 378 nm) initially increases and then decreases. The best luminescence intensity is achieved when x = 1.5 and is approximately 4 times the luminous intensity of the KAlSiO₄:1.5 mol% Tb³⁺ sample, which can further prove that after Li⁺ is added to the lattice, it promotes lattice matching. When x = 1.5, the quenching concentration of KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ can be obtained. At the same time, Li₂CO₃ can be used both as a charge compensation agent and as a flux. When Li₂CO₃ is used as a flux, Li⁺ can modulate the valence of Tb³⁺ ions, and it can contributes to the good light-emitting performance of the phosphor, that is to say, when the doping concentration of Tb³⁺ increases to 2 mol%, the luminescence performance of the sample is declined.

The substitution of K⁺ with Tb³⁺ is an unequal valency substitution. Doping with a small amount of Li⁺ can improve the lattice matching efficiency as it belongs to the same family as K⁺. This makes the cation charge in the crystal reach a relatively balanced state, thereby promoting the successful entry of Tb³⁺ into the K⁺ lattice site, and greatly enhancing the luminous efficiency of the strongest emission peak. This result shows that the incorporation of Li⁺ is beneficial for improving the luminous performance of the new KAlSiO₄:1.5 mol% Tb³⁺ green-emitting phosphor. Hence, the KAlSiO₄:1.5 mol% Tb³⁺, 1.5 mol% Li⁺ green-emitting phosphor is expected have higher luminous efficiency.

Figure 7a shows the lifetime decay curves of the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ series samples at 550 nm. It can be seen that as the Li⁺ concentration increases, the Tb³⁺ lifetime gradually increases. When x = 1.5, the lifetime value reaches the maximum, which is 3.99 ms. This lifetime value is 2.45 ms longer than that reported in¹⁸. The lifetime decay curve is completely consistent with the emission spectrum shown in Fig. 6, indicating that for the KAlSiO₄ matrix, the best doping concentration of both Tb³⁺ and Li⁺ is 1.5 mol%, which results in the highest luminous efficiency and the longest lifetime. It is suitable for use in white LED lighting. The lifetime value is calculated using Eq. (6)¹⁹:

$$\tau^{ * } = \frac{{A_{1} \tau_{1}^{2} + A_{2} \tau_{2}^{2} }}{{A_{1} \tau_{1} + A_{2} \tau_{2} }}$$

(6)

Figure. 7

(a) Lifetime decay curves of KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ series samples at 550 nm; (b) the energy level diagram of Tb³⁺ in KAlSiO₄.

Figure 7b shows the energy level diagram of Tb³⁺ in KAlSiO₄. The energy transfer between Tb³⁺-Tb³⁺ generally occurs in this way. For example, in this system, the excited state electrons will quickly relax to the lower 4f. state, such as⁵D₃,⁵D₄, and then return to ground state.

Figure 8a, b shows the relationship between x and the FWHM and the integrated peak area at 550 nm for the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ series samples. It can be seen from the figure that when x = 1.5, the FWHM value is minimised, which is suitable for backlight LED lighting. The integrated peak area intensity reaches a maximum, which is consistent with the emission spectrum characteristics shown in Fig. 6.

Figure 8

(a) Relationship between x and FWHM at 550 nm for KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ sample; (b) relationship between x and the integrated peak area at 550 nm for KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ sample.

Figure 9 shows the colour coordinates and body colour changes of the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ series samples. It can be seen that the colour coordinates of the samples do not change significantly with the increase in x. The colour coordinates of all the samples in the series are near the green region (0.33, 0.59), which preliminarily shows that the series of samples has good colour stability. The body colour of the sample gradually changes to deep green as x increases.

Figure 9

Colour coordinates and body colour changes of the KAlSiO₄: 1.5 mol% Tb³⁺, x mol% Li⁺ series samples.

Table 1 shows the colour coordinates, colour purity, internal quantum yield (IQY), and colour temperature (CCT) of the KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ series samples. It can be seen that the coordinates of all the samples are approximately (0.32, 0.56). The internal quantum yield is as high as 42%, the colour purity is as high as 83.3%, and the colour temperature of the samples is approximately 5500 K. The colour purity is calculated using Eq. (7)²⁰:

$$C_{p} = \frac{{\sqrt {(x_{s} - x_{i} )^{2} + (y_{s} - y_{i} )^{2} } }}{{\sqrt {(x_{d} - x_{i} )^{2} + (y_{d} - y_{i} )^{2} } }} \times 100\%$$

(7)

C_P is colour purity, (x_d, y_d) = (0.3473, 0.65) is the international standard colour coordinate corresponding to the main wavelength of 550 nm, (x_i, y_i) = (0.333, 0.333) is the colour coordinate of standard white light, and (x_s, y_s) is the colour coordinate of the series of samples. It can be seen from Table 1 that when x = 1.5, the sample colour purity is 83.3% and the quantum yield is 42%.

