A new sol–gel route towards Nd 3+ -doped SiO 2 –LaF 3 glass-ceramics for photonic applications

Glass-ceramic materials with composition 0.9Nd 3+ –80SiO 2 –20LaF 3 were successfully obtained and further heat-treated at 450 1 C for 6 h. Stable and homogeneous LaF 3 nanoparticle suspensions with and without Nd 3+ were first prepared by a chemical route, incorporating polyvinylpyrrolidone (PVP) as dispersant. The suspensions were then concentrated and characterised by XRD, HRTEM and zeta potential, confirming that LaF 3 crystallises as the only phase, with particle size around 16 nm. The suspensions were incorporated in a silica sol to obtain a 0.9Nd 3+ –20LaF 3 –80SiO 2 particulate sol, xerogel and glass-ceramic. HRTEM confirmed the homogeneous incorporation of the doped nanocrystals into the SiO 2 matrix without modification of the nanoparticle structure. Rietveld refinement was used to determine the crystallinity and quantity of LaF 3 nanoparticles present in the glass-ceramic after treatment of the particulate sol at 450 1 C for 6 h. Luminescence measurements of near infrared Nd 3+ ion emissions in the lanthanum fluoride nanoparticles and SiO 2 –LaF 3 glass-ceramic showed well-structured emission spectra with lifetimes similar to those of theoretical Nd +3 in LaF 3 crystals.


Introduction
Glass is a key material with a wide range of applications, ranging from traditional glassware products to advanced optical materials. Optical transparency in an extended spectrum, chemical durability, and manufacturability render glass optimal for producing materials of different shapes. In addition, significant improvements in certain properties may be achieved on preparation of glass ceramics (GCs) through controlled crystallisation. 1 S. D. Stookey first developed a glass-ceramic named Fotoceram in 1957, later called Pyroceram, 2 coining the term glass-ceramic and defining it as: ''. . .made by first melting and forming special glasses containing nucleating agents and then causing controlled crystallization of the glass particles''. 2 For many years, this definition only included materials containing more than 50% of crystals. However, GCs with lower crystal fraction have also been developed in the last 60 years. The definition was updated after the ''12th International Symposium on Crystallization in Glasses and Liquids'', organized by TC07 of the International Commission on Glass (ICG), to include different technologies and processing methods.
''Glass-ceramics are inorganic, non-metallic materials prepared by controlled crystallization of glasses via different processing methods. They contain at least one type of functional crystalline phase and a residual glass. The volume fraction crystallized may vary from ppm to almost 100%''. 3 Particular attention is currently devoted to the preparation of oxide glasses containing fluoride nanocrystals (NCs). Such materials, known as oxyfluoride glass-ceramics (OxGCs), were obtained for the first time in 1998 by Dejneka (1998). Fluoride nanocrystals add unique properties to oxide glasses, making them attractive for photonic applications. They combine the very low phonon energy (300-450 cm À1 ) of fluoride nanocrystals with the high chemical, mechanical and thermal stability of the glass matrices, thereby increasing the luminescence efficiency. [4][5][6] The resulting oxyfluoride glass-ceramics have notable advantages compared with pure glass or ceramic materials. The LaF 3 -SiO 2 system has been investigated due to the behaviour of the LaF 3 crystals as rare-earth (RE) hosts. LaF 3 has superior solid solubility compared with other fluoride crystal phases. 7,8 Among the different techniques employed for the preparation of OxGCs, glass melting-quenching (MQ) is the most relevant. However, high melting temperatures (1400-1700 1C) cause significant fluorine loss, limiting the final fluorine content of the crystal phase and resulting in uncontrollable compositions with respect to fluorine and lanthanide (Ln 3+ ) ions. Many researchers have proposed alternative processing methods to overcome these limitations 9  Sintering (SPS). The preparation of xZrO 2 -(100-x)SiO 2 glassceramics by SPS with a high content of crystalline phase (higher than 45 mol%) 10 has been reported, but LaF 3 -SiO 2 materials have not yet been reported. Moreover, the SPS process is rather expensive and the size and shape of samples are quite limited. 10 On the other hand, the sol-gel process is a promising route for production of glass-ceramic materials, which avoids the drawbacks of melting-quenching, with the versatility to allow differently shaped products such as thin films, powders, and bulk materials obtained at low temperatures. Further advantages of the method include homogeneity and high purity of the resultant materials. However, sol-gel was not widely applied for glass-ceramic processing until significant improvements in structural and optical properties appeared in the late nineties. Precise control of the synthesis and crystallisation process is required to obtain transparent oxyfluoride glass ceramics, which avoids both uncontrolled particle growth and the formation of undesirable phases. Careful process design is, therefore, critical for obtaining well-ordered, transparent, and efficient optical glass-ceramics.
