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Scientific Reports
2045-2322
Nature Publishing Group UK London

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58567
10.1038/s41598-024-58567-w
Article
A comprehensive investigation of Bi2O3 on the physical, structural, optical, and electrical properties of K2O.ZnO.V2O5.B2O3 glasses
Ibrahim S. safeyaibrahim@yahoo.com

1
Ali A. A. 1
Fathi Ahlam M. 2
1 https://ror.org/02n85j827 grid.419725.c 0000 0001 2151 8157 Glass Research Department, National Research Centre, El-Buhouth St., Dokki, Giza, 12622 Egypt
2 https://ror.org/02n85j827 grid.419725.c 0000 0001 2151 8157 Physical Chemistry Department, National Research Centre, El-Buhouth St., Dokki, Giza, 12622 Egypt
12 4 2024
12 4 2024
2024
14 851830 11 2023
1 4 2024
© The Author(s) 2024
2024
https://creativecommons.org/licenses/by/4.0/ Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit http://creativecommons.org/licenses/by/4.0/.
The multi-component glass system has a composition of 10K2O–10ZnO–55 B2O3–(25–x)V2O5–xBi2O3 (x = 4, 5, 7.5, 9, 10 mol%) are synthesized by the melt-quenching method. Using X-ray diffraction examination, the amorphous phase in the material was confirmed. The physical characteristics of the produced compositions are examined using density (D) and molar volume (Vm). Calculations of physical properties showed that adding Bi2O3 from 4 to 10 mol% increased the glass density from 2.7878 to 3.3617 g cm−3 and decreased the molar volume from 40.4196 to 38.5895 cm3/mol. Studies of glass samples using the FTIR show bands of absorption for oxides in different structural groups. Octahedral [BiO6], [BO4], and tetrahedral [BO3] structural units are observed in the present glass matrices. The cutoff wavelength (λC), and optical band gap energy were determined using UV absorption spectra. The increase in non-bridging oxygens can be linked to the decrease in optical band gap energy (Eopt) (direct and indirect) and the increase in cutoff wavelength with an increase in Bi2O3 content. This is attributed to the existence of bismuth ions and the creation of non-bridging oxygens. Besides that, the values of optical parameters, viz., optical electronegativity, refractive index, and molar refractivity, are calculated. The metallization criterion values are less than 1 and the glass samples exhibit an increased tendency towards metallization. Both the conductivity and the dielectric constant increase with the rise in Bi2O3 content, however, the dielectric loss and the impedance reduce. The behavior and values of conductivity for the studied glasses reveal the semiconducting properties of all glass samples. These results suggest that the produced glass samples may be employed as amorphous semiconductors in electronics and memory switching devices.

Keywords

Bi2O3
Borovanadate glasses
FTIR
Optical properties
Urbach energy
Electrical properties
Subject terms

Materials science
Optics and photonics
National Research Centre EgyptOpen access funding provided by The Science, Technology & Innovation Funding Authority (STDF) in cooperation with The Egyptian Knowledge Bank (EKB).

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pmcIntroduction

Glass, an isotropic material, offers many benefits over crystalline materials, including being inexpensive, easy to fabricate, and having no grain boundaries1. The oxide glass family is quite large and is always evolving. Oxide glasses are used in several well-known and highly technical fields, including X-ray protection, fibre optic equipment, and laboratory glassware. Network formers such as silicate, vanadate, borate, borovanadate, and borosilicate, as well as network modifiers like transition metals, alkali, and alkaline earth, make up the oxide glasses2.

Borate glasses are the most effective in forming glass out of all the varieties of glasses. Because of its greater binding strength, smaller cationic size, and lower heat of fusion, B2O3 is a useful glass-forming material3. Glass formation at low temperatures is easy because of its excellent thermal stability and chemical durability4. It demonstrates excellent mechanical stability, optimal bandwidths, better infrared transmissions, and great photonic characteristics5. In borate glasses, the B3+ atom often coordinates with 3 or 4 oxygen atoms to create [BO3] or [BO4] structural units6.

Vanadium oxide, which has good mechanical and optical characteristics, is one of the newest compounds incorporated into the B2O3-based glass. Because they occur in glass networks simultaneously in various coordination’s (i.e., VO4andVO5) as well as different valence states, vanadium ions are the most studied7. The rate of electron hopping between ions is facilitated when vanadium ions are present in either of the two valence states, viz., V4+ or V5+, which eventually results in an increase in electrical conductivity8. Vanadium-containing glasses have numerous uses in memory, solid state batteries, and switching devices9. Because of their wide radial distribution of outer d-electron orbital functions and their extreme sensitivity to changes in the surrounding cations, transition metal ions are often employed in glass structure probes10. Applications for glasses containing V2O5 and B2O3 can be found in optoelectronics and memory switching devices11.

High refractive indexes, high polarizability, high density, high valence cation, strong nonlinear optical susceptibility, and excellent infrared transmission are characteristics of bismuth oxide12. Bi2O3 is not regarded as network-forming because Bi3+ ion has low field strength. However, a wide range of compositions may result in a high probability of glass formation when Bi2O3 and B2O3 are mixed to create bismuth-borate glasses.

When bismuth is in its monoclinic form, the octahedral adjustment of six oxygen atoms is positioned at an ionic radius of 2.14 to 2.29 Å, with three oxygen atoms being much closer, at around 2.29 Å.

The states of bismuth ions are Bi+,Bi3+, Bi4+ and Bi5+. Compared to other Bi cations, Bi3+ the cation exhibits more stability, which further qualifies the glass as a non-linear optical or photonic material with a high non-linear optical susceptibility13. Because of this, these glasses are important materials for low loss optical fibre14, processing devices15, and radiation shields16. Additionally, the glass matrix’s incorporation of zinc oxide reduces the band gap and raises the refractive index. Zinc oxide fills the gaps in the glass matrix to act as both a network former and a network modifier17. Numerous researchers are studying different characteristics of borate glasses with different oxides18–22.

The objective of the current study is therefore to study the influence of Bi2O3 content on the physical, structural, optical, and electrical properties of 10K2O–10ZnO–55B2O3–(25–x) V2O5–xBi2O3 glass systems. The concentration of Bi2O3 is limited from 4 to 10 mol% in the present glass system because the glass formation gets harder and becomes crystalline.

Experimental details

The preparation of samples

Five glass samples GBi1, GBi2, GBi3, GBi4 and GBi5 having chemical composition 10K2O–10ZnO–55 B2O3–(25–x) V2O5–x Bi2O3 (where x varies from 4 to 10 mol%) were fabricated by using melt-quenching technique. The chemical compositions of different glass samples fabricated along with their labels are listed in Table 1. Highly pure analytical grade K2CO3, ZnO, H3BO3, V2O5 and Bi2O3 chemicals were used as starting materials. The well ground mixture of chemicals in appropriate weight ratios were taken in porcelain crucibles and melted in an electrical muffle furnace at temperature 1250 ∘C. The melt was poured on a preheated stainless steel plate. The quenched samples were annealed at 450 ∘C for 3 h and then left in the furnace to cool down to room temperature to reduce the internal stress. These samples were cut and then will undergo polishing and grinding process to analyze the glass samples for its characteristics. Images of the glass samples are displayed in Fig. 1.Table 1 Chemical composition, density and molar volume of the prepared glasses.

Sample ID	Chemical composition (mol%)	Density (g/cm3)	Molar volume (mol/cm3)	Glass forming	
K2O	ZnO	B2O3	V2O5	Bi2O3	
GBi0	10	10	55	25	–	–	–	Crystallized	
GBi1	10	10	55	21	4	2.7878	40.4196	Glass	
GBi2	10	10	55	20	5	2.8789	40.1273	Glass	
GBi3	10	10	55	17.5	7.5	3.1418	39.0299	Glass	
GBi4	10	10	55	16	9	3.2738	38.7579	Glass	
GBi5	10	10	55	15	10	3.3617	38.5895	Glass	
GBi6	10	10	55	–	25	–	–	Crystallized	

Figure 1 Images of all the investigated glass samples.

Samples characterization

To confirm the amorphous nature of the prepared samples, X-ray patterns of the glass samples have been recorded by using a Rigaku Table-Top X-ray diffractometer with source Cu Ka radiation in the 2θ range 10°–80° at a scanning rate of 10 min.

The tightness, rigidity and structural changes of the obtained glass samples can be investigated through the measurement of the density (ρ) of glasses was measured at room temperature based on Archimedes methods and can be calculated by the following equation:1 p=m1m1-m2×p0

Where m1 is the weight of the sample in the air, m2 is the weight in distilled water, respectively, and ρ0 is the density of water (= 0.9989 g/cm3). The value of molar volume (Vm) is related to the compaction of the glass network and can be calculated as follows:2 Vm=∑xiMi/ρ

Where xi is the molar fraction, Mi is the molecular weight of component i.

Fourier transform infrared spectroscopy (FTIR) spectra of the glasses were recorded in the wavenumber range 400–4000 cm−1 using (Jasco-6100, Japan). The measurements were calculated using the KBr pellet technique.

Optical absorption measurements of the prepared samples were performed using a Cary series UV/Vis-spectrophotometer at room temperature in the range of 200–1100 nm.

The conductivity of the prepared samples was measured using Novocontrol Technologies, GmbH& Co. KG, high-resolution alpha analyser (0.1–20 MHz) in the temperature range 25–200 °C and stabilized with an accuracy of more than 0.1o Cusing Quattro temperature controllers employing pure nitrogen gas as the heating agent. The cell used was calibrated using standard materials (air, Trolitul and glass) with different thicknesses ranging from 1 mm up to 7 mm at 10 kHz with an LCR meter. Calibration curves were tested with two Teflon samples of different thicknesses, and it was found that the error in εʹ amounts to ± 2% and that the standard deviation amounts to 0.04.

Results and discussion

X-ray diffraction

Using X-ray diffraction data, the glassy phase of the manufactured glass systems is displayed in Fig. 2. The XRD analysis demonstrated the complete amorphous nature of each glass sample and the absence of a uniform atom arrangement that would have been present in a crystal case. Due to variations in interatomic distance, glasses exhibit a wide range peak, as seen by the emergence of a broad hump in the range of 20∘–40∘ for glass composition23,24. All of the glass samples are in the amorphous or non-crystalline phase, as demonstrated by this behavior. The ability of the borate glass networks to form glass was improved, and bulk glass samples were more transparent and clear as a result of the addition of Bi2O323–25.Figure 2 XRD patterns for all the compositions of glass samples (GBi1 –GBi5).

