# Structural Elucidation of Some Borate Glass Specimen by Employing Ultrasonic and Spectroscopic Studies

Authors: S. Thirumaran; N. Karthikeyan
Journal: Journal of Ceramics
 (2013)

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## Abstract

Quantitative analysis has been carried out in order to obtain more information about the structure of two glass systems, namely, (B2O3-MnO2-PbO) (BML glass system) and (B2O3-Na2CO3-P2O5) (BSP glass system). Their structural elucidation has been carried out by studying the ultrasonic velocities (longitudinal velocities UL and shear velocities US) and density of these glass samples. The present investigation has been interpreted by focusing more on elastic and mechanical properties of glass specimen through ultrasonic study and the elemental analysis study through spectroscopic studies. The scanning electron microscopic (SEM) study was also carried out with a view to throwing more light on their morphological aspects. The results are corroborated in the light of the role of borate (B2O3) glasses in the formation of glassy structural network.


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## Body

## 1. Introduction

The acoustical properties are particularly suitable for describing glasses as a function of composition because they give some information about both the microstructure and the dynamics of the glasses. The elastic properties are related to microscopic properties through the behavior of the network and the modifier. Attempts have been made to measure and interpret the acoustical properties of borate glasses in terms of structural changes [1–3]. Bahatti and Singh [4] discussed the composition dependence of ultrasonic velocity. The ultrasonic nondestructive testing has been found to be one of the best techniques to study the microstructure, characterization, mechanical properties, and phase changes as well as to evaluate elastic constants. One can also characterize the materials such as semiconducting glasses, superconducting glasses, glass ceramics and bioactive glasses by this nondestructive testing technique. The propagation of ultrasonic wave in solids such as glass provides valuable information regarding the solid state motion in the material. Interest in glasses has rapidly increased in recent years because of diverse applications in electronic, nuclear, solar energy and acoustooptic devices. The acoustic wave propagation in bulk glasses has been of considerable interest to understand the mechanical properties [5]. The velocity of sound is particularly suitable for characterising glasses as function of composition because it gives information about the microstructure and dynamics of glasses [6]. The study of elastic properties of the glasses has inspired many researches [7, 8] and significant information about the same has been obtained. The elastic moduli of glasses are influenced by the many physical parameters, which may in turn be studied by measuring the ultrasonic velocities. The dependence of ultrasonic velocity on the composition of glass indicates the various changes in the structural configuration between the network former and modifiers [9].Glass structure is a basic issue to understand the behavior of the material. The velocity of ultrasonic waves and hence the elastic moduli are particularly suitable for characterizing glasses as a function of composition [10]. Ultrasonic investigation of solids is gaining much importance nowadays and interest in glasses has rapidly increased because of improving information technology. Elastic properties are very informative about the structure of solids and they are directly related to interatomic potentials. In recent years, attention has been focused more on glassy materials in few of their larger optical nonlinearity and high optical quality with fast response time [11]. Ultrasonic tools are very important for characterizing materials because they have many applications in physics, chemistry, engineering, biology, food industry, medicine, oceanography, seismology, and so forth.Borate glass is one of the most characteristic glasses having unique superstructure (SS) of intermediate range order (IRO) such as boroxol ring and tetraborate. The conversion between threefold coordinated boron with the addition of modifier oxides is found in short-range order (SRO) and becomes one of the main factors bringing about the variety of SSs [12]. The ability of boron to exist in three- and four-oxygen coordinate environments and the high strength of covalent B–O bonds enable borate to form stable glasses. Coordination number and connectivity (Number of bridging bonds) usually determine the melting point and Poisson’s ratio. Glasses having higher co-ordination number tend to lower the bond strength. A detailed investigation of coordination number is therefore needed to understand the structural properties of glasses. The thermal stability and the lattice vibrations within the glass systems have been related to the measurement of softening and Debye temperature. Boron oxide is one of the best glass formers and its structure consists of a sheet-like arrangement of boron-oxygen triangles connected at all corners to form a continuous network [13]. Physical properties of borate glasses can often be altered by the addition of a network modifier to the basic constituent. The commonly used network modifiers are the alkali and alkaline earth oxides. It was observed that the properties of borate glasses were modified with alkali and alkaline earth oxides. It was observed that the properties of borate glasses modified with alkali oxides showed nonlinear behavior when the alkali oxide was gradually increased [14]. The role of alkali oxide Na2O in the B2O3 network is to modify the host structure through transformation of the structural units of the borate network from BO3 to BO4. The ability of boron atom to exist in three- and four-oxygen coordinated environments and the high strength of the (B–O) bond enable borates to form stable glasses.The present work included preparation of two glass systems, namely, (i) MnO2-B2O3-PbO (BML glasses system) and Na2CO3-B2O3-P2O5 (BSP glasses system) and its measurement of ultrasonic velocities (both longitudinal (UL) and shear (US)) and density of the series. From these sample values, the elastic constants such as longitudinal modulus (L), shear modulus (S), bulk modulus (K), Young’s modulus (E), Poisson’s ratio (α), acoustic impedance P(Z), microhardness (H), Debye temperature (θD), and thermal expansion coefficient (αP) have been calculated, which give more vital information about the rigidity and structure of glasses. To add more support of our claims over the previous glass samples, we also carried out further studies like spectroscopic XRD and scanning electron microscope (SEM) to ascertain the validity of the structural elicitation of the prepared glass samples.


## 2. Materials and Methods

### 2.1. Sample Preparation

The chemicals used in the present research work were analytical reagent (AR) and spectroscopic reagent (SR) grade with minimum assay 99% being obtained from Sd Fine Fhemicals, India, and E-Merck, Germany. The composition in mol% of (increase of B2O3 and decrease of PbO/P2O5 contents) glass specimen is listed in Table 1. The required amounts (approximately 20 g) in mol% of different chemicals in powder form were weighed using single pan digital balance (Model SHIMADZU AX 200) having an accuracy of 0.0001 g.Table 1
Composition of glasses.
S. no.
Glass specimen
Composition in mol%
System-I (B2O3-MnO2-PbO)
1
BML-1
60-10-30
2
BML-2
62-10-28
3
BML-3
64-10-26
4
BML-4
66-10-24
5
BML-5
68-10-22
6
BML-6
70-10-20
System-II (B2O3-Na2CO3-P2O5)
1
BSP-1
50-25-25
2
BSP-2
52-25-23
3
BSP-3
54-25-21
4
BSP-4
56-25-19
5
BSP-5
58-25-17
6
BSP-6
60-25-15The homogenisation of the appropriate mixture of the component of chemicals was effected by repeating grinding using a pestle and mortar. The temperature controlled muffle furnace was gradually raised to a higher temperature at the rate of 100 K per hour and a glass structure was noticed for BML glass system at 1060 K and for BSP glass system 1080 K and eventually the molten glass melt was immediately poured on a heavy copper molding block having the dimension of 12 mm diameter and 6 mm length kept at room temperature. Then the glass samples were annealed at 400 K for two hours to avoid the mechanical strains developed during the quenching process. The two opposite faces of glass were highly polished to ensure a good parallelism. All glasses are cleaned with acetone to remove the presence of any foreign particles. The samples are prepared chemically stable and nonhygroscopic and such glass samples as system-I (BML) and system-II (BSP) are reported in plate-1 and plate-2.


