Phosphate glasses are one of the good hosts of several transition metal oxides (TMO) which show different valence states. The valence state of such metal depends on the content and the properties of the other components of the glasses   . The transition metal ion can locate in the network either in the substitution or interstitial positions. When the ions take the substitution position, it is able to crosslink between the glass former and modifier. But, in the case where the ions locate in the interstitial positions, it can link to non-bridging oxygen (NBO) . Transition metals are used as activators in advanced technologies such as phosphors, lasers, solar energy converters and in a number of electronic devices. Recently, the transition metal oxides doped alkali phosphate glasses have been the subject of intensive investigation in view of their potential applications in various domains of modern technology . The investigation of relationship between structure and properties is essential in material science. Alkali phosphates form good glasses over a wide range of composition. But, one of the major issues that limit the use of phosphate glasses is their poor chemical durability. The improvement of their chemical durability is often realized by the addition of some oxides such as Al2O3, SnO, Fe2O3 . Also, the addition of iron oxide to lead phosphate improves the chemical durability of the glass without substantial change in the physical properties . In addition, iron phosphate glasses have attracted much attention owing to their high chemical durability, wide compositional flexibility and low melting temperature  . These glasses are known for their high chemical durability and for their application in vitrifying nuclear waste  . Owing to the insertion of iron in the phosphate matrix, the easily hydrolysable P-O-P bridging links have been replaced by the water-resist Fe-O-P linkages thereby providing these glasses with excellent chemical durability  . In this context, S. Nakata et al. have reported that the addition of divalent Fe2+ into NaPO3 broke the P-O-P bonds and forms water-resist Fe-O-P linkages in xFeO-(100 − x)NaPO3 glasses . Also, Y. M. Moustafa et al. reported that the increasing Fe2O3 in the xFe2O3-(100 − x)P2O5 system leads to the formation of P-O-Fe2+ and P-O-Fe3+ bonds .
Recently, we have studied the effect of substitution of Li2WO4 by TiO2 inside the Li2O-Li2WO4-TiO2-P2O5 glasses . In the present work our interest is focused on the investigation of the influence of the substitution of Li2WO4 by Fe2O3 with the glasses 20Li2O-(50 − x)Li2WO4-xFe2O3-30P2O5 where (x = 0, 1, 5, 8, 10, 15 mol%). Some physical properties such as density, molar volume, glass transition temperature are studied. The structural approach of the glasses is realized by Infrared spectroscopy. The temperature and composition dependencies of their electrical properties are also investigated.
2. Experimental Procedure
The phosphate 20Li2O-(50 − x)Li2WO4-xFe2O3-30P2O5 (0 ≤ x ≤ 15 mol %) glasses were prepared from precursors purchased from Sigma-Aldrich. Powders of lithium carbonate (Na2CO3), iron trioxide (Fe2O3), lithium tungstate Li2WO4, and hydrogen ammonium phosphate (NH4H2PO4) were weighed to get the required composition and ground in a mortar with pestle for 30 min to obtain homogenous compositions. Each mixture was heated in an electric furnace at 300˚C and 600˚C by placing them in an alumina crucible for several hours. Then, the temperature of the furnace is increased to attain the melt for about 30 min at 900˚C, the preparation temperature until a bubble free liquid was formed. The melt was then rapidly quenched by pouring it on to a stainless steel plate maintained at Tg-20˚C to avoid excess thermal shocks. The obtained glasses were annealed for 3 h at 300˚C to relieve the mechanical strains. The glasses were placed in a desiccator before uses.
X-ray patterns of powdered samples were recorded using a Phillips D5000 diffractometer equipped with a CuKα X-ray source and a Ni filter (Kα = 1.54 Å) at room temperature. The XRD data were recorded in 2θ range (10˚ - 90˚) with 0.02 step width.
The density (ρ) of glasses was measured at room temperature by the Archimedes method using diethyl orthophthalate as the suspension medium. The uncertainty of the measurements is estimated to be ±0.01 g/cm3. Molar volume (Vm) of each glass is derived from the molar weight values (M) and the density (Vm = M/ρ). Oxygen packing density (OPD) of each glass was calculated from the density and composition using the formula OPD = 100 C (ρ/M), C is the number of oxygens per formula unit.
