Classification of phosphate glasses as a function of O/P ratio and Qn tetrahedral sites.
Glasses of the (50-x/2)Na2O-xMO-(50-x/2)P2O5 (M = Zn, Mg or Mn) (0 ≤ x ≤ 33 mol%), (50-x)Na2O-xMO-50P2O5 (M = Zn, Mn) (0 ≤ x ≤ 33 mol%), and (0.9-x)NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol) were prepared by the melt quenching technique. Samples were investigated by means of X-ray diffraction, Archimede’s method, ellipsometry, Fourier-transformed infrared (FTIR), Raman, 31P solid state magic angle spinning nuclear magnetic resonance (MAS-NMR), UV-visible spectroscopy and calorimetry. For zinc, manganese and magnesium phosphate glasses, the increase in density with the addition of MO oxide suggests the compactness of the vitreous network. For zinc phosphate silicate glasses, the variations of density and refractive index were attributed to the structural changes when SiO2 oxide is progressively introduced. The increase in the glass transition temperature (Tg) reflects an increase in the cross-link strength of the structure as MO and SiO2 oxides are gradually incorporated. For all glass composition, spectroscopic investigations revealed the depolymerization of metaphosphate chains (Q2) allowing the formation of phosphate dimers (Q1). Calorimetric dissolution shows that the dissolution is endothermic for lower MO content and become exothermic when x rises. For (50-x/2)Na2O-xZnO-(50-x/2)P2O5 (0 ≤ x ≤ 33 mol%) glasses, the formation enthalpy increases with the incorporation of ZnO oxide.
- phosphate glasses
- phosphate-silicate glasses
- modifier oxide
- calorimetric dissolution
- formation enthalpy
- thermochemical cycle
Over the past several decades, great interests have been considered for phosphate glasses due to their superior physical properties which impart them a several advantages over conventional silicate and borate glasses.
Phosphate-based glasses are an interesting class in the world of glass and glass ceramics owing to their higher thermal expansion, lower melting and softening temperature, higher ultra-violet transmission and optical characteristic. Phosphate glasses have potential of applications in medicine, biology, batteries, laser technology, electronic, telecommunication [1, 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18, 19, 20, 21, 22, 23, 24, 25, 26, 27, 28, 29, 30, 31, 32, 33, 34, 35, 36, 37, 38, 39, 40, 41, 42, 43, 44].
In recent times, phosphate glasses have received considerable interest as a result of the synthesis of new glass composition with high chemical stability. The improvement of this quality induces the application of phosphate glasses in numerous fields of materials science, such as fast ionic conductors, semiconductors, photonic materials, hermetic seals, rare-earth in host solid state lasers and biomedical materials [1, 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18, 19, 20, 21, 22, 23, 24, 25, 26, 27, 28, 29, 30, 31, 32, 33, 34, 35, 36, 37, 38, 39, 40, 41, 42, 43, 44].
Thus, phosphate and silicate glasses are the most important materials which can extensively be used for laser sources and fiber amplifiers .
The basic structure unit of the phosphate network is based on corner-sharing PO4 units which form chains and rings or isolated groups PO4 .
The structure of the three dimensional network is obtained by linking three oxygen atoms with others PO4 tetrahedrons. The metaphosphate groups contain two covalent bridging oxygen atoms. Whereas, the pyrophosphate groups are formed by bending only single oxygen atom with other tetrahedral site.
Recently, the structure of phosphate glass is describes using the O/P ratio [13, 18, 19, 27]. Furthermore, many investigators used the O/P ratio in order to classify the distribution of phosphate groups in the vitreous network. Table 1 reports the classification of phosphate glasses as a function of O/P ratio .
|>3||Polyphosphates||Q2 + Q1|
|O: oxygen atom||P: Phosphorus atom||Q: Phosphorus tetrahedral sites|
For 2.5 < O/P < 3, the glass network is described by the distribution of ultraphosphate groups .
The metaphosphate groups are obtained for O/P ratio equal to 3. The glass network is described by the connection of PO4 tetrahedral anions with neighbors in order to form chains and rings.
For polyphosphate glasses, the O/P ratio is between 3 and 3.5. The structure is described by chains formed by PO4 tetrahedral anions joined with others.
For O/P = 3.5, the structure is obtained by forming the phosphate dimers such as pyrophosphate groups in which two PO4 tetrahedral shared one bridging oxygen . For 3.5 < O/P < 4, the isolated PO43− units are formed such as orthophosphate.
The increase of O/P ratio induces the depolymerization of phosphate groups which suggests the shortening of the average chain length .
The network connectivity of phosphate compound is conventionally expressed as Qn tetrahedral sites (n = 0…3), when n is the number of bridging oxygen (BO) per Q unit to neighbor phosphate tetrahedral [2, 23, 28]. Q0 represents orthophosphates (PO43−), Q3 is pure P2O5 and Q2 (metaphosphates) and Q1 (pyrophosphates) are intermediate structures [11, 13, 16, 19, 20]. Figure 1a shows the nomenclature of phosphate groups as Qn tetrahedral sites also with the variation of an O/P ratio .
Glasses results from many possible combinations of network-forming oxides together with one or several modifier or intermediate oxides which lead to a special physical properties .
Introducing alkali metal oxide or divalent metal oxide to the glass network induces the fundamental optical absorption edge falls in the UV region bellow 400 nm which meets with the requirement for desirable applications in optical systems . These additions not only enhance the chemical durability of the phosphate glasses but also can impart special functions to the glasses and expand the glass application fields.
Furthermore, alkali phosphate glasses have attracted more attention due to their mixed electronic ionic conductivity, low melting point and strong glass-forming character . Among the phosphate-based glasses those containing calcium, magnesium, sodium and zinc have received great attention due to their excellent optical properties, high refractive index, low dispersion and good transparency in the UV and IR region . With the decrease of P2O5 content, the glass become more resistant to moisture attack but restricts the glass formation areas. Thus, MgO oxide was incorporated in order to overcome these problems .
Nevertheless, phosphate-based glasses containing transition metal ions are scientifically interesting materials due to their attractive properties which can be used in many technological applications including electronic and electro-optical devices .
For glasses doped with manganese ions. These latter are presented in the +2 or +3 oxidation states. The content of Mn3+ ions in the glass leads to the staining glass in the color range from light to dark purple depending on the concentration . This characteristic coloration could be explained by the d-d electronic transitions. This color can be associated with the broad absorption band in the visible region at 520 nm, which pertains to the Mn3+ ions [25, 30]. This behavior allows obtaining additional luminescence bands in the red spectral region that shift LED emission from cool white to warm light .
