# Characterization of Waste Material Derived Willemite-Based Glass-Ceramics Doped with Erbium

Authors: G. V. Sarrigani; H. J. Quah; W. F. Lim; K. A. Matori; N. S. Mohd Razali; A. Kharazmi; M. Hashim; H. R. Bahari
Journal: Advances in Materials Science and Engineering
 (2015)

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## Abstract

We reported, for the first time, to the best of our knowledge, the production of erbium doped willemite-based glass-ceramic using waste material. In this work, a willemite-based glass-ceramic was prepared from waste material to obtain excellent crystallinity and then doped with trivalent erbium (Er3+) to yield ([(ZnO)0.5(SLS)0.5]1−x[Er2O3]x) final composition where x
=
3 wt%. The samples were sintered at various temperatures (500–1100°C) to study the effects of sintering temperatures on microstructure and physical properties of the samples. X-ray diffraction (XRD) and Fourier transform infrared (FTIR) were used to determine structural changes and functional groups in the samples, respectively. Field-emission scanning electron microscopy (FE-SEM) equipped with energy dispersive X-ray was used to observe surface morphology and to detect presence of elements in the samples. Findings showed that average grain size of the Er3+ doped glass-ceramic sample increased as a function of the sintering temperature and the optimum temperature was 900°C.


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## Body

## 1. Introduction

In recent years, glass-ceramics doped with rare-earth ions have attracted significant attention because of their wide application in the field of laser technology and optical communications [1]. Thus far, various glass-ceramics (silicates and phosphates) have been utilized as the proper hosts for the rare-earths. However, poor chemical stability and low transition temperature of phosphates have restricted the use of phosphates as the host for these ions [2]. In contrast, silicates demonstrate much superior chemical stability when compared with the phosphates and therefore were advantageous for ion-exchange technique to produce optical waveguides [2]. In addition, silicate materials are more economic due to the traditional technology used for telecommunication application. Recently, different rare-earth ions have been studied as dopants in silicate-based glass-ceramics [3–5]. Among the doped materials, erbium oxide (Er2O3) is one of the promising materials for the use as a dopant in the silicate-based glass ceramics. Besides being a rare-earth oxide, it was anticipated that Er2O3 is unique due to the existence of trivalent charge (Er3+) on the cation, which may lead to the formation of active site for the charge transfer, eventually causing a transition of the absorption bands from 4f 4I13/2 to 4I15/2 [1]. The anticipation provoked, having known that the unique feature found in the rare-earth cerium oxide (CeO2) was attributed to the existence of Ce3+ in the oxide as a result of phase transition from Ce4+ to Ce3+ [6, 7]. This property has brought wide applications of the CeO2 not only as an optical material but also as a high dielectric constant gate oxide used in metal-oxide-semiconductor based devices [8, 9]. To date, the Er3+-doped silicate has been widely used in developing elements and sources for telecommunication systems since the wavelength region for telecommunications, which is around 1500 nm, coincides with the inter-4f 4I13/2→ 4I15/2 transition of Er3+ ion at 1535 nm [1].Amongst the silicate-based glass ceramics, willemite has attained considerable attention over the last 180 years as the zinc silicate material. Following its discovery, interest in the zinc silicate was focused toward its occurrence, crystallography, and application as an industrial material [1]. In addition, glass-ceramics are typically obtained by heat treatment of glassy precursors or by sintering green bodies consisting of glassy and crystalline materials [10, 11]. A number of literatures have been reporting on the preparation of Er3+:SLS (Soda Lime Silicate) glass and zinc silicate composites. Kaewwiset et al. [12] reported the preparation of Er2O3 doped SLS glass using a solid-state reaction at 1200°C. In another study, Cho and Chang [13] used similar solid-state reaction at 1400°C to produce manganese-doped zinc silicate green phosphor with appropriate oxides. To the best of our knowledge, despite extensive researches on producing willemite glass-ceramics, doped with rare-earths and metals using pure materials [14, 15], there is no report regarding the doping of Er3+ into willemite, which is produced from waste material. Therefore, it is of interest to investigate in present study for the production of willemite-based glass ceramics from waste material before being doped with 3 wt% of Er3+ by systematically studying the effects of various sintering temperatures on structural, chemical, and morphological properties of prepared samples.


