Influence of Mg(II) substitution on the structural, magnetic, and permeability properties of R-type hexagonal ferrites European Journal of Chemistry 14 (2) (2023) 165-171 European Journal of Chemistry ISSN 2153-2249 (Print) / ISSN 2153-2257 (Online) – Copyright © 2023 The Authors – Atlanta Publishing House LLC – Printed in the USA. This work is published and licensed by Atlanta Publishing House LLC – CC BY NC – Some Rights Reserved. https://dx.doi.org/10.5155/eurjchem.14.2.165-171.2359 European Journal of Chemistry View Journal Online View Article Online Influence of Mg(II) substitution on the structural, magnetic, and permeability properties of R-type hexagonal ferrites Zahoor Ul Hassan 1, Imran Sadiq 1, Hasan Mehmood Khan 2, Sajjad Hussain 1,*, Farhan Sadiq 3, Mishal Idrees 1, Muhammad Shahbaz 1, Samreen Saeed 1, Muhammad Imran 4, Saira Riaz 1 and Shahzad Naseem 1 1 Centre of Excellence in Solid State Physics, University of the Punjab, Lahore, 54590, Pakistan 2 Institute of Physics, The Islamia University of Bahawalpur, Bahawalpur, 63100, Pakistan 3 State Key Laboratory of Fine Chemicals, School of Chemical Engineering, Dalian University of Technology, Dalian 116024, R. P. China 4 Department of Physics, Division of Science and Technology, University of Education, Lahore, 54770, Pakistan * Corresponding author at: Centre of Excellence in Solid State Physics, University of the Punjab, Lahore, 54590, Pakistan. e-mail: sajjad.phd.cssp@pu.edu.pk (S. Hussain). 10.5155/eurjchem.14.2.165-171.2359 Received: 18 November 2022 Received in revised form: 25 January 2023 Accepted: 04 February 2023 Published online: 30 June 2023 Printed: 30 June 2023 A series of single-phase R-type hexagonal ferrites with the composition Sr1-xMgxFe4Sn2O11 (x = 0.0, 0.1, 0.2, 0.3) were manufactured using the auto-combustion sol-gel method sintered at 800 °C. The objective of this work was to study the effect of Mg additives on the structural, magnetic, and permeability properties of the synthesised material. The X-ray diffraction patterns revealed that all prepared samples have hexagonal structures. The scanning electron micrographs revealed the platelet-like structure of the grains, which would help enhance the magnetic permeability of the materials. Magnetic parameters were investigated in the range of applied field ±12.5 kOe. The hysteresis loops revealed the paramagnetic nature of all the synthesised samples. With the substitution of Mg contents, the maximum magnetization increased from 1.05 to 2.62 (emu/g) and the remanence from 0.02-0.09 (emu/g), while the coercivity also increased. The magnetic permeability was determined over the frequency range of 20 Hz to 20 MHz. The magnetic permeability of the synthesized hexagonal ferrites is enhanced due to the presence of grains having a platelet-like structure. Furthermore, the particle size calculated using Langevin equations varied in the range of 4.7 to 6.5 nm. The calculated magnetic permeability properties make this synthesised ferrite material useful for super-high-frequency devices. Sol-gel method SEM micrographs Magnetic properties Structural properties Magnetic permeability R-Type hexagonal ferrites Cite this: Eur. J. Chem. 2023, 14(2), 165-171 Journal website: www.eurjchem.com 1. Introduction Hexagonal ferrites have enormous applications due to their excellent properties and are especially used as soft/hard magnets [1], magneto-optical devices [2], humidity sensors [3], magnetic recording media [4], microwave absorbers [5], and are also essential systems for military platforms such as radar absorbing materials (RAM) and wireless telecommunication technology such as computer local area networks (LAN) and mobile telephones [6]. R-type hexagonal ferrites (BaM2Fe4O11) are the notable metal oxides that have recently gained more attention among the hexagonal ferrites group. Generally, R-type hexagonal ferrites possess excellent magnetic and attractive saturation magnetisation, high permeability, high Curie temperature, and excellent chemical stability [7]. The crystal structure of R-type hexagonal ferrite is typically divided into two blocks, R and R*, based on the crystalline structure, where * represents the c-axis with a phase shift of 180 ° degree. This R-type hexagonal ferrite crystal structure