Investigation of Structural, Microstructural, Dielectrical and Magnetic Properties of Bi3+ Doped Manganese Spinel Ferrite Nanoparticles for Photonic Applications

The structural, microstructural, and magnetic properties of Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles prepared by solution combustion method were investigated. Rietveld-refined X-ray diffraction patterns confirm the single-phase formation with space group Fd3m having spinel cubic structure. The porous nature of the samples was confirmed by scanning electron microscopy (SEM). Composition values of the theoretical stoichiometry and energy-dispersive spectroscopy (EDS) composition values are well matched for all samples. The dielectric parameters such as real part of dielectric constant, imaginary part of dielectric constant, and dielectric loss tangent decrease with the increase in frequency. The AC conductivity increases with increase in the Bi 3+ concentration. The real part of complex impedance decreases with the increase in frequency. Cole-Cole plots reveal that one semicircle was obtained for each of the samples. The real and imaginary parts of electric modulus vary with frequency. The magnetic hysteresis curves of all samples reveal the soft magnetic material nature. We observed S esteems began uniquely from the higher superparamagnetic, we would have watched the monotonic decrease in S with increase in Bi 3+ concentration. Furthermore, the magnetic parameters were estimated.

and water treatment catalysts [1][2][3][4]. Many researchers focused on the fabrication of spinel ferrite nanoparticles due to their exceptional electrical and magnetic properties [5][6][7][8][9]. To a progressively essential degree, the expanded scaling down and data storage devices of new devices require the utilization of nanosized magnetic attractive particles [10,11]. Manganese spinel ferrite nanoparticles have gotten expanding consideration for their surprising magnetic properties, such as moderate saturation magnetization (M s ) and low coercivity with a mechanical hardness, high permeability, and good chemical stability [12,13]. The significance of thick manganese (Mn) spinel ferrites additionally lies in their potential application, for example, transformers, core materials for coils, information and communication devices, and so forth. The MnFe 2 O 4 nanoparticles have a spinel cubic structure having the general formula AB 2 O 4 , where the A sites are occupied by the Mn 2+ ions and B sites by the Fe 3+ ions. In a unit cell of manganese ferrites, there are 8 divalent Mn 2+ ions, 16 trivalent Fe 3+ ions, and 32 oxygen ions [14].
The spinel MnFe 2 O 4 nanoparticles were prepared by synthesis methods such as sonochemical technique, co-precipitation, sol-gel method, and solution combustion method [15][16][17]. In the current work, the solution combustion method is often chosen because it is safe, cheap, and easy and it requires less time and energy for the preparation of nanoparticles. It also produces a high-purity product. In this method, the crystallite size, particle size, purity, surface area, degree of nature, and porosity can be influenced by the fuel (F) type [18]. However, for the preparation of nanoparticles, there is no requirement for complex tools, high-temperature furnaces, and reaction chambers in the synthesis process.
In the present work, the Bi 3+ -substituted MnFe 2 O 4 spinel nanoparticles were prepared by a solution combustion method using a mixture of fuels such as glucose and urea. The structural, microstructural, dielectrical, and magnetic properties of Bi-doped manganese spinel ferrite nanoparticles were synthesized and investigated through XRD, SEM, EDS, and dielectric and vibrating sample magnetometer (VSM) for photonic applications.

Experimental details 2.1 Materials
For the preparation of Mn (glucose) (Glucomin-D; purity 99.4%, molecular weight 180.156 g/mol) as fuels. Further based on the oxidizer's and fuel's valences of the compounds, the oxidizer-andfuel ratio is maintained to unity.

Synthesis method
The Mn 1-x Bi x Fe 2 O 4 (x = 0.0, 0.05, 0.1, 0.15, and 0.2) spinel nanoparticles were prepared by the solution combustion method using a stoichiometric amount of O and a mixture of F proportions taken as one. Stoichiometric  6 ) are carried and put in a 500-ml Borosil glass beaker, which is then diluted with a double distilled water. The mixture solution was kept on magnetic stirrer about 60 min to get a homogeneous solution. This homogeneous solution was kept in a pre-warmed suppress heater at 450°C. Within 20 min, the burning process was finished. Then, the obtained powder was grained about 30 min using agate mortar and pestle. The flow chart of the Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) solution combustion is shown in Figure 1.