## 2. Experimental

### 2.1. Materials

Willemite-based glass-ceramics doped with Er3+ (Zn2SiO4:Er3+) were prepared using the following materials: high purity ZnO (99.99%, Aldrich), Er2O3 (99.99%, Aldrich), and SLS glass waste bottle.


### 2.2. Preparation

First, SLS glass bottles were cleaned and crushed properly to <63μm using a mortar and pestle. Then, the SLS glass and ZnO powders were carefully mixed at a weight ratio of 1 : 1 during a ball milling process for 24 h. The mixture powder was afterward put in an alumina crucible and melted in an electric furnace at 1400°C for 4 h in air environment. Subsequently, the samples were quenched immediately into water in order to gain glass frit. The frit was again ground to <63 μm particles followed by a heat treatment at 1000°C in order to produce the willemite glass-ceramics. Unlike previous techniques of doping rare-earths [16], in this work 3 wt% of Er2O3 was doped in the last stage whereby the willemite had fully crystallized in the glass-ceramics. The mixing happened in a mortar and pestle for 1 h, followed by ball milling for the next 24 h. The obtained powder was pressed to pellets with 12 mm diameter and subsequently sintered at different temperatures (500–1100°C) for 4 h at a heating and cooling rate of 10°C/min.


### 2.3. Characterization

X-ray diffraction (XRD) analysis was performed by X-ray diffractometer (PANAalytical (Philips) X’Pert Pro PW3050/60) with CuKα radiation (Bragg angle 2θ in the angular range of 20 to 80°) equipped with a copper X-ray tube and scintillation detector. To identify crystalline phases in the analyzed samples, the powder diffraction file (PDF2) was used. Fourier transform infrared (FTIR) spectra of the samples were recorded over the range of 0–4000 cm−1 on a Perkin-Elmer 1752X spectrophotometer (Waltham, MA) using a KBr disc method. In order to obtain good quality FTIR spectra, the samples were crushed in an agate mortar to obtain fine powder. Microstructural observations were performed using a field-emission scanning electron microscopy (FESEM) modelled FEI NOVA NanoSEM 230 and equipped with energy dispersive X-ray (EDX) spectrometer. Finally, grain size of the samples was measured using mean linear intercept method.


## 2.1. Materials

Willemite-based glass-ceramics doped with Er3+ (Zn2SiO4:Er3+) were prepared using the following materials: high purity ZnO (99.99%, Aldrich), Er2O3 (99.99%, Aldrich), and SLS glass waste bottle.


## 2.2. Preparation

First, SLS glass bottles were cleaned and crushed properly to <63μm using a mortar and pestle. Then, the SLS glass and ZnO powders were carefully mixed at a weight ratio of 1 : 1 during a ball milling process for 24 h. The mixture powder was afterward put in an alumina crucible and melted in an electric furnace at 1400°C for 4 h in air environment. Subsequently, the samples were quenched immediately into water in order to gain glass frit. The frit was again ground to <63 μm particles followed by a heat treatment at 1000°C in order to produce the willemite glass-ceramics. Unlike previous techniques of doping rare-earths [16], in this work 3 wt% of Er2O3 was doped in the last stage whereby the willemite had fully crystallized in the glass-ceramics. The mixing happened in a mortar and pestle for 1 h, followed by ball milling for the next 24 h. The obtained powder was pressed to pellets with 12 mm diameter and subsequently sintered at different temperatures (500–1100°C) for 4 h at a heating and cooling rate of 10°C/min.


## 2.3. Characterization

X-ray diffraction (XRD) analysis was performed by X-ray diffractometer (PANAalytical (Philips) X’Pert Pro PW3050/60) with CuKα radiation (Bragg angle 2θ in the angular range of 20 to 80°) equipped with a copper X-ray tube and scintillation detector. To identify crystalline phases in the analyzed samples, the powder diffraction file (PDF2) was used. Fourier transform infrared (FTIR) spectra of the samples were recorded over the range of 0–4000 cm−1 on a Perkin-Elmer 1752X spectrophotometer (Waltham, MA) using a KBr disc method. In order to obtain good quality FTIR spectra, the samples were crushed in an agate mortar to obtain fine powder. Microstructural observations were performed using a field-emission scanning electron microscopy (FESEM) modelled FEI NOVA NanoSEM 230 and equipped with energy dispersive X-ray (EDX) spectrometer. Finally, grain size of the samples was measured using mean linear intercept method.