Contrary to Zn2+ and Mg2+ ions presented in one oxidation state, spectral-luminescent properties of manganese ions in phosphate glasses allow them to be good candidates for interesting optical applications [21, 25, 30].
In borate glasses, manganese exists mainly as Mn3+ ions with octahedral coordination in glass networks whereas in silicate and germinate glasses, it identified as Mn2+ ions with both tetrahedral and octahedral coordination .
Referring to literature, Montagne et al. have been studied the zinc phosphate glasses with a general formula (100-x)NaPO3-xZnO with 0 < x < 33.3 mol% using 31P MAS-NMR, 31P NMR of liquid sample, visible spectroscopy, refractive index measurements, density evolutions, Tg variations, activation energy, chemical durability and chemical analysis [1, 2, 46, 47].
Moreover, Zotov et al. have been studied the manganese phosphate glasses with a general formula (MnO)x(NaPO3)1-x when x = 0.0, 0.024, 0.048 and 0.167 mol .
These investigations have been performed using X ray diffraction, EXAFS and Raman spectroscopy. The increase of MnO content causes the depolymerization of metaphosphate chains leading to the decrease of the average chain length .
Aguiar et al. have been studied the Na2O-MgO-CaO-P2O5-SiO2 bioactive glasses using Raman, 31P MAS-NMR and 29Si MAS-NMR spectroscopies. The glass compositions were prepared with varying SiO2 content from 25 to 54 mol% and the P2O5 proportion from 2 to 11 mol% [2, 20, 24].
Furthermore, Szumera et al. have detailed the effect of MoO3 addition on silicate phosphate glasses using spectroscopic analysis such as FTIR, Raman and 31P MAS-NMR. The molar content of SiO2 decreases from 41.6 to 39.6 mol% and the P2O5 proportion increases from 5.7 to 7.8 mol% . The obtained results revealed the cleavage of oxygen bridges which suggests that acts as a network modifier .
In our knowledge, the thermochemical data of zinc-, magnesium-, and manganese-based phosphate and phosphate-silicate glasses are rare in literature. For this purpose, the aims of this research were to study the correlations between structural changes, thermal investigations, optical properties and thermochemical behaviors of these glassy compounds with the incorporation of zinc, magnesium and manganese oxides.
However, it is well known that phosphate glasses have a poor chemical durability, volatile nature and hygroscopic character. These disadvantages decrease their stability which limits their use in technological applications .
The addition of alkali and alkaline earth cations with the decease of phosphorus content can depolymerize the glass network which suggests the cleavage of P▬O▬P bridges .
The incorporation of certain network modifier cations (Na+, K+, Mg+, Ca2+…) disrupts the glassy network, leading to the structure depolymerization and the formation of non-bridging oxygen atoms (NBO), also named terminal oxygen (OT) [2, 4].
The addition of transition metal oxides (CuO, MgO, ZnO, MnO, CaO…) into the vitreous network (TMO) disrupted the P▬O▬P bridges leading to the structure depolymerization and the formation of non-bridging oxygen atoms (NBO) [2, 5, 6, 8, 9, 13, 21, 25, 32, 35]. Which induces the formation of P▬O▬M bonds replacing the easily hydrosoluble P▬O▬P bridge that improve the chemical durability of the phosphate network .
Among several oxides mentioned above, zinc oxide gained considerable attention because Zinc doped glasses find numerous applications in optic field can be used as LED light sources and substrates for optical waveguides. It can also play an important role in bone formation and mineralization .
Zinc phosphate compositions are chemically durable, have processing temperatures under 400°C and can be co-formed with high temperature under 400°C polymers to produce unusual organic/inorganic composites .
Among the wide class of phosphate glasses, ZnO-based glasses have low glass transition temperature in the region of 280–380°C and significantly high chemical durability .
Furthermore, the addition of ZnO to the glass network is expected to improve the chemical stability of the structure. It can also ameliorate the electrical, optical and magnetic properties of glasses due to the appearance of P▬O▬Zn ionic bond which induces the increase in the compactness and the rigidity of the glass network [5, 13, 32, 35].
In fact, in crystalline solid compound, the structure was described by a repetitive arrangement of a large scale patterns contrary to amorphous structure which exhibits a short range order.
Additionally, ZnO is an intermediate oxide. It can act as former or modifier network depending on his content in phosphate network. When it occupies the tetrahedral sites by forming ZnO4 structural units, ZnO oxide plays the role of glass former. But, when it occupies the octahedral sites coordinated, ZnO oxide acts as glass modifier [7, 25].
The literature concerning zinc in various mixed oxide compounds revealed that with the exception of few structures, zinc has tetrahedral oxygen ligancy and the zinc-oxygen distance varies only slightly [25, 34]. It was concluded that zinc had a coordination number of six in borate and silicate glasses .
Interestingly, the heat treatment of glasses at temperature higher than their glass transition (Tg) or crystallization temperature (Tc) improves the electrical conductivity of the glassy compound due to the “structural relaxation” of the glass network .
ZnO is widely used in glass production because it improves the glass quality by enhancing mechanical properties and chemical durability and by reducing the thermal expansion . Zinc is a microelement that plays an important role in the bone formation and mineralization. Zinc containing glasses and glass ceramics has been developed for bone engineering applications . The small size of Zn ion (0.74 Å) helps it to locate itself into smaller cavities of the network .
Moreover, MgO oxide is of interest from a biological viewpoint because Mg2+ is known to play a physiological role in positively influencing bone strength which can be substituted into apatites [13, 18].
The bioactive behavior of magnesium rich glasses is identified as their ability to react chemically with living tissues, forming with them mechanically strong and lasting bonds. These bone bondings are attributed to the formation of an apatite-like layer on the glass surface, with composition and structure equivalent to the mineral phase of bone.
In fact, bioactive glasses have received special attention due to their better bone bonding ability in vivo. Due to their good bioactive and tailorable degradation properties, these glasses can be used for various biomedical applications such as bone graft, filler, dental, implant coating.
Furthermore, by increasing the concentration of modifier oxides, electrical conductivity of the glass increases. This property was probably influenced by the structural changes resulting from the disruption of the glass network which affected the mobility of the cations and anions when the modifying oxide was progressively introduced .
Glasses containing transition metal oxides possess interesting electronic, optic and magnetic properties due to the ability to exist in more than one valence state. However, the electronic conduction of these glassy compounds is resulting from the electronic transfer of cation that exists in different valence sates [4, 38].