Density and molar volume characterization

Table 1 lists the density values (ρ) for each produced glass sample that was obtained. With the addition of bismuth oxide, the density values exhibit an increasing tendency in the following order: GBi1 < GBi2 < GBi3 < GBi4 < GBi5. This is because Bi2O3 has a high molecular weight and density(465.96 g/mol, 8.9 g cm−3) compared to V2O5 (181.88 g/mol, 3.36 g cm−3), the density increased from 2.7878 to 3.3617 g cm−3 as expected with the substitution of V2O5 with Bi2O326. In the meantime, the molar volume value and the density measurement typically behave in opposite directions. In contrast to the observed density, this investigation showed that the molar volume (Vm) decreases in the order GBi1 > GBi2 > GBi3 > GBi4 > GBi5. Figure 3 shows the molar volume and experimental density of the produced glasses as a function of the Bi2O3 content. Finally, it's possible that Bi2O3 functions as a network modifier, forming non-bridging oxygen’s (NBO’s) atoms that alter the borate glass's structural composition. The concentration of non-bridging oxygens in the glass network increases when the bismuth oxide replaces the vanadium oxide, converting the [BO3] structural units into [BO4] structural units27–29.Figure 3 Density and molar volume as a function of Bi2O3 content in glass samples.

Fourier transforms infrared spectroscopy studies (FTIR)

In order to investigate how the interactions between the different atoms in the samples affected their structure, infrared spectroscopy was employed. Table 2 displays the band positions and peak assignments of the FTIR spectra that were obtained for each produced glass within a 4000–400 cm−1 spectral range, as depicted in Fig. 4.Table 2 Infrared wavenumber and assignments of vibrational modes of 10K2O–10ZnO–55 B2O3–(25–x) V2O5– x Bi2O3 glass systems.

Wavenumber (cm−1)	IR band assignments	
470	Bi–O bending vibrations in BiO6 and/or BiO3 units / Bending of BO4 units	
542	Bending modes of V–O–V bonds and/or Bi–O / Bi–O–Bi stretching vibrations of [BiO6] octahedral structural units	
699	B–O–B bending vibrations BO3 groups in borate network	
930	Stretching vibrations of tetrahedral BO4 units / V=O vibration of [VO5] vanadium group	
1005	B–O stretching vibrations of tetragonal [BO4] units in tri-, tetra- and penta- borate groups	
1267	B–O stretching vibrations of trigonal [BO3] units from boroxol rings with non-bridging oxygen atoms	
1378	Asymmetric B–O stretching vibrations of trigonal [BO3]3− units in meta-, pyro-, and ortho-borate groups	

Figure 4 FTIR spectra of present glasses as a function of Bi2O3 mol%.

The glass network contains a variety of links and vibrational modes. Three basic groups are present in the vibrational modes of borate glass: (600–800) cm−1, (800–1200) cm−1, and (1200–1600) cm−1. In triangular BO3 structural units, the bending vibrations of the B–O–B and the stretching vibrations of the B–O bond are often associated with the first and third absorption regions. However, the second region is caused by the stretching vibrations of the tetrahedral BO4 structural units30.

The well-defined peaks in the infrared spectra located at 470 cm−1 are due to the vibration in the local symmetry of highly distorted BiO6 polyhedral units and/or BiO3 units and/or bending of BO4 units31,32. Another IR peak at 542 cm−1 may be attributed to Bi–O and Bi–O–Bi stretching vibrations of [BiO6] octahedral structural units and/or bending vibration of the V–O–V bond33,34. The BiO3 polyhedra vibration band does not show in the IR absorption35. Therefore, the bismuth structure that exists in the glasses is solely attributed to the [BiO6] octahedral units.

In the borate network, the absorption band detected at 699 cm−1 is connected with B–O–B bending vibrations of BO3 groups36,37. The combination of the V=O vibration of the [VO5] vanadium group and the stretching vibration of the B–O bond in the [BO4] tetrahedral units is responsible for the absorption peak at 930 cm−138,39.

This band obviously changes towards longer wave numbers as a result of the [VO4] groups becoming [VO5] groups40. The absorption band observed at 1005 cm−1 is related to B–O stretching vibrations of tetragonal [BO4] units in tri-, tetra- and penta-borate groups41,42. Absorption peaks at around 1267 cm−1 are produced by the B–O stretching vibrations of trigonal [BO3] units from boroxol rings containing non-bridging oxygen atoms43,44.

Trigonal [BO3] units in the meta-, pyro-, and ortho-borate groups have asymmetric B–O stretching vibrations, which are linked to the absorption band found at 1378 cm−145,46.

However, the absence of the distinctive 800 cm−1 boroxol ring band, which is typically present for borate networks, suggests that there are no boroxol rings in the borate network. As a result, BO3 and BO4 structural groups make up the majority of the glass samples47. In these compositions, bismuth is expected to function as a network modifier. The BO3 triangle's structure, however, changed as the content of Bi2O3 increased to produce the BO4 tetrahedral, which is close to the energy needed to break B–O–B bridges and form non-bridging oxygen and forms different kinds of structural units48.

Optical properties

UV–visible analysis

One effective method for examining the electrical structures of amorphous semiconductors is the examination of optical absorption spectra49. The UV–visible absorption spectra of the glass samples with different Bi2O3 contents are shown in Fig. 5 in the wavelength range of 200–1100 nm. The bandgap, oxygen deprivation, surface roughness, and impurity centres are some of the variables that affect absorbance50. A straight line was drawn to determine the cut-off wavelength (λC), and after the line crossed the wavelength axis, the cut-off wavelength was selected51.Figure 5 Optical absorption spectra of glass series.

The studied samples exhibited an increase in absorbance in the visible region upon increasing the Bi2O3 content. Tetravalent V3+ ions are exactly attributed to the absorption band at 597 nm. It is believed that V3+ ensures three spin-allowed absorption transitions in tetrahedral and octahedral coordination. In oxide glasses, V3+ cause absorption bands that represent the transitions from 3T1g (F) to 3T2g and 3T1g (P) states, respectively52.

It has been observed that as the amount of Bi2O3 in borate glass structures increases, the optical absorption cut-off wavelength shifts from a lower wavelength to a higher wavelength value. As indicated in Table 3, the optical cut-off wavelength of the glasses under study has been moved from 472 to 521 nm. Because of the gradual formation of NBOs in the glass networks, the altered behavior of the absorption cut-off wavelength can be linked to reduced glass structure stiffness. Glass networks are degraded because non-bridging oxygen electron bonding is less tightly bound than bridging oxygen bonding53. Consequently, a decrease in the optical band gap energy would result from the breaking down of the BO's bond and a shift in the absorption edge to a longer wavelength.Table 3 Cutoff wavelength (λc), optical band gap energy Eopt (direct), optical band gap energy Eopt (indirect) and Urbach energy (∆E) of the prepared glasses.

Sample ID	Cut-off wavelength(λc), nm	Eopt (direct), eV	Eopt (indirect), eV	∆E, eV	
GBi1	472	2.7984	2.3627	0.743	
GBi2	488	2.7036	2.3139	0.814	
GBi3	537	2.5444	2.2127	0.830	
GBi4	502	2.6087	2.2573	0.526	
GBi5	521	2.5230	2.1634	0.687	

Glass’s band gap energy is determined by analyzing its UV absorption edge. To get the absorption coefficient α (ν) close to the spectrum edge, use Eq. (3)54:3 αv=2.303A/d

where d represents the glass sample's thickness and A its absorbance. Davis and Mott55 report that optical absorption of amorphous materials occurs above the exponential tail with a larger value of α (ν), following a power law expressed by Eq. (4):4 αvhv=Bhv-Eoptn

where hυ is the incident photon energy, α (ν) is the optical absorption coefficient, B is constant, n is the index that is defined by the type of electronic transitions that occur during the absorption process, and Eopt is the optical band gap energy between the valence band and the conduction band. The value of n can be either n = 1/2 and n = 3/2 for direct allowed and direct forbidden transitions or n = 2 and n = 3 for indirect allowed and indirect forbidden transition.

Plotting (αhυ)0.5 and (αhυ)2 vs the photon energy (hυ), Eq. (4) was used in this work to calculate the indirect and direct allowable optical energy band gap, or Eopt, for glass samples. It is possible to calculate the optical energy band gap by extrapolating the linear portion of the observed curves to lower energy. Table 3 provides a summary of the relationship between Eopt values and Bi2O3content for both direct and indirect transitions, as illustrated in Figs. 6 and 7, respectively.

In borate glass systems, the optical energy gap (Eopt) takes values between 2.7984 and 2.5230 eV in the case of a direct transition (Fig. 6), and ranges from 2.3627 to 2.1643 eV for an indirect transition (Fig. 7). Essentially, the changes in structure within the networks of borate glass are causing the optical band gap to decrease, as previously determined by researchers56,57.Figure 6 (αhν)2 as function of photon energy hν of glass samples (direct transition).

Figure 7 (αhν)0.5 as function of photon energy hν of glass samples (indirect transition).

By producing a concentration of NBO, the replacement of Bi2O3, which acts as a glass modifier, would disrupt the regular structure of borate glass networks, making the glass structure more random58. However, it is also thought that because Bi2O3 elements are highly polarizable and easily deformed by cations, as cation concentrations increase, the bridging oxygen will form a bond with Bi3+ ions and the glass networks will gradually break down59. The concentration of non-bridging oxygens (NBOs) is often increased by an increase in the network modifier concentration, and states originating from NBOs are easier to excite than ones originating from bridging oxygen atoms. As a result, the optical band gap reduces60.

An essential parameter that indicates the degree of disorder in amorphous materials is the Urbach energy (∆E). Following the empirical Urbach rule, the relationship between Urbach energy (∆E) and absorption coefficient α (v) is given61:5 αv=Bexphv/ΔE

where B is constant and ∆E is Urbach energy, which corresponds to the width of the band tails of localized state. The relation can be rewritten as:6 Inαv=hv/ΔE+constant

Urbach energy values for the glass samples are listed in Table 3, and the values of ΔE were computed by taking the reciprocals of the slopes of the linear portion in the low photon energy region of ln(α) versus hν plot (not shown). Also, the tails are affected by the disorder level and the structure of the sample62.