## 3. Results and Discussion

### 3.1. Structural Studies

XRD patterns of Zn2SiO4:Er2O3 samples sintered at different temperatures ranging from 500 to 1100°C for 4 h are discretely presented in Figure 1. The first XRD pattern (the most bottom pattern in Figure 1) shows diffraction peaks detected for pure erbium oxide (Er2O3), followed by the second pattern for glass frits and the third pattern for unsintered and undoped willemite-based glass-ceramics. It was observed that main diffraction peak of erbium oxide (Er2O3) was located at diffraction angles (2θ) of 29.29° while the XRD pattern shown for glass frits indicated amorphous nature of the glass frits. In the willemite sample sintered at 1000°C shown in the third XRD pattern, diffraction peaks detected at 2θ of 22.14°, 25.61°, 31.61°, 38.90°, 49.01°, and 65.87°, respectively, corresponded to the crystalline planes of (3 0 0), (2 2 0), (1 1 3), (4 1 0), (2 2 3), (3 3 3), and (2 2 6). The results agreed well with the findings from previous researchers [17–20], wherein rhombohedral crystalline phase of willemite was formed after the mixing of ZnO and SLS glass followed by a heat treatment at 1000°C [20]. By doping with 3 wt% of Er2O3 into the willemite and sintering at 500°C, an additional peak, ascribed to (222) diffraction plane of cubic crystalline phase of Er2O3, appeared at 2θ = 29.29°. The detection of single diffraction peak associated with Er2O3 indicated that the Er2O3 did not react with the crystalline Zn2SiO4 and therefore remained as an unreacted phase at 500°C. As the sintering temperature was increased from 500 to 700°C, the intensity decreased gently with a dramatic fall when temperature reached 800°C. Beyond 900°C, it was seen that the diffraction peak of crystalline Er2O3 started to diminish, leaving only the main diffraction peaks attributed to the willemite. The occurrence of this might be due to a complete entering of the Er3+ cations into the Zn2SiO4 lattice. Phase formation of the willemite-based glass-ceramics was further confirmed using FTIR.Figure 1
The XRD patterns of the willemite-based glass-ceramic (Zn2SiO4) sample doped with 3 wt% Er2O3 sintered at the temperature of 500–1100°C for 4 h.


### 3.2. FTIR Analysis

FTIR spectroscopy was performed to obtain fundamental information concerning the functional groups of the studied glass-ceramics. FTIR spectra of the willemite-based glass-ceramics with the content of 3 wt% Er2O3 sintered at different temperatures are presented in Figure 2. The bands detected in the FTIR spectra have been summarized in Table 1. The experimental data gained in present work were compared with those of some related vitreous and crystalline compounds [21–25]. It was deduced that the FTIR spectra of glass-ceramic matrix (Zn2SiO4:Er2O3) consisted of eight wide and strong transmission bands, positioned at 395 cm−1, 485 cm−1, 595 cm−1, 702 cm−1, and 902 cm−1. Normally, the metal-oxide vibrations would occur below 1000 cm−1. The transmission peak in the lower wave number of 395 cm−1 was assigned to the asymmetric deformation of SiO4 group (ν
4 SiO4) [26]. The band positioned at 485 cm−1 corresponded to SiO4 asymmetric stretching vibration (ν
3 SiO4) [27, 28]. The peak at 595 cm−1 was marked as the asymmetric stretching vibration of ZnO4 group (ν
3 ZnO4) [29–33]. The distinct band placed at 702 cm−1 could be assigned as the totally symmetric stretching vibration of SiO4 group (ν
1 SiO4) [34–36]. The broad band located at 902 cm−1 corresponded to asymmetric stretching of SiO4 (ν
3 SiO4) [17].Table 1
FTIR transmission features and their assignments for oxide [(ZnO)0.5(SLS)0.5
]
1
-
x[Er2O3
]
x system.
Wavenumber [cm−1]
Assignment
395
Asymmetric deformation stretching of SiO4 (ν
4 SiO4)
485
Asymmetric stretching of SiO4(ν
3SiO4)
595
Asymmetric stretching of ZnO4(ν
3 ZnO4)
702
Totally symmetric stretching of SiO4 (ν
1 SiO4)
902
Asymmetric stretching of SiO4 (ν
3 SiO4)Figure 2
FTIR spectra of the willemite-based glass-ceramic samples doped with 3 wt% Er2O3 sintered at the temperature of 500–1100°C for 4 h.As a whole, the presence of vibrations associated with SiO4 and ZnO4 groups would clearly suggest the formation of Zn2SiO4 phase [37]. The increase of sintering temperature from 500 to 1100°C would cause an increase in intensities of the FTIR bands. On the other hand, at higher temperature of 1100°C, the band situated at 700 cm−1 disappeared. A compositional evaluation of the FTIR properties of the [(ZnO)0.5(SLS)0.5]1−x[Er2O3]x system in present work proposed that the presence of Er3+ ions would affect the surroundings of Si-O bond and the trivalent Er3+ would occupy the position. The literature reported that FTIR spectrum of crystalline (cubic) Er2O3 would show characteristic transmission bands located at 469 cm−1, assigned to the Er-O bond vibrations [38]. Hence, the band located at 469 cm−1 would belong to the vibrations of the Er-O group present in the studied glass-ceramic system. In addition, the most significant modification produced by the addition of Er3+ and the increase of sintering temperature of the studied samples was related with a drop in intensity of the FTIR band located at 702 cm−1. Results indicated that the addition of Er2O3 into willemite as well as the increase of sintering temperature had led to a reduction in the content of SiO4 group.