The most studied oxyfluoride compositions prepared by sol-gel are LnF 3 (Ln = La, Y, Gd) and RLnF 4 (R = Na, K, Li; Ln = Gd, Y), doped with different rare-earth (RE 3+ ) ions (Er 3+ , Eu 3+ , Nd 3+ , etc.). 11,12 The first papers reporting the processing of pure LaF 3 on silica glass substrates by sol-gel were published in 1998 by Fuhijara and Tada (1999), who showed that control of the synthesis parameters and heat-treatment were essential to obtain transparent LaF 3 materials avoiding the precipitation of other phases such as LaOF. 13,14 Up to 2018, the literature typically reported the preparation of oxyfluoride glass-ceramics with nominal contents of 5-10 mol% of active crystal phases, with little innovation related to synthesis and processing conditions. 13,15 Nevertheless, in the past decade, the GlaSS Group of the Instituto de Cerámica y Vidrio (CSIC) has optimised the sol-gel process to obtain oxyfluoride glass-ceramics with high active-phase contents (up to 20 mol%) by sol-gel. Quantitative Rietveld refinement of 80SiO 2 -20LaF 3 bulk samples doped with 0.5Er 3+ and treated at 550 1C for 1 min indicated a crystal fraction B18 wt%, 13 the highest reported in the literature for transparent oxyfluoride glass-ceramics prepared by sol-gel and the highest compared to any glassceramics prepared by melting. However, photoluminescence emission and excitation spectra of SiO 2 :LaF 3 samples exhibited only a few, broad structured bands due to the small size of the nanocrystals (B2 nm for thin films and 8 nm for bulk samples). Gorni et al. 15 proposed that the weak luminescence properties are due to uncontrolled nucleation and growth of the LaF 3 crystals in the sol-gel matrix, because, at high temperatures, the crystals tends dissolve and reach chemical-potential equilibrium. It is essential, therefore, to improve the optical properties by obtaining larger nanocrystal sizes, which is difficult using current synthesis methods based on a two-step chemical process.
An alternative, recently proposed procedure to obtain glassceramics is the production of nano-crystalline powders followed by their dispersion in a sol-gel matrix. Although this method is promising, the luminescence studies are not conclusive. 16 The aim of the current work is the preparation of Nd 3+ doped-LaF 3 nanoparticle suspensions and their incorporation into silica (SiO 2 ) sols prepared by acid catalysis. The dispersion of the nanoparticles and stability of the LaF 3 and LaF 3 -SiO 2 suspensions were studied, confirming that LaF 3 appears as the only crystalline phase. Xerogels and glass-ceramic powders were produced by thermal treatment and characterized by different techniques with promising luminescence results.

Experimental
Synthesis of LaF 3 and Nd 3+ :LaF 3 nanoparticle suspensions Lanthanum chloride (LaCl 3 , Alfa Aesar) and ammonium fluoride (NH 4 F, Merck) were used as reagents without further purification and mixed with deionized water to a La 3+ concentration of 0.04 M. 17 The solution was maintained at 75 1C for 2 h with continuous stirring to obtain the LaF 3 -0.04 M nanoparticle suspension with a final pH = 7. Following the same process, neodymium acetate (Nd(CH 3 CO 2 ) 3 , Alfa Aesar) was added to NH 4 F/LaCl 3 /H 2 O solution in a molar ratio Nd 3+ / LaCl 3 = 0.9. The solution was maintained at 75 1C for 2 h under continuous stirring to obtain a 0.9Nd 3+ -LaF 3 -0.04 M nanoparticle suspension.

