Judd–Ofelt Analysis and Emission Properties of Dy3+ Ions in Borogermanate Glasses

Abstract

Borogermanate glasses singly doped with Dy³⁺ ions were synthesized and then studied using the absorption and luminescence spectra. Spectroscopic changes of Dy³⁺ ions have been examined for compositional-dependent glasses with various molar ratios GeO₂:B₂O₃. In this work, several spectroscopic parameters of Dy³⁺ ions were obtained experimentally and compared to the calculated values from the Judd–Ofelt theory. Luminescence spectra measured for borogermanate glasses consist of blue, yellow and red bands, which correspond to ⁴F_9/2 → ⁶H_15/2, ⁴F_9/2 → ⁶H_13/2 and ⁴F_9/2 → ⁶H_11/2 transitions of Dy³⁺, respectively. Luminescence lifetimes for the ⁴F_9/2 excited state are reduced, whereas the stimulated emission cross-sections for the most intense ⁴F_9/2 → ⁶H_13/2 yellow transition of Dy³⁺ increase with increasing GeO₂ and decreasing B₂O₃ concentrations in glass-hosts. Quantum efficiency of the ⁴F_9/2 (Dy³⁺) excited state is nearly independent on molar ratios GeO₂:B₂O₃. Attractive spectroscopic properties related to the ⁴F_9/2 → ⁶H_13/2 transition of Dy³⁺ ions are found for borogermanate glasses implying their potential utility for yellow laser action and solid-state lighting technology.

1. Introduction

Judd [1] and Ofelt [2] published their pioneering scientific works concerning the absorption intensities of rare earths 60 years ago. Based on the Judd–Ofelt (J-O) framework, several spectroscopic parameters for the optically active ions from the lanthanide series can be determined, which are really important from the optical and laser points of view. The most important of which are the radiative transition probability, the luminescence branching ratio and the radiative lifetime for the upper laser state of rare earth ions. The radiative transition probability and spectral linewidth for luminescent transition of rare earth ions can be used to calculate the peak stimulated emission cross-section, whereas measured emission lifetime and radiative lifetime calculated from the J-O framework are usually applied to estimate the quantum efficiency of the excited state. As a result, many glass matrices doped with rare earths can be quite well evaluated for a variety of possible applications such as for optical components and devices. Therefore, the J–O theory made a huge contribution to the development of optical and laser glasses in modern photonics. Since then, numerous published papers have been devoted to the study of glasses, glass-ceramics and other inorganic compounds singly or doubly doped with rare earth ions [3,4,5,6,7,8] using the theory on the intensities of 4f-4f electronic transitions introduced by Judd and Ofelt in 1962. In particular, the Judd–Ofelt analysis was performed for trivalent Nd³⁺ [9,10,11,12,13,14,15,16,17], Er³⁺ [18,19,20,21,22,23,24,25,26,27,28,29,30], Sm³⁺ [31,32,33,34,35], Pr³⁺ [36,37,38,39,40], Tm³⁺ [41,42,43,44], Ho³⁺ [45,46,47,48,49,50] and Dy³⁺ [51,52,53,54,55,56,57,58] ions in various inorganic glasses. The later trivalent rare earth ions, i.e., Dy³⁺ ions, were successfully used as an optical probe to study the luminescence behavior of inorganic glasses [59]. Recently, systematic investigations indicate that dysprosium doped glasses are excellent candidates for solid-state yellow lasers, white LEDs and other photonic device applications [60,61,62,63]. Their luminescence properties depend strongly on glass-network-modifiers [64], excitation wavelength and activator concentration [65].

In this work, the influence of glass-network-formers on the spectroscopic properties of dysprosium ions in borogermanate glasses has been examined in detail. Previous studies revealed that borogermanate glass belongs to amorphous systems with extremely different glass-network-formers B₂O₃ and GeO₂, influencing the spectroscopic properties of Cr³⁺ and Eu³⁺ [66]. Further investigations revealed that borogermanate glasses are suitable to fabricate CsPbBr_3−xI_x quantum dots with tunable visible emissions ranging from 577 nm to 672 nm [67]. In addition, they are able to accommodate rare earth ions. Thus, borogermanate glasses singly [68] and doubly [69] doped with rare earths are promising for luminescence applications. In recent years, borogermanate glass doped with Dy³⁺ has also been studied, but luminescence properties were analyzed as a function of activator content. Gökçe and Koçyiğit [70] suggest that Dy³⁺ doped gadolinium borogermanate glass matrix with the following composition 30B₂O₃-40GeO₂-(30-x)Gd₂O₃-xDy₂O₃ (where x = 0.25, 0.5, 1) presents excellent luminescence properties and can be used for laser and white LED applications. Numerous works published in recent years are concerned with glasses and their spectroscopic properties varying with activator (Dy³⁺) content [71,72,73,74,75,76,77,78,79,80,81]. These aspects have been discussed along with the reported Dy³⁺ doped glass systems in an excellent paper published last year [82]. However, Dy³⁺-doped glasses have not been examined often as a function of chemical composition and the spectroscopic results are less documented in the literature. Previous studies for compositional-dependent germanosilicate glasses demonstrate that the intensities of emission bands are the largest for glass samples with the molar ratio GeO₂:SiO₂ = 3:1 and the optimal concentration of Dy³⁺ ions equal to 0.5 mol% [83]. It was also confirmed for zinc aluminoborosilicate glasses, where luminescence quenching is observed beyond 0.5 mol% Dy³⁺ ions suggesting the presence of an energy-transfer process through cross-relaxation channels [84].