is frustrated by the replacement of oxygen ions with heavy Ba2+/Sr2+ ions and the alteration of accelerated tetragonal sites into bipyramidal trigonal sites. Hence, this leads to magnetic frustration within the magnetic material [8]. It is well established that the substitution of divalent ions within the pure sample alters the structural, magnetic, and mag- netic permeability properties of the material [9]. Furthermore, other reasons like the method of synthesis, temperature, and particle size are also key factors for this alteration in magnetic properties [10]. To synthesize all ferrite materials, the sol-gel auto-combustion method is well suited because it requires low- cost materials such as precursor salt [11,12]. This study was aimed at developing soft ferrite based on Sr1- xMgxFe4Sn2O11 (x = 0.0, 0.1, 0.2, 0.3), which exhibited a low value of coercivity. Powder X-ray diffraction (XRD) has been done to examine the structural properties of all samples. The scanning electron microscope (SEM) was used to find the grain morphology. The permeability properties have been found for all synthesised materials. Hence, the results predict the possibility that the ferrites could be engineered into desired ABSTRACT RESEARCH ARTICLE KEYWORDS https://dx.doi.org/10.5155/eurjchem.14.2.165-171.2359 https://www.eurjchem.com/ https://dx.doi.org/10.5155/eurjchem.14.2.165-171.2359 mailto:sajjad.phd.cssp@pu.edu.pk http://www.eurjchem.com/ https://crossmark.crossref.org/dialog/?doi=10.5155/eurjchem.14.2.165-171.2359&domain=pdf&date_stamp=2023-06-30 166 Hassan et al. / European Journal of Chemistry 14 (2) (2023) 165-171 2023 – European Journal of Chemistry – CC BY NC – DOI: 10.5155/eurjchem.14.2.165-171.2359 Figure 1. XRD patterns of Sr1-xMgxFe4Sn2O11 with all concentrations (x = 0.0, 0.1, 0.2, and 0.3) of R-type hexagonal ferrites [14]. (1-x)Sr(NO3)2 + xMg(NO3)2 + Sn(NO3)2.6H2O + (4-z)Fe(NO3)3.9H2O + CTAB + Citric acid → Sr1-xMgxFe4Mn2O11 Scheme 1. Synthesis of Sr1-xMgxFe4Sn2O11. applications with a precise magnetic response by a suitable choice of microstructure limitations. 2. Experimental Polycrystalline material, Mg-substituted R-type hexagonal ferrite corresponding to the chemical equation Sr1-xMgxFe4 Sn2O11 with various contents (x = 0.0, 0.1, 0.2, 0.3) was synthesized by using Sol-gel auto-combustion technique. First, the stoichiometric ratios of CTAB, citric acid (≥99.5%), Sr(NO3)2 (≥99.5%), Sn(NO3)2·6H2O (≥99.5%), Fe(NO3)3·9H2O (≥99.5%), and Mg(NO3)3·6H2O (≥99.5%) (Sigma-Aldrich) were added in ultrapure deionized water to prepare the aqueous solution. The chemical equation of the reactants and products is Scheme 1. These solution beakers were then placed on a hot plate to intended for stirring and heating. Continuous stirring is used for 4 hours in the temperature range of 80 °C to make the solution homogeneous. During the stirring process, the KOH solution was mixed drop by drop to maintain the pH level of the solution in the range of 7-8 scale [4]. After heating at 80 °C and continuously stirring for four hours, a viscous gel of brown colour was obtained. After two hours, the gel was completely burnt and turned into ash. To achieve the fine powder, the ash was ground using an agar mortar pestle for 25 to 30 minutes. This powder was then again heated in a furnace box at a temperature of 800 ° C for three hours. After this procedure was completed, the resulting samples were ground to obtain the fine powder. Then this ground powder was converted to pellets through a hydraulic press applying the force of 40 KN for 60 seconds. Finally, these pellets were used for the characteri- sation of magnetic properties, XRD, and permeability pro- perties. For structural analysis, the apparatus used for XRD, named Bruker D8 advanced diffractometer (Billerica, Massachusetts) USA, consisted of X-ray radiations of CuKα source with a wavelength limit of λ = 1.54 Å. The morphological properties of R-type hexagonal ferrites were analysed by scanning electron microscope (Tokyo, Japan). The developed VSM of Lakshore-740 (Hamburg, New York) USA, records the magnetic hysteresis loops for synthesised R-type hexagonal ferrite under an applied magnetic field up to 12.5 kOe at room temperature (300 K). To investigate the magnetic permeability properties of the