# Preparation of Luminescent Glass Aggregates from Soda-Lime Waste Glass

Authors: Vorrada Loryuenyong; Achanai Buasri
Journal: International Journal of Photoenergy
 (2021)

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## Abstract

This research studied the preparation of luminescent glass aggregates prepared from soda-lime waste glass and strontium aluminate-based phosphors. The properties of the samples were determined by means of X-ray diffraction (XRD) technique, scanning electron microscopy (SEM), Archimedes’ method, and photoluminescence (PL) spectroscopy. It was found that the pore characteristics, density, and formation of crystallite phases in the glassy matrix depended on the phosphor content. The addition of fine phosphor powder tended to inhibit the glass crystallization and to reduce the apparent porosity of the aggregates. In general, the disadvantage of phosphors is their luminescent degradation under thermal attacks, which limits their use in applications involving high-temperature annealing. The phosphors, however, still had good luminescent properties and long-term stability with the sintering temperature as high as 750°C. The results indicated that the phosphors could be composited with glasses at high processing temperatures, enabling their widespread application.


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## Body

## 1. Introduction

Glass is a very common material in our daily life. We have used glass in numerous applications including packaging for products, tableware, and construction. As a result, a million tons of glass waste have been generated annually. To conserve raw material resources, glass waste is usually recycled either by being remelted into glass products or reprocessed in various applications. For example, Bernardo et al. used glass waste to replace feldspar sand in the fabrication of glass ceramic stoneware [1]. The resultant products had high strength and high fracture toughness similar to those of conventional stoneware but required lower sintering temperatures. In addition, the use of glass waste also reduced the production costs of glass ceramics by reducing processing steps involving nucleation and crystal growth mechanisms [2].Phosphors are materials that can emit intense and long-lasting light when absorbing high external energy. They are widely used in many applications such as lighting and display devices [3, 4]. Other applications include the use of glow-in-the-dark materials dispersed in self-luminescent cement-based composites [5]. The addition of particular types of phosphors such as strontium aluminate could provide long-lasting luminescence to the cement products. Despite this, it has been reported that the presence of phosphor powder could promote the hydration reaction of nonhydrated particles in cement, which enhanced the mechanical properties of the final products [5].Phosphors could also be composited with other materials such as glasses [6], metals [7], or polymers [8] for energy-saving applications. The luminescence occurs when phosphors absorb the solar light during the day and illuminate at night. Although many applications of phosphor composites have been designed and commercially available, they normally suffer from thermal degradation when sintering at high temperatures [9, 10]. This causes inferior luminescence and limits their use with high-temperature processing materials. Glass ceramics are materials with at least one crystalline phase dispersed in the glass. They are normally formed by the controlled crystallization of the glass. These materials have attracted tremendous attention due to their interesting properties including low thermal expansion, high stability, high mechanical strength, and high toughness. As a result, the incorporation of phosphors in glass ceramic matrix or phosphor-in-glass ceramics should produce luminescent materials with long-term stability, high durability, and long persistent luminescence. The major challenge, however, is to maintain the luminous efficiency of phosphors during the preparation processes at high temperatures.In this study, luminescent or phosphor powder was added into the glass frits from soda-lime waste glass to fabricate glowing glass ceramic aggregates for energy-saving and eco-friendly construction materials. Strontium aluminate (SrAl2O4)-based phosphor, SrAl2O4:Eu2+,Dy3+, was used as a luminescent powder. This material has long persistent luminescence while also being affordable and nontoxic. It can be excited by a wide range of wavelengths of light to produce a blue-green glow, so the material can be charged under sunlight or strong indoor light. The advantages of phosphor materials coupled with economically favorable and environmentally friendly preparation methods could be beneficial for the development of luminescent aggregates or stones for architectural lighting with no electricity.


