Influence of barium oxide on glass-forming ability and glass stability of the tellurite–phosphate oxide glasses
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The effect of BaO content on the glass-forming ability, glass stability and structure of tellurite–phosphate oxide glasses in the 70TeO2–10P2O5–(20-x)ZnO–xBaO (x = 0, 5 and 10 mol%) system has been discussed. From the differential scanning calorimetry, the glass transition (Tg), crystallization (Tc) and the melting (Tm) temperatures were estimated. The decrease in reduced glass transition temperature (Trg) and glass-forming tendency parameter (Kh(Tc1)) with addition and increasing BaO caused a decrease in the glass-forming ability of glasses. It was also found that the thermal stability of these glasses against crystallization decreased with increase in BaO concentration into chemical composition of base glass, i.e., glass without barium oxide. The FTIR spectra were measured to understand the structure of the obtained tellurite–phosphate oxide glasses. The results have shown that phosphorous and tellurium ions were taken part in the formation of the glass network of the studied glasses. The addition of BaO caused significant changes in the FTIR spectra of glasses. More and more TeO3 and TeO3+δ units and PO42− groups (Q1 units) were created when the BaO was added into the chemical composition of the base glass. Increasing barium ions content into the chemical composition of glasses caused depolymerization of the tellurite–phosphate oxide glass network.
KeywordsTellurite–phosphate oxide glasses BaO Glass-forming stability Glass stability Structure
Recently, tellurite glasses have received considerable attention for their potential application as promising materials used for optical devices [1, 2, 3, 4, 5]. Tellurite glasses are characterized by good chemical durability, high luminescence intensity, low glass transition, good chemical resistance and high linear and nonlinear refractive index [3, 4, 5]. The low phonon energy (750 cm−1) of tellurite glass is also attractive for designing near-IR and mid-IR lasers, amplifiers, and passive fibers for power delivery and sensor engineering [6, 7, 8, 9, 10, 11, 12]. It has been reported that up-conversion enhancement in zinc tellurite glass doped with Er3+ ions . Walas et al. reported that tellurite glasses having erbium and dysprosium are good materials for a white light emission .
The tellurite glass structure is based on its parent crystalline forms: the α and β allotropic forms [5, 15, 16]. A number of investigations on the glass formation and structural analysis of binary and tellurite glasses have been reported [5, 17, 18, 19, 20, 21]. There are two basic structural units: TeO4 (trigonal bipyramid), TeO3 (trigonal pyramid), as well as the intermediate TeO3+δ polyhedron [5, 16, 22]. In TeO4 unit, four oxygen atoms are coordinated with one tellurium atom to form a trigonal bipyramid (tbp) with one of the equatorial oxygen positions unoccupied [5, 16, 23, 24]. In the trigonal pyramid structure, there are two bridging oxygen sites and one non-bridging oxygen (NBO) which is a Te = O double bond [5, 16, 25]. This is a unique structural characteristic of TeO2 glass, distinct from other network-forming glasses; e.g., silicates, phosphates and germanates in which only the NBO and bridging oxygen exist as a part of the structural unit [5, 16, 26, 27, 28, 29]. Modifiers such as BaO and ZnO break the random network of glasses, and the concentration of TeO3 and TeO3+δ units increases .