sample at room temperature in the frequency range of 20 Hz to 20 MHz, the impedance analyser model Agilent #E8361A was used. 3. Results and discussion 3.1. Structural characterization The powder X-ray diffractometer with Cu-Kα radiation source of wavelength (λ = 1.54 Å) with a scanning rate of 0.8 °/min was used to investigate the crystalline phase, the crystalline size, and the lattice parameters of the prepared samples. The XRD patterns of R-type hexagonal ferrites Sr1- xMgxFe4Sn2O11 with concentrations (x = 0.0, 0.1, 0.2, 0.3) are depicted in Figure 1. XRD patterns, the unit cell structure, and all other structural parameters of the same materials have already been published in our earlier research paper [13]. The lattice parameter was indexed according to hexagonal ferrite, and, moreover, the crystalline size was in the range of 4.16 to 8.25 nm [13]. 3.2. Grain morphology Figure 2 shows low- and high-magnification SEM micro- graphs of sample R-type hexaferrite Sr0.7Mg0.3Fe4Sn2O11. It can be seen that small particles agglomerate with one another to form large grains. Both micrographs clearly show the platelet structure grains. The small grain size was determined using a line intercept and a range of 28 nm. It is well known that these platelet-like structure grains arrange themselves in response to an externally applied magnetic field, increasing the overall magnetic permeability of the material [14]. As a result, the current synthesised samples can be used in applications requiring high magnetic permeability. 3.3. Magnetic properties The magnetic nature of the synthesized ferrite materials can be examined by knowing about their magnetic parameters, like maximum magnetization, coercivity (Hc), and remanence (Mr). Hassan et al. / European Journal of Chemistry 14 (2) (2023) 165-171 167 2023 – European Journal of Chemistry – CC BY NC – DOI: 10.5155/eurjchem.14.2.165-171.2359 Table 1. The values of coercivity (Hc), maximum magnetization, remanence magnetization (Mr), and particle size of Sr1-xMgxFe4Sn2O11 (x = 0.1, 0.2, 0.3) R-type hexagonal ferrite. Mg concentration Coercivity (Oe) Maximum magnetization (emu/g) Remanence magnetization (emu/g) Particle size (nm) z = 0.0 128 1.05 0.02 6.5 z = 0.1 200.5 1.24 0.03 5.7 z = 0.2 232.5 2.41 0.07 5.5 z = 0.3 223.5 2.62 0.09 4.7 (a) (b) Figure 2. Low magnification (a) and high magnification (b) scanning electron micrographs (SEM) of sample Sr0.7Mg0.3Fe4Sn2O11. Figure 3. Magnetic hysteresis loops of Sr1-xMgxFe4Sn2O11 (x = 0.0, 0.1, 0.2, 0.3) R-type hexagonal ferrites. These magnetic parameters can be evaluated from hysteresis loops for different synthesised materials. Figure 3 represents the magnetic hysteresis loops taken under the applied field strength of ±12.5 kOe for the R-type hexagonal ferrite of composition Sr1-xMgxFe4Sn2O11 (x = 0.0, 0.1, 0.2, 0.3) obtained at room temperature (300 K). It was astonishing to observe that all samples exhibited a paramagnetic nature. The hysteresis parameters of maximum magnetization, remnant magnetization, and coercivity (Hc) are listed in Table 1. It has been observed from hysteresis loops that the values of maximum magnetization and remanence increased with each substitution of Mg2+ ions in pure ferrite. From Table 1, it was observed that for concentration x = 0.0, the material has a minimum magnetization value of 1.05 emu/g and a remanence of 0.02 emu/g, which then increases with the substitution of Mg2+ ions and it reaches its maximum value of 2.62 emu/g and remanence (0.09 emu/g) for concentration at x = 0.3. The following reasons are attributed to this improvement in maximum and remnant magnetization. Tatarchuk et al. repor- ted that this increment may be due to the enhancement in the formula unit magnetic moment [15]. 