Characterisation of Nd 3+ -LaF 3 nanoparticle suspensions
The dispersibility and stability of a LaF 3 -0.04 M nanoparticle suspension was studied through the variation of zeta potential as a function of pH using a Zetasizer Nano ZS instrument (Malvern S, UK). Suspensions of different pH in the range 3-12 were prepared on addition of nitric acid (HNO 3 , Sigma Aldrich) and tetramethylammonium hydroxide (TMHA, Merck) then stabilised for 12 h.
LaF 3 -0.04 M and 0.9Nd 3+ -LaF 3 -0.25 M-PVP(X) suspensions were centrifuged at 6000 rpm for 5 min, and the resulting powders rinsed with deionized water; the process was repeated three times to remove all the organic components. Powders were further dried at 80 1C for 12 h and characterized by X-ray View Article Online diffraction (XRD). Diffractograms were acquired in the range 20-701 2y with a step size of 0.021 and 1 second of integration time using a D8 Advance diffractometer (Bruker, MA). The crystal size was calculated by applying Scherrer's equation, where l is the wavelength of Cu Ka radiation (l = 0.15405 nm), B the full width half maximum of the LaF 3 peak at 2y = 441, y the corresponding diffraction angle and b the correction of the instrument; the constant factor, K, corresponds to spherical crystals and a value of 0.94 is commonly adopted. High Resolution Transmission Electron Microscopy (HRTEM) and Energy-dispersive X-ray spectroscopy (EDX) were used to characterize 0.9Nd 3+ -LaF 3 -0.04 M and 0.9Nd 3+ -LaF 3 -0.25 M-PVP(X) nanoparticles dried at 80 1C for 12 h and redispersed in ethanol employing a JEOL 2100F microscope. The samples were prepared by dropping the suspensions onto a carbon-coated copper grid (Lacey Carbon, LC-200-Cu 25/pk). HRTEM images were processed using ImageJ s software. The lattice parameters of LaF 3 nanoparticles in 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) were determined from the corresponding electrondiffraction pattern.
The crystal fraction of 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) nanoparticles in a glass ceramic treated at 450 1C for 6 h was estimated by the Rietveld method as described previously 4 using the FULLPROF program, 18 with NaF as internal weight standard in an appropriate quantity (5 wt%). The XRD data were collected in the range 201 r 2y r 1201 in a step width of 0.01671 employing a PHILIPS X-PERT PRO y/2y diffractometer operating at 45 kV and 40 mA.

materials
The stability of the 0.9Nd 3+ -80SiO 2 :20LaF 3 particulate sols was determined using an AND Vibro Viscometer on measuring the viscosity once a day for five days.
Differential thermal analysis (DTA) and thermogravimetric analysis (TGA) were performed with a SDT Q600 instrument (TA Instruments, New Castle, DE, USA). Approximately 15 g of 0.9Nd 3+ -20LaF 3 :80SiO 2 xerogel, dried at 80 1C for 12 h, was measured in air from room temperature to 800 1C with a heating rate of 10 1C min À1 .
The compositional and morphological characterization of the xerogels and glass-ceramics obtained from particulate sols was performed by HRTEM and EDX spectroscopy (JEOL 2100F). The 0.9Nd 3+ -20LaF 3 :80SiO 2 particulate sol was dried and treated at 450 1C for 6 h. The powder was re-dispersed in ethanol and a drop of the suspension deposited onto carbon-coated copper grids (Lacey Carbon, LC-200-Cu 25/pk); the size distribution of the particles was determined using ImageJ s software.
The quantitative crystalline fraction of 0.9Nd 3+ -20LaF 3 :80-SiO 2 samples treated at 450 1C for 6 h was determined by the Rietveld method using the parameters and internal weight standard indicated earlier.
Optical characterisation of LaF 3 nanoparticles and Nd 3+ -LaF 3 -SiO 2 glass-ceramics 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) nanoparticle suspensions without any additive were dried at 80 1C and treated at 450 1C before pressing in a uniaxial press for 3 min at 1000 MP for luminescence analysis. The final compact samples were excited with a tuneable Ti-sapphire ring laser (0.4 cm À1 linewidth) in the 770-920 nm spectral range. The emitted light was analysed with a single grating monochromator (focal length 0.25 m), detected by an extended IR Hamamatsu H10330A-75 photomultiplier, and amplified by a standard lock-in technique. Luminescence decay curves were obtained by exciting the samples with a Tisapphire laser pumped by a pulsed frequency-doubled Nd:YAG laser (9 ns pulse width), and detecting the emission with a Hamamatsu H10330A-75 photomultiplier. All measurements were performed at room temperature.