The glass transition temperature (Tg) and crystallization temperature (Tc) of the prepared glasses, they are determinated from DSC curves, which have been obtained by using DSC 131 Evo analyser. The estimated error on the temperature is ±4˚C. As type of, as the DSC curves depend of the particle size of ground glass batches which fixed about at 300 µm Sieve in this study for all glasses. The amount of ground glass batches is about 40 mg in nitrogen atmosphere at heating rate 10˚C/min.
FTIR absorption spectra of the prepared glasses were collected at room temperature in the range 1400 - 400 cm−1 (wavenumber) using the Fourier Transform Infrared FTIR TENSOR27 Spectrometer. The measurement carried out by using the pellets. These pellets were prepared by mixing about 1 mg of glass powder with 100 mg of anhydrous KBr.
The chemical durability tests are realized on the glasses which were cut in parallelepiped shapes. The block of glass was rinsed with acetone and then dried. Each sample of glass was placed in a bottle containing deionized water (pH = 6.8). The bottles were then suspended in a thermostat bath maintained at a temperature of 30˚C for duration of 250 hours. All the experiments are done under the same conditions and the ratio S/V (S: glass surface, V: volume of the altering solution) is maintained at 0.04 cm−1. The mass change (Δm) is determined as a function of time according to the equation: Δm = (m0 − mt)/A, where: m0, mt and A are the initial mass, mass at specific time point and surface area of the specimen (cm2), respectively. The pH values of the test solutions were measured by a pH-meter.
Electrical measurements of the prepared glasses were performed by Impedance Spectroscopy (IS) Hewlett Packard Model 4284 A precision LCR. The amplitude of the DC signal applied across the sample was 0.5 V. These glasses were ground to fine powder and made into pellets with 10 mm diameter and thickness of 1 mm. The pellets were dried and coated with silver paint on either faces. The real and imaginary parts of complex impedance measurements were measured as a function of frequency (20 Hz - 106 Hz) and temperature (328 k - 627 k).
3. Results and Discussion
3.1. X-Ray Diffraction
To ascertain the vitreous state of the prepared glasses we have first of all tested these samples by the X-ray diffraction (XRD) analysis. Figure 1 shows the XRD patterns of the studied samples. These patterns are free from peaks suggesting the absence of any crystalline phases inside the samples thereby confirming their amorphous state. All the glasses are colored except the composition (x = 0) which is colorless suggesting that the transition metal is in its high valence state (W6+) in this composition.
3.2. Density and Molar Volume
Figure 2 illustrates the variations of the density and molar volume as a function of iron content (Fe2O3 in mol %). The addition of Fe2O3 on behalf of tungsten oxide decreases the density and increases the molar volume. The increase of Fe2O3 ratio results in an open glass structure with lower compaction. The density decreases from 4.18 g/cm3 for (x = 0) to 3.61 g/cm3 for the glass (x = 15). The experimental data of these parameters as listed in Table 1. As in our previous
Figure 1. X-ray patterns of the Li2O-Li2OWO4-Fe2O3-P2O5 glasses.
Figure 2. Composition dependence of the density and the molar volume for glasses.
Table 1. Some physical properties for the studied glasses.
work  , the decrease in density can be explained by the large difference in molecular weight between Li2WO4 (261.72 g/mol) and Fe2O3 (159.69 g/mol). The introduction of the lighter molecule in the glass instead of a heavier one leads to decrease the density. On the other hand, the increase of molar volume from 42.92 cm3/mol (x = 0) to 45.26 cm3/mol (x = 15) when Fe2O3 replaced Li2WO4 reveals either an increase of the interatomic spacing or the decrease of the strength constant of the bonds inside the glassy network. The increase of volume with (x) put forward that the interatomic spacing among the atoms of glass network increases when Fe2O3 ratio increases. Specially, the increase of the average length of M-O (M = P, W, Fe) bonds can explain the observed increase of (Vm). This happens when some bridging oxygen (BO) convert to non-bridging oxygen (NBO) in the glassy-matrix.