This paper is concerned with Dy³⁺-doped borogermanate glasses and their emission properties varying with glass-host composition. Absorption and emission properties have been analyzed for glass samples, where the molar ratios of glass-network-formers GeO₂:B₂O₃ are changed significantly and the activator concentration is equal to 0.5 mol% Dy³⁺. In particular, several spectroscopic parameters for Dy³⁺ ions were obtained experimentally and compared with theoretical values calculated from the J–O theory.

2. Materials and Methods

Borogermanate glasses doped with Dy³⁺ ions with the following composition given in molar%: (60-x)GeO₂-xB₂O₃-30BaO-9.5Ga₂O₃-0.5Dy₂O₃ (x = 0, 5, 10, 20, 30, 40, 50, 60) were prepared previously and details are given in Ref. [85]. For better clarity, glass codes and chemical compositions of the studied samples varying with glass formers GeO₂ and B₂O₃ marked in bold are shown in Table 1.

Glass samples were synthesized using a melt-quenching technique. Starting components of high purity 99.99% (Aldrich Chemical Co., St. Louis, MO, USA) were used for glass synthesis. All oxide components were mixed in an agate mortar for homogenization. Then, glass batches were placed in an Al₂O₃ crucible and melted at temperature T = 1250 °C for t = 45 min in an electric furnace. The received glass samples were cooled to room temperature and then polished for optical measurements. Photographs of the Dy³⁺ doped glass samples are shown in Figure 1.

The refractive indices of glass series were determined using the Metricon 2010 prism coupler at a wavelength of 632.8 nm. The optical absorption spectra measurements were performed using the UV-VIS-NIR spectrophotometer (Cary 5000, Agilent Technology, Santa Clara, CA, USA). The emission spectra and decays were recorded using laser equipment, which consists of a Photon Technology International (PTI) Quanta-Master 40 (QM40) UV/VIS Steady State Spectrofluorometer (Photon Technology International, Birmingham, NJ, USA) with a xenon lamp as an excitation source, Nd:YAG laser (Opotek Opolette 355 LD, OPOTEK, Carlsband, CA, USA) with a tunable pulsed optical parametric oscillator, double 200 mm monochromator and multimode UVVIS PMT R928 detector (PTI Model 914). Resolution for emission spectra measurements was 0.1 nm, whereas decays were measured with an accuracy of 1 µs.

3. Theoretical Background

The measured oscillator strengths of transitions were obtained from the absorption bands of Dy³⁺ ions. They were estimated by measuring the areas under the absorption bands of Dy³⁺ ions using the equation:

(1)${\mathrm{P}}_{\mathrm{meas}}=4.318\times {10}^{-9}\int \mathsf{\epsilon }(\mathsf{\nu })\mathrm{d}\mathsf{\nu }$

where: ∫ε(ν) represents the area under the absorption line and ε(ν) = A/(c × l), A indicates the absorbance, c is the concentration of the Dy³⁺ ion (in mol × l⁻¹) and l denotes the optical path length. The theoretical oscillator strengths for each absorption transition of Dy³⁺ ions were calculated using the Judd–Ofelt theory [1,2]. The theoretical oscillator strength is defined as follows:

(2)${\mathrm{P}}_{\mathrm{calc}}=\frac{8{\mathsf{\pi }}^2\mathrm{m}\mathrm{c}{({\mathrm{n}}^2+2)}^2}{3\mathrm{h}\mathsf{\lambda }(2\mathrm{J}+1)\mathsf{\cdot }9\mathrm{n}}\times {\displaystyle \sum _{\mathrm{t}=2,4,6}{\mathsf{\Omega }}_{\mathrm{t}}}{(<4{\mathrm{f}}^{\mathrm{N}}\mathrm{J}\Vert {\mathrm{U}}^{\mathrm{t}}\Vert 4{\mathrm{f}}^{\mathrm{N}}{\mathrm{J}}^{\prime }>)}^2$

where λ denotes the mean wavelength of each transition, whereas m, c, h and n are the mass of the electron, the velocity of light, the Planck constant and the refractive index of the medium, respectively. In this relation, ║U^t║² represents the square of the matrix elements of the unit tensor operator U^t. The values of ║U^t║² used for Dy³⁺ were adopted from Ref. [86]. The theoretical oscillator strengths were compared to the experimental values obtained from the optical absorption spectra of Dy³⁺ ions in borogermanate glasses and the phenomenological intensity parameters Ω_t (where t = 2, 4, 6) were determined. The fit quality was expressed by the magnitude of the root-mean-square deviation. It was defined by rms = Σ (P_meas − P_calc)². These three Judd–Ofelt intensity parameters Ω_t (t = 2, 4, 6) were used to calculate the radiative transition probabilities, the luminescence branching ratios and the radiative lifetimes. The radiative transition probabilities A_J for the excited states of Dy³⁺ ions were calculated using the relation given below:

(3)${\mathrm{A}}_{\mathrm{J}}=\frac{64{\mathsf{\pi }}^4{\mathrm{e}}^2}{3\mathrm{h}(2\mathrm{J}+1){\mathsf{\lambda }}^3}\times \frac{\mathrm{n}{({\mathrm{n}}^2+2)}^2}{9}\times {\displaystyle \sum _{\mathrm{t}=2,4,6}{\mathsf{\Omega }}_{\mathrm{t}}}{(<4{\mathrm{f}}^{\mathrm{N}}\mathrm{J}\Vert {\mathrm{U}}^{\mathrm{t}}\Vert 4{\mathrm{f}}^{\mathrm{N}}{\mathrm{J}}^{\prime }>)}^2$

The luminescence branching ratio β is related to the relative intensities of transitions from the excited state to all terminal states of Dy³⁺ ions.

