Crystallization Process and Site-Selective Excitation of Nd 3+ in LaF 3 /NaLaF 4 Sol–Gel-Synthesized Transparent Glass-Ceramics

: In this study, transparent oxyﬂuoride glass-ceramics (GCs) with NaLaF 4 nanocrystals (NCs) were prepared by the sol–gel method for the ﬁrst time. Three different molar ratios of La(CH 3 COO) 3 /Na(CH 3 COO) were used to obtain the GCs, which were sintered at 450, 550 and 650 ◦ C for 1 min. X-ray diffraction (XRD) was employed to follow the evolution of the xerogel during the heat treatments and to study crystal growth for the three temperatures. In all cases, the LaF 3 crystalline phase was present, but crystallization of NaLaF 4 was only promoted at 650 ◦ C. Thermogravimetric and thermodifferential analysis (TGA-DTA) and Fourier transform infrared spectroscopy (FTIR) were used to analyze the crystallization process. High-resolution transmission electron microscopy (HRTEM) was employed to conﬁrm NaLaF 4 crystallization and determine the size distribution. The incorporation of Nd 3+ ion into NaLaF 4 and LaF 3 nanocrystals was conﬁrmed by site-selective emission and excitation spectra. The Nd 3+ emission intensities in both phases depend not only on the NaLaF 4 /LaF 3 ratio but also on their emission efﬁciencies.


Introduction
In recent years, transparent oxyfluoride glass-ceramics have attracted considerable attention due to their widespread application in scintillators, phosphors, photovoltaics and solid-state lasers [1][2][3]. In particular, rare-earth (RE) fluoride crystals are excellent hosts for up-and down-conversion luminescence associated with their unique characteristics, such as their low lattice phonon energy (lower than 500 cm −1 ) [4,5]. The short lifetime of the SiO 2 glass matrix, due to its high phonon energy, is compensated with the incorporation of the RE-fluoride nanocrystals. The final material combines the excellent mechanical and chemical properties of the glass with the luminescence of the crystalline phases [6].
The NaLnF 4 (Ln = Y, Gd, La and Lu) series acts as a host material with excellent physical and chemical stability, as well as low phonon energy. Moreover, the multisite nature of the crystalline structure imparts high efficiency in light emission [7,8]. In comparison with conventional lanthanides, such as Y or Gd, NaLaF 4 has the lowest phonon energy (290 cm −1 ) with a potentially higher up-conversion efficiency due to its non-radiation transitions [9]. It is a difficult challenge to obtain a single NaLaF 4 nanocrystal phase because the strong La 3+ -F − ionic bond favors precipitation of LaF 3 phase, which has significantly 2 of 11 lower free energy of formation than NaLaF 4 [9][10][11]. A mechanism to improve the crystallization of NaLaF 4 involves doping with rare-earth ions, which helps to stabilize the alkaline fluorides when its crystallization competes with that of other phases, such as LaF 3 [12,13].
Recently, transparent glass-ceramics containing NaLaF 4 as the only crystalline phase enclosed in a SiO 2 -enriched barrier have been synthesized by a conventional melting technique at 1600 • C, using LaF 3 as a precursor. However, very low crystalline fractions, around 5 wt.%, were reported to maintain the transparency after crystallization at 520 • C [14,15]. Controllable LaF 3 /NaLaF 4 crystallization by melt-quenching has also been reported recently; however, increasing the content of NaLaF 4 active phase was not achieved [16,17].
Alternative techniques have been proposed to avoid the drawbacks of melt-quenching, which involve reducing high-temperature fluoride loss. The sol-gel method (SG), based on the hydrolysis and polycondensation of metal salts or metal alkoxide precursors in a solvent, is a cheap and low-temperature technique that allows fine control of the chemical composition of glass-ceramic materials. SG also permits the incorporation of optical active particles or molecules into the glass matrix [18]. An important contribution regarding the preparation of sol-gel oxyfluoride glass-ceramics was made by Fujihara et al. by employing trifluoracetic acid (TFA) as a precursor of oxyfluoride GCs for the first time [19]. This process allows for the formation of fluoride nanocrystals instead of a random dispersion of La 3+ ions in the SiO 2 matrix. To date, sol-gel preparation of different oxyfluoride glass-ceramics doped with REs has proven suitable for controlling the synthesis and crystallization processes [19][20][21][22], with promising optical results [23][24][25][26][27] and unique location of the RE dopants in the fluoride host. However, the preparation of oxyfluoride of NaLaF 4 by an SG route has not yet been reported. The main objective of this work is to gain a first insight into the synthesis and optical properties of NaLaF 4 with a view to its application in the field of photonics. To this end, SiO 2 -NaLaF 4 GCs doped with Nd 3+ were prepared using different heat treatment conditions and varying the precursor ratios. Site-selective emission and excitation spectra allow the emission of Nd 3+ in the crystalline phases to be identified.