Results and discussion
Characterisation of LaF 3 and Nd 3+ :LaF 3 nanoparticle suspensions Fig. 1a shows the variation of zeta potential as a function of pH for the LaF 3 -0.04 M nanoparticle suspension from an initial pH of 7, corresponding with a zeta potential of À22 mV. The addition of HNO 3 modified the zeta potential to more positive values, from À22 mV (pH 7) to 10 mV (pH 3), reaching the isoelectric point (x-potential = 0) at a pH of 4.8. On the other hand, the zeta potential remains practically constant, BÀ25 mV, with the addition of TMAH. The variation of the zeta potential provides information on the stability of the nanoparticle suspension, which greatly depends on the pH. A high zeta potential, in absolute values, often indicates more stable suspensions, hence a pH of 7 was selected to prepare the LaF 3 -0.04 M nanoparticle suspension, corresponding with a zeta potential of À22 mV. Zeta potential and particle size of LaF 3 -0.04 M nanoparticle suspensions at pH 7 were measured as a function of PVP wt%, Fig. 1b. Although a slight decrease of the zeta potential is observed up to 3 wt% PVP, it remains constant, around À35 mV, with the increment of PVP. However, as observed in Fig. 1b, the hydrodynamic particle size of the nanoparticles decreases with the addition of PVP. In general, the addition of PVP to LaF 3 -0.04 M-PVP(X) nanoparticle suspensions produces a significant increase in its stability, related to the repulsive forces from the hydrophobic carbon chains of the PVP molecules. 19 In comparison with previous works of G. Gorni et al., 16 starting from a two-step process with further precipitation of NP, larger particle sizes have been obtained using this new method.
No limitation to crystal growth occurs because crystallization occurs in the liquid phase and the ion mobility facilitates the diffusion and growth of NPs. A maximum hydrodynamic size of 27 nm was obtained, which is an order of magnitude greater than that reported by G. Gorni. 22 Concentrations of 0 and 10 wt% PVP were selected to prepare the corresponding suspensions that were later added to the SiO 2 sol. Fig. 2 shows the XRD patterns of LaF 3 nano powders obtained after drying the LaF 3 -0.04 M and 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) suspensions at 80 1C. The XRD analysis revealed crystallisation of LaF 3 with hexagonal symmetry (JCPDS 03-1013); no other crystalline phases were detected. The desired crystallisation was achieved for the LaF 3 -0.04 M suspension as well as for the doped and concentrated suspensions. This confirms that nanocrystal growth is affected neither by the incorporation of the rare-earth acetates nor by the dispersant. Moreover, the nanocrystals remain stable in size after the concentration of the suspensions from 0.04 to 0.25 M in the rotavapor.
The particle size (T) of the powders determined using the Debye-Scherrer equation, was 12 and 15 nm respectively, much higher than particle sizes reported in the literature. [20][21][22] 0.9Nd 3+ -LaF 3 -0.04 M and 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) NP suspensions were dried at 80 1C and analysed by HRTEM to complete characterisation of the morphology. Fig. 3a shows the presence of aggregated LaF 3 nanoparticles with a tubular form and average size, B18 nm. In the case of 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10), the increase in concentration from 0.04 to 0.25 M produces greater aggregation of the LaF 3 nanoparticles (Fig. 3b), although the morphology and the particle size remained constant. The crystal phase was analysed with the ImageJ s software (Fig. 3c), giving a planar distance (d spacing) of 0.325nm, which corresponds to the lattice distance between the (101) planes of the LaF 3 hexagonal phase. A Fast Fourier Transform (FFT) also performed with ImageJ s , Fig. 3(d), shows the corresponding diffraction rings and white spots in the electron-diffraction pattern where (101) is identified at 2y = 27.421. Fig. 3e shows the EDX analysis of the 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) sample corresponding to the area shown in Fig. 3c. The chemical analysis reveals the presence of F, La and Nd, providing clear evidence of Nd 3+ incorporation in the nanoparticles.