(4)$\mathsf{\beta }=\frac{{\mathrm{A}}_{\mathrm{J}}}{{\displaystyle \sum _{\mathrm{i}}{\mathrm{A}}_{\mathrm{J}\mathrm{i}}}}$

The radiative lifetime τ_rad is the inverse of the total radiative transition probability (the sum of the A_J terms). Its value was compared to the experimental lifetime received from the luminescence decay curve. Both calculated and measured lifetimes were applied to determine the quantum efficiency of an excited state η. The appropriate relations are given below:

(5)${\mathsf{\tau }}_{\mathrm{rad}}=\frac{1}{{\displaystyle \sum _i{\mathrm{A}}_{\mathrm{J}\mathrm{i}}}}=\frac{1}{{\mathrm{A}}_{\mathrm{T}}}$

(6)$\mathsf{\eta }=\frac{{\mathsf{\tau }}_{\mathrm{m}}}{{\mathsf{\tau }}_{\mathrm{rad}}}\times 100\%$

Finally, the emission linewidth Δλ referred as full width at half maximum (FWHM) and the radiative transition probability A_J were successfully used to calculate the peak stimulated emission cross-section σ_em using the following expression:

(7)${\mathsf{\sigma }}_{\mathrm{em}}=\frac{{\mathsf{\lambda }}_{\mathrm{p}}^4}{8\mathsf{\pi }\mathrm{c}{\mathrm{n}}^2\Delta \mathsf{\lambda }}{\mathrm{A}}_{\mathrm{J}}$

where λ_p is the peak emission wavelength for the electronic transition of Dy³⁺.

All theoretical and experimental spectroscopic parameters for Dy³⁺ ions in the studied borogermanate glasses are summarized in Table 2.

4. Results and Discussion

Judd–Ofelt analysis of Dy³⁺ ions in mixed borogermanate glasses with various GeO₂:B₂O₃ molar ratios equal to 11:1, 5:1, 2:1, 1:1, 1:2 and 1:5 was carried out. Theoretical and experimental results were compared to GeO₂-BaO-Ga₂O₃ and B₂O₃-BaO-Ga₂O₃ glasses. Absorption and emission properties have been examined for glass samples, where the concentration of Dy³⁺ ions was the same (0.5 mol%). Firstly, the absorption spectra measurements for Dy³⁺ ions in borogermanate glasses were carried out at room temperature. The absorption spectra of borogermanate glasses doped with Dy³⁺ ions were measured in the UV-visible and near-infrared spectral ranges, respectively. The spectra consist of inhomogeneously broadened absorption bands characteristic for 4f⁹-4f⁹ electronic transitions of Dy³⁺. The absorption bands correspond to transitions originating from the ⁶H_15/2 ground state to the following excited states: ⁶H_11/2, ⁶F_11/2, ⁶F_9/2, ⁶F_7/2, ⁶F_3/2, ⁴F_9/2, ⁴I_15/2, ⁴G_11/2, ⁴I_13/2, ⁴F_7/2, (⁴M_19/2+⁴D_3/2+⁶P_5/2), ⁶P_7/2 and ⁶P_3/2. The later transition, i.e., ⁶H_15/2 → ⁶P_3/2 transition, is clearly visible for GeO₂-BaO-Ga₂O₃ glass contrary to B₂O₃-BaO-Ga₂O₃ glass. For mixed borogermanate glasses, the ⁶H_15/2 → ⁶P_3/2 transition of Dy³⁺ lies on the absorption edge. This indicates that the absorption edge is shifted to longer wavelengths from GeO₂-BaO-Ga₂O₃ glass via mixed B₂O₃-GeO₂-BaO-Ga₂O₃ compositions to B₂O₃-BaO-Ga₂O₃ glass, respectively. The absorption spectra are presented in Figure 2.

From the optical absorption spectra, the experimental oscillator strengths for Dy³⁺ ions have been determined. Owing to the standard procedure, the x-axes of absorption spectra were converted to wavenumbers (given in cm⁻¹). In the next step, the baseline was fitted individually to each absorption band. The integrated areas of absorption bands were calculated. The intensities of absorption lines of Dy³⁺ ions presented in Figure 2 were estimated by measuring the areas under the bands, and then applied to determine the experimental oscillator strengths using relation (1). The commercially available software OriginPro was used during the calculation procedure.

The theoretical oscillator strengths for each transition of Dy³⁺ ions were calculated from the J–O framework (Part 3) using relation (2). In order to perform the analysis, the refractive index of the medium was used for calculations. The refractive index is changed from 1.736 for GeO₂-BaO-Ga₂O₃ glass to 1.605 for B₂O₃-BaO-Ga₂O₃ glass. The refractive indices for the studied glass samples are schematized in Figure 3.

The experimental oscillator strengths from the absorption spectra and theoretical oscillator strengths were compared. They are shown in Table 3 and Table 4.