An extensive list of tellurite glass compositions with glass-forming ranges is reported in literature [17, 18, 19, 20]. There are a large number of strongly covalent glass-forming oxides (B2O3, P2O5, GeO2), and intermediates formers (WO3, Nb2O5, V2O5) combine with TeO2 [17, 18, 19, 20, 24, 31, 32]. Although attractive properties of tellurite glasses have been revealed, few studies have been made on the compositional dependence of basic properties such as glass-forming and thermal properties, which are essential for the design of glass materials. The tellurium–germanate glasses are also a potential glass host for optical fibers [33, 34]. Germanium-based glasses possess higher phonon energy in comparison with tellurium-based glasses. However, germanium-based glasses are characterized by higher thermal stability and higher mechanical strength than tellurium-based glasses . The barium gallo-germanate glasses modified with tellurium oxide were studied as a potential glass host for Eu3+ ions to induce emission in the UV region. Significant addition of tellurium oxide to the glass set causes host glass structure polymerization and a decrease in emission intensity . Last authors’ results suggested that modification of tellurite glasses with germanium oxide may be a perspective approach into efficient luminescent optical fiber light sources. However, key parameters are the control of viscosity and crystal nucleation and growth which tends to minimize the extrinsic scattering loss due to the presence of crystals during glass preform and fiber fabrication . Further examinations in the glass–ceramic in the system of TeO2-GeO2 will be performed in order to obtain a laser emission and second harmonic generation [37, 38]. Glass features mentioned above can be controlled by the analysis of the thermal properties and for that purposes, differential scanning calorimetry (DSC) is commonly used [19, 29]. Liu et al.  reported the glass transition and devitrification characteristics of two different families of glass-forming systems: NZT [(90-x)TeO2–10ZnO–xNa2O, x = 50, 10, 20 and 30 mol%)] and TZX [70TeO2–10ZnO–20X, X = 5ZnO, Li2O, Na2O and K2O]. In general, the absence of alkali oxides tends to lower the thermal stability of tellurite glass. By incorporating alkali oxide in the tellurite glass compositions, the glass stability increases as determined. It is evident that the presence of Na2O in the TZN glass system is essential for reducing the crystallization tendency when the TeO2/Na2O ratio is lower than 2:1 . For a sodium–tellurite composition, the highest value of Hrubby parameter was found for 20 mol% of Na2O, which is why this composition was modified by incorporating 10 mol% ZnO . According with Kaur et al. , as the concentration of BaO increases in xBaO–(100-x)TeO2 (where x = 10, 15 and 20 mol%) from 10 to 20 mol%, the value of ΔT decreases from 140 °C to 100 °C. Therefore, the thermal stability of glasses against crystallization decreases.
Phosphate gasses have shown better thermal stability and tensile strength than tellurite glasses. For these reasons, tellurite–phosphate glasses have received increasing attention with the goal to find a good compromise between the pure tellurite and phosphate glass properties . Konishi et al.  were first to report a phase diagram in the ternary TeO2–P2O5–ZnO system. The authors investigated the glass-forming region, the compositional dependence of the glass transition temperature and the coloring property for these (PTZ) systems. Konishi et al.  concluded that ZnO in all glass samples acts as a network former which bridges between the PO4 and TeO4 chains so that the glass transition temperature increases with the increase in ZnO content.
Apart from applications of tellurite–phosphate glasses, there is a lack of data on structural investigations as well as the thermal properties of these glass systems in the literature. Therefore, the aim of this research is to study the effect of barium on the thermal properties and structure of tellurite–phosphate glass system in order to understand the fundamental origin of such properties.
In the present work, the main aim was to study the glass-forming ability and glass stability parameters of the tellurite–phosphate glasses in the 70TeO2–10P2O5–(20-x)ZnO–xBaO (x = 0, 5 and 10 mol%) system. These parameters are formulated by different combinations of the following characteristic differential scanning calorimetry (DSC) temperatures: the glass transition temperature (Tg), the crystallization temperature (Tc) and the melting temperature (Tm). Additionally, FTIR spectra of glasses were analyzed in order to identify the contribution of each component to the local structure that determined the physical properties of these glasses.
The glass samples with molar compositions of 70TeO2–10P2O5–(20-x)ZnO–xBaO (x = 0, 5 and 10 mol%) were successfully synthesized by the melt-quenching method. Samples were prepared by using tellurium dioxide (purity ≥ 99.0%), phosphate pentoxide (purity ≥ 99.9%), zinc oxide, ZnO (purity > 99.9%) and barium oxide (purity 99.9%). The powder chemicals were weighed using an electronic digital weighting machine with an error of ± 0.0001 g. Each batch was heated from room temperature to 850 °C at a rate 10° min−1 in PtIr crucible in the melting furnace in air atmosphere. The melt was held at maximum temperature for 20 min until a bubble-free liquid was formed. The homogeneous melt was quenched by pouring it onto a preheated stainless steel mold to avoid excess thermal shocks. The glasses were annealed for 2 h at 20 °C below than the glass transition temperature to release the mechanical strains. The transformation temperature was based on literature data [3, 30, 41].