Some other optical parameters

The Dimitrov-Sakka relation can be used to calculate the refractive index from optical band gap energy63.7 n2-1n2+2=1-Eopt20

where Eopt is optical band gap energy and n is the refractive index. Because glasses are amorphous by nature, most indirect transitions occur as a result of the electrons' undefined momentum. For this reason, the refractive index is only determined via indirect bandgap energy. Table 4 shows that there is a slight increase in refractive index with increasing Bi2O3 content, ranging from 2.5939 to 2.6686. Since non-bridging oxygens are more polarizable than bridging oxygens, this kind of increase may be explained by an increasing amount of these oxygens. The glass structure is changed by the non-bridging oxygens, making the molecular packing denser. The reason for this denser packing is that more network modifiers are occupied at intestinal sites. Given that a glass system's refractive index and density are closely correlated, a glass with a higher density will also have a higher refractive index64.Table 4 Optical parameters of the studied glasses.

Sample ID	Refractive Index, (n)	Molar refraction, (Rm) (cm3/mol)	Metallization criterion, (M)	Optical electronegativity, (χ)	Dielectric constant, (ε)	Optical dielectric constants, (εopt)	Optical polarizability, (α0)	
GBi1	2.5939	26.5270	0.3437	0.6351	6.7283	5.7283	2.9284	
GBi2	2.6115	26.4784	0.3401	0.6220	6.8199	5.8199	2.9402	
GBi3	2.6494	26.0478	0.3326	0.5948	7.0193	6.0193	2.9647	
GBi4	2.6325	25.7374	0.3359	0.6068	6.9300	5.9300	2.9539	
GBi5	2.6686	25.8976	0.3289	0.5815	7.1214	6.1214	2.9766	

Lorentz–Lorentz provides the correlation between molar refractivity (Rm) and molar volume65.8 Rm=n2-1n2+2Vm

Molar refractivity values have opposite trends in the optical energy and its values decrease from 26.5270 to 25.8976. Also, molar refractivity is essential for understanding and predicting a material's conduction behavior.

Glass is determined to be metallic or insulator by calculating the metallization criterion (M), which takes into consideration the ratio of Rm/Vm and can be stated as follows66.9 M=1-RmVm

Herzfeld's metallization theory67 specifies the criteria for classifying solids as either non-metallic (Rm/Vm < 1) or metallic (Rm/Vm ≥ 1) depending on their characteristics. The calculated values of M are listed in Table 4. If metallization criterion reaches to 1 means the materials are becoming insulators, instead if it reaches to 0 the materials becoming conductors66. The glasses under investigation show a greater tendency towards metallization as determined by the criterion of small metallization (Rm/Vmis large). The obtained optical band gap energy measurements are in agreement with the results of the metallization criteria68.

The refractive index was used to compute the dielectric constants and optical dielectric constants of the prepared samples, as indicated by the following expressions:10 ε=n2

11 εopt=ε-1

The empirical formulas were used to calculate characteristics like electronegativity (χ) and optical polarizability (α0)69.12 X=0.2688∗Eopt

13 α0=-0.9x+3.5

One property of oxide glasses called electronegativity shows how strongly an ion may bind electrons. There is weaker bonding across ion networks as a result of the ions' reduced electronegativity, which causes them to attract adjacent oxide ions less strongly68. The values of the optical polarizability of the prepared glasses increased from 2.9284 to 2.9766 due to a decrease in electronegativity (χ). These parameter values are listed in Table 4.

Electrical properties

Ac-conductivity

Studying the behavior of alternating-current conductivity (σac) of the prepared glasses is very important to determine the extent of the glasses to conduction under the effect of an electric field. Ac-conductivity of different glass compositions GBi1, GBi2, GBi3, GBi4, and GBi5 over the frequency region 10−1–106 Hz at room temperature are shown in Fig. 8a.Figure 8 (a) The frequency dependence of ac conductivity (σac) for glasses (GBi1-GBi5), (b) The Bi2O3 content dependence of exponent factor s.

The frequency (f) dependence of Ac-conductivity (σac) is usually expressed by the following Jonscher relation Eq. (14) and Almond-West formalism Eq. (15)70,71:14 σac=σdc+Aωs

15 σtotalω=σdc[1+ωωH]s

Where ω represents the frequency and equals to 2πf and called as the angular frequency, s is the frequency-exponent which have values (0 < s ≤ 1), σdc is the dc-conductivity, A is a constant, and ωH is the crossover frequency which indicates the frequency at which the frequency-independent region separates from the dispersion conductivity region. Figure 8a shows a delay in the values of σac with decreasing the frequency due to the presence of free charge carriers at the electrode surface that causes electrode polarization (EP)72. At very low frequency values, the conductivity attains nearly constant value which is attributed to the dc-conductivity (σdc) which originated from the jumping of ions to the adjacent vacant site or from the diffusion of the ionic charge carriers73. In our samples, the reason of this conduction is mainly due to the electron transfer through V4+-O-V5+74. The data of Fig. 8a was non-linearly fitted by Almond-West formalism and the parameters of the fitting were listed in Table 5. As listed in the table, the values of σdc are ranging from 10−6–10−9 S cm−1, which in agreement with the behavior of glasses contains transition metal where the electronic conductivity of these glasses is predominant74. The estimated values of s are used to define the mechanism by which the charge transferred75–77. As shown from Table 5, s < 1 indicates that the conduction occurs through hopping of charges between two potential barrier sites78,79.Table 5 DC conductivity (σdc), crossover frequency (ωH) and frequency factor (s) of the glasses synthesized in the system.

Sample ID	σdc, S cm−1	ωH	s	
GBi1	5.6 × 10−9	2.6	0.80	
GBi2	1.1 × 10−6	19.2	0.83	
GBi3	1.8 × 10−7	10.7	0.93	
GBi4	8.1 × 10−8	11.2	0.85	
GBi5	1.1 × 10−8	3.2	0.87	

The conductivity increases with increasing the frequency which indicates the semiconductor character of the examined samples, it also increases as the amount of Bi2O3 in borate glass structures increases due to the presence of two oxidation state of Bi3+ and Bi5+ that share in the jumping process where one of them plays as a donor and the other as acceptor, respectively80. The presence of Bi in the structure of glass containing transition metal (V) can lead to decrease the bond distance in V–O–V that leads to increase in the V5+/V4+ ratio81–83. In addition to the production of the tetrahedral BO4 increases by increasing the Bi2O3 content that results in increasing the donner Bi3+ and the formation of non-bridging oxygen as discussed in the IR results. Also, the presence of shift in the wave number of [VO4] towards longer wave numbers indicates its change to the trigonal bipyramids [VO5] groups40.

It is worth to mention that the values of conductivity for all the samples are ranging from ~ 10−8 at low frequency to ~ 10−2 at high frequency that specifies the semiconductor character of the samples. The s values were drawn as a function of the Bi2O3 content in borate glass as shown in Fig. 8b, where s increases with increasing Bi content till 7.5% then decreases but still its value > GBi1, this behavior is due to the formation of NBO with the increase in Bi2O3 content, while the decrease of s value for Bi2O3 content > 7.5% may be because of the disturbance in the NBO in glasses84.

The permittivity and dielectric loss

To identify the stored energy in the studied glasses under the effect of electric current, the real part of the dielectric constant (permittivity) (ε') was measured.

The frequency dependence of ε' for the studied glasses is shown in Fig. 9a, it is noted that ε' is affected by both the composition of the glasses and the frequency of the electric field, it increases with increasing the Bi2O3 content due to the increase of both polarizability of glass and nonbridging oxygen (NBO)85. For all the studied glass compositions, it attains high value at low frequency due to the presence of different kinds of polarization such as the space charge and the dipole polarizations86. As the glass is amorphous, therefore there is a defect in its bulk interface that results in transferring the space charges at the presence of an electric field. Therefore, the predominant polarization of glass in low frequency values is space charge polarization87,88. Then, a gradual decrease in ε' was observed with raising the frequency due to the dielectric relaxation phenomenon that happened because of the instability of the localization of charge carrier localization under the electric field effect89. At frequency > 104 Hz, unchanged ε' value is achieved indicating the independence of ε' on the electric field.Figure 9 The frequency dependence of (a) dielectric constant (εʹ), (b) dielectric loss (tanδ) for the glass samples (GBi1-GBi5).

To recognize the dissipated of energy in the studied glasses, the tangent loss (tanδ) was calculated from the dielectric loss (ε'') and ε' as the following equation:16 tanδω=ε′′ε′

Figure 9(b) shows the change in tanδ with frequency for the studied glass samples, which looks like the change of ε' with frequency. At low frequency, tanδ have high values that decreases gradually as the frequency increases till 100 Hz, after that it reaches nearly constant, then a relaxation peak is observed at nearly 31.6 kHz which may be dipolar relaxation. It was also noted that tanδ decreased with increasing Bi2O3 content and GBi2 achieves the highest value of dielectric constant and the lowest value of dielectric loss.

Impedance measurements

The measurement of impedance for the studied samples is represented by the Nyquist plots that give how can the real part of impedance changed with the imaginary parts at room temperature are shown in Fig. 10. This relation can help in understanding the role of the microscopic elements of the material, such as the grain, electrode effect, and relaxation process90. Inclined lines tend to bend at the x-axis to shape as semi-circles that interrelated to the capacitance and resistance of the bulk were observed in the figure. The angle by which the line is inclined decreases with increasing the Bi2O3 content that means the semicircle radius reduces that indicates the increase in the conductivity of the bulk with Bi2O3 concentration rising. This behavior is coincidence with the conductivity measurements. As the semicircle is asymmetric (depressed), therefore a deviation from Debye relaxation occurs that may be due to different factors such as the dipole groups formation, a defect in the atomic distribution and formation of nonpolar clusters91. Grain orientation, defect in the atomic distribution of the grain boundaries and the stress strain in the glass materials are from the factors that causes this nonideal behavior. However, the presence of one semicircle reveals that the glass system conducting behavior comes mainly from the grains rather than the grain boundaries92.Figure 10 Nyquist plots for the glass samples (GBi1-GBi5) at room temperature.