The main calculation process is related to three phenomenological Judd–Ofelt intensity parameters Ω_t (t = 2, 4, 6), which were obtained by comparison of the experimental oscillator strengths from the absorption spectra with the theoretical oscillator strengths from Equation (2) of the Judd–Ofelt framework (Part 3) using the fitting procedure. The quality of the fit shown in Table 3 and Table 4 expressed by the rms deviation defined by Σ(P_meas − P_calc)² (see Part 3) is quite good. The rms deviations for the studied glass systems varying with GeO₂/B₂O₃ molar ratios are in the range 0.23–0.58 (×10⁻⁶). The error is within the acceptable range compared to similar glass doped with Dy³⁺ [70], which was studied using the Judd–Ofelt framework. The three Judd–Ofelt intensity parameters Ω_t (t = 2, 4, 6) are necessary to calculate some spectroscopic parameters such as the radiative transition probabilities and the luminescence branching ratios, and then the radiative lifetimes, the quantum efficiencies of excited states and the peak stimulated emission cross-sections for electronic transitions of Dy³⁺ ions. The three Judd–Ofelt intensity parameters Ω_t (t = 2, 4, 6) for Dy³⁺ ions in borogermanate glasses are given in Table 5.

It is generally accepted that the phenomenological Judd–Ofelt intensity parameter Ω₂ reflects the asymmetry of the environment of trivalent dysprosium ions. In other words, the values of Ω₂ exhibit the degree of covalency between Dy³⁺ ions and their nearest surroundings. For the studied glass systems, the Judd–Ofelt parameter Ω₂ is reduced from 8.73 × 10⁻²⁰ cm² for GeO₂-BaO-Ga₂O₃ glass to 5.92 × 10⁻²⁰ cm² for B₂O₃-BaO-Ga₂O₃ glass suggesting more ionic bonding between Dy³⁺ ions and ligands with increasing B₂O₃ concentration. The results are in good agreement with values of Ω₂ calculated for similar germanate or germanate-tellurite glasses based on Na₂O-MgO-Al₂O₃-GeO₂ composition (Ω₂ = 8.62 × 10⁻²⁰ cm²) referred to as NMAG [87] and Na₂O-ZnO-PbO-GeO₂-TeO₂ composition (Ω₂ = 7.34 × 10⁻²⁰ cm²) referred to as NZPGT [88] as well as obtained for similar borate glasses based on the B₂O₃-CaF₂-CaO-BaO-Al₂O₃ system (Ω₂ = 5.98 × 10⁻²⁰ cm²) referred to as CFB [89] and B₂O₃-ZnO-Al₂O₃-Bi₂O₃ (Ω₂ = 6.20 × 10⁻²⁰ cm²) referred to as ZnAlBiB [90]. Following that, the Judd–Ofelt intensity parameters Ω₄ and Ω₆ are structure-dependent, i.e., the parameter Ω₄ describes the viscosity of the glass medium while the parameter Ω₆ is connected with the rigidity of the glass medium. Interestingly, GeO₂-BaO-Ga₂O₃ glass and borogermanate glasses with lower B₂O₃ content (GeO₂:B₂O₃ from 11:1 to 2:1) exhibit Ω₄ > Ω₆, whereas B₂O₃-BaO-Ga₂O₃ glass and borogermanate glasses with relatively higher B₂O₃ content (GeO₂:B₂O₃ = 1:2 and 1:5) possess Ω₄ < Ω₆ (Table 3). The same situation was observed earlier for germanate, germanate-tellurite and tellurite glasses [87,87,91], where Ω₄ > Ω₆ contrary to borate or phosphate glasses [90,92,93], where Ω₄ < Ω₆. However, further investigations for borate-based glasses suggest that Ω₄ < Ω₆ can be changed to Ω₄ > Ω₆ with decreasing Dy³⁺ concentration [94]. For glass with GeO₂:B₂O₃ = 1:1 both the Judd–Ofelt parameters Ω₄ and Ω₆ are nearly the same as Dy³⁺ doped silicate glass based on SiO₂–Al₂O₃–PbF₂–AlF₃–YbF₃–DyF₃ composition [95].

It was concluded that the intensity parameters Ω₄ and Ω₆ depend not only on the viscosity and rigidity, but they are also affected by the acidity and basicity of the glass-host, i.e., the highest Ω₄ and Ω₆ indicates the lowest basicity of the glass and the highest hardness [83]. In particular, the parameter Ω₆ is reduced systematically with increasing basicity and decreasing rigidity of the glass [96]. The calculation results given in Table 5 clearly indicate that the intensity parameter Ω₆ increases from GeO₂-BaO-Ga₂O₃ glass to B₂O₃-BaO-Ga₂O₃ glass. The values of Ω₆ are larger for glass samples containing higher B₂O₃ concentrations suggesting their lower basicity and higher rigidity. Further studies suggest that the Judd–Ofelt intensity parameters Ω₄ and Ω₆ not only influence the physicochemical properties of glasses but also strongly affect the radiative transition probabilities as a result of the interaction between trivalent dysprosium ions and their nearest environments [97].

Following that, the spectroscopic quality parameter χ referred to as the magnitude of Ω₄/Ω₆ belongs to important factors characterizing the optical potential of the currently prepared glass. It was presented and discussed in detail for several glass systems doped with Dy³⁺ ions [91]. For borogermanate glass systems, the values of χ are relatively large, which demonstrates quite well the intense luminescent transitions of Dy³⁺ ions. Luminescence studies for multicomponent glass based on B₂O₃–Bi₂O₃–SrO–Al₂O₃–PbO–Dy₂O₃ revealed that the spectroscopic quality factor χ ≥ 0.50, can be suggested as a good optical candidate for the lasing action of dysprosium ions [80].