Compared with phosphate glasses, silicate glasses exhibit superior chemical resistance which makes them compatible with the fabrication process in the development of optical devices .
Silicate glasses are an attractive host matrix for transition metal ions due to their excellent optical and mechanical properties, good chemical durability, good chemical stability and low thermal expansion coefficient leading to strong thermal resistance . Silicate glasses have many advantages rather than phosphate glasses. Silicate-based glasses are chemically durable, thermally stable and optically transparent at excitation and lasing wavelength. However, the higher viscosity of these glasses allows the glass to be formed without crystallization process. In addition, these amorphous materials are useful in optics as lenses or beam splitters in optical telecommunications, micro- and optoelectronics and in near IR-windows [6, 39, 40].
2. Experimental procedures
2.1 Glass preparation
Glasses of the (50-x/2)Na2O-xMO-(50-x/2)P2O5 (M = Zn, Mn, Mg) (0 ≤ x ≤ 33 mol%), (50-x)Na2O-xMO-50P2O5 (M = Zn, Mn) (0 ≤ x ≤ 33 mol%), and (0.9-x)NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol) compositions have been prepared using a melt quenching technique.
A series of glasses were prepared by varying the MO (M = Zn, Mn, Mg) content from 0 to 33 mol% using reagent grade compounds, NaH2PO4, NH4H2PO4, MgO, ZnO, MnCO3 with a high purity (99% purity), in the suitable proportions.
The mixture corresponding to the desired compositions was heated in platinum crucible at 400°C in order to evaporate water and start the condensation of phosphate groups. The temperature was then progressively increased to 750–900°C, depending on glass composition, and held constant for 30 min. The batch was finally quenched to room temperature under air atmosphere in order to produce vitreous compounds.
Using the same technique, phosphate-based silicate glasses with a general formula (0.9-x)NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol) have been synthesized using reagent grade compounds, NaH2PO4.H2O ZnO and SiO2 with a high purity (99% purity) with the desired compositions.
The mixture was then putted in platinum crucible at 400°C for 1 hour in order to eliminate residual water. The temperature was raised progressively to 1200°C for 30 min in order to homogenize the melting mixture. Finally, the batch was quenched to room temperature under air atmosphere in order to obtain glasses.
The amorphous state was confirmed by X-ray diffraction. All the products were annealed at about 20°C below their glass transition temperature for 2 hours in order to eliminate internal tensions and get a more homogenized sample.
2.2 ICP analysis
Phosphorus, sodium, magnesium, zinc, manganese and silica were analyzed by inductively coupled plasma atomic emission spectroscopy (Jobin Yvon Ultra C).
2.3 Physical properties
2.3.1 Density and molar volume
Density of glass is a strong function of its composition and its intrinsic property which shed light on the short range structure of the glassy material [4, 37]. This work presents a series of glasses with various amounts of modifier oxides. These modifies, depending on their polarity and size, tend to occupy the interstices within the network and form new bonds resulting in a change in the structure and properties of the glass [4, 37].
Glass density measurements have been determined using the standard Archimedes method using diethyl orthophthalate as immersion fluid. The relative error of these measurements is ±3%.
The molar volume of glasses has been calculated from the density (Vm = M/ρ) and the molar weight.
For (50-x/2)Na2O-xMO-(50-x/2)P2O5 (M = Zn, Mn, Mg) where 3 ≤ O/P ≤ 3.49 and (50-x)Na2O-xMO-50P2O5 (M = Zn, Mn) with O/P = 3 (0 ≤ x ≤ 33 mol%) series glasses, the density increases gradually with the incorporation of MO oxide. The increase in density indicates that the MO oxide reticulate the vitreous network because P▬O▬M bond are more ionic than P▬O▬P [11, 12, 13, 15, 29, 32, 33, 42].
Table 2 shows that the molar volume deceases monotonically with the increase of ZnO content for phosphate glasses.
|Glass composition||X||Density (g cm−3)||Vm (cm3 mol−1)||Tg (°C)||Tc (°C)||ΔT (°C)|
|2.43 ± 0.07|
2.47 ± 0.07
2.62 ± 0.08
2.70 ± 0.08
2.75 ± 0.08
2.85 ± 0.09
2.93 ± 0.09
2.98 ± 0.09
|42.00 ± 1.30|
41.00 ± 1.23
38.15 ± 1.14
36.63 ± 1.10
35.60 ± 1.10
34.00 ± 1.02
32.70 ± 1.00
32.00 ± 1.00
|280 ± 5|
285 ± 5
287 ± 5
294 ± 5
306 ± 5
314 ± 5
|290 ± 5|
371 ± 5
368 ± 5
439 ± 5
456 ± 5
446 ± 5
The decrease in the molar volume for (50-x/2)Na2O-xMO-(50-x/2)P2O5 (M = Zn, Mn, Mg) where 3 ≤ O/P ≤ 3.49 and (50-x)Na2O-xMO-50P2O5 (M = Zn, Mn) with O/P = 3 (0 ≤ x ≤ 33 mol%) series glasses could be explained by the higher field ΔF (ΔF = Z/r2; with z is the valence cation and r is the ionic radius) of M2+ compared to that of Na+ [11, 12, 13, 15, 29, 32, 33, 42].
The decrease in the molar volume is extensively related to structural changes due to the incorporation of MO oxide that disrupted the average chain length of metaphosphate resulting from the following reaction:
The variation of these properties is closely related to the structural modification when M2+ ion is progressively introduced.
The effect of composition on the density and molar volume for zinc phosphate-silicate glass, having a general formula: (0.9-x)NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol), shows that the replacement of NaPO3 by SiO2 oxide induces a decrease of density as mentioned Table 3. This is due to the lower molecular weight of SiO2 than that of NaPO3 (, ) [11, 12, 13, 15, 29, 32, 33, 42].
|Glass composition||x||Density (gcm−3)||Vm (cm3 mol−1)||n||Tg (°C)||Tc (°C)||ΔT (°C)|
|2.60 ± 0.10|
2.58 ± 0.10
2.57 ± 0.10
2.55 ± 0.10
2.55 ± 0.10
2.53 ± 0.10
|38.50 ± 1.20|
38.35 ± 1.20
38.24 ± 1.20
38.13 ± 1.10
38.00 ± 1.10
37.80 ± 1.10
|1.44 ± 0.05|
1.45 ± 0.05
1.46 ± 0.05
1.47 ± 0.05
1.48 ± 0.05
1.49 ± 0.05
|280 ± 5|
287 ± 5
289 ± 5
293 ± 5
294 ± 5
296 ± 5
|371 ± 5|
400 ± 5
427 ± 5
439 ± 5
475 ± 5
466 ± 5
As the same for the molar volume, this quantity decreases monotonically with the incorporation of SiO2 oxide (Table 3). This variation indicates that SiO2 oxide reticulates the vitreous network suggesting the increase in the rigidity of the structure.