The electrical modulus analysis

To investigate the relaxation process and to understand the response of the bulk, the variation of the real part of electric modulus Mʹ, and its imaginary part M″ with the frequency was investigated as in Fig. 11a,b. Low values of M' were observed at low frequency, then a gradual enhancement in Mʹ occurred and went to higher values with rising the frequency, then accomplished maximum value at f > 20 Hz. This behavior demonstrates the dispersion of the relaxation processes along all the studied frequency range93. The mobility of the charge carriers is the reason for the increase in M′, where the effect of the electric field on their mobility is restricted94.Figure 11 The frequency dependence of (a) M′ (real part), (b) M″ (imaginary part) of electric modulus for the glass samples (GBi1-GBi5).

The behavior of changing M″ with frequency (Fig. 11b) shows an indication of a peak at low frequencies and its position changed to lower values of frequency as the Bi2O3 content increases which directs the involvement of dc-conductivity95,96. Another peak with lower height is observed at high frequency and its height reduces with high Bi2O3 content (inset Fig. 11b). Control in the charge carriers occurred between the two peaks.

Conclusions

In this study, potassium–zinc–borovanadate glass containing different concentrations of bismuth oxide was examined with respect to physical, structural, optical, and electrical properties. To achieve this, a new glass series with composition 10K2O–10ZnO–55B2O3– (25–x) V2O5– x Bi2O3 (x: 0, 4, 5, 7.5, 9, 10 mol%) was synthesized using the traditional melt-quenching route. A broad peak was identified by analyzing the XRD pattern of the samples, indicating that they are non-crystalline or amorphous in nature. Various physical characteristics were identified, including density and molar volume. The density of the glass samples increases with an increase in the content of Bi2O3 and causes a corresponding decrease in the molar volume. The glasses' UV–VIS spectra demonstrate that the addition of Bi2O3 caused the absorption edge to move towards a higher wavelength. Additionally, the glasses' direct and indirect optical band gaps showed a tendency to decrease upon the addition of Bi2O3 and the enhancement in Urbach energies (ΔE) of glasses. The development of non-bridging oxygen in the glass system is responsible for this, due to an increase in BiO6 octahedral units, as observed from FTIR analysis. The metallization criteria (M) indicate that the glasses have a greater tendency towards metallization. Both the conductivity and the dielectric constant increase with the rise in Bi2O3 content due to increasing the polarizability and NBO; however, the dielectric loss and the impedance reduce. The values of conductivity for the studied glasses ranged from ~ 10−8 to ~ 10−1. The produced glass samples may be employed as amorphous semiconductors in electronics and memory switching devices.

Author contributions

SI: conceptualization, methodology, validation, investigation, data curation, writing—original draft, and writing—review and editing. AMF: conceptualization, validation, investigation, data curation, writing—original draft, and writing—review and editing. AAA: conceptualization, methodology, validation, investigation, data curation, writing—original draft, and writing—review and editing.

Funding

Open access funding provided by The Science, Technology & Innovation Funding Authority (STDF) in cooperation with The Egyptian Knowledge Bank (EKB).

Data availability

The datasets used and/or analyzed during the current study available from the corresponding author on reasonable request.

Competing interests

The authors declare no competing interests.

Publisher's note

Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
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References