The three phenomenological J–O intensity parameters Ω_t (t = 2, 4, 6) were applied to calculate the radiative transition probabilities and the luminescence branching ratios using the appropriate Relations (3) and (4) given in Part 3. The results are summarized in Table 6 and Table 7. The total radiative transition probability A_TOTAL referred to as the sum of the A_J terms from the ⁴F_9/2 excited state of dysprosium ions increases with increasing GeO₂ concentration. The value of A_TOTAL changed from 904 s⁻¹ for B₂O₃-BaO-Ga₂O₃ glass to 933 s⁻¹ (GeO₂:B₂O₃ = 1:5), 1065 s⁻¹ (GeO₂:B₂O₃ = 1:2), 1095 s⁻¹ (GeO₂:B₂O₃ = 1:1), 1124 s⁻¹ (GeO₂:B₂O₃ = 2:1), 1278 s⁻¹ (GeO₂:B₂O₃ = 5:1), 1311 s⁻¹ (GeO₂:B₂O₃ = 11:1) and 1495 s⁻¹ for GeO₂-BaO-Ga₂O₃ glass, respectively. In all cases, the luminescence branching ratio is the highest for the ⁴F_9/2 → ⁶H_13/2 electronic transition of Dy³⁺ ions at 573 nm. Its value changed from 69.1% to 74.5% depending on the chemical composition of the glass-host. The calculation results suggest that the studied borogermanate glass systems are promising for yellow emission independently on molar ratios GeO₂:B₂O₃. The luminescence spectra measurements confirm this hypothesis.

Figure 4 presents the luminescence spectra of Dy³⁺ ions in borogermanate glasses. The spectra for glasses based on B₂O₃-BaO-Ga₂O₃ and GeO₂-BaO-Ga₂O₃ are also indicated. The emission spectra show three characteristic bands of Dy³⁺ ions located at blue, yellow and red spectral range. These luminescence bands are attributed to ⁴F_9/2 → ⁶H_15/2 (blue), ⁴F_9/2 → ⁶H_13/2 (yellow) and ⁴F_9/2 → ⁶H_11/2 transitions of trivalent dysprosium. In previous work [85], the influence of glass former (GeO₂), oxide (CaO/SrO/BaO) and fluoride (CaF₂/SrF₂/BaF₂) glass modifiers on spectral properties, the yellow-to-blue luminescence intensity ratios and CIE coordinates of Dy³⁺ in borate-based glasses have been examined in detail. The studies revealed that the CIE chromaticity coordinates (x, y) are changed significantly with molar ratios GeO₂:B₂O₃ in glass composition. The CIE coordinates are changed from (x = 0.405, y = 0.452) to (x = 0.430, y = 0.472) with increasing GeO₂ content, which contributes to color modification of the borogermanate glass system from greenish to yellowish. These experimental results are presented and discussed in the previously published work [85]. The luminescent transitions of Dy³⁺ ions are indicated in the energy level diagram shown in Figure 5.

The luminescent results presented in Figure 4 indicate that the intensities are the highest for yellow bands related to the ⁴F_9/2 → ⁶H_13/2 transition of Dy³⁺, independently on GeO₂:B₂O₃ ratios. In addition, the ⁴F_9/2 → ⁶H_13/2 transition of Dy³⁺ ions is so-called hypersensitive transition, which follows the selection rules ⏐S⏐ = 0, ⏐ΔL⏐ ≤ 2 and ⏐ΔJ⏐ ≤ 2. The emission intensities as well as the spectral profiles and positions are very sensitive to even small changes of the nearest environment around dysprosium ions. The same situation is observed for the absorption band centered near 1250 nm due to transition originating from the ⁶H_15/2 ground state to the ⁶F_11/2 state. Figure 6 shows hypersensitive absorption and emission transitions of Dy³⁺ varying with GeO₂:B₂O₃ molar ratios. In order to compare the spectral profile and position of hypersensitive transitions, the spectra were normalized. Spectroscopic analysis indicates that the spectra are broader with increasing B₂O₃ content. These effects are significantly stronger for absorption than emission bands.

Further luminescent studies suggest that yellow-to-blue factor Y/B (Dy³⁺) due to the ratio of the integrated emission intensities (⁴F_9/2 → ⁶H_13/2)/(⁴F_9/2 → ⁶H_15/2) is changed significantly with molar ratios GeO₂:B₂O₃ in glass composition. The values of Y/B (Dy³⁺) are reduced from 4.22 for GeO₂-BaO-Ga₂O₃ glass to 2.80 for B₂O₃-BaO-Ga₂O₃ glass with increasing B₂O₃ concentration suggesting more ionic bonding between Dy³⁺ ions and surrounding ligands. The results are in a good agreement with the calculated values of the intensity parameters Ω₂, which decrease from 8.73 for GeO₂-BaO-Ga₂O₃ glass to 5.92 for B₂O₃-BaO-Ga₂O₃ glass indicating more ionic bonding in character. It was schematized on Figure 7.

The same situation is also observed for the peak stimulated emission cross-section calculated from Equation (7) in Part 3 for the ⁴F_9/2 → ⁶H_13/2 transition of Dy³⁺ at 573 nm, which is decreased with increasing B₂O₃ content (Figure 7). The values of σ_em given in 10⁻²¹ cm² are changed from 3.05 for GeO₂-BaO-Ga₂O₃ glass to 2.63 (GeO₂:B₂O₃ = 11:1), 2.54 (GeO₂:B₂O₃ = 5:1), 2.25 (GeO₂:B₂O₃ = 2:1), 2.22 (GeO₂:B₂O₃ = 1:1), 2.13 (GeO₂:B₂O₃ = 1:2), 1.99 (GeO₂:B₂O₃ = 1:5) and 1.93 for B₂O₃-BaO-Ga₂O₃ glass, respectively.