Furthermore, the regular decrease in the molar volume is closely related to the nature of bending in the glass structure, because P▬O▬Si are more ionic than P▬O▬P bridges, suggesting the compactness of the vitreous network [11, 12, 13, 15, 29, 32, 33, 42].
2.3.2 DSC investigations
Generally, the glass transition phenomenon occurs due to the increasing viscosity of the overcooled liquids so Tg strongly depends on the polymerization ratio of the network .
The glass transition temperatures were determined on 40–50 mg of samples using DSC-ATD Netzsch 404 PC with a 10°C/min heating rate (accuracy ±5°C).
With increasing MO content, glass transition temperature, Tg, increases linearly for all glass compositions as mentioned Table 2.
This behavior is undoubtedly corresponding to some changes in the nature of bonding in the structural network. This parameters is strictly related to the bond strength of the glass network which can be explained in terms of bond length (which is the charge divided by the square of the cation-oxygen distance) affected by the cation field strength resulting in a higher of Tg values [11, 12, 13, 15, 29, 32, 33, 42].
These variations indicate the progressive increase of the reticulation and the rigidity of the glass network by gathering the non-bridging oxygen atoms (NBO) with the increase of MO proportion. As a result the formation of P▬O▬M bonds suggesting the increase in the rigidity and the compactness of the structure that ameliorate the chemical durability of glasses.
According to Dietezel, the thermal stability of glasses (ΔT) can be expressed by the temperature difference between Tg and Tc, ΔT = Tc–Tg, in which Tg and Tc are the glass transition and crystallization temperature. Increasing ΔT delays the nucleation process, indicating a better stability of the glass .
∆T increases when SiO2 oxide is progressively added, indicating a better stability of the glass. The larger value of ∆T, the stronger is the inhibition to nucleation and crystallization process as mentioned Table 3 [12, 13, 15, 29, 32, 33].
2.3.3 Refractive index measurements
The ability to control the physical properties of glasses, e.g., the refractive index, by variation in glass composition suggests the feasibility of chemically controlling the materials according to the needs of a given application .
For glassy compounds, refractive index is a fundamental parameter that strongly relevant to optical devices performance and reliability in the basic elements in all optical instruments. Hence, a large number of researchers have carried out investigations to ascertain the relation between refractive index and glass composition .
The carat eristic feature of phosphate glasses is the low value of the refractive index that is in the order of 1.49. The variation of this quantity for zinc phosphate-based silicate glasses is presented in Table 4. Inspecting these data, one can note that n increases from 1.44 to 1.49 when x rises from 0 to 10 mol% of SiO2 oxide which suggests that the refractive index of glassy compounds depends essentially on the density of glass network [3, 10, 11].
|Glass composition||n||αm (Å3)||Rm (cm3 mol−1)||Eopt (ev)||(αm/Vm) × 10−25|
In addition to density, many parameters can prevails the refractive index such as density, polarizability of the first neighbor ions coordinated with it (anion), coordination number of ion, electronic polarizability of the oxide ion and optical basicity [3, 10, 11]. The molar refractivity (Rm) was estimated from the refractive index and the molar volume (Vm) using the Lorenz-Lorenz Equation [3, 10, 11]:
where the value of ∏N is known as the Lorentz function and N is the Avogadro number. Table 4 reports the values of Rm and αm. These parameters increase gradually with the incorporation of SiO2 oxide.
Table 4 shows that Rm increases from 10.23 to 10.60 m3 mol−1 and αm are between 4.06 and 4.20 Å. These variations indicate that the refractive index as a function of both density and molar electric polarizability of glassy compounds [3, 10, 11].
In the present work, we found that the refractive index (n) depends on the ratio (). This quantity shows that the refractive index (n) of the studied glasses increases linearly versus () ratio. This variation can be probably due to the electronic polarizability of oxide ions.
Duffy et al. suggested that increasing the optical basicity () indicates an increase in the effective electronic density of the oxide ions and accordingly, increasing covalency in the oxygen-cation bonding [3, 10, 11].
The decrease in the molar volume for zinc-based phosphate-silicate glasses induces an increase in the rigidity and the compactness of the vitreous network, when SiO2 oxide is progressively introduced, because Si▬O▬P bonds are more ionic that P▬O▬P.
2.4 Spectroscopic analysis
2.4.1 FTIR spectroscopy
Infrared spectra of the glass series have been recorded by Perkin-Elmer (FTIR 2000) spectrometer using KBr pellets in the frequency range 400–4000 cm−1 at room temperature. The samples were prepared by grinding about 9 mg of glass powder with 300 mg of spectroscopic grade dried KBr.
For undoped zinc phosphate glasses, NaPO3, FTIR spectrum revealed an asymmetric and symmetric stretching vibration band of PO2 groups in metaphosphate chains situated respectively at 1280 and 1150 cm−1. The asymmetric and symmetric stretching vibration bands of PO3 chain end groups situated respectively at 1100 and 1000 cm−1 [12, 13, 15, 29, 32, 33].
Furthermore, the asymmetric and symmetric stretching vibrations of P▬O▬P bands are around 880, 780 and 720 cm−1. The deformation mode of P▬O▬(PO43−) groups at 535 and 480 cm−1 [12, 13, 15, 29, 32, 33].
As MO oxide is introduced, the asymmetric band of PO2 shifts from 1280 cm−1 shift to lower frequency as showed Figures 1a and b indicating the depolymerization of phosphate chains when x increases [12, 13, 15, 29, 32, 33].
For higher ZnO content, FTIR spectra revealed the displacement of the asymmetric stretching mode vibration of the P▬O▬P band from 880 to 920 cm−1 when x rises from 0 to 33 mol%. This result can be correlated to the increase in the covalence character of P▬O▬P bridges when monovalent cation Na+ was replaced by divalent cation (such as Zn2+) [12, 13, 15, 29, 32, 33].
It may be also attributed to the shortening of phosphate chain length due to the higher field strength and the size of the metallic cation, when the ratio O/P increases for (50-x/2)Na2O-xZnO-(50-x/2)P2O5 [12, 13, 15, 29, 32, 33].