3.3. DSC Analysis
The DSC curves of the prepared glasses are shown in Figure 3. The endothermic peaks in DSC traces represent glass transition phenomena and the onset temperature of endothermic peak corresponds glass transition temperature (Tg). An exothermic peak represents the crystallization occurring at the peak temperature (Tc). The DSC curves of the glasses (x = 0, 1 and 5) are characterized by an
Figure 3. DSC curves of the studied glasses.
endothermic peak (Tg) and an exothermic peak (Tc1). However, the glasses with the compositions (x = 8, 10 and 15) show two exothermic peaks (Tc1, Tc2). The values of Tg, Tc1 and Tc2 for the prepared glasses are summarized in Table 1. The substitution Li2WO4 with Fe2O3 increases the glass transition temperature (Tg) from Tg = 407˚C ± 2˚C to Tg = 432˚C ± 2˚C.
From the analysis of Figure 4 and data of Table 1, one can see that Tg increases with increasing Fe/P ratio. The increase of Tg reflects an increase of the glass viscosity as well as the formation of stronger bonding in the glass such as P-O-Fe bonds. The increase of Tg with iron content can also be associated to the reticulation effect of iron in the network. If such assumption is true one can expect an increase of the oxygen packing density (OPD) when the iron ratio increases. However, an opposite trend for (OPD) is obtained (Figure 4). Therefore, the most prominent reason for increasing Tg with iron oxide is the formation of strong bonds in the glass network.
4. Infrared Spectroscopy
The structure approach of the prepared glasses has been investigated by using FTIR spectroscopy in frequency range 400 - 1400 cm−1. Such study allows us to check the phosphate units and other vibrational modes present in the network. The obtained IR spectra of the glasses are shown in Figure 5. The assignment of the different bands is realized according to previous literature data  . The band positions and their assignments are gathered in Table 2.
Figure 4. Glass transition temperature (Tg) and oxygen packing density (OPD) of the studied glasses.
Figure 5. Infrared spectra of the studied glasses.
Table 2. IR band assignments in the 400 - 1400 cm−1 range frequency for the studied phosphate glasses.
The principal bands are observed in the range 950 to 1220 cm−1. They correspond to symmetric and asymmetric stretching modes of non-bridging oxygen on different P-tetrahedra. The band νas(PO2)−(Q2) in metaphosphate is located in the range 1220 - 1200 cm−1, νas(PO3)2−(Q1) of pyrophosphate groups and the mode vibration of isolated orthophosphate groups (Q0) are situated in the range 1040 - 1000 cm−1. The band at 970 - 930 cm−1 is assigned to the asymmetric vibrations νas(P-O-P) and/or νas(P-O-M) (M = W, Fe). The band at 730 - 720 cm−1 is attributed to the symmetric stretching modes νs(P-O-P). The broad band in the range 500 - 480 cm−1 belongs to bending vibrations of basic structural units of phosphate glasses. The substitution of Li2WO4 by Fe2O3 leads to changing in frequency and intensity of some bands. With the increase of the iron content in the glasses, it is observed that the intensity of the band associated to Q1 species increases. Also, the intensity of Q0 species (1040 - 1000 cm−1) increases with increasing the iron content. It seems that the iron oxide depolymerizes the network and its content increasing induces the formation of pyrophosphate and orthophosphate structural units in the network.
5. Chemical Durability
Generally, the dissolution process of the glasses depends on several parameters such as surface of the glass, layer formation, and solution chemistry. The dissolution behavior of the glass is controlled by the reaction of the glass network and the type of ions existing in the solution .