From the series of the studied glass samples, the stimulated emission cross section is the highest (σ_em = 3.05 × 10⁻²¹ cm²) for GeO₂-BaO-Ga₂O₃ glass. Its value is comparable to the one obtained for the ⁴F_9/2 → ⁶H_13/2 transition of Dy³⁺ ions in germanate-tellurite glasses based on GeO₂-TeO₂-SrF₂ composition (σ_em = 3.1 × 10⁻²¹ cm²) referred as GTS [98] and Na₂O-ZnO-PbO-GeO₂-TeO₂ composition (σ_em = 3.66 × 10⁻²¹ cm²) known as NZPGT [88].

Finally, luminescence decays from the ⁴F_9/2 state of Dy³⁺ ions have been analyzed in detail. Decay curves for the ⁴F_9/2 (Dy³⁺) state in borogermanate glasses were measured under excitation 454 nm and monitoring emission wavelength 573 nm. The luminescence decay curves for Dy³⁺ are presented in Figure 8. The obtained results clearly demonstrated that decays are longer with increasing B₂O₃ concentration in glass composition.

Based on decay curve measurements, luminescence lifetimes for the ⁴F_9/2 state of Dy³⁺ ions were determined. Next, measured lifetimes were compared to the radiative lifetimes (Equation (5), Part 3) calculated from the J–O theory. Both measured τ_m and radiative τ_rad lifetimes were used to calculate quantum efficiency (Equation (6), Part 3). The measured lifetimes and quantum efficiencies for the ⁴F_9/2 state of Dy³⁺ varying with GeO₂:B₂O₃ molar ratios are schematically shown in Figure 9.

The ⁴F_9/2 lifetime of Dy³⁺ ions in GeO₂-BaO-Ga₂O₃ glass is close to 348 µs and its value is comparable to the results (τ_m = 356 µs) obtained for lead germanate glass based on PbO-Ga₂O₃-GeO₂ [99]. The experimental values of τ_m for mixed borogermanate glasses are equal to 352 µs (GeO₂:B₂O₃ = 11:1), 367 µs (GeO₂:B₂O₃ = 5:1), 407 µs (GeO₂:B₂O₃ = 2:1), 424 µs (GeO₂:B₂O₃ = 1:1), 452 µs (GeO₂:B₂O₃ = 1:2), and 473 µs (GeO₂:B₂O₃ = 1:5). The ⁴F_9/2 lifetime of Dy³⁺ ions is the highest (τ_m = 513 µs) for B₂O₃-BaO-Ga₂O₃ glass. In contrast to the dependences of luminescence intensity ratio Y/B and the peak stimulated emission cross-section for the ⁴F_9/2^® 6H_13/2 transition (Figure 7), the luminescence lifetime for the ⁴F_9/2 state of Dy³⁺ increases with increasing B₂O₃ content. It is experimentally evidenced that the non-radiative multiphonon relaxation probabilities of rare earth ions are increased significantly with increasing phonon energy from GeO₂ to B₂O₃. Glass based on GeO₂-BaO-Ga₂O₃ (~800 cm⁻¹) has relatively smaller phonon energy than B₂O₃-BaO-Ga₂O₃ glass (~1400 cm⁻¹). Thus, the measured lifetimes of rare earth ions are reduced from GeO₂ to B₂O₃ because multiphonon relaxation probabilities become higher with increasing B₂O₃ content. For example, this situation is observed for Er³⁺ ions, where the energy separation between the excited state ⁴I_13/2 and next lower-lying ground state ⁴I_15/2 is relatively small and non-radiative multiphonon relaxation provides an important contribution to the total relaxation process. The opposite effects are observed for other rare earth ions such as Tb³⁺, Eu³⁺ or Dy³⁺, where the energy gaps between the interacting levels are relatively large and non-radiative relaxation probabilities are negligibly small. Thus, luminescence lifetimes ⁴F_9/2 (Dy³⁺) are nearly equal to radiative lifetimes calculated from the J–O theory and their experimental values increase from GeO₂-BaO-Ga₂O₃ glass to B₂O₃-BaO-Ga₂O₃ glass. It was also confirmed earlier by the measurements of luminescence decay curves for rare earth ions in heavy metal oxide glasses referred to as HMOG. Previously published work clearly demonstrated that the dependence of experimental luminescence lifetimes on the phonon energies of HMOG glass systems is completely different for the ⁵D₀ state of Eu³⁺ than for the ⁴I_13/2 state of Er³⁺ [100].

Further studies indicate that the quantum efficiency of excited state ⁴F_9/2 (Dy³⁺) is almost unchanged with increasing B₂O₃ concentration. The quantum efficiency for the ⁴F_9/2 state of Dy³⁺ in mixed borogermanate glasses seems to be 47 ± 1%, independently of GeO₂:B₂O₃ molar ratios. For GeO₂-BaO-Ga₂O₃ glass (η = 52%) the quantum efficiency is above 50%. The results obtained for borogermanate glasses singly doped with Dy³⁺ ions suggest their potential luminescent applications in the yellow spectral range [71,101].

5. Conclusions

Borogermanate glasses doped with Dy³⁺ have been studied experimentally and theoretically using the Judd–Ofelt framework. Based on absorption and emission spectra measurements, several spectroscopic parameters for Dy³⁺ ions were determined, such as the measured and calculated oscillator strengths, the Judd–Ofelt intensity parameters, the radiative transition probabilities, the luminescence branching ratios, the peak stimulated emission cross-sections, the measured and radiative (calculated) luminescence lifetimes and the quantum efficiencies of excited state. They have been examined as a function of GeO₂:B₂O₃ molar ratios in glass composition. The systematic investigations demonstrated that the peak stimulated emission cross-sections for the most intense ⁴F_9/2 → ⁶H_13/2 yellow transition of Dy³⁺ ions decrease, whereas the ⁴F_9/2 luminescence lifetimes are enhanced with increasing B₂O₃ concentration. The quantum efficiencies for the ⁴F_9/2 state of Dy³⁺ ions are close to η = 47 ± 1% and their values are nearly independent of GeO₂:B₂O₃ ratios. It was suggested that the results for borogermanate glasses doped with Dy³⁺ are attractive for yellow luminescence, providing an important contribution to the development of optical glasses and celebrating the 60th anniversary of the Judd–Ofelt theory.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The data presented in this study are available on request from the author.