Characterizations
The XRD patterns were gotten by using CuK α radiation having a wavelength (λ) = 1.5406 Å, and the 2θ values run from 10° to 80° under the step size of 0.02°. The crystalline nature and phase structure can be understood from the XRD patterns. The SEM and EDS micrographs were collected by using JEOL (model JSM-840) to obtain the surface morphology and elemental composition of the samples. To study the electrical properties, the samples are made into pellets using a hydraulic press under the 5-ton pressure using an 11-mm die set. The prepared pellets are sintered at 650°C for 3 h. The sintered pellets are silver coated for a good electrical contact. The electrical properties of all samples are tested at room temperature in the frequency up to 20 MHz using the Wayne Kerr 6500B Series Impedance Analyzer. The magnetic properties were measured at room temperature using a physical properties measurement system (PPMS; Quantum Design, Inc.) up to a field of 20 kOe.  profile factor ratio (R wp /R p ), which is less than one, and goodness-of-fit factor (χ 2 ), which is low, are given in Table 1. The refined XRD patterns confirm the single phase with a spinel cubic structure having a space further without any additional impurity peaks. The indexed (hkl) values are well matched with the Joint Committee of Powder Diffraction Standards (JCPDS) card number 74-2400. Figure 3 clearly shows that the lattice parameters increase with the increase of Bi 3+ concentration due to the difference in ionic radius of Mn 2+ and Bi 3+ ions. The ionic radius of Mn 2+ (0.83 Å) is less than the ionic radius of Bi 3+ (1.03 Å). The average crystallite size was calculated by using the equation below [19]: where k is the Scherrer constant (k = 0.9), λ is the wavelength of Cu-k α radiation, β is the full width half maximum, and θ is the angle of diffraction. The estimated crystallite size decreases with the increase of Bi 3+ concentration (Figure 3). Further internal strain, X-ray density, and hopping length were increased with Bi 3+ concentration increasing (Figure 4). The lattice parameters, average crystallite size, internal strain, X-ray density, and hopping lengths were tabulated in Table 1 Table 2. The estimated stoichiometry as listed in Table 3 is very near to the composition of theoretical values.

Real (ε′) and imaginary (ε′′) parts of dielectric constant
The real (ε′) and imaginary (ε′′) parts of the dielectric constant as a function of frequency at room temperature for Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles are depicted in Figure 7(a) and Figure 7(b), respectively. At low frequency, the real and imaginary parts of dielectric constants show the dispersion for all samples. The dielectric constant values sharply decrease with increasing in frequency, and it is due to Maxwell-Wagner interfacial-type polarization according to Koop's phenomenological theory [21]. At the lower-frequency region, the interfacial polarization contributes to the dispersion. A systematic variation is observed due to the dispersion of dielectric constant with substitution. At the higher-frequency region, it cannot follow the alternating electric field, so real and imaginary parts of dielectric constants are independent of frequency at that region. In ferrites, the maximum dielectric constant is observed in samples having higher Fe 2+ content. At the lower-frequency region, the hopping (exchange  of electron) between Fe 2+ and Fe 3+ at octahedral sites follows the alternating electric field. Many literatures on AB 2 O 4 ferrites indicate that high-temperature sintering leads to the exchange of the Fe 3+ ions to Fe 2+ ions at octahedral sites to some degree [22]. However, the hopping process, involving between the Fe 3+ and Fe 2+ ions, is attributed to the dielectric properties of the samples. Thus, the increase of Bi 3+ concentration results in the increase of dielectric constant. The grain size also influences the dielectric properties, since, in ferrite samples, the dielectric constant of the poorly conducting grain boundary is less than the dielectric constant of highly conducting grains. Thus, size reduction introduces more grain boundaries and hence increases changes in electron polarization at the grain boundaries. Since the size decreases with bismuth substitution increasing, it also increases the dielectric constant.