### 2.2. Measurement of Ultrasonic Velocities in Glass Samples

The ultrasonic longitudinal and shear velocities of the glass specimen were determined by using the pulse-echo overlapping methods at room temperature by making use of 5 MHz X-cut and Y-cut transducers. These transducers act as both transmitters and receivers of the ultrasonic pulse. The transducers were brought into contact with each of the twelve samples by means of a couplant, in order to ensure that there was no air void between the transducer and the specimen.By applying constant pressure on the probe the echo waveforms were obtained on the display unit and stored in the memory. Figures2(a) and 2(b) show one of such echo waveforms obtained for longitudinal and shear waves (for BML and BSP systems).


### 2.3. Density of Glass Samples

The density of the glass samples was measured using relative measurement technique. Benzene was used as a buoyant liquid. The glass samples were weighed both in air and after immersing in benzene at 303 K. The weight of the glass samples was measured in a single pan with an accuracy of 0.0001 g. The density was calculated using the formula(1)ρ=ρBW1W1-W2,
where W1 and W2 are the weights of the glass samples in air and in benzene and ρB is the density of the benzene at 303 K.


## 2.1. Sample Preparation

The chemicals used in the present research work were analytical reagent (AR) and spectroscopic reagent (SR) grade with minimum assay 99% being obtained from Sd Fine Fhemicals, India, and E-Merck, Germany. The composition in mol% of (increase of B2O3 and decrease of PbO/P2O5 contents) glass specimen is listed in Table 1. The required amounts (approximately 20 g) in mol% of different chemicals in powder form were weighed using single pan digital balance (Model SHIMADZU AX 200) having an accuracy of 0.0001 g.Table 1
Composition of glasses.
S. no.
Glass specimen
Composition in mol%
System-I (B2O3-MnO2-PbO)
1
BML-1
60-10-30
2
BML-2
62-10-28
3
BML-3
64-10-26
4
BML-4
66-10-24
5
BML-5
68-10-22
6
BML-6
70-10-20
System-II (B2O3-Na2CO3-P2O5)
1
BSP-1
50-25-25
2
BSP-2
52-25-23
3
BSP-3
54-25-21
4
BSP-4
56-25-19
5
BSP-5
58-25-17
6
BSP-6
60-25-15The homogenisation of the appropriate mixture of the component of chemicals was effected by repeating grinding using a pestle and mortar. The temperature controlled muffle furnace was gradually raised to a higher temperature at the rate of 100 K per hour and a glass structure was noticed for BML glass system at 1060 K and for BSP glass system 1080 K and eventually the molten glass melt was immediately poured on a heavy copper molding block having the dimension of 12 mm diameter and 6 mm length kept at room temperature. Then the glass samples were annealed at 400 K for two hours to avoid the mechanical strains developed during the quenching process. The two opposite faces of glass were highly polished to ensure a good parallelism. All glasses are cleaned with acetone to remove the presence of any foreign particles. The samples are prepared chemically stable and nonhygroscopic and such glass samples as system-I (BML) and system-II (BSP) are reported in plate-1 and plate-2.


## 2.2. Measurement of Ultrasonic Velocities in Glass Samples

The ultrasonic longitudinal and shear velocities of the glass specimen were determined by using the pulse-echo overlapping methods at room temperature by making use of 5 MHz X-cut and Y-cut transducers. These transducers act as both transmitters and receivers of the ultrasonic pulse. The transducers were brought into contact with each of the twelve samples by means of a couplant, in order to ensure that there was no air void between the transducer and the specimen.By applying constant pressure on the probe the echo waveforms were obtained on the display unit and stored in the memory. Figures2(a) and 2(b) show one of such echo waveforms obtained for longitudinal and shear waves (for BML and BSP systems).


## 2.3. Density of Glass Samples

The density of the glass samples was measured using relative measurement technique. Benzene was used as a buoyant liquid. The glass samples were weighed both in air and after immersing in benzene at 303 K. The weight of the glass samples was measured in a single pan with an accuracy of 0.0001 g. The density was calculated using the formula(1)ρ=ρBW1W1-W2,
where W1 and W2 are the weights of the glass samples in air and in benzene and ρB is the density of the benzene at 303 K.