Acknowledgments

The author thanks Marta Kuwik for luminescence spectra measurements. The research activities were co-financed by the funds granted under the Research Excellence Initiative of the University of Silesia in Katowice.

Conflicts of Interest

The author declares no conflict of interest.

Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Figures and Tables

Figure 1. Photographs of the Dy3+ doped glass samples: GeO2-BaO-Ga2O3 (1), GeO2:B2O3 = 11:1 (2), GeO2:B2O3 = 5:1 (3), GeO2:B2O3 = 2:1 (4), GeO2:B2O3 = 1:1 (5), GeO2:B2O3 = 1:2 (6), GeO2:B2O3 = 1:5 (7) and B2O3-BaO-Ga2O3 (8).

Figure 2. Absorption spectra for Dy3+ ions in borogermanate glasses with various molar ratios GeO2:B2O3 compared to GeO2-BaO-Ga2O3 and B2O3-BaO-Ga2O3 glasses. The spectra were measured in the UV-visible (a) and near-infrared (b) spectral ranges.

Figure 3. The refractive indices for borogermanate glasses.

Figure 4. Luminescence spectra for borogermanate glasses doped with Dy3+.

Figure 5. Energy level diagram for Dy3+ ions. Luminescent transitions are also indicated.

Figure 6. Hypersensitive absorption and emission transitions Dy3+ ions.

Figure 7. Luminescence intensity ratio Y/B (on left) and the peak stimulated emission cross-section for the 4F9/2 → 6H13/2 transition of Dy3+ ions in borogermanate glasses (on right).

Figure 8. Luminescence decay curves for the 4F9/2 state of Dy3+ ions in borogermanate glasses.

Figure 9. Luminescence lifetimes and quantum efficiencies for the 4F9/2 state of Dy3+ ions in borogermanate glasses.

Table 1

Glass codes and chemical compositions for glass samples doped with Dy³⁺ ions.

No	Glass Code	Chemical Composition [mol%]
(1)	GeO2-BaO-Ga2O3	60GeO2-30BaO-9.5Ga2O3-0.5Dy2O3
(2)	GeO2:B2O3 = 11:1	55GeO2-5B2O3-30BaO-9.5Ga2O3-0.5Dy2O3
(3)	GeO2:B2O3 = 5:1	50GeO2-10B2O3-30BaO-9.5Ga2O3-0.5Dy2O3
(4)	GeO2:B2O3 = 2:1	40GeO2-20B2O3-30BaO-9.5Ga2O3-0.5Dy2O3
(5)	GeO2:B2O3 = 1:1	30GeO2-30B2O3-30BaO-9.5Ga2O3-0.5Dy2O3
(6)	GeO2:B2O3 = 1:2	20GeO2-40B2O3-30BaO-9.5Ga2O3-0.5Dy2O3
(7)	GeO2:B2O3 = 1:5	10GeO2-50B2O3-30BaO-9.5Ga2O3-0.5Dy2O3
(8)	B2O3-BaO-Ga2O3	60B2O3-30BaO-9.5Ga2O3-0.5Dy2O3

Table 2

Theoretical and experimental spectroscopic parameters for Dy³⁺ in borogermanate glasses.

Parameters	Symbols	Units
Theoretical oscillator strength	Pcalc	-
Measure oscillator strength	Pmeas	-
Judd–Ofelt intensity parameters	Ωt (t = 2, 4, 6)	10−20 cm2
Spectroscopic quality parameter	χ (Ω4/Ω6)	-
Radiative transition probability	AJ	s−1
Total radiative transition probability	AT	s−1
Luminescence branching ratio	β	%
Radiative lifetime	τrad	µs
Measured lifetime	τmeas	µs
Quantum efficiency	η	%
Peak emission wavelength	λp	nm
Emission linewidth	Δλ	nm
Full width at half maximum	FWHM	nm
Peak stimulated emission cross-section	σem	10−21 cm2

Table 3

Measured and calculated oscillator strengths (P × 10⁻⁶) for Dy³⁺ ions in GeO₂-BaO-Ga₂O₃ glass and mixed borogermanate glasses with GeO₂:B₂O₃ = 11:1, 5:1 and 2:1.

Levels	Energy[cm−1]	GeO2-BaO-Ga2O3		GeO2:B2O3 = 11:1		GeO2:B2O3 = 5:1		GeO2:B2O3 = 2:1
		Pmeas	Pcalc	Pmeas	Pcalc	Pmeas	Pcalc	Pmeas	Pcalc
6H11/26F11/26F9/26F7/26F3/24F9/24I15/24G11/24F7/2,4I13/24M19/2,4D3/2,6P5/26P7/2	60407960930011,29013,45021,20022,20023,60025,90027,50028,700	1.2608.2201.5801.4100.0900.1500.3300.0750.8200.7303.070	1.1098.2401.7831.3910.1170.1050.3600.0630.6010.9322.364	1.0608.1501.5001.2600.0900.0800.3300.0700.7500.6503.200	0.9808.1611.6771.1680.0920.0870.3110.0690.5970.7542.648	1.1907.6001.5001.5800.1000.0800.3100.0650.7500.7202.910	1.0897.6131.7481.4170.1220.1070.3570.0570.5730.9602.157	1.1206.9801.4701.3100.1000.0700.3500.0900.9000.7002.770	0.9876.9981.6511.2980.1100.0980.3220.0570.5460.8712.160

Table 4

Measured and calculated oscillator strengths (P × 10⁻⁶) for Dy³⁺ ions in B₂O₃-BaO-Ga₂O₃ glass and mixed borogermanate glasses with GeO₂:B₂O₃ = 1:1, 1:2 and 1:5.