Dielectric loss tangent (tan δ)
The dielectric loss tangent as a function of frequency at room temperature for Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles is shown in Figure 8. The figure shows the dielectric loss tangent decreases with the increase of the frequency. The dielectric loss tangent is a result of the string in polarization in accordance with the applied external electric field. The materials with high dielectric loss tangent are engaged for manufacturing high-frequency heating devices. The tan δ was calculated using the relation tan δ = ε′/ε″, where ε′ and ε″ are the real and imaginary parts of the dielectric constant, respectively [23].
The tan δ decreases with the increase of the frequency, and then it becomes constant at higher frequencies for all samples. The dielectric loss tangent depends on a number of factors, such as homogeneity, stoichiometry, synthesis method,  ferric content, and composition. The frequency increases with the decrease of the dielectric loss tangent; it may be characterized by the Maxwell-Wagner polarization and conduction mechanism in ferrites.

AC conductivity (σ ac )
The variation of σ ac as a function of frequency at room temperature for Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles is shown in Figure 9. From the figure, it may well be seen that at first the conductivity stays steady in the low frequencies, bit by bit increments in the middle of the road frequencies, and afterward shows scattering for high frequencies in consistence with the Jonscher power law. The AC conductivity was calculated by using the equation σ ac = 2πf ɛ 0 × tan δ , where ɛ 0 is the permittivity of free space, f is the frequency, and tan δ is the dielectric loss tangent. Here, the figure shows that σ ac increases with the increase of the frequency according to the hopping model [24]. In the lower frequencies, grain limits are increasingly adequate; thus the recurrence-free conducts are accomplished. Be that as it may, at high-frequency system, the increase in σ ac is credited to the increased hopping of charge bearers between the Fe 2+ and Fe 3+ particles and Mn 2+ and Mn 3+ particles at the octahedral site and further as a  result of grain impact. With increasing substitution of Bi 3+ by Mn 2+ particles, it very well may be seen that at first conductivity diminishes because of the decrease in the quantity of Mn 2+ -Mn 3+ particles which confines the portability of charge transporters at the octahedral destinations. Figure 10(a) and (b) shows the real and imaginary parts of complex impedance as a function of frequency at room temperature for Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles, respectively. These types of frequency dependence complex impedance have been used for the study of the contribution of grains and grain boundaries on the electrical properties of nanoferrites. The obtained results showed the complex impedance versus frequency for the cobalt  = 0.0, 0.05, 0.1, 0.15, and 0.2)  ferrites. Figure 10(a) indicates that the magnitude of the real part of dielectric constant Z′ decreased with the increase of frequency. The real part of dielectric constant curves tended to merge in the high-frequency region. Such behavior is related to the effect of space charge polarization in the material [25]. Figure 10(b) indicates that the imaginary part of dielectric constant Z′′ reached a maximum value at the low-frequency region and then decreased with further increasing of the frequency, approaching a small value at high-frequency region. Further, it was observed that the height of the peak curve decreased with the concentration increasing, indicating a decrease in the relaxation time. The observed relaxation peak in the magnitude of Z′′ demonstrated the existence of space charge relaxation. Figure 11 shows the Cole-Cole plots of Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles at room temperature. Cole-Cole plot shows the real part complex impedance (Z′) and the imaginary part of complex impedance (Z′′) along x-axis and y-axis, respectively. Figure 11 clearly shows one semicircle was obtained for each of the samples, due to the grain boundary effect. The effects of grain boundary of the material are contributed by the parallel combination of grain boundary resistance and capacitance. However, the radius of curvature of each semicircular arc is reasonably shifted from the magnitude of Z′ when the concentration increased, which is attributed to the presence of a non-Debye type of relaxation phenomenon [26]. Further, the radius of curvature of each semicircular arc is indirectly proportional to the electrical conductance of the material and directly proportional to the electrical resistance. The position of the semicircular arc depends on its relaxation times.   = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles at room temperature.