1. Effendy N Zaid MHM Sidek HAA Halimah MK Shabdin MK Yusof KA Mayzan MZH The elastic, mechanical and optical properties of bismuth modified borate glass: Experimental and artificial neural network simulation Opt. Mater. 2022 126 112170 10.1016/j.optmat.2022.112170
Effendy, N. et al. The elastic, mechanical and optical properties of bismuth modified borate glass: Experimental and artificial neural network simulation. Opt. Mater. 126, 112170 (2022).10.1016/j.optmat.2022.112170
2. Rani A Parmar R Kundu RS Structural, physical and optical study of calcium modified bismuth borovanadate glasses: V2O5-B2O3-Bi2O3-CaO Opt. Mater. 2023 143 114135 10.1016/j.optmat.2023.114135
Rani, A., Parmar, R. & Kundu, R. S. Structural, physical and optical study of calcium modified bismuth borovanadate glasses: V2O5-B2O3-Bi2O3-CaO. Opt. Mater. 143, 114135 (2023).10.1016/j.optmat.2023.114135
3. Madhu A Joseph CM Dadami ST Srinatha N Structural and spectroscopic studies of V2O5 incorporated lithium-bismuth-boro-tellurite glass ceramics Mater. Today Proc. 2022 62 5489 5493 10.1016/j.matpr.2022.04.154
Madhu, A., Joseph, C. M., Dadami, S. T. & Srinatha, N. Structural and spectroscopic studies of V2O5 incorporated lithium-bismuth-boro-tellurite glass ceramics. Mater. Today Proc. 62, 5489–5493. 10.1016/j.matpr.2022.04.154 (2022).10.1016/j.matpr.2022.04.154
4. Kamath SD Wagh A Ajithkumar MP Composition dependent structural and thermal properties of Sm2O3 Doped zinc fluoroborate glasses Energy Res. J. 2013 4 2 52 58 10.3844/erjsp.2013.52.58
Kamath, S. D., Wagh, A. & Ajithkumar, M. P. Composition dependent structural and thermal properties of Sm2O3 Doped zinc fluoroborate glasses. Energy Res. J. 4(2), 52–58 (2013).10.3844/erjsp.2013.52.58
5. Deopa N Rao AS Spectroscopic studies of Sm3+ ions activated lithium lead alumino borate glasses for visible luminescent device applications Opt. Mater. 2017 72 31 39 10.1016/j.optmat.2017.04.067
Deopa, N. & Rao, A. S. Spectroscopic studies of Sm3+ ions activated lithium lead alumino borate glasses for visible luminescent device applications. Opt. Mater. 72, 31–39 (2017).10.1016/j.optmat.2017.04.067
6. Purnima M Stalin S Edukondalu A Samee MA Ahmmad SK Rahman S Spectroscopic studies on Li2O–MgO–Bi2O3–B2O3 glasses Chin. J. Phys. 2020 66 517 526 10.1016/j.cjph.2020.05.031
Purnima, M. et al. Spectroscopic studies on Li2O–MgO–Bi2O3–B2O3 glasses. Chin. J. Phys. 66, 517–526 (2020).10.1016/j.cjph.2020.05.031
7. Dalal S Khasa S Dahiya MS Agarwal A Seth VP Dahiya S Effect of substituting iron on structural, thermal and dielectric properties of lithium borate glasses Mater. Res. Bull. 2015 70 559 566 10.1016/j.materresbull.2015.05.017
Dalal, S. et al. Effect of substituting iron on structural, thermal and dielectric properties of lithium borate glasses. Mater. Res. Bull. 70, 559–566 (2015).10.1016/j.materresbull.2015.05.017
8. Khasa S Yadav A Dahiya MS Seema A Agarwal A Effect of mixed transition metal ions on DC conductivity in lithium bismuth borate glasses AIP Conf. Proc. 2015 10.1063/1.4917877
Khasa, S., Yadav, A., Dahiya, M. S., Seema, A. & Agarwal, A. Effect of mixed transition metal ions on DC conductivity in lithium bismuth borate glasses. AIP Conf. Proc.10.1063/1.4917877 (2015).10.1063/1.4917877
9. Rocha MVJ Carvalho HWP Lacerda LCT Simoes G de Souza GGB Ramalho TC Ionic desorption in PMMA–gamma-Fe2O3 hybrid materials induced by fast electrons: An experimental and theoretical investigation Spectrochim. Acta. A 2014 117 276 283 10.1016/j.saa.2013.08.029
Rocha, M. V. J. et al. Ionic desorption in PMMA–gamma-Fe2O3 hybrid materials induced by fast electrons: An experimental and theoretical investigation. Spectrochim. Acta. A 117, 276–283 (2014).10.1016/j.saa.2013.08.029
10. Hassan MA Farouk M Abdullah AH Kashef I ElOkr MM ESR and ligand field theory studies of Nd2O3 doped borochoromate glasses J. Alloys Compd. 2012 539 233 236 10.1016/j.jallcom.2012.06.060
Hassan, M. A., Farouk, M., Abdullah, A. H., Kashef, I. & ElOkr, M. M. ESR and ligand field theory studies of Nd2O3 doped borochoromate glasses. J. Alloys Compd. 539, 233–236. 10.1016/j.jallcom.2012.06.060 (2012).10.1016/j.jallcom.2012.06.060
11. Gosh A Memory switching in bismuth-vanadate glasses J. Appl. Phys. 1998 64 2652 2655 10.1063/1.341605
Gosh, A. Memory switching in bismuth-vanadate glasses. J. Appl. Phys. 64, 2652–2655. 10.1063/1.341605 (1998).10.1063/1.341605
12. Ardelean I Cora S Lucacel RC Hulpus O EPR and FT-IR spectroscopic studies of B2O3-Bi2O3-MnO glasses Solid State Sci. 2005 7 11 1438 1442 10.1016/j.solidstatesciences.2005.08.017
Ardelean, I., Cora, S., Lucacel, R. C. & Hulpus, O. EPR and FT-IR spectroscopic studies of B2O3-Bi2O3-MnO glasses. Solid State Sci. 7(11), 1438–1442. 10.1016/j.solidstatesciences.2005.08.017 (2005).10.1016/j.solidstatesciences.2005.08.017
13. Bala R Agarwal A Sanghi S Singh N Effect of Bi2O3 on nonlinear optical properties of ZnO.Bi2O3.SiO2 glasses Opt. Mater. 2013 36 352 356 10.1016/j.optmat.2013.09.021
Bala, R., Agarwal, A., Sanghi, S. & Singh, N. Effect of Bi2O3 on nonlinear optical properties of ZnO.Bi2O3.SiO2 glasses. Opt. Mater. 36, 352–356 (2013).10.1016/j.optmat.2013.09.021
14. Torrengo S Paul MC Halder A Das S Dhar A Sahu JK Jain S Kir’yanov AV d’Acapito F EXAFS studies of the local structure of bismuth centers in multicomponent silica glass based optical fiber preforms J. Non-Cryst. Solids 2015 410 82 87 10.1016/j.jnoncrysol.2014.11.027
Torrengo, S. et al. EXAFS studies of the local structure of bismuth centers in multicomponent silica glass based optical fiber preforms. J. Non-Cryst. Solids 410, 82–87 (2015).10.1016/j.jnoncrysol.2014.11.027
15. Aitken, B.G., Badding, M. E., Borrelli, N. F., Lonnroth, N. T. & Quesada, M. A. U.S. Patent and Trademark Office, Washington. U.S. Patent No. 9,011,720, (2015).
16. Saddeek YB Mohamed GY Hassan HS Mostafa AMA Abdelfadeel G Effect of gamma irradiation on the FTIR of cement kiln dust–bismuth borate glasses J. Non-Cryst. Solids 2015 419 110 117 10.1016/j.jnoncrysol.2015.03.021
Saddeek, Y. B., Mohamed, G. Y., Hassan, H. S., Mostafa, A. M. A. & Abdelfadeel, G. Effect of gamma irradiation on the FTIR of cement kiln dust–bismuth borate glasses. J. Non-Cryst. Solids 419, 110–117 (2015).10.1016/j.jnoncrysol.2015.03.021
17. Kumari S Yadav S Mohan D Nonlinear optical characterization of zinc doped tellurite glasses for optical limiting performance Optik 2021 228 166193 10.1016/j.ijleo.2020.166193
Kumari, S., Yadav, S. & Mohan, D. Nonlinear optical characterization of zinc doped tellurite glasses for optical limiting performance. Optik 228, 166193 (2021).10.1016/j.ijleo.2020.166193
18. Kolavekar SB Ayachit NH Rajaramakrishna R Pramod NG J Kaewkhao, Reddish-orange emission and Judd-Ofelt investigation of Sm3+ ions doped in zince-bismuth-phospho-tellurite glasses for solid lighting application J. Lumin. 2020 226 117498 10.1016/j.jlumin.2020.117498
Kolavekar, S. B., Ayachit, N. H., Rajaramakrishna, R., Pramod, N. G. & J,. Kaewkhao, Reddish-orange emission and Judd-Ofelt investigation of Sm3+ ions doped in zince-bismuth-phospho-tellurite glasses for solid lighting application. J. Lumin. 226, 117498 (2020).10.1016/j.jlumin.2020.117498
19. Kolavekar SB Hiremath GB Badiger NM Ayachit NH Investigation of the influence of TeO2 on the elastic and radiation shielding capabilities of phosphot-tellurite glasses doped with Sm2O3 Nucl. Sci. Eng. 2023 197 7 1506 1519 10.1080/00295639.2022.2149232
Kolavekar, S. B., Hiremath, G. B., Badiger, N. M. & Ayachit, N. H. Investigation of the influence of TeO2 on the elastic and radiation shielding capabilities of phosphot-tellurite glasses doped with Sm2O3. Nucl. Sci. Eng. 197(7), 1506–1519 (2023).10.1080/00295639.2022.2149232
20. Sangeeta B KolavekarAyachit NH Impact of variation of TeO2 on the thermal properties of lead borate glasses doped with Pr2O3 Eur. Phys. J. Plus 2022 137 4 1 8 34909366
Sangeeta, B. & KolavekarAyachit, N. H. Impact of variation of TeO2 on the thermal properties of lead borate glasses doped with Pr2O3. Eur. Phys. J. Plus 137(4), 1–8 (2022).34909366
21. Sangeeta B KolavekarAyachit NH Ionic conductivity and dielectric relaxations in Li+ ions doped zinc borate glass system ECS J. Solid State Sci. Technol. 2022 11 10 10300 10.1149/2162-8777/ac942d
Sangeeta, B. & KolavekarAyachit, N. H. Ionic conductivity and dielectric relaxations in Li+ ions doped zinc borate glass system. ECS J. Solid State Sci. Technol. 11(10), 10300. 10.1149/2162-8777/ac942d (2022).10.1149/2162-8777/ac942d
22. Kolavekar SB Ayachit NH Vinayak PattarAnavekar RV Transport properties of phospho-vanadate glasses containing bismuth AIP Conf. Proc. 2016 1731 1 070029 10.1063/1.4947861
Kolavekar, S. B., Ayachit, N. H. & Vinayak PattarAnavekar, R. V. Transport properties of phospho-vanadate glasses containing bismuth. AIP Conf. Proc. 1731(1), 070029 (2016).10.1063/1.4947861
23. Kaur P Singh KJ Thakur S Singh P Bajwa BS Investigation of bismuth borate glass system modified with barium for structural and gamma-ray shielding properties Spectrochim. Acta. Pt. A-Mol. Biomol. Spectrosc. 2019 206 367 377 10.1016/j.saa.2018.08.038
Kaur, P., Singh, K. J., Thakur, S., Singh, P. & Bajwa, B. S. Investigation of bismuth borate glass system modified with barium for structural and gamma-ray shielding properties. Spectrochim. Acta. Pt. A-Mol. Biomol. Spectrosc. 206, 367–377. 10.1016/j.saa.2018.08.038 (2019).10.1016/j.saa.2018.08.038