## 3. Result and Discussion

### 3.1. Ultrasonic Study

The experimental values of density and ultrasonic velocity (both longitudinal (UL) and shear (US)) of the different glass specimens with respect to change in mol% of PbO and P2O5 are listed in Table 2. The calculated elastic moduli such as longitudinal modulus (L), shear modulus (G), bulk modulus (K), and Young’s modulus (E) are reported in Table 2. The perusal of Table 3 shows the value of Poisson’s ratio (α), acoustic impedance (Z), microhardness (H), Debye’s temperature (θD), and thermal expansion coefficient (αP) for the two glass systems (BML and BSP). Figure 3 shows the variation of Debye temperature for the BML glasses with the composition of PbO (mol%). In a similar manner, the variation of the previous parameters with the composition of P2O5 (mol%) for BSP glasses is depicted in Figure 3.Table 2
Values of density (ρ), longitudinal velocity (UL), shear velocity (US), and elastic moduli of BML and BSP glass systems.
Name of the glass samples
Densityρ(Kg/m3)
Ultrasonic velocity (m/s)
Elastic moduli
Longitudinalvelocity(UL)
Shearvelocity(US)
Longitudinal moduli (L)×10−9 Nm−2
Shear moduli (G)×10−9 Nm−2
Bulk moduli (K)×10−9 Nm−2
Young’s moduli (E)×10−9 Nm−2
System-I  BML glass systems (B2O3-MnO2-PbO)
BML-1
1304.19
4073.34
2463.94
21.63
7.91
11.08
19.17
BML-2
1324.64
4177.83
2472.42
23.12
8.08
12.32
19.92
BML-3
1353.70
4403.66
2533.10
26.25
8.68
14.66
21.76
BML-4
1359.31
4526.08
2610.90
27.84
9.27
15.49
23.17
BML-5
1372.54
4550.28
2661.44
28.42
9.72
15.55
24.44
BML-6
1384.01
4615.91
2693.84
29.48
10.00
16.12
25.35
System-II  BSP glass systems (B2O3-Na2CO3-P2O5)
BSP-1
1707.92
5145.35
2875.35
45.22
14.1
26.38
34.25
BSP-2
1743.67
5256.24
3055.06
48.17
16.2
26.47
40.52
BSP-3
1756.72
5291.56
3153.57
49.19
17.4
25.89
42.76
BSP-4
1762.19
5379.13
3186.69
50.98
17.7
27.62
43.39
BSP-5
1779.83
5631.24
3222.86
56.44
18.4
31.79
46.43
BSP-6
1792.60
6034.69
3296.34
65.28
1.95
39.31
50.13Table 3
Values of Poisson’s ratio (σ), acoustic impedance (Z), microharness (H), Debye temperature (θD), and thermal expansion coefficient (αP) of BML and BSP glass systems.
Name of the glass samples
Poisson’s ratio (σ)
Acoustic impedanceZ   (×107 Kg · m2s−1)
MicrohardnessH (×10−9 Nm−2)
Debye temperatureθD (K)
Thermal expansion coefficientαP (K−1)
System-I  BML glass systems (B2O3- MnO2-PbO)
BML-1
0.211
0.5312
2.6390
144.92
94488.1
BML-2
0.230
0.5534
1.4100
146.49
96912.4
BML-3
0.252
0.5961
1.4300
151.54
102151.5
BML-4
0.250
0.6152
1.5370
156.37
104991.7
BML-5
0.257
0.6245
1.5750
159.72
105553.1
BML-6
0.262
0.6388
1.5935
162.12
107075.7
System-II  BSP glass systems (B2O3-Na2CO3-P2O5)
BSP-1
0.212
0.8782
2.7130
197.68
119358.7
BSP-2
0.244
0.9165
2.9830
210.31
121931.4
BSP-3
0.224
0.9295
3.0145
211.38
122750.8
BSP-4
0.238
0.9479
3.0600
223.36
124782.4
BSP-5
0.256
1.0022
3.0710
224.03
130631.4
BSP-6
0.287
1.0817
3.1765
230.16
139991.4Density is an effective tool to explore the degree of structural compactness, modification of the geometrical configuration of the glass network, change in coordination, and the variation of the dimension of the interstitial holes [15]. In our present study, the density of glasses (both BML and BSP glass systems) exhibits continuous increases with increase in mol% B2O3. From Table 2, one can notice the monotonic increase of density with increase of B2O3 concentration which can be attributed to the structure changes occurring in the coordination of boron glass network. The structure of crystalline as well as amorphous B2O3 is made up of planar (BO3) triangles units as reported by Bray [16]. In amorphous B2O3, most of these triangles are arranged into boroxol rings in which three oxygen are part of the rings and three oxygen are outside the ring. These rings are randomly interconnected through the loose (BO3) units. Due to the addition of B2O3, the three coordinated triangle boron (BO3) units are converted to four coordinated boron tetrahedra (BO4) and thus the network dimensionality and connectivity increase. This would lead to efficient packing and compactness in the structure, which will be reflected in increase of density of the glass systems. In the present study, the higher values of density are found in BSP glass systems and hence the magnitudes of density values are in the order BSP glass system > BML glass system.One can notice from Table2 that the longitudinal (UL) and shear velocities (US) increase linearly with increase in mol% B2O3 in both BML and BSP glass systems. It is observed that the rate of increase of UL is greater than that of US. Bahatti and Singh [4] suggested that the addition of PbO and P2O5 to B2O3 changes the structure to a rigid and compact structure due to change in the coordination number of boron from 3 to 4, which causes increase in ultrasonic velocities. The variation of ultrasonic velocities and elastic moduli can be explained on the basis of the structural consideration of glassy network. From Table 2, the values of longitudinal ultrasonic velocity (UL) increases from 4073.34 to 4615.91 ms-1 for BML glass and 5145.35 to 6034.69 ms-1 for BSP glass systems. Similarly, shear velocity (US) increases from 2463.94 to 2693.84 ms-1 for BML glass and 2875.35 to 3296.34 ms-1 for BSP glass systems on increasing the Borate content.According to Higazy and Bridge [17] the longitudinal strain changes directly with bond stretching force constant. On the other hand, as reported by Reisfeld et al. [18], the shear strain changes with bond bending force constant. The increasing trend of both ultrasonic velocities may be attributed to the increase in rigidity of the glass network.Glass is considered as an elastic substance and it can be characterized through a modulus of elasticity [19, 20]. This modulus increases as the lengthening of certain applied stress diminishes. This will be the case: if the glass structure is rigid and therefore contains the fewest possible nonbridging oxygen atoms with increase of B2O3 content, the structure becomes more rigid and so this leads to the increases in density as well as ultrasonic