The nature of each sample was confirmed by using X-ray diffraction (XRD). X-ray diffraction studies were carried out on powdered samples on X’Pert Pro X-ray diffractometer supplied by PANalytical with Cu Kα1 radiation (λ = 1.54,056 Å) in the 2θ range of 10°–90°. The step size, time per step and scan speed were as follows: 0.017°, 184.79 s and 0.011° s−1. The X-ray tube was operated at 40 kV and 40 mA, and a scintillation detector was used to measure the intensity of the scattered X-rays.
Microstructure observations of glasses were made using a scanning electron microscope SEM–FEI Nova 200 NanoSEM with an analyzer of the element composition in micro-areas (EDS).
The thermal characteristic temperatures such as the glass transition (Tg), the crystallization (Tc) and the melting (Tm) temperatures were measured by using a Jupiter DTA STA 449 F3 thermal analyzer supplied by NETZSCH thermal analysis, operating in heat flux DSC with a heating rate of 10 °C min−1 in the 260–760 °C temperature range. Characteristic temperatures have been determined at the peak maximum.
The FTIR absorption spectra of the glasses in the 520–1200 cm−1 range were obtained with a Fourier spectrometer (Bruker Optics-Vertex 70 V). The measurements were done using the KBr pellet technique. Absorption spectra were recorded at 128 scans and the resolution of 4 cm−1.
The glass samples were labeled with the first letters of the components (TeO2–T, P2O5–P, ZnO–Z, BaO–B) and in accordance with the BaO content, i.e., 0 mol% of BaO (TPZ0B), 5 mol% of BaO (TPZ5B) and 10 mol% of BaO (TPZ10B).
Results and discussion
Chemical composition of samples
After melting the glass samples, each sample was determined by visual inspection. All obtained samples were transparent and bubble free.
The molar composition of samples
Glass-forming ability parameters
The thermal properties (Tg, Tc1 and Tm1) from DSC curves, values of glass-forming ability parameters (Trg and Kh) and values of glass-forming stability parameters (Kw, Kl and ∆T)
Several parameters or criteria have been proposed to reflect the relative glass-forming ability (GFA) among bulk glasses on the basis of different calculation methods [43, 44]. One is the reduced glass transition temperature Trg = Tg/Tf1 which is the ratio between the glass transition temperature Tg and the first melting temperature Tf1 of the corresponding glass-forming system [45, 46]. Another parameter is also used as a measure of the glass-forming tendency of materials: Kh = (Tc1 − Tg)/(Tf1 − Tc1), where Tc1 is the first crystallization temperature .
Using the data shown in Fig. 5 and Table 2, the reduced glass transition temperature (Trg) values for glasses vary from 0.62 (TPZ0B) to 0.55 (TPZ10P). For glasses containing a concentration of barium oxide, Kh(Tc1) parameter decreases from 0.20 to 2.33 as shown in Table 2. The decrease in Trg and Kh(Tc1) parameters with addition and with increase in BaO no incorporation supports the glass-forming ability. The GFA decreases with a decrease in BaO concentration.
Glass stability parameters
Values of Kw(Tc1) parameter and parameter Kl(Tc1) decrease when BaO concentration is added in the ternary system TeO2–P2O5–ZnO (Table 2). Generally, the difference, ∆T(Tc1) = Tc1 − Tg, gives a measure of the thermal stability of the glass . For the present study, its values are found to be 114 °C on the ternary system TeO2–P2O5–ZnO and 106–102 °C on the four-component system (containing 5 and 10 mol% BaO). It is obvious that the thermal stability of these glasses against crystallization decreased with increase in BaO concentration.
FTIR spectroscopy study
The bands at around 630 cm−1 and 680 cm−1 are due to the Te–O stretching vibration in TeO3 and TeO3+δ units, respectively, whereas band at 730 cm−1 is due to stretching vibrations of P–O–P vibrations in Q1 units, (1: number of link) (Fig. 6) [14, 15, 52].