### 3.3. Surface Morphological Analysis

Figures3(a)–3(f) show FESEM images of the willemite-based glass ceramics doped with of 3 wt% of Er3+ as a function of sintering temperature (500–1000°C) (Figures 3(b)–3(f)) in comparison with the willemite glass ceramic without the doping (Figure 3(a)). As it can be observed in Figure 3(a), the crystallized particles aggregated and were irregular in shape. In addition, the willemite surface showed a homogenous distribution of rhombohedral-like particles. By observing Figure 3(b), it could be seen that when the willemite was doped with 3 wt% of Er3+ and sintered at the temperatures of 700°C, the Er3+ ions were dispersed on surface of the willemite and did not contribute to the ceramic’s lattice. On the other hand, after increasing the sintering temperature up to 800°C and 900°C (Figures 3(c) and 3(d)), surface morphology of the impact powder became granular and appeared to have a homogenous distribution, which could be due to a reaction of the Er3+ with the willemite. However, agglomeration of the willemite occurred while approaching the temperature of 1000°C (Figure 3(e)) whereby the clustered Er3+ remained on the surface. Subsequently, at the temperature of 1100°C (Figure 3(f)), the willemite melted and had completely covered the dopant particles. As a conclusion, it could be said that the amorphous phase was reduced during sintering. In addition, as the temperature was increased to 1000°C, less grain boundaries were present due to grain growth. However, at the temperature of 1100°C, it was impossible to calculate grain size of the sample due to the melting process. A summary of the obtained grain sizes of the samples has been presented in Figure 4. The distribution of Er3+ in the willemite matrix was confirmed by FESEM-EDX analysis, as shown in Figure 5. The EDX spectrum distinctly showed the presence of Zn, O, Si, Al, and Er, in addition to the Au peak, resulting from the sputtered gold on the surface during the characterization process. However, the detection of Al peak was due to the SLS glass from the waste material. The sintering temperature was at or above 1200°C [39, 40] in most of the recently reported investigations; however, it had been decreased to a lower temperature (900°C) in the present work. In addition, other impurities, such as ferum and ferum oxide were not detected for all of the investigated samples.Figure 3
FESEM micrographs of willemite and Er3+ doped glass-ceramic pellets sintered 4 h at different temperatures: (a) willemite, (b) 700°C, (c) 800°C, (d) 900°C, (e) 1000°C, and (f) 1100°C.
(a)
(b)
(c)
(d)
(e)
(f)Figure 4
Grain size distribution of 3 wt% Er3+ doped willemite-based glass-ceramic crystals in the glass-ceramic samples sintered at 900°C for 4 h.Figure 5
FESEM-EDX analysis of the distribution of Er3+ in the willemite-based glass-ceramic doped with 3 wt% Er3+ and sintered at the temperature of 900°C.