velocities [21–23]. The increase in velocities is attributed to the increases in rigidity of the glass network [21, 24]. Addition of B2O3 with PbO and P2O5 increases the elastic moduli such as the longitudinal modulus (L), shear modulus (G), bulk modulus (K), and Young’s modulus (E) in both glass (BML and BSP) systems. The elevation of such elastic moduli in both glass systems can be interpreted on the basis of the structural consideration of borate network. Further, the addition of P2O5 and PbO with B2O3 network creates (BO4) units and this leads to increase in the network dimensionality and connectivity of the network. The increasing trend of elastic moduli in all two glass systems indicates resistance to deformation and is most probably due to the presence of number of layers of covalent bonds. The continuous increase of Poisson’s ratio as well as microhardness in the present study reveals the absence of nonbridging oxygen (NBO) and this causes the formation of glassy network. Rajendran et al. [25] observed that increase in elastic moduli with addition of B2O3 confirms the rigidity and hence the formation of stronger structural building units in this glassy network.Poisson’s ratio is an effective tool in exploring the degree of cross-link density of the glass network and its magnitude increases the cross-link density, and it is the ratio of transverse and linear strains for a linear stress. According to Bridge et al. [26] glass networks having a connectivity of two (zero cross-link density) have Poisson’s ratio of = 0.4. Glass networks having connectivity of three (one cross-link density) have Poisson’s ratio of = 0.3, while networks having a connectivity of four (two cross-link densities) have Poisson’s ratio of  = 0.15. It can be seen from the present study that Poisson’s ratio increases from 0.211 to 0.262 for BML glass systems and from 0.212 to 0.287 for BSP glass systems (Figures 1 and 5; Tables 4 and 5). The perusal of Table 3 exhibits the values of Poisson’s ratio obtained in this study suggesting that the network of these glasses has two-dimensional structure. The increase in Poisson’s ratio with increasing content of B2O3 is attributed to increase in the average cross-link density of the glass as proposed by Higazy and Bridge [17]. The increasing values of Poisson’s ratio are attached to strengthening of network linkage and hardening of the network structure. This has been attributed to the fact that the concentration of bonds resisting a transverse deformation decreases in that order [27].Table 4
System-I—B2O3-MnO2-PbO (BML glass system).
Glass name
Peak’s positions (cm−1)
BMP-1
540.91
641.10
805.48
1021.55
1156.16
1194.52
1456.13
1646.37
2854.79
2926.03
3243.84
3426.50
BMP-2
541.39
697.29
876.71
1072.71
1156.16
—
1431.18
1645.70
2854.79
2915.07
3221.84
3428.01
BMP-3
541.84
641.10
—
1024.96
1156.16
1189.04
1448.39
1633.99
2854.32
2923.98
3243.84
3430.60
BMP-4
541.18
646.10
—
1021.48
—
1194.52
1451.49
1632.16
2854.79
2922.24
3232.88
3415.72
BMP-5
542.87
645.63
821.92
1059.75
—
1193.22
1457.52
1637.84
2854.79
2920.55
3227.57
3397.91
BMP-6
541.36
—
—
1062.96
—
—
1441.72
1631.96
2854.19
2923.87
—
3427.05Table 5
System-II—B2O3-Na2CO3-P2O5(BSL glass system).
Glass name
Peak’s positions (cm−1)
BSP-1
685.50
1025.04
1357.27
2849.32
2909.59
3408.38
BSP-2
679.45
—
1342.75
2854.79
2926.03
3441.50
BSP-3
676.52
1059.84
1355.92
2854.79
2923.52
3433.21
BSP-4
675.91
1062.56
1350.71
2854.79
2924.60
3431.07
BSP-5
686.37
1060.61
1351.76
2849.32
2920.55
3433.66
BSP-6
676.64
1028.97
1350.85
2843.84
2915.07
3431.14(a) and (b) Photograph for BML and BSP glass systems.
(a)
(b)(a) Longitudinal and shear waveforms for BML-I glass system; (b) longitudinal and shear waveforms for BSP-I glass system.
(a)
(b)Debye temperature (θD) with variation of B2O3 (mol%) for system I and system II.
(a)
(b)Microhardness expresses the stress required to eliminate the free volume (deformation of the network) of the glass. The present study of increasing value of microhardness in all the two glass systems studied indicates the increase in rigidity of the glass. The softening point is temperature at which viscous flow changes to plastic flow. It determines the temperature stability of the glass. The higher the value of softening temperature, the greater is the stability of its elastic properties [28]. As seen from Table 3, the values of microhardness increase with B2O3 content. The increase of microhardness implies an increase in the rigidity of the glass system. The present investigation shows that the BSP glass systems possess the highest values of microhardness suggesting that BSP glasses are stronger than BML glass systems.Debye’s temperature represents the temperature at which nearly all modes of vibration in a solid are excited and its increasing trend implies an increase in the rigidity of the glass [28]. The perusal of Figure 3 describes the variation of Debye temperature with B2O3 content.The gradual increase of Debye’s temperature from 144.92 K to 162.12 K for BML glass systems and from 197.68 to 230.16 K for BSP glass systems indicates the increase in the rigidity of these glass systems. Such an enhancement of Debye’s temperature is attributed to the increase in the number of atoms in the chemical formula of the glass and increase in the ultrasonic velocity [28]. This also further suggests the strengthening in the glass structure which is due to the creation of nonbridging oxygen ions [24]. In our present investigation, the higher values of Debye temperature are reported in BSP glass system. The continuous increase of Debye temperature also suggests the compactness in the structure leading to increase in mean sound velocity [29].The perusal of Table3 exhibits the values of acoustic impedance (Z) and the thermal expansion coefficient of the two glass systems studied. The increasing trend of their values for both glass (BML and BSP) systems clearly support this and confirms the strengthening of the glass network in the system. This supports well our earlier conclusions derived from the previous parameters.