The real (M′) and imaginary (M′′) parts of electric modulus
x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles, respectively. M′ approaches zero in lower-frequency district and shows constant scattering moving in midfrequency area, while it displays a level sort conduct in higher frequency. This sort of conduct is emerged from the unimportant electrode polarization in lower frequencies and short-range and long-range versatility of charge transporters contributing for the conduction wonders in midfrequencies and recurrence-free electrical conduction in higher frequencies, individually [27]. Also, the focus increment M′′ shows the unwinding tops from lower-frequency area to higher-frequency area. The relaxation tops moving plainly demonstrate the spread of relaxation time of the material. The presence of relaxation tops at lower-, center-, and higher-frequency areas is ascribed to the commitment of capacitance to the grain limit, structural, and grain stage attributes, separately, which is very much concurred with the revealed writing. 2) nanoparticles, and it shows the single semicircular segment for all samples, which is beginning from the grain limit commitments of the material. The Nyquist plot reveals the presence of a non-Debye type of relaxation phenomenon, which is further validated from the electrical modulus analysis [28]. Also, each crescent bend is almost overlapped with each other and no variety is observed, which calls attention to the nearness of electrical unwinding process in the material.  [8,29]. At room temperature, the magnetic parameters such as M r , M s , H c , S, η B , K c , and K u decrease with the increase of Bi 3+ concentration (Figures 15-17). In ferrites, the coercive force is gotten by inversion of the direction of the divider development and that of domain turning around the bearing of the applied field. Generally, the successful sticking for domain wall causes the coercivity; it is understood that the greater grain size reduces H C [30]. In the present examination, the coercive values are low; thus, the likelihood of domain rotation is lower. The materials with bigger grain size have been used to accomplish lower core loss. Strikingly, as anticipated, the estimation of the reduced remanence value was found to be the lowest for x = 0.20 concentration sample ( Table 4). We observed S esteems began interestingly from the higher super paramagnetic and the monotonic decrease in S with

Conclusion
The Mn 1-x Bi x Fe 2 O 4 (where x = 0.0, 0.05, 0.1, 0.15, and 0.2) nanoparticles are synthesized by the solution combustion method using a mixture of fuels as carbamide and glucose. The crystallite sizes were found in nanometer, and the crystallite size decreases with the increase of Bi 3+ concentration. The lattice parameter increases with the increase of Bi 3+ concentration due to the difference in ionic radius of Mn 2+ and Bi 3+ ions. The porous nature of the samples was confirmed by scanning electron microscopy. The elemental composition was analyzed by EDS composition. The dielectric parameters such as real part and imaginary parts of dielectric constant and dielectric loss tangent decrease with the increase of frequency, and this behavior could be explained by a Maxwell-Wagner interfacial-type polarization. All dielectric parameters increase with the increase of Bi 3+ concentration. The AC conductivity increases with the increase of frequency according to the hopping model. The real part of complex impedance decreases with the increase of frequency. The observed relaxation peak in the magnitude of imaginary part of complex impedance Z′′ demonstrated the existence of space charge relaxation. The Cole-Cole plot reveals one semicircle was obtained for each of the samples, due to the grain boundary effect. It is attributed to the presence of a non-Debye type of relaxation phenomenon. The real and imaginary parts of electric modulus vary with frequency. The Nyquist plot reveals the presence of a non-Debye type of relaxation phenomenon, which is further validated from the electrical modulus analysis. The magnetic hysteresis curves of all samples reveal the soft magnetic material nature. The magnetic parameters such as remanent magnetization, saturation magnetization, and coercivity field were decreased with the increase of Bi 3+ concentration. © 2020 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution License (http://creativecommons.org/licenses/ by/3.0), which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.