## 3.1. Structural Studies

XRD patterns of Zn2SiO4:Er2O3 samples sintered at different temperatures ranging from 500 to 1100°C for 4 h are discretely presented in Figure 1. The first XRD pattern (the most bottom pattern in Figure 1) shows diffraction peaks detected for pure erbium oxide (Er2O3), followed by the second pattern for glass frits and the third pattern for unsintered and undoped willemite-based glass-ceramics. It was observed that main diffraction peak of erbium oxide (Er2O3) was located at diffraction angles (2θ) of 29.29° while the XRD pattern shown for glass frits indicated amorphous nature of the glass frits. In the willemite sample sintered at 1000°C shown in the third XRD pattern, diffraction peaks detected at 2θ of 22.14°, 25.61°, 31.61°, 38.90°, 49.01°, and 65.87°, respectively, corresponded to the crystalline planes of (3 0 0), (2 2 0), (1 1 3), (4 1 0), (2 2 3), (3 3 3), and (2 2 6). The results agreed well with the findings from previous researchers [17–20], wherein rhombohedral crystalline phase of willemite was formed after the mixing of ZnO and SLS glass followed by a heat treatment at 1000°C [20]. By doping with 3 wt% of Er2O3 into the willemite and sintering at 500°C, an additional peak, ascribed to (222) diffraction plane of cubic crystalline phase of Er2O3, appeared at 2θ = 29.29°. The detection of single diffraction peak associated with Er2O3 indicated that the Er2O3 did not react with the crystalline Zn2SiO4 and therefore remained as an unreacted phase at 500°C. As the sintering temperature was increased from 500 to 700°C, the intensity decreased gently with a dramatic fall when temperature reached 800°C. Beyond 900°C, it was seen that the diffraction peak of crystalline Er2O3 started to diminish, leaving only the main diffraction peaks attributed to the willemite. The occurrence of this might be due to a complete entering of the Er3+ cations into the Zn2SiO4 lattice. Phase formation of the willemite-based glass-ceramics was further confirmed using FTIR.Figure 1
The XRD patterns of the willemite-based glass-ceramic (Zn2SiO4) sample doped with 3 wt% Er2O3 sintered at the temperature of 500–1100°C for 4 h.


## 3.2. FTIR Analysis

FTIR spectroscopy was performed to obtain fundamental information concerning the functional groups of the studied glass-ceramics. FTIR spectra of the willemite-based glass-ceramics with the content of 3 wt% Er2O3 sintered at different temperatures are presented in Figure 2. The bands detected in the FTIR spectra have been summarized in Table 1. The experimental data gained in present work were compared with those of some related vitreous and crystalline compounds [21–25]. It was deduced that the FTIR spectra of glass-ceramic matrix (Zn2SiO4:Er2O3) consisted of eight wide and strong transmission bands, positioned at 395 cm−1, 485 cm−1, 595 cm−1, 702 cm−1, and 902 cm−1. Normally, the metal-oxide vibrations would occur below 1000 cm−1. The transmission peak in the lower wave number of 395 cm−1 was assigned to the asymmetric deformation of SiO4 group (ν
4 SiO4) [26]. The band positioned at 485 cm−1 corresponded to SiO4 asymmetric stretching vibration (ν
3 SiO4) [27, 28]. The peak at 595 cm−1 was marked as the asymmetric stretching vibration of ZnO4 group (ν
3 ZnO4) [29–33]. The distinct band placed at 702 cm−1 could be assigned as the totally symmetric stretching vibration of SiO4 group (ν
1 SiO4) [34–36]. The broad band located at 902 cm−1 corresponded to asymmetric stretching of SiO4 (ν
3 SiO4) [17].Table 1
FTIR transmission features and their assignments for oxide [(ZnO)0.5(SLS)0.5
]
1
-
x[Er2O3
]
x system.
Wavenumber [cm−1]
Assignment
395
Asymmetric deformation stretching of SiO4 (ν
4 SiO4)
485
Asymmetric stretching of SiO4(ν
3SiO4)
595
Asymmetric stretching of ZnO4(ν
3 ZnO4)
702
Totally symmetric stretching of SiO4 (ν
1 SiO4)
902
Asymmetric stretching of SiO4 (ν
3 SiO4)Figure 2
FTIR spectra of the willemite-based glass-ceramic samples doped with 3 wt% Er2O3 sintered at the temperature of 500–1100°C for 4 h.As a whole, the presence of vibrations associated with SiO4 and ZnO4 groups would clearly suggest the formation of Zn2SiO4 phase [37]. The increase of sintering temperature from 500 to 1100°C would cause an increase in intensities of the FTIR bands. On the other hand, at higher temperature of 1100°C, the band situated at 700 cm−1 disappeared. A compositional evaluation of the FTIR properties of the [(ZnO)0.5(SLS)0.5]1−x[Er2O3]x system in present work proposed that the presence of Er3+ ions would affect the surroundings of Si-O bond and the trivalent Er3+ would occupy the position. The literature reported that FTIR spectrum of crystalline (cubic) Er2O3 would show characteristic transmission bands located at 469 cm−1, assigned to the Er-O bond vibrations [38]. Hence, the band located at 469 cm−1 would belong to the vibrations of the Er-O group present in the studied glass-ceramic system. In addition, the most significant modification produced by the addition of Er3+ and the increase of sintering temperature of the studied samples was related with a drop in intensity of the FTIR band located at 702 cm−1. Results indicated that the addition of Er2O3 into willemite as well as the increase of sintering temperature had led to a reduction in the content of SiO4 group.