Taking into account the FTIR results reported about some phosphate glasses may be assumed that the bands centered at around 930 cm−1 and 985 cm−1 are due to the P-O-P asymmetric stretching vibrations in Q2 units  and band at around 1048 cm−1 is assigned to the stretching vibrations of the PO42− groups (Fig. 6) [50, 51, 52].
As is shown in Fig. 6, the addition of BaO caused significant changes in the FTIR spectra of glasses. The intensity of the band at around 630 cm−1 and 680 cm−1 increased with addition and increase in BaO content in the base glass, as expected, since there are lower Te–O–Te linkages. This means that more non-bridging units are formed in the tellurite–phosphate network [30, 53, 54]. The addition of barium oxide contributed to a decrease in the intensity of the bands at around 930 cm−1, 985 cm−1 and an increase in the intensity of the band at 1048 cm−1. In fact, more and more PO42− groups (Q1 units) were created, when the BaO was added to the chemical composition of TPZ glass.
Characteristic temperatures, such as transition, crystallization and melting temperatures, play an important role in understanding the physical properties of glasses. Glasses with a close-packed network will have thermal stability, while those with loose-packed network will have instability . Generally, the Ba2+ ions are incorporated into the glass network as modifier ions, resulting in the loose packing of the glass network. Sekiya et al.  have been suggested that the binary tellurite glasses containing less than 20 mol% of BaO have a continuous network composed of TeO4 tbps, TeO3+1 polyhedra and TeO3 tps sharing vertices. In these glasses, an increase in BaO content promoted conversion of TeO4 tbps into TeO3+1 polyhedra and TeO3 tps. These data have also been confirmed by Sokolow et al.  and Kaur et al. . Modifier ions such as Ba2+ ions broke the random network of glasses, and the concentration of TeO3 tps and TeO3+1 polyhedra increased . The decrease in transition temperature value with increase in Ba2+ ions content contributes to a decrease in thermal stability of the glasses leading to loose-packed network . The decrease in the glass transition temperature values implies that the number of bridging oxygen groups decreases. This is mainly due to the addition of BaO which weakens the bond between each atom glass, increasing the number of NBOs atoms. The bond is easier to break, and hence, the transition temperature of the glass decreased. It also implies a decrease in rigidity of the glass network [30, 55]. In our study, the addition of BaO in TeO2-P2O5 network no caused the decreasing values of the transition temperature. Also, the glass-forming ability parameters and glass stability parameters decreased when Ba2+ ions were incorporated in the structure of TPZ glass. Probably, it is due to the change in the network of glasses, i.e., more non-bridging Te–O− units and PO42− groups are formed in the tellurite–phosphate network when the BaO was added to the chemical composition of base glass. The evolution of the network can be explained by the depolymerization of tellurite–phosphate glass network. The phosphate chain length decreased in the glasses with high BaO content due to the depolymerization of the tellurite–phosphate network, leading to an increase in the number of short phosphate chain units or rings . The addition of barium oxide also increased the TeO3 and TeO3+δ units, at the expense of TeO4 units. This consequently led to a decrease in the average cross-link density and the number of bonds per unit volume, which have a direct relation with characteristic temperatures of glasses. In this way, the thermal stability of these glasses against crystallization decreased with increase in BaO concentration and barium oxide no incorporation supports the glass-forming ability of glasses.
Tellurite–phosphate glasses without and with 5 and 10 mol% of BaO were prepared and characterized by differential scanning calorimetry (DSC) and FTIR spectroscopy. All presented glasses after heat treatment were fully amorphous materials. The crystalline phases were found as transition phases that dissolved above 590 °C in the tellurite–phosphate liquid during heat treatment.
Based on spectroscopic studies, it was found that barium ions are present in the network of the studied glasses as modifying ions that depolymerized the glass network. This led to a weakening of the tellurite–phosphate network and increase in the PO42−, TeO3 and TeO3+δ units. It resulted in a reduction of glass-forming ability and glass stability of the tellurite–phosphate glasses when the BaO was added to the TeO2–P2O5 system.
The work is the result of the Research Project No. 2016/23/B/ST8/00706 funded by the National Science Centre, Poland.
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