Finally, three different SiO 2 -NaLaF 4 /LaF 3 sols were prepared depending on the employed Na(CH 3 COO)/La(CH 3 COO) 3 molar ratio; the labels employed for the different samples are listed in Table 1.

Characterization
Thermogravimetric analysis (TGA) and differential thermal analysis (DTA) were performed using an SDT Q600-TA instrument to study the thermal transformation of the powder on the Sol-0.95 xerogel. The sample was heated from 25 • C to 800 • C with a heating rate of 10 • C/min under an inert atmosphere (Ar).
X-ray diffraction (XRD) was employed to identify the crystalline phases of the powders for Nd-GC-0.95, Nd-GC-1.2 and Nd-GC-1.5 samples using an X-ray powder diffractometer (D8 advance, Bruker) working with CuKα 1 radiation (λ = 1.5406 Å). The diffraction patterns were acquired in the range 10 • ≤ 2θ ≤ 70 • . The size of the nanocrystals (NCs) was estimated from the Scherrer equation: where D hkl is the calculated crystallite size, k = 0.94 for spherical crystals, θ is the Bragg angle and β is the full width at half maximum intensity of the peak (FWHM). To determine the weight ratios of NaLaF 4 and LaF 3 phases, Rietveld refinement was performed with the Fullprof program using interpolation of points to model the background. [28]. Fourier transform infrared spectra (FTIR) was recorded employing a Perkin-Elmer 100 FT-IR instrument in the range 4000-450 cm −1 , with a resolution of 4 cm −1 .The microstructure of the GC-0.95, GC-1.2 and GC-1.5 samples was analyzed with a high-resolution transmission electron microscope (HRTEM, JOEL JEM-2100F, Akishima, Tokyo, Japan) operating at 200 kV. The sample was prepared by dispersing a fine powder of sample in ethanol and then depositing some drops onto the carbon-enhanced copper grid.

Optical Characterization
Site-selective steady-state emission and excitation spectra were recorded by exciting the samples with a continuous wave (cw) Ti:sapphire ring laser (0.4 cm −1 linewidth) in the 770-920 nm spectral range. The fluorescence was analyzed with a 0.25 m monochromator; the signal was detected by an extended IR Hamamatsu H10330A-75 photomultiplier and amplified by a standard lock-in technique.

Results and Discussion
Transparent, homogeneous, and stable sols were obtained from Sol-0.95, Sol-1.2 and Sol-1.5 sols. After drying at 50 • C, xerogels of 20 mm in diameter were successfully obtained ( Figure 1a). All samples are transparent to view when evaluated on paper, indicating high quality; suitable long-term stability was also observed.
The thermal behavior of Sol-0.95 xerogel was evaluated by DTA-TGA ( Figure 1b) under an Ar atmosphere at a heating rate of 10 • C/min. In general, a two-stage thermal degradation profile was observed in the temperature range between (1) 80-110 • C and (2) 300 • C. The first interval corresponds with an endothermic peak and a weight loss of 30% attributable to desorption of water and solvent removal. The second degradation step, accompanied by an exothermic peak around 300 • C and a weight loss of 40%, is related to the chemical decomposition and further crystallization of fluorides. The decomposition of La(CF 3 COO) 3 (obtained during the chemical reaction between lanthanum(III) acetate and TFA) occurred together with the crystallization of LaF 3 , as previously reported [27]. Although crystallization does not generally involve mass loss, in the case of GCs prepared by SG, the chemical reactions between the TFA and lanthanide salts occurred concomitantly with crystallization, such that significant mass loss also took place. In this case, crystallization of NaLaF 4 and LaF 3 occurred simultaneously because no additional peaks were observed in the plot.
The crystallization process differs from that reported for GCs prepared by meltquenching. De Pablos-Martín et al. [14] and Elts et al. [17] reported the crystallization of pure NaLaF 4 during the heat treatment of a melt-quenched glass, finding an exothermic peak between 600 and 700 • C [14,17]. These authors attributed the high crystallization temperature of the NaLaF 4 to the increase in viscosity during glass formation, inhibiting atom diffusion and crystal growth and producing a resistance to crystallization. On synthesis by SG, this drawback did not occur, and fluoride crystallization took place at the same time as the precursor reaction.