24. Devaraja C Gowda GVJ Eraiah B Keshavamurthy K Optical properties of bismuth tellurite glasses doped with holmium oxide Ceram. Int. 2021 47 7602 7607 10.1016/j.ceramint.2020.11.099
Devaraja, C., Gowda, G. V. J., Eraiah, B. & Keshavamurthy, K. Optical properties of bismuth tellurite glasses doped with holmium oxide. Ceram. Int. 47, 7602–7607. 10.1016/j.ceramint.2020.11.099 (2021).10.1016/j.ceramint.2020.11.099
25. Gaikwad DK Sayyed MI Botewad SN Obaid SS Khattari ZY Gawai UP Afaneh F Shirshaf MD Pawar PP Physical, structural, optical investigation and shielding features of tungsten bismuth tellurite based glasses J. Non-Cryst. Solids 2019 503–504 158 168 10.1016/j.jnoncrysol.2018.09.038
Gaikwad, D. K. et al. Physical, structural, optical investigation and shielding features of tungsten bismuth tellurite based glasses. J. Non-Cryst. Solids 503–504, 158–168. 10.1016/j.jnoncrysol.2018.09.038 (2019).10.1016/j.jnoncrysol.2018.09.038
26. Sangeeta B Ayachit KNH Synthesis of praseodymium trioxide doped lead-boro-tellurite glasses and their optical and physical properties J. Materiomics 2019 5 3 455 462. 10.1016/j.jmat.2019.01.010
Sangeeta, B. & Ayachit, K. N. H. Synthesis of praseodymium trioxide doped lead-boro-tellurite glasses and their optical and physical properties. J. Materiomics 5(3), 455-462. (2019).10.1016/j.jmat.2019.01.010
27. Chauhan S Bala R Gaur S Rani S Effect of Bi2O3 on structural and optical properties of Li2O-PbO-Bi2O3-B2O3 glasses J. Mater. Sci. Mater. Electron. 2022 33 22835 22850 10.1007/s10854-022-09050-7
Chauhan, S., Bala, R., Gaur, S. & Rani, S. Effect of Bi2O3 on structural and optical properties of Li2O-PbO-Bi2O3-B2O3 glasses. J. Mater. Sci. Mater. Electron. 33, 22835–22850 (2022).10.1007/s10854-022-09050-7
28. Kavita Hanamar BG Hegde SBK Ayachit NH Pramod AG Keshavamurthy K Anandalli MH Bhajantri RF Physical, structural, and photoluminescence characteristics of Sm2O3 doped lithium zinc borate glasses bearing large concentrations of modifier J. Inorg. Organomet. Polym. Mater. 2023 33 6 1612 1620 10.1007/s10904-023-02585-0
Kavita Hanamar, B. G. et al. Physical, structural, and photoluminescence characteristics of Sm2O3 doped lithium zinc borate glasses bearing large concentrations of modifier. J. Inorg. Organomet. Polym. Mater. 33(6), 1612–1620 (2023).10.1007/s10904-023-02585-0
29. Sangeeta D Kolavekar B Ayachit NH Density and molar volume of bismuth oxide doped lithium lead borate glass system J. Phys. Conf. Ser. 2020 10.1088/1742-6596/1455/1/012018
Sangeeta, D., Kolavekar, B. & Ayachit, N. H. Density and molar volume of bismuth oxide doped lithium lead borate glass system. J. Phys. Conf. Ser.10.1088/1742-6596/1455/1/012018 (2020).10.1088/1742-6596/1455/1/012018
30. Vassilev T Penkov I Tzvetkova C Pascova R Glass transition temperatures and structures of multicomponent borate glasses: Influence of modifier cation field strengths J. Non-Cryst. Solids 2016 438 1 6 10.1016/j.jnoncrysol.2016.02.007
Vassilev, T., Penkov, I., Tzvetkova, C. & Pascova, R. Glass transition temperatures and structures of multicomponent borate glasses: Influence of modifier cation field strengths. J. Non-Cryst. Solids 438, 1–6 (2016).10.1016/j.jnoncrysol.2016.02.007
31. Cheng Y Xiao H Guo W Guo W Structure and crystallization kinetics of Bi2O3–B2O3 glasses Thermochim. Acta. 2006 444 2 173 178 10.1016/j.tca.2006.03.016
Cheng, Y., Xiao, H., Guo, W. & Guo, W. Structure and crystallization kinetics of Bi2O3–B2O3 glasses. Thermochim. Acta. 444(2), 173–178. 10.1016/j.tca.2006.03.016 (2006).10.1016/j.tca.2006.03.016
32. Ait Hana N Aride J Haddad M Benkhouja K Sahraoudi B Taibi M Electric and structural analysis xPbO−(1−x) B2O3 (0.3≤x≤0.9) of glasses Mol. Cryst. Liq. Cryst. 2016 627 1 106 117 10.1080/15421406.2015.1137125
Ait Hana, N. et al. Electric and structural analysis xPbO−(1−x) B2O3 (0.3≤x≤0.9) of glasses. Mol. Cryst. Liq. Cryst. 627(1), 106–117. 10.1080/15421406.2015.1137125 (2016).10.1080/15421406.2015.1137125
33. Ramesh Babu A Rajyasree Ch Srinivasa Rao P Vinaya Teja PM Krishna Rao D Vanadyl ions influence on spectroscopic and dielectric properties of glass network J. Mol. Struct. 2011 1005 83 90 10.1016/j.molstruc.2011.08.024
Ramesh Babu, A., Rajyasree, Ch., Srinivasa Rao, P., Vinaya Teja, P. M. & Krishna Rao, D. Vanadyl ions influence on spectroscopic and dielectric properties of glass network. J. Mol. Struct. 1005, 83–90 (2011).10.1016/j.molstruc.2011.08.024
34. Berwal N Dhankhar S Sharma P Kundu RS Punia R Kishore N Physical, structural and optical characterization of silicate modified bismuth-borate-tellurite glasses J. Mol. Struct. 2017 1127 636 644 10.1016/j.molstruc.2016.08.033
Berwal, N. et al. Physical, structural and optical characterization of silicate modified bismuth-borate-tellurite glasses. J. Mol. Struct. 1127, 636–644 (2017).10.1016/j.molstruc.2016.08.033
35. Ahmed SA Rajiya S Samee MA Ahmmad SK Jaleeli KA Density of bismuth boro zinc glasses using machine learning techniques J. Inorg. Organomet. Polym. Mater. 2022 32 3 941 953 10.1007/s10904-021-02183-y 35069058
Ahmed, S. A., Rajiya, S., Samee, M. A., Ahmmad, S. K. & Jaleeli, K. A. Density of bismuth boro zinc glasses using machine learning techniques. J. Inorg. Organomet. Polym. Mater. 32(3), 941–953 (2022).35069058 10.1007/s10904-021-02183-y
36. Prakash Singh Sh Chakradhar RPSR Karmakar JL B EPR, FTIR, optical absorption and photoluminescence studies of Fe2O3 and CeO2 doped ZnO–Bi2O3–B2O3 glasses J. Alloys Compd. 2010 493 1–2 256 262 10.1016/j.jallcom.2009.12.075
Prakash Singh, Sh., Chakradhar, R. P. S. R., Karmakar, J. L. & B,. EPR, FTIR, optical absorption and photoluminescence studies of Fe2O3 and CeO2 doped ZnO–Bi2O3–B2O3 glasses. J. Alloys Compd. 493(1–2), 256–262 (2010).10.1016/j.jallcom.2009.12.075
37. Kamitsos EI Chryssikos GD Borate glass structure by raman and infrared spectroscopies J. Mol. Struct. 1991 247 1 1 16 10.1016/0022-2860(91)87058-P
Kamitsos, E. I. & Chryssikos, G. D. Borate glass structure by raman and infrared spectroscopies. J. Mol. Struct. 247(1), 1–16. 10.1016/0022-2860(91)87058-P (1991).10.1016/0022-2860(91)87058-P
38. Hassaan MY Osman HM Hassan HH El-Deeb AS Helal MA Optical and electrical studies of borosilicate glass containing vanadium and cobalt ions for smart windows applications Ceram. Int. 2017 43 1795 1801 10.1016/j.ceramint.2016.10.137
Hassaan, M. Y., Osman, H. M., Hassan, H. H., El-Deeb, A. S. & Helal, M. A. Optical and electrical studies of borosilicate glass containing vanadium and cobalt ions for smart windows applications. Ceram. Int. 43, 1795–1801 (2017).10.1016/j.ceramint.2016.10.137
39. Abid M El-Labirou M Taibi M Structure and DC conductivity of lead sodium ultraphosphate glasses Mater. Sci. Eng. B 2003 97 1 20 24 10.1016/S0921-5107(02)00390-2
Abid, M., El-Labirou, M. & Taibi, M. Structure and DC conductivity of lead sodium ultraphosphate glasses. Mater. Sci. Eng. B 97(1), 20–24. 10.1016/S0921-5107(02)00390-2 (2003).10.1016/S0921-5107(02)00390-2
40. Singh GP Kaur P Kaur S Singh DP Conversion of covalent to ionic character of V2O5–CeO2–PbO–B2O3 glasses for solid state ionic devices Phys. B 2012 407 4269 4273 10.1016/j.physb.2012.07.015
Singh, G. P., Kaur, P., Kaur, S. & Singh, D. P. Conversion of covalent to ionic character of V2O5–CeO2–PbO–B2O3 glasses for solid state ionic devices. Phys. B 407, 4269–4273 (2012).10.1016/j.physb.2012.07.015
41. Baia L Stefan R Kiefer W Popp J Simon SJ Structural investigations of copper doped B2O3–Bi2O3 glasses with high bismuth oxide content J. Non-Cryst. Solids 2002 303 3 379 386 10.1016/S0022-3093(02)01042-6
Baia, L., Stefan, R., Kiefer, W., Popp, J. & Simon, S. J. Structural investigations of copper doped B2O3–Bi2O3 glasses with high bismuth oxide content. J. Non-Cryst. Solids 303(3), 379–386. 10.1016/S0022-3093(02)01042-6 (2002).10.1016/S0022-3093(02)01042-6
42. Doweidar AH Saddeek YB FTIR and ultrasonic investigations on modified bismuth borate glasses J. Non-Cryst. Solids 2009 355 6 348 354 10.1016/j.jnoncrysol.2008.12.008
Doweidar, A. H. & Saddeek, Y. B. FTIR and ultrasonic investigations on modified bismuth borate glasses. J. Non-Cryst. Solids 355(6), 348–354. 10.1016/j.jnoncrysol.2008.12.008 (2009).10.1016/j.jnoncrysol.2008.12.008
43. Sharma G Singh K Manupriya MS Singh H Bindra S Effects of gamma irradiation on optical and structural properties of PbO–Bi2O3– B2O3 glasses Radiat. Phys. Chem. 2006 75 9 959 966 10.1016/j.radphyschem.2006.02.008
Sharma, G., Singh, K., Manupriya, M. S., Singh, H. & Bindra, S. Effects of gamma irradiation on optical and structural properties of PbO–Bi2O3– B2O3 glasses. Radiat. Phys. Chem. 75(9), 959–966. 10.1016/j.radphyschem.2006.02.008 (2006).10.1016/j.radphyschem.2006.02.008
44. Bale Sh Srinivas Rao N Rahaman S Spectroscopic studies of Bi2O3–Li2O–ZnO–B2O3 glasses Solid State Sci. 2008 10 3 326 331 10.1016/j.solidstatesciences.2007.09.017
Bale, Sh., Srinivas Rao, N. & Rahaman, S. Spectroscopic studies of Bi2O3–Li2O–ZnO–B2O3 glasses. Solid State Sci. 10(3), 326–331 (2008).10.1016/j.solidstatesciences.2007.09.017
45. Narayana Reddy C Damle R Anavekar RV Spectroscopic and structural studies on calcium borate glasses containing V2O5 Phys. Chem. Glasses 2006 47 1 34 40