The FTIR spectra of NaPO3 glasses revealed also two bands in the frequency range 780–720 cm−1 which are attributed to the presence of two P▬O▬P bridges in metaphosphate chains based on (P2O6)2− groups (Figure 1a and b) [12, 13, 15, 29, 32, 33]. However, it is interesting to note that for the series glasses containing 30 and 33 mol% ZnO FTIR spectra exhibit only a single band at 740 cm−1 assigned to the P▬O▬P linkage in pyrophosphate group (P2O7)4− (Figure 1a) [12, 13, 15, 29, 32, 33]. These spectral changes depend essentially on the glass composition.
On the other hand, this result could be explained by disruption of the infinite metaphosphate chains when MO oxide is gradually incorporated suggesting the depolymerization of the skeleton of (P2O62−)∞ into short phosphate groups such as: P2O74− and PO43− [12, 13, 15, 29, 32, 33].
Similar FTIR spectra have been recorded for zinc phosphate-based silicate glasses, with a general formula: (0.9-x)NaPO3-xSiO2-0.1ZnO, (0 ≤ x ≤ 0.1 mol) as mentioned Figure 1b.
The FTIR spectra of zinc phosphate-based silicate glasses revealed the appearance of some bands assigned to phosphate-silicate glasses in the range 1000–1300 cm−1 as shown Figure 1b. The asymmetric stretching vibration bands of silicate and phosphate tetrahedron is located at 1100 cm−1. It seems that a smaller band at 840 cm−1 is attributed to the symmetric stretching vibration of O▬Si▬O in metasilicate (Q2) when SiO4 tetrahedron shared two oxygen with their neighbor (Si▬O▬2NBO). The symmetric stretching vibration band Si▬O▬Si is about 1080 cm−1. In addition, the bending vibration of Si▬O▬Si and O▬Si▬O bonds is around 460 cm−1 [12, 13, 15, 29, 32, 33].
When SiO2 is incorporated, FTIR spectra revealed the displacement of the asymmetric stretching mode vibration of PO2 band from 1280 to 1250 cm−1 when x increases from 0 to 10 mol%. This result can be probably due to the depolymerization of the infinite metaphosphate chains with the addition of SiO2 oxide.
Furthermore, for 0.8 NaPO3-0.1 SiO2-0.1 ZnO glass composition, FTIR spectrum revealed the appearance of a only a single band at 760 cm−1 assigned to P▬O▬P bands in phosphate dimers (P2O74−) as mentioned Figure 1b. These spectral changes have been observed for magnesium and manganese phosphate glasses that could be attributed to the reduction of infinite phosphate groups (P2O62−) into shorter phosphate groups such as: P2O74− and PO43− [12, 13, 15, 29, 32, 33].
2.4.2 Raman spectroscopy
Raman spectroscopy is an adequate technique for the analysis of glass matrix structure. Raman bands are generally characteristics of structures involving chains of linked tetrahedral that may be found in crystalline, glassy phosphates and silicate because it can detect the local changes in the environment of Si▬O▬Si and P▬O▬P bonds [1, 2].
The Raman spectra were recorded on powder of glasses using a Labram HR800 micro Raman model operating in the 50–4000 cm−1 range at room temperature equipped with an internal He-Ne laser source (λ = 488 nm).
Figure 2a reported the Raman spectra of zinc phosphate glasses having a general formula (50-x/2)Na2O-xZnO-(50-x/2)P2O5 (0 ≤ x ≤ 33 mol%) with an O/P ratio varies from 3 to 3.49.
For undoped zinc phosphate glasses, Raman spectrum revealed a large band around 1274 cm−1 and three weaker peaks at 1164, 685, and 380 respectively as shown in Figure 2a.
The bands located at 1274 and 1164 cm−1 are assigned to the asymmetric and symmetric vibrations of PO2 groups in metaphosphate chains (Q2) [12, 13, 15, 29, 32, 33]. The large band at about 685 cm−1 is attributed to the symmetric vibration of the bridging oxygen linking two PO4 tetrahedrons (P▬O▬P) in metaphosphate chains [12, 13, 15, 29, 32, 33]. The low frequency attributed to the faint band at 380 cm−1 is related to the bending motion of phosphate polyhedral [12, 13, 15, 29, 32, 33].
With increasing MO content, we observe some decrease of the overall background located at 600–800 cm−1 and 1100–1300 cm−1. These spectral changes can be correlated to the distortion of P▬O▬P band which induces the shortening of the infinite metaphosphate chains suggesting the formation of pyrophosphate groups (Q1) with the increase of the O/P ratio [12, 13, 15, 29, 32, 33].
From Figure 2a, it seems that the intensity of bands located at 1164 and 685 cm−1 decrease when MO oxide is progressively introduced. However, the Raman spectra revealed the displacement of these bands to higher frequencies to 1180 (d, e) and 780 cm−1 (d, e, f) with 30 and 33 mol% of MO level. This result can be probably due to the higher π character of P▬NBO bands that induces the depolymerization of infinite metaphosphate chains when MO oxide is progressively added.
Similar Raman spectroscopic analysis have been recorded for (0.9-x) NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol) glass compositions as shown in Figure 2b.
The incorporation of SiO2 oxide to the phosphate network generates the appearance of the asymmetric band around 850 cm−1 attributed to Si▬O▬Si bending modes. The band located at 560 cm−1 is attributed to Si▬O▬Si intertetrahedral linkages obtained in calcium and magnesium rich silicate glasses in order to link the distorted metaphosphate groups when SiO2 oxide is added [12, 13, 15, 29, 32, 33].
2.4.3 31P MAS-NMR spectroscopy
The 31P MAS-NMR spectra of (50-x/2)Na2O-xZnO-(50-x/2)P2O5 glasses are shown in Figure 3.
The characteristic features of undoped zinc phosphate glasses are isotopic peaks at −21 and −6.88 ppm. The first one is attributed to the Q2 tetrahedral sites in metaphosphate groups and the second is assigned to the Q1 groups at the end of chain [12, 13, 15, 29, 32, 33].
Based on literature, the chemical shift at +1.4 ppm is attributed to NaPO3 chain end groups. From Figure 3, one can note the appearance of two isotopic peaks around 21–−18.80 ppm and −6.88–−3.90 ppm for the glass series.
When the MO oxide is introduced to the vitreous network, the intensity peak attributed to Q1 tetrahedral sites increases and becomes the major spectral feature [12, 13, 15, 29, 32, 33]. These results are in good agreement for zinc phosphate glasses with the structural study of (100-x)NaPO3-xZnO glasses (0 ≤ x ≤ 33.3 mol%) performed by Montagne et al. [12, 13, 15, 29, 32, 33].