Levels	Energy[cm−1]	GeO2:B2O3 = 1:1		GeO2:B2O3 = 1:2		GeO2:B2O3 = 1:5		B2O3-BaO-Ga2O3
		Pmeas	Pcalc	Pmeas	Pcalc	Pmeas	Pcalc	Pmeas	Pcalc
6H11/26F11/26F9/26F7/26F3/24F9/24I15/24G11/24F7/2,4I13/24M19/2,4D3/2,6P5/26P7/2	60407960930011,29013,45021,20022,20023,60025,90027,50028,700	1.1606.8501.6501.1400.1400.1300.3500.0750.7500.7702.470	1.0006.8711.6901.3460.1150.1020.3280.0560.5510.9062.160	1.1706.1201.7201.8600.1000.0900.3600.0700.8000.8702.120	1.1376.1251.8671.6990.1550.1300.3860.0460.5491.1861.745	1.1205.6001.5801.4000.1000.0800.3400.0650.7500.8801.970	1.0045.6151.6591.4810.1340.1130.3390.0430.4961.0291.637	1.0905.3901.7401.6500.1600.1000.3300.0850.8100.7402.000	1.0385.3971.8101.6120.1460.1230.3530.0460.5311.1171.800

Table 5

Judd–Ofelt intensity parameters for Dy³⁺ ions in the studied glass systems.

Glasses	Judd–Ofelt Intensity Parameters Ωt (t = 2, 4, 6) [in 10−20 cm2 Units]			χ (Ω4/Ω6)
	Ω2	Ω4	Ω6
GeO2-BaO-Ga2O3GeO2:B2O3 = 11:1GeO2:B2O3 = 5:1GeO2:B2O3 = 2:1GeO2:B2O3 = 1:1GeO2:B2O3 = 1:2GeO2:B2O3 = 1:5B2O3-BaO-Ga2O3	8.73 ± 0.228.42 ± 0.178.09 ± 0.237.52 ± 0.217.45 ± 0.196.72 ± 0.176.27 ± 0.165.92 ± 0.13	1.44 ± 0.211.60 ± 0.151.52 ± 0.221.35 ± 0.201.37 ± 0.181.11 ± 0.151.06 ± 0.141.18 ± 0.12	1.33 ± 0.141.03 ± 0.101.40 ± 0.141.29 ± 0.131.36 ± 0.121.87 ± 0.101.65 ± 0.101.81 ± 0.08	1.081.551.091.051.000.600.640.65

Table 6

The radiative transition probabilities and luminescence branching ratios for Dy³⁺ ions in GeO₂-BaO-Ga₂O₃ glass and mixed borogermanate glasses with GeO₂:B₂O₃ = 11:1, 5:1 and 2:1.

Transition	λ [nm]	GeO2-BaO-Ga2O3		GeO2:B2O3 = 11:1		GeO2:B2O3 = 5:1		GeO2:B2O3 = 2:1
		AJ [s−1]	β	AJ [s−1]	β	AJ [s−1]	β	AJ [s−1]	β
4F9/2 → 6F1/26F3/26F5/26F7/26H5/26H7/26F9/26F11/26H9/26H11/26H13/26H15/2	137312751156992918836830749746662573480	>0.1>0.11564191136251251088165	--0.0100.0040.0030.0130.0070.0240.0170.0840.7280.110	>0.1>0.1134317103223108976125	--0.0100.0030.0020.0130.0080.0240.0180.0820.7450.095	>0.1>0.112431693022100932150	--0.0090.0040.0030.0130.0070.0230.0170.0780.7290.117	>0.1>0.11143158261988818132	--0.0100.0040.0030.0130.0070.0230.0170.0780.7280.117

Table 7

The radiative transition probabilities and luminescence branching ratios for Dy³⁺ ions in B₂O₃-BaO-Ga₂O₃ glass and mixed borogermanate glasses with GeO₂:B₂O₃ = 1:1, 1:2 and 1:5.

Transition	λ [nm]	GeO2:B2O3 = 1:1		GeO2:B2O3 = 1:2		GeO2:B2O3 = 1:5		B2O3-BaO-Ga2O3
		AJ [s−1]	β	AJ [s−1]	β	AJ [s−1]	β	AJ [s−1]	β
4F9/2 → 6F1/26F3/26F5/26F7/26H5/26H7/26F9/26F11/26H9/26H11/26H13/26H15/2	137312751156992918836830749746662573480	>0.1>0.11043158251985792134	--0.0090.0040.0030.0140.0070.0230.0170.0780.7230.122	>0.1>0.1943157231876743167	--0.0080.0040.0030.0140.0070.0220.0160.0710.6980.157	>0.1>0.1832136201667656142	--0.0090.0030.0020.0140.0070.0210.0170.0720.7030.152	>0.1>0.1732136191563625151	--0.0080.0030.0020.0140.0070.0210.0170.0700.6910.167

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