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Quantitative Rietveld refinement of LaF 3 (not shown) was performed for 0.9Nd 3+ -LaF 3 -0.25 M-PVP(10) nanoparticles treated at 450 1C for 6 h. A crystallised fraction of 13 wt% was determined, below that expected and indicating that the LaF 3 nanoparticles are highly amorphous. It should also be considered that a lower limit of detection occurs when the peaks become so broad due to the small particle size that they disappear into the background radiation. Although there is no exact limit to define when this occurs, particles of low size are likely to appear amorphous and special conditions such as a slow stem scan are required.
Characterisation of 0.9Nd 3+ -20LaF 3 :80SiO 2 particulate sol The stability of the sol with time was studied through the evolution of viscosity. Fig. 4 shows the variation of the viscosity with aging time of the 0.9Nd 3+ -20LaF 3 :80SiO 2 particulate sol up to its gelification. The initial viscosity, measured two hours after the sol synthesis, was 4.1 mPa s. increasing to 4.2 mPa s. after 42 hours. During the following days, the viscosity was measured once per day achieving a value of 8.5 mPa s on the fifth day, before gelation occurred the following day. Although these values are high for depositing thin films, they are suitable for producing xerogels in a shorter time from stable sols. Fig. 5 shows the DTA and TGA analysis for the 0.9Nd 3+ -20LaF 3 :80SiO 2 xerogel measured in air. Weight loss occurs in four different steps. The first step, around 25-100 1C, is associated with an endothermic process at 76.7 1C, corresponding to the elimination of water and adsorbed ethanol, confined in large pores. The OH groups of the silica network generate hydrogen bridges, increasing the energy required to desorb the ethanol and water. 23 The second step, between 100-200 1C, is usually assigned to the evaporation of solvents absorbed in small pores. The combustion of remaining organic material is responsible for the third step, occurring in the range 250-500 1C, along with final elimination of trapped solvents and water molecules in nanopores up to 500 1C. 24 A sharp exothermic peak at 607 1C appears associated with the final weight loss event, corresponding to the crystallisation of LaOF, as confirmed by XRD (not shown).
The structural characterisation of LaF 3 nanoparticles incorporated in the 0.9Nd 3+ -20LaF 3 :80SiO 2 particulate sol was analysed by HRTEM. Fig. 6a shows the HRTEM image of the 0.9Nd 3+ -20LaF 3 :80SiO 2 sample treated at 450 1C for 6 h, showing well-dispersed nanoparticles. The average particle size is B16 nm according to the size distribution given in Fig. 6b. This particle size is consistent with that determined by XRD and HRTEM ( Fig. 2 and 3). Furthermore, the LaF 3 nanoparticles maintained their oval shape after incorporation into the silica   sol. Fig. 6c shows a planar distance of 0.32 nm corresponding to the (101) plane for the nanocrystalline particles, similar to that of the 0.9Nd 3+ -LaF 3 nanoparticles before their incorporation into the silica sol. Fig. 6d confirms the presence of Nd accompanying La and F, measured by STEM analysis. It is confirmed that no new crystallisation process occurs, and that the shape and size of the LaF 3 nanoparticles are not affected either by incorporation into the silica sol or by the heat treatment at 450 1C for 6 h. Incorporation in the silica matrix does not produce agglomerations or growth of the nanoparticles.
Quantitative Rietveld refinement of the 0.9Nd 3+ -20LaF 3 :80-SiO 2 glass-ceramic treated at 450 1C for 6 h provided a weight fraction of 5.2 wt% of crystalline phase (Fig. 7). Considering the low crystalline fraction obtained for the nanopowders of LaF 3 (13%), it is likely that incorporation in the silica sol and further thermal treatment increases the average particle size and improves crystallisation of the NPs, leading to a higher relative crystalline fraction.
Optical characterisation of Nd 3+ :LaF 3 nanoparticles before and after their incorporation in a silica matrix The near-infrared emission spectra corresponding to the 4F 3/2 -4I 11/2 laser transition were obtained for all samples at room temperature by exciting at 786 nm in the 4I 9/2 -4F 5/2 absorption band. Fig. 8a shows the emission spectrum of the 0.9Nd 3+ -LaF 3 nanoparticle suspension treated at 80 1C, together with the experimental decay of the 4F 3/2 level. The emission spectrum shows similar spectral features to the Nd 3+ emission of the LaF 3 crystal. However, the experimental decay of the 4F 3/2 level obtained under excitation at 786 nm with collection of luminescence at 1064 nm shows a different behaviour.