## 2. Materials and Methods

An experimental study was carried out to investigate the preparation of luminescent aggregates from the soda-lime glass waste obtained from soda water bottles (Singha Corporation, Thailand) and commercial SrAl2O4-based phosphor powder (45-55 μm, fluorescent glow powder, Amhere Intertrade, Ltd., Thailand). Table 1 summarizes the chemical compositions of glass wastes and phosphor powders, in wt.%, which were determined by an X-ray fluorescence spectrometer (ZSX Primus, Rigaku). The glass wastes were first cleaned, crushed, and grinded using ball-milling technique to obtain sand-like particles. The glass powder was then sieved into a particle size between 50 and 70 μm.Table 1
Chemical composition (wt.%) of the glass and phosphor powders.
MaterialsOxide (wt.%)Glass fritSiO2CaONa2OAl2O3MgOFe2O3K2OSO3TiO268.61817.4858.8632.1701.9300.2840.2240.1920.103P2O5ZrO2SrOPbOZnOMnO0.0320.0520.0190.0120.0050.011PhosphorSrOAl2O3P2O5SO3Dy2O3Eu2O3BaOCaOSiO263.02516.83311.3947.2591.1350.8200.1540.1120.048MgOCuOGa2O30.0190.0100.004To prepare the aggregate mix, glass powder was mixed with phosphor powder at various amounts (5%, 10%, 15%, and 20% by total weight of the mixture), using an agate and pestle grinder. Since the glass powder could not well harden on its own, a small amount of inorganic binder was added. In this research, sodium silicate solution was added into the mixture at a binder/glass waste weight ratio of 1.00. The final mixture was then poured into a ball-molding machine to produce spherical-shaped phosphor-in-glass aggregates. The samples were then sintered in air at 750°C for 30 min with a heating rate of 10°C/min.The crystal structures of as-prepared luminescent glass aggregates were analyzed using an X-ray diffractometer with CuKα radiation (XRD-6200, Shimadzu). Archimedes’ method was used to calculate the bulk density and apparent porosity. The photoluminescence (PL) spectra of the samples were recorded using a spectrophotometer (AvaSpec-2048TEC, Avantes). Microstructural images were studied through scanning electron microscopy (SEM, TM3030, Hitachi). Afterglow behaviour of luminescent aggregates was measured using an autoranging light meter (CEM, DT-1309).