5.1. Weight Loss
Figure 6 shows the weight loss as a function of time for the 20Li2O-(50 − x)Li2WO4-xFe2O3-30P2O5 glasses (0 ≤ x ≤ 15). When the content of Fe2O3 is increased from x = 0 mol% to x = 15 mol%, we can differentiate two stages: 1) for t < 100 h, the dissolution is almost linear. The initial corrosion rate is also
Figure 6. Evolution of the weight loss of the glasses as a function of time (h).
determined; 2) for 100 h < t < 250 h, there is a marked slowdown in dissolution. Indeed, Li2WO4 substitution by Fe2O3 has observable effect on the dissolution behavior of synthesized glasses. The temporal evolution of the dissolution shows that the glass of composition (x = 0) is characterized by a faster initial dissolution than that of the other glasses (x = 1 or 5 mol %). The solubility of the glasses studied depends on the degree of substitution of Li2WO4 by Fe2O3. It can be said that Fe2O3 leads to the improvement of the chemical durability of the network by the formation of P-O-Fe type bonds, which have been identified by the use of infrared spectroscopy of Fe2O3-containing glasses. These results are consistent with thermal analysis which showed that the introduction of Fe2O3 into the phosphate glass network makes the glass matrix harder. The correlation between the results of the dissolution and the results of the thermal analysis showed that the introduction of Fe2O3 in the vitreous network leads to the reinforcement of the chains constituting the vitreous matrix of the glass prepared .
The enhancement of the chemical durability of the glasses with high iron content could be due to the low rate of glass surface hydration. Bunker et al. developed the general description for the dissolution reactions between phosphate glasses and water . The first stage of dissolution is controlled by diffusion, including penetration of H2O into the glass network and diffusion of ions through the developing hydrated layer back into solution. Water hydrates the phosphate anions by reacting with the metal (alkali, Fe)-O-P bonds that link neighboring P-anions . At longer times, linear reaction kinetic dominates as the hydrated metals and phosphate anions are released into solution.
5.2. pH Variation
From the measurements of the pH of the leachate solution (Figure 7), it is observed that pH values decrease with time. For the glasses without (x = 0) or with lower iron content the measured pH corresponds to acidic solutions. From the analysis of Figure 7 we observed that the pH values of the leachates show two phases: 1) before 48 h there is a sudden alteration or the thermodynamic imbalance between the glass and the altering solution is great which creates a sudden decrease in pH; 2) after 48 h, a phase of slowing down of corrosion which is associated with the saturation of the altering solution which leads to the formation of a protective layer against the diffusion through the surface of the glass.
This pH variation depends on the chemical composition of the glass. We can say that the alkaline ions and the phosphate ions of the glass surface were released into the solution. This ion exchange plays a major role in defining the acid-base character of the solution. Indeed, the decrease of the pH can be attributed to the disintegration of the phosphatic entities towards the altering solution and the possibility of formation of phosphoric acid controlled by the entities. These entities are obtained from the dissociation of orthophosphoric acid in water     :
Figure 7. Variation of the pH versus time for the glasses.
The dissociation constants allowed us to conclude that the dihydrogen phosphate ions in the water are much more abundant compared to the monohydrogen phosphate ions and phosphate ions .
5.3. Electrical Properties
The conductivity for the prepared glasses is determined according to Equation (1):
where “σ” is the conductivity, “t” is the thickness, “a” is the cross-section area of the pellet and “ ” is the bulk resistance.
Figure 8 shows the temperature dependence of the conductivity for the studied glasses. It increases with increasing temperature and follows an Arrhenius law (2):
where, Ea is the activation energy, is the pre-exponential term and kB is the Boltzmann constant.
These electrical parameters are determined (Table 3). The conductivity of the glasses depends on the composition of iron oxide. It increases with Fe2O3 content up to (x = 10), then it decreases. The variation of the activation energy follows an opposite trend to that of the conductivity. It seems that up to (x = 10) the mobility is the more influencing parameter since the concentration of lithium ion decreases with Fe2O3 content. However, when the ratio of iron reaches x = 15 mol% the decrease of the conductivity may be due to the low lithium content in the glasses.
Figure 8. log(σdc∙T) vs 1000/T plots for the glasses.
Table 3. Electrical parameters of the studied glasses.
The obtained data of electrical measurements are analyzed by the modulus formalism ( ). The real and imaginary parts of (M) are calculated from the measured impedance data using Equations (3) and (4):
where, and are the real and imaginary parts of the impedance, respectively. ω is the angular frequency and C0 is the vacuum capacitance of the cell.