From Figure 3, it seem that 31P MAS-NMR spectra exhibit only single peak assigned to Q1 tetrahedral sites attributed to pyrophosphate groups resulted from the distortion of metaphosphate chains when MO oxide is progressively introduced.
Furthermore, the phosphorus chemical shift depends essentially on the phosphorus-ligand bond (P-O) for phosphate compounds and the electronic density of the non-bridging oxygen (NBO). Figure 3 mentioned that the Q2 chemical shift becomes less shielded when MO is added. This decrease is probably due to the higher electronegativity of M2+ compared to Na+ also the increase of π fraction of P-NBO resulting from the decondensation of phosphate chains when ZnO is incorporated. This suggests that Zn2+ ions are only bonded to pyrophosphate groups described by Q1 tetrahedral sites. As a result the increase of shielding Q2 sites from −21 ppm in NaPO3 glass to −18.80 ppm in 33.5 Na2O-33 ZnO-33.5 P2O5 glass composition [12, 13, 15, 29, 32, 33].
2.4.4 UV-VIS spectroscopy
UV-VIS-NIR absorption spectra of the glassy compounds were carried out by means of Perkin-Elmer Lambda 950 spectrometer at room temperature under air. Optical measurements were recorded in the range of 200 and 1800 nm.
Optical absorption, particularly the absorption edge, is useful for the investigation of optically-induced transitions and for getting information about the band gap energy [4, 10, 11, 14, 16, 37, 41]. This parameter is very interesting for the applications of the materials to be studied. It is known that the optical transition occurs through the region between conduction and valence bands (optical band gap) directly or indirectly.
where d represents the thickness of the glass composition and ln is the absorbance.
According to Davis and Mott, the expression of the absorption coefficient α (ν) as a function of photon energy (hν) for direct and indirect optical absorption, was given by the relation as follows:
A: an energy-independent constant
Eopt: the optical band gap energy
Figure 4 represents the variation (αhν)2 versus photon energy (hν) for (0.9-x)NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol) series glasses.
The values of indirect optical band gap energy (Eopt) were determined by the extrapolation of the linear region of (αhν)2 against photon energy (hν) plots at (αhν)2 = 0. This latter shows that the Eopt increases with the incorporation SiO2 from 1.5 to 2.35 eV. This quantity is not only influenced by the chemical composition also by the structural rearrangement in the glass matrix [4, 10, 11, 14, 16, 37, 41]. Figure 5 shows clearly that the Eopt values dependent strongly on the composition of the glass also on the oxygen bonding in the vitreous network [4, 10, 11, 14, 16, 37, 41]. Any changes of oxygen bonding suggesting the formation of non-bridging oxygen (NBOs) causes a change of the absorption characteristics of the glass [4, 10, 11, 14, 16, 37, 41].
When x increases from 0 to 10 mol% of SiO2, the optical band gap energy rises from 1.5 to 2.35 eV. This variation can be explained by the structural modifications which suggest the distortion of metaphosphate chains inducing the increase in the number of non-bridging oxygen (NBOs).
Because the NBOs bonds are predominantly ionic character and consequently have lower bond energies . The higher value of the band gap energy revealed the increase of the cross-linking network due the introduction of SiO2 [4, 10, 11, 14, 16, 37, 41].
From Figure 5, it seems that the Eopt is in the order of 2.35 eV for 0.82 NaPO3-0.08 SiO2-0.1 ZnO and 0.8 NaPO3-0.1 SiO2-0.1 ZnO glass compositions. This result can be correlated to the structural changes due to the formation of P-O-Si ionic bands .
3. Thermochemical study of phosphate glasses
3.1 Calorimetric dissolution of zinc, manganese and magnesium phosphate glasses
Phosphate glasses are soluble in mineral acids [11, 12, 13, 15, 29, 32, 33, 42]. Furthermore, the dissolution process has been carried out in order to find the suitable solvent which dissolves entirely the glassy compounds and should not give rise to any secondary phenomena.
For this purpose, our investigations were covered all the usual acids, bases and their mixtures such as: HNO3, HCl, NaOH, KOH, CH3COOH.
The calorimetric profile shows that the 4.5% weight of phosphoric acid solution is the best solvent for the thermochemical requirements of phosphate glasses.
The dissolution of phosphate glasses were recorded by means the C80 (SETARAM) at 25°C. This equipment possesses two identical cells: the reference and the measuring cell. The reference cell should contain only the solvent but the measuring cell was provided with the solid to be dissolved or the liquid to be mixture. The superior compartment contains the attack solution (solvent) which is tightly separated from the lower one by a movable cover.
The reference and the measuring cell are surrounded by thermoelectric piles with high performance. These latters permit to detect the heat flow resulted from the dissolution, mixing or dilution process. The integration of the raw signal determined the heat dissolution of the studied compound.
Experiments were carried out by dissolving the same mass of solids (25 mg) in 4.5 ml of solvent.
The plots of heat dissolution of glasses (ΔsolH (kJ mol−1)) are shown in Figure 6.
For (50-x/2)Na2O-xZnO-50-x/2)P2O5 glass composition, it seems that the dissolution phenomenon is endothermic for lower ZnO content and becomes exothermic when ZnO oxide is progressively incorporated in the vitreous network.
Furthermore, the change in thermal signs is probably correlated to structural modifications of metaphosphate groups (Q2) suggesting the formation of pyrophosphate units (Q1) when ZnO oxide is introduced.
These results were correlated to spectroscopic investigations which revealed the formation of pyrophosphate groups for zinc, manganese and magnesium phosphate glasses, resulting from the cleavage of the P-O-P bridges when the amount of MO oxide is progressively increases [11, 12, 13, 15, 29, 32, 33, 42].
3.2 Thermochemical study of zinc phosphate glasses
Calorimetric study of glasses has been carried out for several decades. However, the thermochemical investigations of glassy compounds have been considered using a thermodynamic approach based on the Miedema’s model in order to evaluate the formation enthalpy of binary alloys .
In the case of glassy compounds, the knowledge of the formation enthalpy is an important chemical data which can be used to determine the Gibbs free energy of formation of the selected compounds and to have an idea about their stability.
The determination of the formation enthalpy of (100-x)NaPO3-xZnO glass series involves the formation enthalpy of sodium trimetaphosphate, (NaPO3)3, crystal). Because of the very old value reported in literature , this quantity has been determined again by the same technique.
3.2.1 Synthesis and characterization of samples
Sodium trimetaphosphate (NaPO3)3, was synthesized by thermal decomposition of sodium dihydrogen phosphate (NaH2PO4). This later was obtained by thermal dehydration of its commercial monohydrate from NaH2PO4.H2O (Fluka of purity higher than 99%) at 150°C during 24 hours.