Crystals 2021, 11, x FOR PEER REVIEW 4 of 12 degradation profile was observed in the temperature range between (1) 80-110 °C and (2) 300 °C. The first interval corresponds with an endothermic peak and a weight loss of 30% attributable to desorption of water and solvent removal. The second degradation step, accompanied by an exothermic peak around 300 °C and a weight loss of 40%, is related to the chemical decomposition and further crystallization of fluorides. The decomposition of La(CF3COO)3 (obtained during the chemical reaction between lanthanum(III) acetate and TFA) occurred together with the crystallization of LaF3, as previously reported [27]. Although crystallization does not generally involve mass loss, in the case of GCs prepared by SG, the chemical reactions between the TFA and lanthanide salts occurred concomitantly with crystallization, such that significant mass loss also took place. In this case, crystallization of NaLaF4 and LaF3 occurred simultaneously because no additional peaks were observed in the plot. The crystallization process differs from that reported for GCs prepared by meltquenching. De Pablos-Martín et al. [14] and Elts et al. [17] reported the crystallization of pure NaLaF4 during the heat treatment of a melt-quenched glass, finding an exothermic peak between 600 and 700 C [14,17]. These authors attributed the high crystallization temperature of the NaLaF4 to the increase in viscosity during glass formation, inhibiting atom diffusion and crystal growth and producing a resistance to crystallization. On synthesis by SG, this drawback did not occur, and fluoride crystallization took place at the same time as the precursor reaction.    were clearly identified at all treatment temperatures. However, at 450 C, a preferential crystallization of LaF3 phase was observed, confirming that precipitation of LaF3 requires a lower free energy of formation compared to NaLaF4. Upon increasing temperature, NaLaF4 crystallization was promoted and, at 650 C, the maximum NaLaF4 crystal fraction was reached. The LaF3 and NaLaF4 nanocrystal sizes for GC-0.95 samples were both around 35 nm, as estimated using the Scherrer equation (Equation 1). It was not possible to determine the nanocrystal size of NaLaF4 at 450 and 550 C due to the low resolution of the diffraction peaks. However, the NaLaF4 nanocrystals appeared to be larger than those of LaF3. XRD confirms that crystallization is achieved in the sol-gel materials with only one minute of heat treatment. It was    were clearly identified at all treatment temperatures. However, at 450 • C, a preferential crystallization of LaF 3 phase was observed, confirming that precipitation of LaF 3 requires a lower free energy of formation compared to NaLaF 4 . Upon increasing temperature, NaLaF 4 crystallization was promoted and, at 650 • C, the maximum NaLaF 4 crystal fraction was reached. The LaF 3 and NaLaF 4 nanocrystal sizes for GC-0.95 samples were both around 35 nm, as estimated using the Scherrer equation (Equation (1)). It was not possible to determine the nanocrystal size of NaLaF 4 at 450 and 550 • C due to the low resolution of the diffraction peaks. However, the NaLaF 4 nanocrystals appeared to be larger than those of LaF 3 . XRD confirms that crystallization is achieved in the sol-gel materials with only one minute of heat treatment. It was previously reported that longer treatment times do not augment the crystal fraction [29]. Further characterization was performed on GCs treated at 650 • C for 1min. cated that, up to a ratio of NaCH3COO/LaCH3COO3 = 1.2, the size remained constant, with greater crystallites observed for NaLaF4 in comparison to LaF3 (Figure 2c). Upon increasing the La concentration to 59.8 wt% (GC-1.5), the crystallites of both phases grew to the range 45-48 nm. The calculated crystallite sizes are significantly greater than those reported by the melt-quenching technique (smaller than 25 nm) but are similar in size to the nanoparticles obtained outside the glass matrix in aqueous media [9,14].  The FTIR spectra of Sol-0.95 xerogel and GC-0.95 glass-ceramic treated at The effect of the Na/La molar ratio was analyzed by XRD (Figure 2b), employing Rietveld refinement to calculate the weight percent fraction of crystallized NaLaF 4 and LaF 3 ( Table 2). Additional peaks of NaF were observed for all samples. In addition to NaF, an unidentified phase was observed in both GC-1.2 and GC-1.5; the intensity of the most intense peak of the additional phase (I) as a percentage of the most intense peak of the pattern (I max ) was~5% in both cases. An optimum Na/La molar ratio of the crystalline Crystals 2021, 11, 464 6 of 11 phase was found, which corresponds to the maximum formation of NaLaF 4 (46.2 wt.%) compared to LaF 3 (53.8 wt%). Although an increase in NaLaF 4 content is expected when increasing the Na/La ratio, this was not observed (Table 2). XRD (Figure 2b) showed that the decrease in NaLaF 4 content was accompanied with a higher content of an unidentified phase, likely associated with the remaining sodium. On the other hand, crystallite sizes for GCs obtained for different NaCH 3 COO/ LaCH 3 COO 3 molar ratios, also calculated with the Scherrer equation, indicated that, up to a ratio of NaCH 3 COO/LaCH 3 COO 3 = 1.2, the size remained constant, with greater crystallites observed for NaLaF 4 in comparison to LaF 3 (Figure 2c). Upon increasing the La concentration to 59.8 wt% (GC-1.5), the crystallites of both phases grew to the range 45-48 nm. The calculated crystallite sizes are significantly greater than those reported by the melt-quenching technique (smaller than 25 nm) but are similar in size to the nanoparticles obtained outside the glass matrix in aqueous media [9,14].