## 3.3. Surface Morphological Analysis

Figures3(a)–3(f) show FESEM images of the willemite-based glass ceramics doped with of 3 wt% of Er3+ as a function of sintering temperature (500–1000°C) (Figures 3(b)–3(f)) in comparison with the willemite glass ceramic without the doping (Figure 3(a)). As it can be observed in Figure 3(a), the crystallized particles aggregated and were irregular in shape. In addition, the willemite surface showed a homogenous distribution of rhombohedral-like particles. By observing Figure 3(b), it could be seen that when the willemite was doped with 3 wt% of Er3+ and sintered at the temperatures of 700°C, the Er3+ ions were dispersed on surface of the willemite and did not contribute to the ceramic’s lattice. On the other hand, after increasing the sintering temperature up to 800°C and 900°C (Figures 3(c) and 3(d)), surface morphology of the impact powder became granular and appeared to have a homogenous distribution, which could be due to a reaction of the Er3+ with the willemite. However, agglomeration of the willemite occurred while approaching the temperature of 1000°C (Figure 3(e)) whereby the clustered Er3+ remained on the surface. Subsequently, at the temperature of 1100°C (Figure 3(f)), the willemite melted and had completely covered the dopant particles. As a conclusion, it could be said that the amorphous phase was reduced during sintering. In addition, as the temperature was increased to 1000°C, less grain boundaries were present due to grain growth. However, at the temperature of 1100°C, it was impossible to calculate grain size of the sample due to the melting process. A summary of the obtained grain sizes of the samples has been presented in Figure 4. The distribution of Er3+ in the willemite matrix was confirmed by FESEM-EDX analysis, as shown in Figure 5. The EDX spectrum distinctly showed the presence of Zn, O, Si, Al, and Er, in addition to the Au peak, resulting from the sputtered gold on the surface during the characterization process. However, the detection of Al peak was due to the SLS glass from the waste material. The sintering temperature was at or above 1200°C [39, 40] in most of the recently reported investigations; however, it had been decreased to a lower temperature (900°C) in the present work. In addition, other impurities, such as ferum and ferum oxide were not detected for all of the investigated samples.Figure 3
FESEM micrographs of willemite and Er3+ doped glass-ceramic pellets sintered 4 h at different temperatures: (a) willemite, (b) 700°C, (c) 800°C, (d) 900°C, (e) 1000°C, and (f) 1100°C.
(a)
(b)
(c)
(d)
(e)
(f)Figure 4
Grain size distribution of 3 wt% Er3+ doped willemite-based glass-ceramic crystals in the glass-ceramic samples sintered at 900°C for 4 h.Figure 5
FESEM-EDX analysis of the distribution of Er3+ in the willemite-based glass-ceramic doped with 3 wt% Er3+ and sintered at the temperature of 900°C.


## 4. Conclusions

Structural changes induced by sintering temperature in the willemite-based glass-ceramic doped with trivalent erbium ions were well reflected in X-ray diffraction patterns, FTIR spectra, and FESEM images. Sintering of the samples produced homogeneity. The presence of willemite and Er3+ was being evidenced by X-ray diffraction analysis. The FTIR data suggested the presence of SiO4, ZnO4, and Er-O structural units. The microstructural study proposed that, by increasing the sintering temperature, the grain size increased. One of the most dominant results of this work was regarding the sintering of the synthesized pellets at a relatively lower temperature (900°C), which resulted in the formation of polycrystalline erbium-doped willemite samples. The structural properties of synthesized samples were comparable with previously reported materials.



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*Source: 953659-2015-06-09.xml*