NaH2PO4 was placed in the furnace, then the temperature increases from 200 to 300°C during 24 hours in order to eliminate residual water and volatile gases. After any heat treatment, the powder was crushed.
Then, the temperature increases and maintains 500°C for one night. The final product was tested using an X-ray diffraction equipped by SEIFERT-XRD 3000 TT diffractometer which confirms that the final product is the sodium trimetaphosphate.
3.3 Cycle for sodium trimetaphosphate ((NaPO3)3, crystal)
Generally, the direct determination of the formation enthalpy of any compounds is impossible. For this reason, our investigation is based on considering a particular reaction which involves the studied compounds with other reactants and products.
The knowledge of the enthalpy of the hypothetical reaction and the formation enthalpy of the reactants and products allow determining the formation enthalpy of the compound to be studied.
For the sodium trimetaphosphate ((NaPO3)3, crystal); the following thermochemical cycle has been studied . This later put into consideration the chemical reaction which involves dissolution, dilution and mixing processes.
The designed states from E1 to E4 are the solutions obtained from different chemical operations :
E1 state presents the phenomena of dissolution for NaH2PO4 in Slv2 (4.45%) (ΔsolH1).
E2 state designed the dissolution process of (NaPO3)3 in Slv1 (4.5%) (ΔsolH2).
E3 state designed the dilution process of 3H2O(liq) (ΔdiH1).
E4 state designed the mixing process of E2 + E3 states (ΔmixH1).
ΔrH1 can be expressed as ΔrH1 = 3 ΔsolH1 + ΔmixH2 − ΔmixH1 − ΔsolH2− ΔdilH1 in which ΔsolH are molar quantities.
So the whole results allow to derive the enthalpy of reaction (R1) at 298.15 K. Taking into account the enthalpies of formation of NaH2PO4 (s) and H2O (liq) , we can derive that for sodium trimetaphosphate ((NaPO3)3, (crystal)) at 298.15 K.
3.4 Cycle for Na2O-ZnO-P2O5 series glass
For zinc-based phosphate glasses, the formation enthalpy of the glass series can be determined by considering a hypothetical reaction based on ((NaPO3)3(crystal)) and ZnO (sd). Their formation enthalpies can be derived by considering the following cycle which involves dissolution and mixing processes. The designed states from E5 to E8 are the solutions resulted from the different chemical operations :
E5 state presents the phenomena of dissolution for (NaPO3)3 in Slv1 (4.5%) (ΔsolH2).
E6 state designed the dissolution process of ZnO in Slv1 (4.5%) (ΔsolH3).
E7 state designed the mixing process of E5 + E6 states (ΔmixH3).
E8 state designed the dissolution process of glasses in Slv1 (4.5%) (ΔsolH4).
According to this cycle ΔrH2 can be expressed as: ΔrH2 = (100-x) ΔsolH2 + 3x ΔsolH3 + ΔmixH3 + ΔmixH4 − 3ΔsolH4 when E7 and E8 states are identical (ΔmixH4 ≈ 0) . This quantity also equals:
So, the standard enthalpy of formation of the glass can be derived as:
3.4.1 Dissolution processes
|NaH2PO4 (sd) in Slv2 (ΔsolH1)|
|n (mmol)||Qr (J)||uQr (J)|
|(NaPO3)3(cr) in Slv1 (ΔsolH2)|
|n (mmol)||Qr (J)||uQr (J)|
|ZnO (sd) in Slv1 (ΔsolH3)|
|n (mmol)||Qr (J)||u(Qr) (J)|
Table 5 presents the dissolution process of NaH2PO4 with the variation of the quantity (n (mmol)) to be dissolved in 4.5 ml of phosphoric acid solution (4.45% (w/w) H3PO4) (Slv2).
Table 6 presents the dissolution process of (NaPO3)3 with the variation of the quantity (n (mmol)) to be dissolved in 4.5 ml of phosphoric acid solution (4.5% (w/w) H3PO4) (Slv1).
Table 7 presents the dissolution process for ZnO with the variation of the quantity (n (mmol)) to be dissolved in 4.5 ml of phosphoric acid solution (4.5% (w/w) H3PO4) (Slv1).
The plots of the variation of the measuring heats as a function of the moles number of solid leads to straight lines whose expressed as: Qr = An+b.
The slope (A) presents the molar dissolution enthalpy (ΔsolH) and b is the intercept increment.
Referring to a mathematical treatment developed in literature, the increment b is statistically not significant which leads to derive the dissolution enthalpy as :
where (wi) is the reciprocal of the variance on ΔHi (wi = 1/σ2ΔHi), and ΔHi is the energy resulting by dissolving ni (mol) of the corresponding product in the phosphoric acid solution.
Equations of the lines are as follows :
for (NaH2PO4) (sd) in 4.45% weight of H3PO4 solution.
for ((NaPO3)3, (cristal)) in 4.5% weight of H3PO4 solution.
For ZnO (sd) in 4.5% weight of H3PO4 solution.
Table 8 gathers the values of molar dissolution enthalpies with the corresponding errors.
|Compound||NaH2PO4 (sd) in Slv2||(NaPO3)3 (sd) in Slv1||ZnO (sd) in Slv1|
|ΔsolH (kJ/mol)||ΔsolH1 = 4.01 ± 0.47||ΔsolH2 = 4.66 ± 0.44||ΔsolH3 = −95.5 ± 2.7|
For zinc phosphate glasses, experiments were carried out by dissolving the same mass of solids (25 mg) in 4.5 ml of 4.5% weight of H3PO4 solution .
Table 9 reports the variation of the heat dissolution for the glass series published in a previous work . This evolution shows that the dissolution heat decreases linearly with the incorporation of ZnO oxide. As a result the inversion in the thermal signs for the studies glasses. This variation can be explained by the structural changes of the phosphate network suggesting the distortion of metaphosphate chains revealed by 31P MAS-NMR analysis.
|Composition||ΔsolH (kJ/mol)||u (ΔsolH) (kJ/mol)|
|95 NaPO3-5 ZnO||3.70||0.20|
|90 NaPO3-10 ZnO||2.92||0.15|
|85 NaPO3-15 ZnO||1.70||0.10|
|80 NaPO3-20 ZnO||−1.15||0.10|
|75 NaPO3-25 ZnO||−3.21||0.20|
|70 NaPO3-30 ZnO||−6.34||0.32|
|67 NaPO3-33 ZnO||−13.05||1.00|
Plotting of dissolution heat versus ZnO proportion (ΔsolH (kJ mol−1)) is reported in Figure 6. It seems that the calorimetric dissolution of the glass series is endothermic for lower ZnO proportion and becomes exothermic above 18 mol% of ZnO. This variation can be correlated to the cleavage of P▬O▬P bridges which suggests the appearance of pyrophosphate groups (Q1), revealed by 31P MAS-NMR spectroscopic analysis, when ZnO oxide is progressively incorporated in the vitreous network .