Figure 9 shows the variation of as a function of frequency in the range (20 Hz - 106 Hz) at different temperatures for the prepared glasses (x = 0 and x = 10). These spectra are slightly asymmetric suggesting that the relaxation present in the material was non-Debye. The maximum in the peak shifts to higher frequency with increasing temperature. The shift in peak maximum corresponds to the conductivity relaxation. This behavior suggests that the dielectric relaxation is thermally activated. The relaxation frequency fp of the charge carriers is determined from the maximum of . The variation of the determined peak frequency (fp) as a function of temperature is shown in Figure 10. From the analysis of this latter figure, it is observed that the frequency relaxation is thermally activated and
Figure 9. The frequency dependence of for the glasses (x = 0) and (x = 10).
follows an Arrhenius behavior with activation energy (Ef). In order to determine the mechanism of conduction, we plotted in the same figure the temperature dependence of the conductivity as shown in Figure 10 for the glasses (x = 5, and x = 15). We observe that both lines are quasi-parallel and the activation energies issued from impedance (Ea) and modulus (Ef) spectra are very similar (Table 3). This result suggests that the electrical conductivity in the glasses under study is probably due to hopping mechanism .
The asymmetric nature of spectra suggested that the relaxation behavior was non-Debye and could be characterized by the stretched exponent parameter β < 1 . For an ideal dielectric material, for which the dipole-dipole interaction is negligible, the value of β is equal to unity (β = 1). The stretched exponent parameters, β, can be obtained from the peak relaxation frequency (β = 1.14/FWHM), where (FWHM) is the width at half-maximum of M"(f) curves. For each glass, it is found that the value of β is independent of temperature and
Figure 10. Temperature dependence of logσdc ∙ T and logfp for the glasses (x = 5) and (x = 15).
the obtained values of β for all the compositions are regrouped in Table 3. The values of β are found to be less than unity. This demonstrated the non-Debye nature of the dielectric relaxation inside the glasses.
The electrical impedance data are also analyzed by the dielectric formalism ( ) by using the following Equation (5)  :
where, is the real part of the permittivity (resistive) and is the imaginary part of the permittivity (reactive), C0 the capacitance of the empty cell. These parameters are determinate according to Equations (7) and (8) respectively:
The dielectric constant values measured from the impedance data are plotted as a function of frequency at different temperatures in Figure 11. It is observed
Figure 11. Variation of the permittivity as a function of the frequency for the glass (x = 5).
that the glasses showed high values of the permittivity at low frequency and high temperature. This can be explained on the basis of the polarization existing in the sample. The increased dielectric constant value at lower frequencies region is related to the contribution from space charge/interfacial polarization. Indeed, the higher values of these amorphous glasses at lower frequencies were explained by the presence of bulk interfacial. Interfacial contains defects such as dangling bonds, vacancies, and vacancy clusters. Thus, the space charges can move under the application of an external field and when they are trapped by the defects, lots of dipole moments (space charge polarization) are formed . The increase in with temperature is due to the weakening of binding force between molecules/atoms with the increase in temperature, permitting the molecules/atoms to vibrate more and more which in turn increase the polarization, hence increase in the dielectric constant . In addition, the decrease in with the frequency is explained by the decreasing number of dipoles which contribute to polarization. As a matter fact, the application of the electrical field with low frequency assists electron hopping between two different sites in the glasses. Whereas, at high frequency, the charge carriers will be unable to rotate with enough speed, so their oscillation is going to vanish .
The glasses inside the 20Li2O-(50 − x)Li2WO4-xFe2O3-30P2O5 system were prepared by melt-quenching method. The substitution of Li2WO4 by Fe2O3 increases the density and the glass transition temperature Tg. The analysis of the glasses by IR spectroscopy has revealed that the introduction of Fe2O3 content in the glasses transforms some metaphosphate groups (Q2) to pyrophosphate (Q1) and orthophosphate (Q0) structural units. The formation of the Fe-O-P water-resist bonds in the glass network is highlighted and this iron bond-type improved their chemical durability. The electrical conductivity of the glasses is thermally activated and follows an Arrhenius behavior. The dielectric relaxation behavior inside the glasses is non-Debye.
The authors would like to thank CNRST and OCP for their financial support of this work (PPR project).
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