The FTIR spectra of Sol-0.95 xerogel and GC-0.95 glass-ceramic treated at 650 • C for 1 min are shown in Figure 3. The spectrum of the xerogel shows absorption bands at 460, 800 and 1080 cm −1 associated with stretching, bending and out-of-plane Si-O-Si bonds of SiO 2 , respectively [28,29]. Some bands corresponding to TFA and acetate precursors appeared between 1400 and 1750 cm −1 . In addition, a broad band from 2800 to 3760 cm −1 was present in the xerogel spectrum, associated with O-H and C-H groups of the ethanol and water formed during condensation [30]. The peaks associated with TFA, acetate and water disappeared in the spectrum of the GC-0.9 glass-ceramic, and the bands corresponding to Si-O-Si increased in intensity. The band at 460 cm −1 , observed in the spectrum of the GC-0.95 glass-ceramic, is attributed to vibration of fluorine in the crystal lattice, consistent with crystallization. A broad band between 900 and 1400 cm −1 , associated with tetrafluoride compounds, provides further evidence of NaLaF 4 crystallization [31,32].
Microstructural characterization of the GC-0.9, GC-1.2 and GC-1.5 glass-ceramics heat treated at 650 • C for 1 min was performed by HRTEM (Figure 4a-c). Spherical nanoparticles of various sizes were identified, indicating their different nature. The average nanoparticle size is shown in Figure 4d, where an increase in average size with increasing Na/La molar ratio may be observed, in accordance with the crystallite sizes determined by XRD. Although the size of the crystals is similar to that described for particles synthesized in aqueous media, the spherical shape of the SG-synthesized particles differs to the tubular shape reported previously in the literature.
The Microstructural characterization of the GC-0.9, GC-1.2 and GC-1.5 glass-ceramics heat treated at 650 °C for 1 min was performed by HRTEM (Figure 4a-c). Spherical nanoparticles of various sizes were identified, indicating their different nature. The average nanoparticle size is shown in Figure 4d, where an increase in average size with increasing Na/La molar ratio may be observed, in accordance with the crystallite sizes determined by XRD. Although the size of the crystals is similar to that described for particles synthesized in aqueous media, the spherical shape of the SG-synthesized particles differs to the tubular shape reported previously in the literature.