The decay deviates from a single exponential function and the lifetime is unexpectedly short. The average lifetime.
where I(t) represents the luminescence intensity at time t corrected for the background, is reduced to 61 ms.
On the other hand, the near-infrared emission spectrum of 0.9Nd 3+ -LaF 3 nanoparticles treated at 450 1C for 6 h (Fig. 8b) shows a series of peaks with emissions of comparable intensity, around 1047 and 1064 nm. The spectral features correspond to the emission of Nd 3+ ions in LaF 3 , 25 which confirms the incorporation of the rare-earth ion in the LaF 3 NPs. Moreover, the fluorescence decay curve of the 4F 3/2 level obtained under   excitation at 786 nm on collecting the luminescence at 1064 nm can be described to a good approximation by a single exponential function with a lifetime of 528 ms, which is close to the lifetime reported for Nd 3+ in a LaF 3 crystal (522 ms). These results unambiguously confirm the incorporation of Nd 3+ ions in the LaF 3 NPs.
The lifetime of NPs treated at 80 1C is nearly one order of magnitude shorter than that observed in the NPs heat treated for 6 h at 450 1C. This strong quenching of the lifetime could be related to the presence of aggregated LaF 3 nanoparticles; however, this is not appreciated in the HRTM micrographs. The most probable explanation is that NPs treated at 80 1C still contain a high percentage of PVP, which is eliminated on treatment at 450 1C.
For the 0.9Nd 3+ -20LaF 3 :80SiO 2 sample treated at 450 1C for 6 h, both the emission spectrum and the lifetime (Fig. 9) correspond to those obtained for LaF 3 NPs with the same treatment. This result agrees with the structural characterisation, which indicates that LaF 3 nanoparticles are not affected by their incorporation in the silica sol, maintaining their high efficiency as active phase.
On the other hand, emission measurements performed in 0.9Nd 3+ -LaF 3 :SiO 2 glass-ceramics with three different LaF 3 concentrations (5, 10 and 20%), treated at 450 1C for 6 h, confirmed that the increase in the crystalline fraction results in a nearly linear increase of the emission intensity (Fig. 10).
This promising innovative process which produces optically active oxyfluoride glass-ceramics is under further investigation to produce optically efficient transparent glass-ceramics coatings with wide and diverse applications.

Conclusions
Stable Nd 3+ -doped LaF 3 nanoparticle suspensions with particle size B 16 nm, were obtained using a rather simple precipitation process. The incorporation of PVP as dispersant increases the stability of the LaF 3 NP suspensions.
The incorporation of Nd 3+ ions into the LaF 3 nanoparticles, as well as in SiO 2 -LaF 3 powders, was confirmed by HRTEM, STEM and optical characterisation. The luminescence spectra of Nd 3+ -doped LaF 3 nanoparticles treated at 450 1C for 6 h confirms the incorporation of Nd 3+ ions in the nanoparticles and the complete elimination of PVP after suitable heat treatment. A lifetime of 528 ms was determined, similar to that of Nd 3+ in pure LaF 3 crystals.
Moreover, stable SiO 2 -LaF 3 sols with and without Nd 3+ were prepared by mixing the LaF 3 NP suspension with a silica sol, up to a maximum molar ratio of 20% LaF 3 NPs. To the best of our knowledge, this is the first time that Nd 3+ NPs incorporated into a glass-ceramic has been produced by this route.
Rietveld refinement indicated that LaF 3 NPs present a crystalline fraction of 13%, likely related to a high percentage of amorphous fraction. However, the relative crystallised fraction in the silica matrix with 20% of NP determined by the same method increases to B5%.
The Nd 3+ -LaF 3 nanoparticles are not affected by their incorporation into the silica sol, maintaining their composition, shape and size. The luminescence response of 0.9Nd 3+ -20LaF 3 :80SiO 2 glass-ceramic treated at 450 1C for 6 h confirms the efficiency of the active phase.

Conflicts of interest
There are no conflicts to declare. 1 G. Gorni, M. J. Pascual and A. Caballero, Effect of processing on the structure and properties of glass and glass-ceramics for

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