### 3.2. X-Ray Diffraction Study (XRD)

X-ray diffraction studies were carried out on each glass sample to confirm the amorphous nature of prepared glasses. An X-ray diffractometer (PW1700: Philips Eindhoven, The New Netherlands) was used with CuK as a radiation source between 20° and 80°.The prepared glass samples were washed gently in double-distilled water. The washed glass samples were dried at room temperature, ground, and then used to obtain the XRD patterns as discussed previously. The XRD spectrum shows a number of lines of evidence of unmelted (W) crystalline particles in quarchal glasses. Such XRD spectrums of one of the BML-I and BSP-I glasses systems are shown in Figures 4(a) and 4(b).(a) X-ray diffractogram for BML-I glass system-I; (b) X-ray diffractogram for BSP-I glass system-II.
(a)
(b)(a) FTIR spectrum for BML glass system; (b) FTIR spectrum for BSP glass system.
(a)
(b)


### 3.3. Spectroscopic Study: FTIR Interpretation

The infrared transmission spectra of the glasses are measured at room temperature in the wavenumber range 400–4000cm-1 by a Fourier transform computerised infrared spectrometer type (Perkin Elmer spectrometer). The prepared glass samples are mixed in the form of fine powder with KBr in the ratio of 1 : 100 mg glass powder : KBr, respectively. The weighed mixtures are then subjected to pressure of 150 kg/cm2 to produce homogeneous pellets. The infrared transmission measurements are measured immediately after preparing the pellets. Normalized FTIR absorption spectra of B2O3-Na2CO3-P2O5 and B2O3-PbO-MnO2 are shown in Figures. The goal of vibrational analysis to find vibrational modes is connected with content of glass samples. The observed infrared transmission peak around at 540–541.87 cm-1 is attributed to stretching vibrations of Pb–O [30, 31]. The composition of mole percentage of PbO is in decreasing trend giving rise to vibrational bands which are slightly shifted to lower wavenumber (Table 6). These vibrational bands do not appeared in the system II because of absence of PbO content. From FTIR and mole percentage results, the role of PbO in this glass structures has been explored. Infrared transmission spectra indicate that when composition of PbO is in the range 20%<x<30%, the Pb2+ ions that are in the borate glass act as a network modifier [31, 32]. In general, the vibrational modes of the borate network are active mainly in three regions: the first region that lies between 600 and 800 cm-1 is due to bending vibration of various borate segments, the second region that lies between 850–1200 cm-1 is due to stretching vibrations of tetrahedral BO4 units, and the third region that lies between 1200 and 1600 cm-1 is due to stretching vibrations of B–O in BO3 triangles. In the present study, the peak observed at around the range 641.1–697.29 cm-1 is assigned as B–O–B bending vibration of borate groups which are composed of BO4 and BO3 units. The stretching normal mode of MnO2 is also observed in the previous region; these two vibrational modes overlap with each other [32–34]. The absorption peak identified at the region 805.48–876.71 cm-1 is due to stretching vibration of BO4 groups [35, 36]. The infrared spectra of the existing structural borate groups and their rearrangement are observed to be slightly affected by the change of glass composition.Table 6
Wavenumber (cm−1)
Band assignment
540.91–542.87
Deformation vibrations of the Pb–O.
641.10–697.29
B–O–B bonding vibration of  BO3 groups and stretching vibration of MnO.
805.48–876.71
Stretching vibration of B–O–B lineages in borate network.
1021.48–1072.71
B–O bond stretching of the tetrahedral BO4units.
1156.16
BO4 stretching vibration.
1189.04–1646.37
B–O symmetric stretching vibration of BO3 units in metaborate, paraborate, and orthoborate groups.
1025.04–1062.56
PO3 symmetric stretching.
1342.75–1357.27
Symmetric stretching of P–O–P group.
1631–1646.3
O–H bending vibrations of water.
2854.32–3415.72
O–H stretching vibrations of water.In system I, the bands that appeared in the region 1021.48–1072.71cm-1 are assigned as symmetric stretching vibration of BO4 tetrahedral units [34, 37]. But in system II, the absorption peaks at around the range 1025.04–1062.56 cm-1 are due to symmetric stretching vibration of PO3 groups. The previous two stretching vibration modes overlap with each other [38, 39]. The absorption peak identified at 1156.1 cm-1 is due to presence of BO4 stretching vibration. The spectrum of borate glass exhibited vibrational bands at the region 1189.04–1646.37 cm-1 which is due to increasing percentage of B2O3 in both systems. The [40, 41] B–O asymmetric stretching vibrations of BO3 units in metaborate, orthoborate, and paraborate appeared at the region 1431.18–1457.52 cm-1 [42, 43]. The vibrational bands observed at the region 1342.75–1357.27 cm-1 are assigned as antisymmetrical stretching vibrations of PO2 groups. This region may also consist of bands due to P=O stretching vibrations. This absorption is typically metaphosphate chains. Due to decreasing percentage of P2O5, in system II, the vibrational bands are slightly shifted to lower wavenumber [44, 45]. In particular, the atmospheric moisture is easily absorbed by the sample or by the pellet causing the appearance of IR band belonging to H2O molecules. The peak at around the region 1631.96–1646.37 cm-1 indicates a change from BO3 triangles to BO4 tetrahedra and this peak may also be assigned to the bending modes of molecular water. The IR bands from 2854.32–3415.72 cm-1 are due to superposition of asymmetric and symmetric stretching vibration of OH. In system I, with the liberation of CO2, the Na2CO3 is converted into Na2O because of its glass transition temperature at 1050°C. Thus the spectral absorption band of Na2CO3 is very feeble. IR absorption spectra of the studied samples show various vibrational bands which are characteristics of triangular and tetrahedral borate units together with small bands due to water OH and BOH. The FTIR studies confirm the presence of various contents of borate network. These vibrational assignments are in good agreement with literature values.


### 3.4. Scanning Electron Microscopic Study

Scanning electron microscope (SEM) is used in a wide range of fields as a tool for observing surfaces at nanometer level. The main advantage of SEM is its ability to study the heterogeneity of glass composites to visualize various mineral components and their relation in terms of overall micrographic and texture. SEM covers the observation from the fine structures of a surface of specimen to elemental analysis of a microarea without destroying the specimen. The SEM photographs of the samples are given in Figures6(a) and 6(b). It is obtained that different sized grain particles are distributed. The particle size seems to vary in each micrograph. It consists of density packed grains free from holes.(a) SEM system-I for BML glass specimen; (b) SEM system-II for BSP glass specimen.
(a)
(b)The particles are angular or spherical in nature. From these figures, it is known that large particles may be monomineralic, but a majority is likely to be composite. Some sphere-like agglomerates found spreading are the glass surfaces, due to deposition of amorphous apatite. This suggests that during glass formation, the presence of clusters composed of fibers is formed. Also, the glass may consist of large particles, aggregates, agglomerates, and clusters, which clearly explain the surface of morphology of glass samples.