The   The presence of Nd 3+ -doped LaF3 and NaLaF4 nanocrystals was also confirmed by site-selective laser spectroscopy. The 4 F3/2 4 I11/2 laser transition was measured at room temperature for the GC-0.95/1.2/1.5 samples heat treated at 650 °C for 1 min by exciting with a Ti-sapphire laser at different wavelengths in resonance with the 4 I9/2 4 F5/2, 2 H9/2 absorption band. As an example, Figure 5 shows the normalized emission spectra for the GC-0.95 sample obtained under excitation at 786 and 792 nm. These excitation wavelengths correspond to Nd 3+ ions in LaF3 and NaLaF4 crystalline phases, respectively [33,34]. The spectrum obtained under excitation at 786 nm presents well-resolved peaks at around 1036, 1040, 1047, 1058 and 1063 nm, which is in agreement with the emission of Nd 3+ in LaF3 nanocrystals [34]. Under 792 nm excitation, the spectrum shows a main peak at around 1055 nm, together with a less intense one at 1049 nm, which corresponds to the Nd 3+ emission in the hexagonal NaLaF4 crystalline phase. In addition to this emission, weak peaks at 1036 and 1040 nm were also observed due to the spectral overlapping of the spectra of both crystalline phases.  The presence of Nd 3+ -doped LaF 3 and NaLaF 4 nanocrystals was also confirmed by site-selective laser spectroscopy. The 4 F 3/2 → 4 I 11/2 laser transition was measured at room temperature for the GC-0.95/1.2/1.5 samples heat treated at 650 • C for 1 min by exciting with a Ti-sapphire laser at different wavelengths in resonance with the 4 I 9/2 → 4 F 5/2 , 2 H 9/2 absorption band. As an example, Figure 5 shows the normalized emission spectra for the GC-0.95 sample obtained under excitation at 786 and 792 nm. These excitation wavelengths correspond to Nd 3+ ions in LaF 3 and NaLaF 4 crystalline phases, respectively [33,34]. The spectrum obtained under excitation at 786 nm presents well-resolved peaks at around 1036, 1040, 1047, 1058 and 1063 nm, which is in agreement with the emission of Nd 3+ in LaF 3 nanocrystals [34]. Under 792 nm excitation, the spectrum shows a main peak at around 1055 nm, together with a less intense one at 1049 nm, which corresponds to the Nd 3+ emission in the hexagonal NaLaF 4 crystalline phase. In addition to this emission, weak peaks at 1036 and 1040 nm were also observed due to the spectral overlapping of the spectra of both crystalline phases. temperature for the GC-0.95/1.2/1.5 samples heat treated at 650 °C for 1 min by exciting with a Ti-sapphire laser at different wavelengths in resonance with the 4 I9/2 4 F5/2, 2 H9/2 absorption band. As an example, Figure 5 shows the normalized emission spectra for the GC-0.95 sample obtained under excitation at 786 and 792 nm. These excitation wavelengths correspond to Nd 3+ ions in LaF3 and NaLaF4 crystalline phases, respectively [33,34]. The spectrum obtained under excitation at 786 nm presents well-resolved peaks at around 1036, 1040, 1047, 1058 and 1063 nm, which is in agreement with the emission of Nd 3+ in LaF3 nanocrystals [34]. Under 792 nm excitation, the spectrum shows a main peak at around 1055 nm, together with a less intense one at 1049 nm, which corresponds to the Nd 3+ emission in the hexagonal NaLaF4 crystalline phase. In addition to this emission, weak peaks at 1036 and 1040 nm were also observed due to the spectral overlapping of the spectra of both crystalline phases. The emission spectra are similar for the three GC samples, with the only difference being the relative intensity of the Nd 3+ emission in the two crystalline phases, which depends on the molar relation of both phases. Assuming that 786 and 792 nm correspond to excitations of Nd 3+ ions in the LaF 3 and NaLaF 4 nanocrystals, respectively, the highest intensity for the Nd 3+ emission in LaF 3 corresponds to the GC-1.2 sample in agreement with the higher LaF 3 content of this sample. Figure 6 shows the emission spectra for the three GC samples.
These results are confirmed by the excitation spectra corresponding to the 4 I 9/2 → 4 F 5/2 , 4 F 3/2 transitions obtained by collecting the luminescence at two different wavelengths. Figure 7 shows, as an example, the normalized excitation spectra of the GC-1.2 sample performed in the 770-890 nm spectral range on collecting the luminescence at 1040 and 1055 nm (the emission peaks corresponding to Nd 3+ emission in LaF 3 and NaLaF 4 crystalline phases respectively). As observed in the spectrum obtained by collecting the luminescence at 1040 nm, the 4 I 9/2 → 4 F 5/2 band is composed of several peaks at 786, 790, 792, 796 and 800 nm. The peaks at 786, 790, 796 and 800 nm correspond to Nd 3+ in the LaF 3 nanocrystals, whereas the one at 792 nm can be attributed to Nd 3+ in the NaLaF 4 crystalline phase. Moreover, the 4 I 9/2 → 4 F 3/2 transition presents two peaks at 859 and 862 nm, corresponding to Nd 3+ emission in LaF 3 nanocrystals, together with another peak at 864.5 nm attributable to NaLaF 4 nanocrystals. The presence of excitation peaks from both crystalline phases is due to the spectral overlapping of both emissions at 1040 nm ( Figures 5 and 6). The excitation spectrum obtained by collecting the luminescence at 1055 nm presents two main peaks for the 4 I 9/2 → 4 F 5/2 band at 792 and 801 nm, which correspond to Nd 3+ in the NaLaF 4 crystalline phase. The 4 I 9/2 → 4 F 3/2 transition shows the two expected Stark components of the 4 F 3/2 level in a well-defined crystal field site. However, the high-energy component superimposes the peak at 859 nm corresponding to the LaF 3 nanocrystals.