Narayana Reddy, C., Damle, R. & Anavekar, R. V. Spectroscopic and structural studies on calcium borate glasses containing V2O5. Phys. Chem. Glasses 47(1), 34–40 (2006).
46. Prakash Singh Sh Chakradhar RPSR Karmakar JL Basudeb EPR, FTIR, optical absorption and photoluminescence studies of Fe2O3 and CeO2 doped ZnO–Bi2O3–B2O3 glasses J. Alloys Compd. 2010 10.1016/j.jallcom.2009.12.075
Prakash Singh, Sh., Chakradhar, R. P. S. R., Karmakar, J. L. & Basudeb,. EPR, FTIR, optical absorption and photoluminescence studies of Fe2O3 and CeO2 doped ZnO–Bi2O3–B2O3 glasses. J. Alloys Compd.10.1016/j.jallcom.2009.12.075 (2010).10.1016/j.jallcom.2009.12.075
47. Saravanan S Rajesh S Palani R Thermal and structural properties of mixed alkali and transition metal ions in sodium borate glass J. Recent Res. Rev. 2015 8 1 9
Saravanan, S., Rajesh, S. & Palani, R. Thermal and structural properties of mixed alkali and transition metal ions in sodium borate glass. J. Recent Res. Rev. 8, 1–9 (2015).
48. Pascuta P Pop L Rada S Bosca M Culea E The local structure of bismuth borate glasses doped with europium ions evidenced by FT-IR spectroscopy J. Mater. Sci. Mater. Electron. 2008 19 424 428 10.1007/s10854-007-9359-5
Pascuta, P., Pop, L., Rada, S., Bosca, M. & Culea, E. The local structure of bismuth borate glasses doped with europium ions evidenced by FT-IR spectroscopy. J. Mater. Sci. Mater. Electron. 19, 424–428. 10.1007/s10854-007-9359-5 (2008).10.1007/s10854-007-9359-5
49. Pierce DT Spicer WE Electronic structure of amorphous Si from photoemission and optical studies Phys. Rev. B Solid State 1972 5 3017 3029 10.1103/PhysRevB.5.3017
Pierce, D. T. & Spicer, W. E. Electronic structure of amorphous Si from photoemission and optical studies. Phys. Rev. B Solid State 5, 3017–3029. 10.1103/PhysRevB.5.3017 (1972).10.1103/PhysRevB.5.3017
50. Thamarai Selvi E Meenakshi Sundar S Effect of replacing Sn4+ ions by Zn2+ ions on structural, optical and magnetic properties of SnO2 nanoparticles Appl. Phys. A 2017 123 383 10.1007/s00339-017-0995-1
Thamarai Selvi, E. & Meenakshi Sundar, S. Effect of replacing Sn4+ ions by Zn2+ ions on structural, optical and magnetic properties of SnO2 nanoparticles. Appl. Phys. A 123, 383. 10.1007/s00339-017-0995-1 (2017).10.1007/s00339-017-0995-1
51. Kaur N Khanna A Structural characterization of borotellurite and luminoborotellurite glasses J. Non-Cryst. Solids 2014 404 116 123 10.1016/j.jnoncrysol.2014.08.002
Kaur, N. & Khanna, A. Structural characterization of borotellurite and luminoborotellurite glasses. J. Non-Cryst. Solids 404, 116–123 (2014).10.1016/j.jnoncrysol.2014.08.002
52. Abdelghany AM ElBatal HA Structural evaluation and shielding behavior of gamma irradiated vanadium doped silicophosphate glasses J. Mol. Struct. 2012 1024 47 53 10.1016/j.molstruc.2012.05.038
Abdelghany, A. M. & ElBatal, H. A. Structural evaluation and shielding behavior of gamma irradiated vanadium doped silicophosphate glasses. J. Mol. Struct. 1024, 47–53 (2012).10.1016/j.molstruc.2012.05.038
53. Mahraz ZAS Sahar MR Ghoshal SK Dousti MR Concentration dependent luminescence quenching of Er3+-doped zinc boro-tellurite glass J. Lumin. 2013 144 139 145 10.1016/j.jlumin.2013.06.050
Mahraz, Z. A. S., Sahar, M. R., Ghoshal, S. K. & Dousti, M. R. Concentration dependent luminescence quenching of Er3+-doped zinc boro-tellurite glass. J. Lumin. 144, 139–145. 10.1016/j.jlumin.2013.06.050 (2013).10.1016/j.jlumin.2013.06.050
54. Wen H Cheng BM Tanner PA Optical properties of selected 4d and 5d transition metal ion-doped glasses RSC Adv. 2017 7 42 26411 26419 10.1039/C7RA04062H
Wen, H., Cheng, B. M. & Tanner, P. A. Optical properties of selected 4d and 5d transition metal ion-doped glasses. RSC Adv. 7(42), 26411–26419 (2017).10.1039/C7RA04062H
55. Davis EA Mott NF Conduction in non-crystalline systems V Conductivity, optical absorption and photoconductivity in amorphous semiconductors Philos. Mag. J. Theor. Exp. Appl. Phys. 1970 22 179 903 922
Davis, E. A. & Mott, N. F. Conduction in non-crystalline systems V Conductivity, optical absorption and photoconductivity in amorphous semiconductors. Philos. Mag. J. Theor. Exp. Appl. Phys. 22(179), 903–922 (1970).
56. Zamyatina EV Karzanov VV Zamyatin OA Optical properties of the zinc-tellurite glasses doped with Cr3+ ions J. Non-Cryst. Solids 2020 528 119759 10.1016/j.jnoncrysol.2019.119759
Zamyatina, E. V., Karzanov, V. V. & Zamyatin, O. A. Optical properties of the zinc-tellurite glasses doped with Cr3+ ions. J. Non-Cryst. Solids 528, 119759. 10.1016/j.jnoncrysol.2019.119759 (2020).10.1016/j.jnoncrysol.2019.119759
57. Abouhaswa AS Sayyed MI Altowyan AS Al-Hadeethi Y Mahmoud KA Synthesis, optical and radiation shielding capacity of the Sm2O3 doped borate glasses J. Non-Cryst. Solids 2021 553 120505 10.1016/j.jnoncrysol.2020.120505
Abouhaswa, A. S., Sayyed, M. I., Altowyan, A. S., Al-Hadeethi, Y. & Mahmoud, K. A. Synthesis, optical and radiation shielding capacity of the Sm2O3 doped borate glasses. J. Non-Cryst. Solids 553, 120505. 10.1016/j.jnoncrysol.2020.120505 (2021).10.1016/j.jnoncrysol.2020.120505
58. Jlassi I Elhouichet H Ferid M Thermal and optical properties of tellurite glasses doped erbium J. Mater. Sci. 2011 46 806 812 10.1007/s10853-010-4820-x
Jlassi, I., Elhouichet, H. & Ferid, M. Thermal and optical properties of tellurite glasses doped erbium. J. Mater. Sci. 46, 806–812 (2011).10.1007/s10853-010-4820-x
59. Saritha D Markandeya Y Salagram M Vithal M Singh AK Bhikshamaiah G Effect of Bi2O3 on physical, optical and structural studies of ZnO–Bi2O3–B2O3 glasses J. Non-Cryst. Solids 2008 354 52–54 5573 5579 10.1016/j.jnoncrysol.2008.09.017
Saritha, D. et al. Effect of Bi2O3 on physical, optical and structural studies of ZnO–Bi2O3–B2O3 glasses. J. Non-Cryst. Solids 354(52–54), 5573–5579. 10.1016/j.jnoncrysol.2008.09.017 (2008).10.1016/j.jnoncrysol.2008.09.017
60. Suziki T Hirano M Hosono H Optical gaps of alkali borate and alkali fluoroborate glasses J. Appl. Phys. 2002 91 4149 4153 10.1063/1.1456946
Suziki, T., Hirano, M. & Hosono, H. Optical gaps of alkali borate and alkali fluoroborate glasses. J. Appl. Phys. 91, 4149–4153 (2002).10.1063/1.1456946
61. Urbach F The long-wavelength edge of photographic sensitivity and of the electronic absorption of solids Phys. Rev. 1953 92 1324 10.1103/PhysRev.92.1324
Urbach, F. The long-wavelength edge of photographic sensitivity and of the electronic absorption of solids. Phys. Rev. 92, 1324 (1953).10.1103/PhysRev.92.1324
62. Ahmed RM El-Bashir SM Structure and physical properties of polymer composite films doped with fullerene nanoparticles Int. J. Photo. 2010 2011 1 6
Ahmed, R. M. & El-Bashir, S. M. Structure and physical properties of polymer composite films doped with fullerene nanoparticles. Int. J. Photo. 2011, 1–6 (2010).
63. Dimitrov V Sakka S Linear and nonlinear optical properties of simple oxides II, J. Appl. Phys. 1995 79 3 1741 1745 10.1063/1.360963
Dimitrov, V. & Sakka, S. Linear and nonlinear optical properties of simple oxides. II, J. Appl. Phys. 79(3), 1741–1745. 10.1063/1.360963 (1995).10.1063/1.360963
64. El-Mallawany R Abdalla MD Ahmed IA New tellurite glass: Optical properties Mater. Chem. Phys. 2008 109 291 296 10.1016/j.matchemphys.2007.11.040
El-Mallawany, R., Abdalla, M. D. & Ahmed, I. A. New tellurite glass: Optical properties. Mater. Chem. Phys. 109, 291–296. 10.1016/j.matchemphys.2007.11.040 (2008).10.1016/j.matchemphys.2007.11.040
65. Lorentz HA On the relationship between the speed of propagation of light and body density Ann. Phys. 1880 245 4 641 665 10.1002/andp.18802450406
Lorentz, H. A. On the relationship between the speed of propagation of light and body density. Ann. Phys. 245(4), 641–665. 10.1002/andp.18802450406 (1880).10.1002/andp.18802450406
66. Dimitrov V Komatsu T An interpretation of optical properties of oxides and oxide glasses in terms of the electronic ion polarizability and average single bond strength J. Univ. Chem. Technol. Metall. 2010 45 3 219 250
Dimitrov, V. & Komatsu, T. An interpretation of optical properties of oxides and oxide glasses in terms of the electronic ion polarizability and average single bond strength. J. Univ. Chem. Technol. Metall. 45(3), 219–250 (2010).
67. Herzfeld KF On atomic properties which make an element a metal Phys. Rev. J. 1927 29 701 705 10.1103/PhysRev.29.701
Herzfeld, K. F. On atomic properties which make an element a metal. Phys. Rev. J. 29, 701–705. 10.1103/PhysRev.29.701 (1927).10.1103/PhysRev.29.701
68. Chauhan S Bala R Gaur S Rani S Effect of Bi2O3 on structural and optical properties of Li2O-PbO- Bi2O3-B2O3 glasses J. Mater. Sci. Mater. Electron 2022 33 22850 10.1007/s10854-022-09050-7
Chauhan, S., Bala, R., Gaur, S. & Rani, S. Effect of Bi2O3 on structural and optical properties of Li2O-PbO- Bi2O3-B2O3 glasses. J. Mater. Sci. Mater. Electron 33, 22850 (2022).10.1007/s10854-022-09050-7
69. Kaur A Khanna A Gonzez F Pesquera C Chen B Structural, optical, dielectric and thermal properties of molybdenum tellurite and borotellurite glasses J. Non-Cryst. Solids 2016 444 1 10 10.1016/j.jnoncrysol.2016.04.033
Kaur, A., Khanna, A., Gonzez, F., Pesquera, C. & Chen, B. Structural, optical, dielectric and thermal properties of molybdenum tellurite and borotellurite glasses. J. Non-Cryst. Solids 444, 1–10 (2016).10.1016/j.jnoncrysol.2016.04.033
70. Jonsche AK The ‘universal’ dielectric response Nature 1977 267 673 679 10.1038/267673a0