Table 1 Colour coordinates, colour purity, colour temperature, and internal quantum yield of KAlSiO₄: 1.5 mol % Tb³⁺, x mol % Li⁺ samples.

Figure 10 shows the emission spectrum of the KAlSiO₄: 1.5 mol% Tb³⁺, 1.5 mol% Li⁺ when it is stored and exposed to air for 0, 10, 20, and 30 days. The relationship between the sample body colour and the number of storage days is also shown in the figure. It can be seen from the figure that the emission intensity is gradually weakened. However, the luminous intensity is reduced by half, and the sample main body colour still emits green light when irradiated with a 365 nm UV lamp. This further shows that the new green-emitting fluorescent phosphor has good stability and is suitable for the green component of the three-primary white LED.

Figure 10

Variation of the emission peak intensity and sample body colour of KAlSiO₄:1.5 mol% Tb³⁺, 1.5 mol% Li⁺ with number of storage days.

The luminous performance of the phosphor suitable for white LED devices is generally determined by measuring the thermal stability of the phosphor. Figure 11 shows the variation of the intensity of the spectrum corresponding to KAlSiO₄: 1.5 mol% Tb³⁺, 1.5 mol% Li⁺ with temperature. It can be seen from the figure that when the temperature rises, the emission peak intensities of the phosphor at 550 nm at 50 °C, 100 °C, and 200 °C are 96.5%, 96%, and 95.1% at room temperature, respectively. This shows that the silicate phosphor has good luminous efficiency and good thermal stability. This shows that the luminescence performance of the silicate phosphor has room for improvement. It is expected to be suitable for green phosphors in LED devices for a new generation of solid-state lighting.

Figure 11

Variation of spectral light intensity of KAlSiO₄:1.5 mol% Tb³⁺, 1.5 mol% Li⁺ with temperature.

Conclusion

We have prepared a new green-emitting phosphor, KAlSiO₄:1.5 mol %Tb³⁺, x mol% Li⁺ (x = 0, 0.5, 1, 1.5, 2). The chemical structure of this series of samples is found to be highly stable. The doping of Tb³⁺ and Li⁺ does not affect the crystal structure of the matrix. After the small-radius rare earth ions replace K⁺, the grain size decreases by 11.4% with an increase in the concentration of Li⁺ doping. The optimal doping concentration of Li⁺ in KAlSiO₄:1.5 mol% Tb³⁺ was found to be 1.5 mol%. When x = 1.5, the sample strongly absorbs the ultraviolet light in the range from 250 to 400 nm. The luminous intensity of the KAlSiO₄:1.5 mol% Tb³⁺ sample at 550 nm is increased by 4 times. The sample lifetime increased to 3.99 ms, the integrated peak area at 550 nm reached the maximum, and the full width at half maximum dropped to 13.83 nm. These results are closely related to the highly symmetrical crystal structure of the sample matrix. The colour purity of the sample series was found to be 83.3%. The body colour of the samples showed a little change with the increase in storage days. The samples exhibited good colour stability and thermal stability. The experimental results show that the developed phosphor is expected to become a candidate material for the green component of solid-state lighting white LEDs.

Experiment

Sample preparation and characterisation

KAlSiO₄:1.5 mol% Tb³⁺, x mol% Li⁺ (x = 0.5, 1, 1.5, 2) was prepared in an MF-1750C Beyke high-temperature box furnace by the high-temperature solid-phase method at 1350 °C for 210 min. The main raw materials used are listed in Table 2. The Li₂CO₃ can act as a flux, which contributes to the favorable properties of the KAlSiO₄:1.5 mol% Tb³⁺ phosphors in this work¹.

Table 2 Raw materials of KAlSiO₄: Tb³⁺, Li⁺ phosphor.

The quality of all the raw materials was calculated by the stoichiometric molar ratio method (mol%). The weighed materials were placed into an agate mortar and ground for 35 min. The uniformly mixed series of samples were placed into corundum crucibles and calcined in a high-temperature box furnace at a heating rate of 5 °C/min. After cooling the sample to room temperature, it was removed and ground again for the sample loading test.

The instrument parameters and experimental methods used in this study are presented in Table 3.

Table 3 Instrument parameters and experimental methods used in this study.