It is worth noting that despite the lower crystalline fraction of the tetrafluoride phase compared to that of LaF 3 , Nd 3+ emission is much more efficient in NaLaF 4 due to its higher emission cross-section [35,36].
The emission spectra are similar for the three GC samples, with the only difference being the relative intensity of the Nd 3+ emission in the two crystalline phases, which depends on the molar relation of both phases. Assuming that 786 and 792 nm correspond to excitations of Nd 3+ ions in the LaF3 and NaLaF4 nanocrystals, respectively, the highest intensity for the Nd 3+ emission in LaF3 corresponds to the GC-1.2 sample in agreement with the higher LaF3 content of this sample. Figure 6 shows the emission spectra for the three GC samples. These results are confirmed by the excitation spectra corresponding to the 4 I9/2 4 F5/2, 4 F3/2 transitions obtained by collecting the luminescence at two different wavelengths. Figure 7 shows, as an example, the normalized excitation spectra of the GC-1.2 sample performed in the 770-890 nm spectral range on collecting the luminescence at 1040 and 1055 nm (the emission peaks corresponding to Nd 3+ emission in LaF3 and NaLaF4 crystalline phases respectively). As observed in the spectrum obtained by collecting the luminescence at 1040 nm, the 4 I9/2 4 F5/2 band is composed of several peaks at 786, 790, 792, 796 and 800 nm. The peaks at 786, 790, 796 and 800 nm correspond to Nd 3+ in the LaF3 nanocrystals, whereas the one at 792 nm can be attributed to Nd 3+ in the NaLaF4 crystalline phase. Moreover, the 4 I9/2 4 F3/2 transition presents two peaks at 859 and 862 nm, corresponding to Nd 3+ emission in LaF3 nanocrystals, together with another peak at 864.5 nm attributable to NaLaF4 nanocrystals. The presence of excitation peaks from both crystalline phases is due to the spectral overlapping of both emissions at 1040 nm ( Figures 5 and 6). The excitation spectrum obtained by collecting the luminescence at 1055 nm presents two main peaks for the 4    It is worth noting that despite the lower crystalline fraction of the tetrafluoride phase compared to that of LaF3, Nd 3+ emission is much more efficient in NaLaF4 due to its higher emission cross-section [35,36].

Conclusions
Nd 3+ -doped SiO2-NaLaF4 GCs with the presence of LaF3 were successfully obtained for the first time by sol-gel after heat treatment in the range 450-650 °C for 1 min. Lower temperatures did not produce significant quantities of NaLaF4, but LaF3 crystallized for all heat treatment temperatures. Both phases also appeared for different relations of precursors; however, deficiency of Na in the precursors generated the maximum percentage

Conclusions
Nd 3+ -doped SiO 2 -NaLaF 4 GCs with the presence of LaF 3 were successfully obtained for the first time by sol-gel after heat treatment in the range 450-650 • C for 1 min. Lower temperatures did not produce significant quantities of NaLaF 4 , but LaF 3 crystallized for all heat treatment temperatures. Both phases also appeared for different relations of precursors; however, deficiency of Na in the precursors generated the maximum percentage of NaLaF 4 in the final GCs. ATD, FTIR and XRD confirmed the presence of LaF 3 and NaLaF 4 phases in the GCs, and the HRTEM images confirm the crystal sizes obtained by XRD, which tended to increase upon increasing the Na/La molar ratio in the precursors.
As in other GCs prepared by SG, the chemical reactions between the TFA and lanthanide salts occurred concomitantly with crystallization. Moreover, NaLaF 4 and LaF 3 crystallization took place at the same time as the precursor reaction. Site-selective excitation and emission spectra performed for the 4 I 9/2 ↔ 4 F 3/2 / 4 F 5/2 transitions confirm the presence of Nd 3+ ions inside both LaF 3 and NaLaF 4 crystalline phases for all GC samples. Notwithstanding the more abundant LaF 3 phase in the GC samples, the most efficient emission corresponds to Nd 3+ located in the NaLaF 4 crystalline phase. The luminescence results also show that the highest Nd 3+ emission intensity in the LaF 3 phase corresponds to the GC-1.2 sample, in accordance with its higher LaF 3 content.