3.4.2 Mixing processes
18.104.22.168 For ((NaPO3)3, crystal) cycle
E2 was provided with various amounts of (NaPO3)3 (6–9 mg) which have been dissolved in 4.5% (w/w) H3PO4 solution but E3 is 4.4% (w/w) H3PO4 solution. Mixing the same volumes of E2 and E3 (around 2 ml) leads to a solution having the mean value of acid composition (E4 with 4.45% (w/w) H3PO4 or [H3PO4.116.90H2O]. Consequently, the concentration of Slv2 was fixed as 4.45% (w/w) H3PO4 in order to get identical E1 and E4 states. Table 10 reports E2 + E3 mixing enthalpy for different mole number (n) of (NaPO3)3 added in E2. This allowed to express ΔmixH1 as: ΔmixH1 = 0.07 n (R2 = 0.995) leading to a value of 0.07 kJ per (NaPO3)3 mole .
|n (mmol)||Qr (J)||u(Qr) (J)|
(E1 + E4) mixing process, which noted as (ΔmixH2), was considered in order to check whether or not they correspond to the same final state. This operation led to an undetectable thermal effect .
22.214.171.124 For Na2O-ZnO-P2O5 glasses cycle
Mixing the same volumes (around 2 ml) of E5 and E6 which have the same concentration of phosphoric acid (4.5% (w/w) H3PO4), led to E7 solution. Were previously added to while The E5 sate was obtained by dissolving the average mass of ((NaPO3)3, (cristal)) (27.3 mg) whereas the E6 state was considered by dissolving the various amounts of ZnO so the variation of energy (Table 11) is due to the presence of ZnO in the solution. The mixture of E7 and E8 states has no detectable thermal effect .
|Composition||ΔmixH3 (E5 + E6) (kJ/ZnO mole)||u(ΔmixH3) (kJ/mol)||ΔmixH4 (E7 + E8) (kJ/mol)|
|95 NaPO3-5 ZnO||10.15||0.10||≈0|
|90 NaPO3-10 ZnO||4.00||0.13||≈0|
|85 NaPO3-15 ZnO||5.10||0.21||≈0|
|80 NaPO3-20 ZnO||3.23||0.24||≈0|
|75 NaPO3-25 ZnO||2.74||0.25||≈0|
|70 NaPO3-30 ZnO||3.00||0.15||≈0|
|67 NaPO3-33 ZnO||2.12||0.20||≈0|
3.4.3 Dilution processes
For the cycle corresponding to the sodium trimetaphosphate, addition of water to Slv1 [H3PO4.115.54 H2O] corresponds to a dilution process. The corresponding energy was calculated by linear interpolation of literature data considering the interval to which belongs each enthalpies of solution of the initial (4.5% (w/w) H3PO4) and final states (4.4% (w/w) H3PO4) .
The formation and dilution enthalpies were calculated from Ref.  and listed below:
Calculation gives ΔdilH1 = −0.017 kJ mol−1 H3PO4.
The formation enthalpy of sodium trimetaphosphate ((NaPO3)3, crystal) has been deduced as (−3762.5 ± 175) kJ mol−1. The obtained value differs from the older by only 2.4%. It seems that the calculated value of the formation enthalpy of sodium trimetaphosphate ((NaPO3)3, crystal) is in good agreement with this determined previously in 1968. This confirms that the synthesized product is probably the sodium trimetaphosphate and not a mixture.
|95 NaPO3-5 ZnO||−1213||49|
|90 NaPO3-10 ZnO||−1174||47|
|85 NaPO3-15 ZnO||−1132||45|
|80 NaPO3-20 ZnO||−1090||44|
|75 NaPO3-25 ZnO||−1070||43|
|70 NaPO3-30 ZnO||−1003||40|
|67 NaPO3-33 ZnO||−973||39|
The influence of ZnO, MgO, MnO and SiO2 addition on the structure, physical and optical properties of phosphate glasses and phosphate-based silicate glasses having a general formula: (50-x/2)Na2O-xMO-(50-x/2)P2O5 (M = Zn, Mn, Mg) where 3 ≤ O/P ≤ 3.49; (50-x)Na2O-xMO-50P2O5 (M = Zn, Mn) with O/P = 3 (0 ≤ x ≤ 33 mol%) and (0.9-x)NaPO3-xSiO2-0.1ZnO (0 ≤ x ≤ 0.1 mol).
Amorphous state was investigated by means of FTIR, Raman, MAS-NMR and UV-visible spectroscopy in order to study the structural role of MO oxide.
Spectroscopic analysis revealed the formation of pyrophosphate groups (Q1) resulting from the depolymerization of infinite metaphosphate groups (Q2) when the modifying oxide is gradually incorporated.
Furthermore, the indirect optical band gap energy for zinc phosphate-based silicate glasses increases with the addition of SiO2 oxide. This suggests the increase in the NBOs resulting from the modification of P▬O▬P bridges which revealed the shortening of the metaphosphate chains.
On the other hand, the dissolution process is endothermic at lower MO content and become exothermic when MO oxide is progressively incorporated. The change in thermal sign could be correlated to the structural modification inducing the formation of P▬O▬M ionic bond which increases the rigidity and the compacity of the vitreous network.
Furthermore, the glass formation enthalpy of (100-x)NaPO3-xZnO (0 ≤ x ≤ 33 mol%) glass series were determine by considering a thermochemical cycle involving the formation enthalpy of sodium trimetaphosphate ((NaPO3)3, crystal). This later was checked in this work.
The glass formation enthalpy increases when ZnO oxide is progressively incorporated in the vitreous network.
When replacing of P by Zn induced a decrease in the binding energy which suggest the increase of the formation enthalpy of the glass series.
Furthermore, the variation of Tg values reflects an increase of the rigidity of the glass network due to the formation of P▬O▬Zn ionic bonds. As a result, the increase in the stability of the phosphate network which is tightly related to the Gibbs free energy of formation ΔrG°.
Because of the large disorder that exists in the vitreous structure, the entropy factor (ΔrS°) should prevail and induce the decrease in ΔrG° value when ZnO concentration increases.