## 3. Results and Discussion

Figure1 shows XRD patterns of phosphor-in-glass ceramic aggregates with varying phosphor contents in comparison to bare phosphor sintered at 750°C for 30 min. The XRD pattern of bare phosphor shows sharp characteristic peaks at 2θ=28.5°, 29.4°, 30.0°, and 35.2°, which agree well with the standard pattern of the monoclinic SrAl2O4 crystal structure (JCPDS PDF no. 00-028-1204). In our previous work [10], we found that phosphors had good structural stability at high temperatures up to 750°C. The luminescent intensity was also optimized at this temperature due to the highest crystallinity of the phosphors, even though they might suffer from the oxidation of the luminescent center (Eu2+, Dy3+).Figure 1
XRD patterns of bare phosphor and phosphor-in-glass ceramic aggregates with varying phosphor contents. The samples were sintered at 750°C for 30 min. The image in (b) is a zoom for CaSiO3 and SiO2 XRD peaks.For pure glass aggregates, the patterns show the appearance of crystalline peaks, which indicate the crystallization within the glassy matrix. The peaks are matched to the cristobalite (SiO2) (JCPDS PDF no. 00-028-1204) and wollastonite (CaSiO3) (JCPDS PDF no. 00-031-0300) crystals, which are consistent with previous reports [11, 12]. In general, the crystallization of glass is obtained from the heat treatment processes. Based on previous researches [10, 13, 14], the crystallization could be enhanced by impurities or surfaces of preexisting interfaces. As shown in Table 1, the major components of the glass frits used in this work are SiO2, CaO, and Na2O. Various other oxides with small quantities include Al2O3, MgO, Fe2O3, K2O, and TiO2. It has been reported that a small amount of oxides such as MgO and Al2O3 in soda-lime glasses could induce the crystallization of devitrite (Na2Ca3Si6O16), wollastonite (CaSiO3), and SiO2 polymorphs [12]. The crystallization of these phases is normally a surface crystallization [12, 15], which may cause an increase in surface roughness and high porosity. With the addition of phosphor in the glassy matrix, the reverse effect is observed. The SrAl2O4-based phosphors could act as a network modifier and weaken the glass structure. The incorporation of Sr2+ and Al3+ from SrAl2O4-based phosphors in the glass structure inhibits the crystallization process of amorphous glasses, resulting in the degradation of the phosphor’s structure. The cristobalite and wollastonite peaks, as a consequence, become weaker with the addition of phosphor powder. This is consistent with previous researches [16, 17].Figure2 shows the bulk density and apparent porosity of the samples. At low phosphor content, there is no significant change in the density of the samples, while their apparent porosity increases with increasing phosphor content. This is probably due to the surface crystallization and the inhibition of the viscous flow of glass particles by the presence of phosphor, thereby reducing the densification of the glasses and increasing the porosity. The nearly constant density is, therefore, the competition between the high density of crystalline phases, the low density of glassy phases, and the porous structure [18]. When the phosphor content increased to 15 and 20 wt.%, however, both apparent porosity and bulk density are decreased. This could be because the crystallization of the glass is decreased, promoting the amorphous structure of the glass. It is found that the addition of a sufficient amount of phosphor could enhance the formation of the glassy phase. Similar observations have been previously reported that SrAl2O4-based phosphor could react with the matrix glass, causing the destruction of the SrAl2O4 structure [16, 19]. This is consistent with the broader XRD peaks of the SrAl2O4 phase in glass aggregates, as shown in Figure 1. The increase in porosity from 15% to 20% could be because an excessive amount of phosphor could act as a rigid inclusion, retarding the viscous sintering and densification process to occur properly. To study any dimensional changes of samples during heating, the samples were heated in a tube furnace at 750°C, and pictures taken at different times were reported in Figure 3. It was found that all the samples did not experience any substantial shape changes. The heat treatment only caused a shrinkage due to the densification process. However, the degree of shrinkage tends to increase with increasing phosphor content.Figure 2
Bulk density and apparent porosity of phosphor-in-glass ceramic aggregates with varying phosphor contents.Figure 3
Digital images of samples during the heat treatment at 750°C for 30 min.The crystallization of the wollastonite phase in the glassy matrix could be confirmed from the microstructures of the samples (Figure4). For 0 wt.% phosphor content, the surface was rough with a number of pores randomly distributed in the glassy matrix. The presence of wollastonite, which occurred as rod-shaped crystals, could also be clearly seen. On the contrary, when phosphor powder was added, wollastonite crystals became larger in size but less in quantities. At a low phosphor/glass ratio, the grain growth might be restrained by the presence of the crystallite phases. It could also be observed that, with high phosphor concentration, the amounts of pores and crystalline phases were decreased in agreement with the previous discussion. To optimize the required properties of phosphor-in-glass ceramic aggregates, therefore, a suitable amount of glass frit and phosphor powder must be used.Figure 4
SEM micrograph of fractured surfaces of phosphor-in-glass ceramic aggregates with varying phosphor contents. The bar shows a 30μm scale. The samples were etched in HF solution for 30 s.PL spectra of luminescent glass aggregates with the excitation wavelength of 345 nm are displayed in Figure5. For the sample with 0% phosphor, a small emission peak could be observed between 400 and 600 nm. This peak could be obtained from the wollastonite crystals. Previous research has reported that wollastonite could be a potential host for luminescent materials [20]. Their emission peaks could be between 350 and 800 nm depending upon its doping. For phosphor-in-glass ceramic aggregates, there is a dominant emission peak centered at 520 nm, which could be assigned to the 4f65d1→4f7 transition of Eu2+ in SrAl2O4. A shoulder peak is also observed at around 500 nm. This could be due to the crystal field splitting of the Eu2+. The PL intensity increased with increasing phosphor contents.Figure 5
PL spectra of phosphor-in-glass ceramic aggregates with varying phosphor contents.Figure6 shows the physical appearance and the glowing effect of luminescent glass aggregates. The samples were exposed to UV light for 15 min to enable the glowing effect in the dark. With UV light exposure, the glass aggregates emitted a greenish glow. The glow was brighter with increasing phosphor content. The brightest apparent glow was observed in the sample with the highest phosphor content (20%).Figure 6
Phosphor-in-glass ceramic aggregates with varying phosphor contents with UV light exposure and in daylight.To study the afterglow duration time, the glass aggregates were exposed to UV light for 15 min, and the luminescence intensity was measured with time, as shown in Figure7. It could be seen that the photoluminescence of the samples exhibited fast initial decay. However, with full energy absorption from the UV light, the samples can produce a long greenish afterglow luminescence. In addition, the luminescence intensity increased with increasing phosphor content.Figure 7
Luminescence decay curves of phosphor-in-glass ceramic aggregates with varying phosphor contents.


## 4. Conclusions

The crystallization, microstructure, and properties of phosphor-in-glass ceramic aggregates were studied in this research. The presence of a large amount of SrAl2O4-based could promote the amorphous structure of glass and inhibit the crystallization of glass. The resultant aggregates could emit their glow and release their stored light energy after the light source was removed. This self-emitting material could be beneficial for lighting outdoor landscape architects such as walkways, pathways, and patios.



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