## 3.1. Ultrasonic Study

The experimental values of density and ultrasonic velocity (both longitudinal (UL) and shear (US)) of the different glass specimens with respect to change in mol% of PbO and P2O5 are listed in Table 2. The calculated elastic moduli such as longitudinal modulus (L), shear modulus (G), bulk modulus (K), and Young’s modulus (E) are reported in Table 2. The perusal of Table 3 shows the value of Poisson’s ratio (α), acoustic impedance (Z), microhardness (H), Debye’s temperature (θD), and thermal expansion coefficient (αP) for the two glass systems (BML and BSP). Figure 3 shows the variation of Debye temperature for the BML glasses with the composition of PbO (mol%). In a similar manner, the variation of the previous parameters with the composition of P2O5 (mol%) for BSP glasses is depicted in Figure 3.Table 2
Values of density (ρ), longitudinal velocity (UL), shear velocity (US), and elastic moduli of BML and BSP glass systems.
Name of the glass samples
Densityρ(Kg/m3)
Ultrasonic velocity (m/s)
Elastic moduli
Longitudinalvelocity(UL)
Shearvelocity(US)
Longitudinal moduli (L)×10−9 Nm−2
Shear moduli (G)×10−9 Nm−2
Bulk moduli (K)×10−9 Nm−2
Young’s moduli (E)×10−9 Nm−2
System-I  BML glass systems (B2O3-MnO2-PbO)
BML-1
1304.19
4073.34
2463.94
21.63
7.91
11.08
19.17
BML-2
1324.64
4177.83
2472.42
23.12
8.08
12.32
19.92
BML-3
1353.70
4403.66
2533.10
26.25
8.68
14.66
21.76
BML-4
1359.31
4526.08
2610.90
27.84
9.27
15.49
23.17
BML-5
1372.54
4550.28
2661.44
28.42
9.72
15.55
24.44
BML-6
1384.01
4615.91
2693.84
29.48
10.00
16.12
25.35
System-II  BSP glass systems (B2O3-Na2CO3-P2O5)
BSP-1
1707.92
5145.35
2875.35
45.22
14.1
26.38
34.25
BSP-2
1743.67
5256.24
3055.06
48.17
16.2
26.47
40.52
BSP-3
1756.72
5291.56
3153.57
49.19
17.4
25.89
42.76
BSP-4
1762.19
5379.13
3186.69
50.98
17.7
27.62
43.39
BSP-5
1779.83
5631.24
3222.86
56.44
18.4
31.79
46.43
BSP-6
1792.60
6034.69
3296.34
65.28
1.95
39.31
50.13Table 3
Values of Poisson’s ratio (σ), acoustic impedance (Z), microharness (H), Debye temperature (θD), and thermal expansion coefficient (αP) of BML and BSP glass systems.
Name of the glass samples
Poisson’s ratio (σ)
Acoustic impedanceZ   (×107 Kg · m2s−1)
MicrohardnessH (×10−9 Nm−2)
Debye temperatureθD (K)
Thermal expansion coefficientαP (K−1)
System-I  BML glass systems (B2O3- MnO2-PbO)
BML-1
0.211
0.5312
2.6390
144.92
94488.1
BML-2
0.230
0.5534
1.4100
146.49
96912.4
BML-3
0.252
0.5961
1.4300
151.54
102151.5
BML-4
0.250
0.6152
1.5370
156.37
104991.7
BML-5
0.257
0.6245
1.5750
159.72
105553.1
BML-6
0.262
0.6388
1.5935
162.12
107075.7
System-II  BSP glass systems (B2O3-Na2CO3-P2O5)
BSP-1
0.212
0.8782
2.7130
197.68
119358.7
BSP-2
0.244
0.9165
2.9830
210.31
121931.4
BSP-3
0.224
0.9295
3.0145
211.38
122750.8
BSP-4
0.238
0.9479
3.0600
223.36
124782.4
BSP-5
0.256
1.0022
3.0710
224.03
130631.4
BSP-6
0.287
1.0817
3.1765
230.16
139991.4Density is an effective tool to explore the degree of structural compactness, modification of the geometrical configuration of the glass network, change in coordination, and the variation of the dimension of the interstitial holes [15]. In our present study, the density of glasses (both BML and BSP glass systems) exhibits continuous increases with increase in mol% B2O3. From Table 2, one can notice the monotonic increase of density with increase of B2O3 concentration which can be attributed to the structure changes occurring in the coordination of boron glass network. The structure of crystalline as well as amorphous B2O3 is made up of planar (BO3) triangles units as reported by Bray [16]. In amorphous B2O3, most of these triangles are arranged into boroxol rings in which three oxygen are part of the rings and three oxygen are outside the ring. These rings are randomly interconnected through the loose (BO3) units. Due to the addition of B2O3, the three coordinated triangle boron (BO3) units are converted to four coordinated boron tetrahedra (BO4) and thus the network dimensionality and connectivity increase. This would lead to efficient packing and compactness in the structure, which will be reflected in increase of density of the glass systems. In the present study, the higher values of density are found in BSP glass systems and hence the magnitudes of density values are in the order BSP glass system > BML glass system.One can notice from Table2 that the longitudinal (UL) and shear velocities (US) increase linearly with increase in mol% B2O3 in both BML and BSP glass systems. It is observed that the rate of increase of UL is greater than that of US. Bahatti and Singh [4] suggested that the addition of PbO and P2O5 to B2O3 changes the structure to a rigid and compact structure due to change in the coordination number of boron from 3 to 4, which causes increase in ultrasonic velocities. The variation of ultrasonic velocities and elastic moduli can be explained on the basis of the structural consideration of glassy network. From Table 2, the values of longitudinal ultrasonic velocity (UL) increases from 4073.34 to 4615.91 ms-1 for BML glass and 5145.35 to 6034.69 ms-1 for BSP glass systems. Similarly, shear velocity (US) increases from 2463.94 to 2693.84 ms-1 for BML glass and 2875.35 to 3296.34 ms-1 for BSP glass systems on increasing the Borate content.According to Higazy and Bridge [17] the longitudinal strain changes directly with bond stretching force constant. On the other hand, as reported by Reisfeld et al. [18], the shear strain changes with bond bending force constant. The increasing trend of both ultrasonic velocities may be attributed to the increase in rigidity of the glass network.Glass is considered as an elastic substance and it can be characterized through a modulus of elasticity [19, 20]. This modulus increases as the lengthening of certain applied stress diminishes. This will be the case: if the glass structure is rigid and therefore contains the fewest possible nonbridging oxygen atoms with increase of B2O3 content, the structure becomes more rigid and so this leads to the increases in density as well as ultrasonic velocities [21–23]. The increase in velocities is attributed to the increases in rigidity of the glass network [21, 24]. Addition of B2O3 with PbO and P2O5 increases the elastic moduli such as the longitudinal modulus (L), shear modulus (G), bulk modulus (K), and Young’s modulus (E) in both glass (BML and BSP) systems. The elevation of such elastic moduli in both glass systems can be interpreted on the basis of the structural consideration of borate network. Further, the addition of P2O5 and PbO with B2O3 network creates (BO4) units and this leads to increase in the network dimensionality and connectivity of the network. The increasing trend of elastic moduli in all two glass systems indicates resistance to deformation and is most probably due to the presence of number of layers of covalent bonds. The continuous increase of Poisson’s ratio as well as microhardness in the present study reveals the absence of nonbridging oxygen (NBO) and this causes the formation of glassy network. Rajendran et al. [25] observed that increase in elastic moduli with addition of B2O3 confirms the rigidity and hence the formation of stronger structural building units in this glassy network.Poisson’s ratio is an effective tool in exploring the degree of cross-link density of the glass network and its magnitude increases the cross-link density, and it is the ratio of transverse and linear strains for a linear stress. According to Bridge et al. [26] glass networks having a connectivity of two (zero cross-link density) have Poisson’s ratio of = 0.4. Glass networks having connectivity of three (one cross-link density) have Poisson’s ratio of = 0.3, while networks having a connectivity of four (two cross-link densities) have Poisson’s ratio of  = 0.15. It can be seen from the present study that Poisson’s ratio increases from 0.211 to 0.262 for BML glass systems and from 0.212 to 0.287 for BSP glass systems (Figures 1 and 5; Tables 4 and 5). The perusal of Table 3 exhibits the values of Poisson’s ratio obtained in this study suggesting that the network of these glasses has two-dimensional structure. The increase in Poisson’s ratio with increasing content of B2O3 is attributed to increase in the average cross-link density of the glass as proposed by Higazy and Bridge [17]. The increasing values of Poisson’s ratio are attached to strengthening of network linkage and hardening of the network structure. This has been attributed to the fact that the concentration of bonds resisting a transverse deformation decreases in that order [27].Table 4
System-I—B2O3-MnO2-PbO (BML glass system).
Glass name
Peak’s positions (cm−1)
BMP-1
540.91
641.10
805.48
1021.55
1156.16
1194.52
1456.13
1646.37
2854.79
2926.03
3243.84
3426.50
BMP-2
541.39
697.29
876.71
1072.71
1156.16
—
1431.18
1645.70
2854.79
2915.07
3221.84
3428.01
BMP-3
541.84
641.10
—
1024.96
1156.16
1189.04
1448.39
1633.99
2854.32
2923.98
3243.84
3430.60
BMP-4
541.18
646.10
—
1021.48
—
1194.52
1451.49
1632.16
2854.79
2922.24
3232.88
3415.72
BMP-5
542.87
645.63
821.92
1059.75
—
1193.22
1457.52
1637.84
2854.79
2920.55
3227.57
3397.91
BMP-6
541.36
—
—
1062.96
—
—
1441.72
1631.96
2854.19
2923.87
—
3427.05Table 5
System-II—B2O3-Na2CO3-P2O5(BSL glass system).
Glass name
Peak’s positions (cm−1)
BSP-1
685.50
1025.04
1357.27
2849.32
2909.59
3408.38
BSP-2
679.45
—
1342.75
2854.79
2926.03
3441.50
BSP-3
676.52
1059.84
1355.92
2854.79
2923.52
3433.21
BSP-4
675.91
1062.56
1350.71
2854.79
2924.60
3431.07
BSP-5
686.37
1060.61
1351.76
2849.32
2920.55
3433.66
BSP-6
676.64
1028.97
1350.85
2843.84
2915.07
3431.14(a) and (b) Photograph for BML and BSP glass systems.
(a)
(b)(a) Longitudinal and shear waveforms for BML-I glass system; (b) longitudinal and shear waveforms for BSP-I glass system.
(a)
(b)Debye temperature (θD) with variation of B2O3 (mol%) for system I and system II.
(a)
(b)Microhardness expresses the stress required to eliminate the free volume (deformation of the network) of the glass. The present study of increasing value of microhardness in all the two glass systems studied indicates the increase in rigidity of the glass. The softening point is temperature at which viscous flow changes to plastic flow. It determines the temperature stability of the glass. The higher the value of softening temperature, the greater is the stability of its elastic properties [28]. As seen from Table 3, the values of microhardness increase with B2O3 content. The increase of microhardness implies an increase in the rigidity of the glass system. The present investigation shows that the BSP glass systems possess the highest values of microhardness suggesting that BSP glasses are stronger than BML glass systems.Debye’s temperature represents the temperature at which nearly all modes of vibration in a solid are excited and its increasing trend implies an increase in the rigidity of the glass [28]. The perusal of Figure 3 describes the variation of Debye temperature with B2O3 content.The gradual increase of Debye’s temperature from 144.92 K to 162.12 K for BML glass systems and from 197.68 to 230.16 K for BSP glass systems indicates the increase in the rigidity of these glass systems. Such an enhancement of Debye’s temperature is attributed to the increase in the number of atoms in the chemical formula of the glass and increase in the ultrasonic velocity [28]. This also further suggests the strengthening in the glass structure which is due to the creation of nonbridging oxygen ions [24]. In our present investigation, the higher values of Debye temperature are reported in BSP glass system. The continuous increase of Debye temperature also suggests the compactness in the structure leading to increase in mean sound velocity [29].The perusal of Table3 exhibits the values of acoustic impedance (Z) and the thermal expansion coefficient of the two glass systems studied. The increasing trend of their values for both glass (BML and BSP) systems clearly support this and confirms the strengthening of the glass network in the system. This supports well our earlier conclusions derived from the previous parameters.