Jonsche, A. K. The ‘universal’ dielectric response. Nature 267, 673–679 (1977).10.1038/267673a0
71. Ghosh BK Adhikari S Deb B Mondal R Das AS Kabi S Singh LS Effect of Ag2S on electrical conductivity and dielectric relaxation in Ag2O-MoO3-P2O5 ionic glassy systems J. Non-Cryst. Solids 2022 597 121893 10.1016/j.jnoncrysol.2022.121893
Ghosh, B. K. et al. Effect of Ag2S on electrical conductivity and dielectric relaxation in Ag2O-MoO3-P2O5 ionic glassy systems. J. Non-Cryst. Solids 597, 121893 (2022).10.1016/j.jnoncrysol.2022.121893
72. Dyre JC The random free-energy barrier model for ac conduction in disordered solids J. Appl. Phys. 1988 64 2456 2468 10.1063/1.341681
Dyre, J. C. The random free-energy barrier model for ac conduction in disordered solids. J. Appl. Phys. 64, 2456–2468 (1988).10.1063/1.341681
73. Clark MJ Electricity and Magnetism 1873 Clarendon Press
Clark, M. J. Electricity and Magnetism (Clarendon Press, 1873).
74. Kolavekar SB Ayachit NH Conductivity and dielectric relaxations in Bi2O3-doped phospho-vanadate glasses J. Mater. Sci. Mater. Electron. 2019 30 432 449 10.1007/s10854-018-0308-2
Kolavekar, S. B. & Ayachit, N. H. Conductivity and dielectric relaxations in Bi2O3-doped phospho-vanadate glasses. J. Mater. Sci. Mater. Electron. 30, 432–449 (2019).10.1007/s10854-018-0308-2
75. Elliott SR A theory of ac conduction in chalcogenide glasses Philos. Mag. 1977 36 1291 1304 10.1080/14786437708238517
Elliott, S. R. A theory of ac conduction in chalcogenide glasses. Philos. Mag. 36, 1291–1304 (1977).10.1080/14786437708238517
76. Long R Electronic transport in amorphous semiconductors Adv. Phys. 1982 31 553 637 10.1080/00018738200101418
Long, R. Electronic transport in amorphous semiconductors. Adv. Phys. 31, 553–637 (1982).10.1080/00018738200101418
77. Ghosh A Frequency-dependent conductivity in bismuth-vanadate glassy semiconductors Phys. Rev. B 1990 41 1479 1488 10.1103/PhysRevB.41.1479
Ghosh, A. Frequency-dependent conductivity in bismuth-vanadate glassy semiconductors. Phys. Rev. B 41, 1479–1488 (1990).10.1103/PhysRevB.41.1479
78. Elliott SR Ac conduction in amorphous chalcogenide and pnictide semiconductors Adv. Phys. 1987 36 135 217 10.1080/00018738700101971
Elliott, S. R. Ac conduction in amorphous chalcogenide and pnictide semiconductors. Adv. Phys. 36, 135–217 (1987).10.1080/00018738700101971
79. Elliott SR Frequency-dependent conductivity in ionically and electronically conducting amorphous solids Solid State Ionics 1994 70–71 27 40 10.1016/0167-2738(94)90284-4
Elliott, S. R. Frequency-dependent conductivity in ionically and electronically conducting amorphous solids. Solid State Ionics 70–71, 27–40 (1994).10.1016/0167-2738(94)90284-4
80. El-Alaily NA Mohamed RM Effect of irradiation on some optical properties and density of lithium borate glass J. Mater. Sci. Eng. B 2003 98 193 203 10.1016/S0921-5107(02)00587-1
El-Alaily, N. A. & Mohamed, R. M. Effect of irradiation on some optical properties and density of lithium borate glass. J. Mater. Sci. Eng. B 98, 193–203 (2003).10.1016/S0921-5107(02)00587-1
81. Sujatha B Viswanatha R Nagabushana H Reddy CN Electronic and ionic conductivity studies on microwave synthesized glasses containing transition metal ions J. Mater. Res. Technol. 2017 6 1 7 12 10.1016/j.jmrt.2016.03.002
Sujatha, B., Viswanatha, R., Nagabushana, H. & Reddy, C. N. Electronic and ionic conductivity studies on microwave synthesized glasses containing transition metal ions. J. Mater. Res. Technol. 6(1), 7–12 (2017).10.1016/j.jmrt.2016.03.002
82. Saritha D Markandeya Y Salagram M Vithal M Singh AK Bhikshamaiah G Effect of Bi2O3 on physical, optical and structural studies of ZnO–Bi2O3–B2O3 glasses J. Non-Cryst. Solids 2008 354 5573 5579 10.1016/j.jnoncrysol.2008.09.017
Saritha, D. et al. Effect of Bi2O3 on physical, optical and structural studies of ZnO–Bi2O3–B2O3 glasses. J. Non-Cryst. Solids 354, 5573–5579 (2008).10.1016/j.jnoncrysol.2008.09.017
83. Abdel-Hameed SAM Fathi AM Eltohamy M Structure, optical and electrical behavior of x (2Bi2O3. MnO). (10–x) B2O3 glasses J. Non-Crystalline Solids 2019 510 71 80 10.1016/j.jnoncrysol.2019.01.010
Abdel-Hameed, S. A. M., Fathi, A. M. & Eltohamy, M. Structure, optical and electrical behavior of x (2Bi2O3. MnO). (10–x) B2O3 glasses. J. Non-Crystalline Solids 510, 71–80 (2019).10.1016/j.jnoncrysol.2019.01.010
84. Ali AA Shaaban MH Electrical properties and scaling behaviour of Sm3+ doped CaF2-bismuth borate glasses Bull. Mater. Sci. 2011 34 491 10.1007/s12034-011-0103-7
Ali, A. A. & Shaaban, M. H. Electrical properties and scaling behaviour of Sm3+ doped CaF2-bismuth borate glasses. Bull. Mater. Sci. 34, 491 (2011).10.1007/s12034-011-0103-7
85. Mariyappan M Marimuthu K Sayyed MI Dong MG Kara U Effect Bi2O3 on the physical, structural and radiation shielding properties of Er3+ ions doped bismuth sodiumfluoroborate glasses J. Non-Cryst. Solids 2018 499 75 85 10.1016/j.jnoncrysol.2018.07.025
Mariyappan, M., Marimuthu, K., Sayyed, M. I., Dong, M. G. & Kara, U. Effect Bi2O3 on the physical, structural and radiation shielding properties of Er3+ ions doped bismuth sodiumfluoroborate glasses. J. Non-Cryst. Solids 499, 75–85 (2018).10.1016/j.jnoncrysol.2018.07.025
86. Barsoum MW Fundamentals of Ceramics 2019 CRC Press
Barsoum, M. W. Fundamentals of Ceramics (CRC Press, 2019).
87. Bahgat AA Abou-Zeid YM Mixed alkali Effect in the K2O-Na2O-TeO2, glass system Phys. Chem. Glasses 2001 42 361 370
Bahgat, A. A. & Abou-Zeid, Y. M. Mixed alkali Effect in the K2O-Na2O-TeO2, glass system. Phys. Chem. Glasses 42, 361–370 (2001).
88. Ali AA Fathi AM Ibrahim S Material characteristics of WO3/Bi2O3 substitution on the thermal, structural, and electrical properties of lithium calcium borate glasses Appl. Phys. A. 2023 129 4 299 10.1007/s00339-023-06537-w
Ali, A. A., Fathi, A. M. & Ibrahim, S. Material characteristics of WO3/Bi2O3 substitution on the thermal, structural, and electrical properties of lithium calcium borate glasses. Appl. Phys. A. 129(4), 299 (2023).10.1007/s00339-023-06537-w
89. Nelson JK Fothergill JC Internal charge behaviour of nanocomposites Nanotechnology 2004 15 586 10.1088/0957-4484/15/5/032
Nelson, J. K. & Fothergill, J. C. Internal charge behaviour of nanocomposites. Nanotechnology 15, 586 (2004).10.1088/0957-4484/15/5/032
90. Gouitaa N Lamcharfi T Bouayad M Abdi F Hadi N Impedance, modulus and conductivity studies of Fe3+ doped BaTiO3 ceramics prepared by solid state method J. Mater. Sci. Mater. Electron. 2018 29 6797 6804 10.1007/s10854-018-8666-3
Gouitaa, N., Lamcharfi, T., Bouayad, M., Abdi, F. & Hadi, N. Impedance, modulus and conductivity studies of Fe3+ doped BaTiO3 ceramics prepared by solid state method. J. Mater. Sci. Mater. Electron. 29, 6797–6804 (2018).10.1007/s10854-018-8666-3
91. Amara SFCB Hammami H Effect of iron oxide on the electrical conductivity of soda-lime silicate glasses by dielectric spectroscopy J. Mater. Sci. Mater. Electron. 2019 30 13543 13555 10.1007/s10854-019-01722-1
Amara, S. F. C. B. & Hammami, H. Effect of iron oxide on the electrical conductivity of soda-lime silicate glasses by dielectric spectroscopy. J. Mater. Sci. Mater. Electron. 30, 13543–13555 (2019).10.1007/s10854-019-01722-1
92. Satya Gopal Rao P Rajesh Siripuram S Sripada Impedance analysis of TeO2-SeO2-Li2O nano glass system Result. Phys. 2019 13 102133 10.1016/j.rinp.2019.02.069
Satya Gopal Rao, P., Rajesh Siripuram, S. & Sripada,. Impedance analysis of TeO2-SeO2-Li2O nano glass system. Result. Phys. 13, 102133 (2019).10.1016/j.rinp.2019.02.069
93. Abdel-hameed SAM Fathi AM Elwan R Margha FH Effect of F- and B3+ ions and heat treatment on the enhancement of electrochemical and electrical properties of nanosized LiTi2(PO4)3 glass-ceramic for lithium-ion batteries J. Alloys Compd. 2010 832 154943 10.1016/j.jallcom.2020.154943
Abdel-hameed, S. A. M., Fathi, A. M., Elwan, R. & Margha, F. H. Effect of F- and B3+ ions and heat treatment on the enhancement of electrochemical and electrical properties of nanosized LiTi2(PO4)3 glass-ceramic for lithium-ion batteries. J. Alloys Compd. 832, 154943 (2010).10.1016/j.jallcom.2020.154943
94. Ranjan R Kumar R Kumar N Behera B Choudhary R Impedance and electric modulus analysis of Sm-modified Pb (Zr0.55Ti0.45)1–x/4O3 ceramics J. Alloys Compd. 2011 509 6388 6394 10.1016/j.jallcom.2011.03.003
Ranjan, R., Kumar, R., Kumar, N., Behera, B. & Choudhary, R. Impedance and electric modulus analysis of Sm-modified Pb (Zr0.55Ti0.45)1–x/4O3 ceramics. J. Alloys Compd. 509, 6388–6394 (2011).10.1016/j.jallcom.2011.03.003
95. Elissalde B Ravez J Ferroelectric ceramics: Defects and dielectric relaxations J. Mater. Chem. 2001 11 1957 1967 10.1039/b010117f
Elissalde, B. & Ravez, J. Ferroelectric ceramics: Defects and dielectric relaxations. J. Mater. Chem. 11, 1957–1967 (2001).10.1039/b010117f
96. Ragab Mahani A Helmy Kh Fathi AM Electrical, optical, and electrochemical performances of phosphate-glasses-doped with ZnO and CuO and their composite with polyaniline Sci. Rep. 2024 14 1169 10.1038/s41598-023-51065-5 38216612
Ragab Mahani, A., Helmy, Kh. & Fathi, A. M. Electrical, optical, and electrochemical performances of phosphate-glasses-doped with ZnO and CuO and their composite with polyaniline. Sci. Rep. 14, 1169 (2024).38216612 10.1038/s41598-023-51065-5