## 3.2. X-Ray Diffraction Study (XRD)

X-ray diffraction studies were carried out on each glass sample to confirm the amorphous nature of prepared glasses. An X-ray diffractometer (PW1700: Philips Eindhoven, The New Netherlands) was used with CuK as a radiation source between 20° and 80°.The prepared glass samples were washed gently in double-distilled water. The washed glass samples were dried at room temperature, ground, and then used to obtain the XRD patterns as discussed previously. The XRD spectrum shows a number of lines of evidence of unmelted (W) crystalline particles in quarchal glasses. Such XRD spectrums of one of the BML-I and BSP-I glasses systems are shown in Figures 4(a) and 4(b).(a) X-ray diffractogram for BML-I glass system-I; (b) X-ray diffractogram for BSP-I glass system-II.
(a)
(b)(a) FTIR spectrum for BML glass system; (b) FTIR spectrum for BSP glass system.
(a)
(b)


## 3.3. Spectroscopic Study: FTIR Interpretation

The infrared transmission spectra of the glasses are measured at room temperature in the wavenumber range 400–4000cm-1 by a Fourier transform computerised infrared spectrometer type (Perkin Elmer spectrometer). The prepared glass samples are mixed in the form of fine powder with KBr in the ratio of 1 : 100 mg glass powder : KBr, respectively. The weighed mixtures are then subjected to pressure of 150 kg/cm2 to produce homogeneous pellets. The infrared transmission measurements are measured immediately after preparing the pellets. Normalized FTIR absorption spectra of B2O3-Na2CO3-P2O5 and B2O3-PbO-MnO2 are shown in Figures. The goal of vibrational analysis to find vibrational modes is connected with content of glass samples. The observed infrared transmission peak around at 540–541.87 cm-1 is attributed to stretching vibrations of Pb–O [30, 31]. The composition of mole percentage of PbO is in decreasing trend giving rise to vibrational bands which are slightly shifted to lower wavenumber (Table 6). These vibrational bands do not appeared in the system II because of absence of PbO content. From FTIR and mole percentage results, the role of PbO in this glass structures has been explored. Infrared transmission spectra indicate that when composition of PbO is in the range 20%<x<30%, the Pb2+ ions that are in the borate glass act as a network modifier [31, 32]. In general, the vibrational modes of the borate network are active mainly in three regions: the first region that lies between 600 and 800 cm-1 is due to bending vibration of various borate segments, the second region that lies between 850–1200 cm-1 is due to stretching vibrations of tetrahedral BO4 units, and the third region that lies between 1200 and 1600 cm-1 is due to stretching vibrations of B–O in BO3 triangles. In the present study, the peak observed at around the range 641.1–697.29 cm-1 is assigned as B–O–B bending vibration of borate groups which are composed of BO4 and BO3 units. The stretching normal mode of MnO2 is also observed in the previous region; these two vibrational modes overlap with each other [32–34]. The absorption peak identified at the region 805.48–876.71 cm-1 is due to stretching vibration of BO4 groups [35, 36]. The infrared spectra of the existing structural borate groups and their rearrangement are observed to be slightly affected by the change of glass composition.Table 6
Wavenumber (cm−1)
Band assignment
540.91–542.87
Deformation vibrations of the Pb–O.
641.10–697.29
B–O–B bonding vibration of  BO3 groups and stretching vibration of MnO.
805.48–876.71
Stretching vibration of B–O–B lineages in borate network.
1021.48–1072.71
B–O bond stretching of the tetrahedral BO4units.
1156.16
BO4 stretching vibration.
1189.04–1646.37
B–O symmetric stretching vibration of BO3 units in metaborate, paraborate, and orthoborate groups.
1025.04–1062.56
PO3 symmetric stretching.
1342.75–1357.27
Symmetric stretching of P–O–P group.
1631–1646.3
O–H bending vibrations of water.
2854.32–3415.72
O–H stretching vibrations of water.In system I, the bands that appeared in the region 1021.48–1072.71cm-1 are assigned as symmetric stretching vibration of BO4 tetrahedral units [34, 37]. But in system II, the absorption peaks at around the range 1025.04–1062.56 cm-1 are due to symmetric stretching vibration of PO3 groups. The previous two stretching vibration modes overlap with each other [38, 39]. The absorption peak identified at 1156.1 cm-1 is due to presence of BO4 stretching vibration. The spectrum of borate glass exhibited vibrational bands at the region 1189.04–1646.37 cm-1 which is due to increasing percentage of B2O3 in both systems. The [40, 41] B–O asymmetric stretching vibrations of BO3 units in metaborate, orthoborate, and paraborate appeared at the region 1431.18–1457.52 cm-1 [42, 43]. The vibrational bands observed at the region 1342.75–1357.27 cm-1 are assigned as antisymmetrical stretching vibrations of PO2 groups. This region may also consist of bands due to P=O stretching vibrations. This absorption is typically metaphosphate chains. Due to decreasing percentage of P2O5, in system II, the vibrational bands are slightly shifted to lower wavenumber [44, 45]. In particular, the atmospheric moisture is easily absorbed by the sample or by the pellet causing the appearance of IR band belonging to H2O molecules. The peak at around the region 1631.96–1646.37 cm-1 indicates a change from BO3 triangles to BO4 tetrahedra and this peak may also be assigned to the bending modes of molecular water. The IR bands from 2854.32–3415.72 cm-1 are due to superposition of asymmetric and symmetric stretching vibration of OH. In system I, with the liberation of CO2, the Na2CO3 is converted into Na2O because of its glass transition temperature at 1050°C. Thus the spectral absorption band of Na2CO3 is very feeble. IR absorption spectra of the studied samples show various vibrational bands which are characteristics of triangular and tetrahedral borate units together with small bands due to water OH and BOH. The FTIR studies confirm the presence of various contents of borate network. These vibrational assignments are in good agreement with literature values.


## 3.4. Scanning Electron Microscopic Study

Scanning electron microscope (SEM) is used in a wide range of fields as a tool for observing surfaces at nanometer level. The main advantage of SEM is its ability to study the heterogeneity of glass composites to visualize various mineral components and their relation in terms of overall micrographic and texture. SEM covers the observation from the fine structures of a surface of specimen to elemental analysis of a microarea without destroying the specimen. The SEM photographs of the samples are given in Figures6(a) and 6(b). It is obtained that different sized grain particles are distributed. The particle size seems to vary in each micrograph. It consists of density packed grains free from holes.(a) SEM system-I for BML glass specimen; (b) SEM system-II for BSP glass specimen.
(a)
(b)The particles are angular or spherical in nature. From these figures, it is known that large particles may be monomineralic, but a majority is likely to be composite. Some sphere-like agglomerates found spreading are the glass surfaces, due to deposition of amorphous apatite. This suggests that during glass formation, the presence of clusters composed of fibers is formed. Also, the glass may consist of large particles, aggregates, agglomerates, and clusters, which clearly explain the surface of morphology of glass samples.


## 4. Conclusion

(i)
The gradual increase in density with mol% B2O3 of the glass specimen indicates the dependence of density on weight of metal atom in the network modifier. The magnitude of the density is in the order BSP > BML.
(ii)
The ultrasonic velocities (UL and US) of BML and BSP glasses vary linearly with the addition of glass former (B2O3) and the magnitude is in the order BSP > BML.
(iii)
The evaluated acoustical, elastic, and mechanical properties of BML and BSP glasses throw light on rigidity and compactness in structural network.
(iv)
The observed increasing trend of microhardness and Poison’s Ratio for both glass systems (BML and BSP) indicates that BSP glass system is stronger than BML system.
(v)
The BSP glass possesses higher rigidity and compactness in structural network over the BML.
(vi)
The functional groups present in the glass sample have been confirmed by FTIR spectral analysis. The topological aspects of the glass samples are reported from the SEM micrography.



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*Source: 485317-2013-04-21.xml*