168 Hassan et al. / European Journal of Chemistry 14 (2) (2023) 165-171 2023 – European Journal of Chemistry – CC BY NC – DOI: 10.5155/eurjchem.14.2.165-171.2359 (a) (b) (c) (d) Figure 4. Magnetic hysteresis loops of Sr1-xMgxFe4Sn2O11 R-type hexagonal ferrite (x = 0.0 (a), 0.1 (b), 0.2 (c), 0.3 (d)). Since Mg2+ ions possess only two electrons in their outermost electronic configuration of 3s, these both electrons are oriented in the paired up state hence exhibiting magnetic nature. This leads to an increment in the net magnetic moment which is the key point for the enhancement in the overall values of remanence and maximum magnetization. The substitution of Fe3+ ions (having spin-up direction) with Mg2+ ions increases the magnetization of the material. Narang et al. reported that the substitution of Fe3+ ions with down-spin (4fI and 4fII) results in the enhancement of magnetization, while the substi- tution of spin-up Fe3+ (12k, 2a, 2b) causes a decrease in net magnetization [16]. Table 1 shows the worth-noting point that the value of coercivity for the pure sample is minimum 128 Oe, which then enhances with Mg doping and reaches to its maximum value of 233.5 Oe for a doping concentration of additives x = 0.2. The Langevin function was also used to determine particle sizes [17]: M(H) = Ms L(𝑦𝑦) (1) and L(𝑦𝑦) = Coth(𝑦𝑦) − 1 𝑦𝑦 (2) 𝑦𝑦 = µ0 µ𝐻𝐻(𝑦𝑦) − 1 𝑦𝑦 (3) Here (𝜇𝜇0) vacuum permeability, (µ) magnetic moments of nanoparticles, (H) applied magnetic field, (𝐾𝐾𝐵𝐵) Boltzmann constant and (T) Temperature. For a given temperature, the particle sizes are estimated using formula [18]; 𝐷𝐷3 = 18 𝐾𝐾𝐵𝐵𝑇𝑇𝑇𝑇 π 𝜇𝜇0𝑀𝑀𝑀𝑀2 (4) The estimated particle size values of the substituted samples with rare earth elements are calculated using expression (4). From the M-H loop, the volume susceptibility χ of the samples is also calculated. The saturation magnetisation values of the nanoparticles are determined by working with the expressions (1) and (2). The particle sizes values for each sample, calculated using the above formulations, are given in Table 1. The coercivity of the material is directly related to particle size; with Mg substitution, the size of the sample particles decreases throughout the Mg doping, so the value of coercivity increased and reaches its maximum value at Mg concentration of x = 0.2 [18]. So, at that time, the multi-domain material becomes converted into a single domain below the critical point, then the material exhibits the paramagnetic nature, hence the hysteresis loop becomes shortened as depicted in Figure 4 for all substitutions. Hassan et al. / European Journal of Chemistry 14 (2) (2023) 165-171 169 2023 – European Journal of Chemistry – CC BY NC – DOI: 10.5155/eurjchem.14.2.165-171.2359 Figure 5. Variation of the real part µ' of complex permeability versus frequency for Sr1-xMgxFe4Sn2O11 (x = 0.1, 0.2, 0.3) R-type hexagonal ferrites. Another remarkable reason is that, in hexagonal ferrites, the c-axis also plays an active role in reducing coercivity. When the magnetic field is applied in a perpendicular manner, the loosely orientated crystals try to orient themselves along the c- axis. Therefore, the substitution of Mg2+ ions that possess large ionic radii leads to the production of more disruption in the crystal lattice that might enhance the magnetic crystalline anisotropy, thus increasing the value of coercivity [19]. It was worth noted that the magnetic parameters determine from magnetic loops. From the Ms values suggested that this Sr1- xMgxFe4Sn2O11 (x = 0.0, 0.1, 0.2, 0.3) R-type hexagonal ferrite possesses paramagnetic nature. 3.4. Magnetic permeability analysis The permeability behavior is one of the most imperative characteristics of ferrites, which significantly influenced by the preparation situations, e.g., sintering time, additive amount, type, and temperature. The magnetic permeability properties of all samples were measured at 300 K over the 20-Hz to 20-MHz frequency range. The variation of the real part of the permeability with frequency is illustrated in Figure 5. The trend clearly demonstrated that the real (µ′) part of permeability exhibited high values at low frequency and dropped rapidly and became constant with the increase of frequency. Several factors are responsible for the change in permeability properties of the material like crystallinity, process of magnetization (spin rotation occurring in single domain grain, movement of domain-wall occurring in multi-domain grain) and grain volume [20]. Generally, at higher frequencies, the domain wall is damped and does not respond during applied electric and magnetic field oscillations and only spin rotation occurs at higher frequency ranges. The worthwhile relation between initial permeability and resonant frequency fR is given by a law known as Snoek’s law [21]. 𝑓𝑓𝑅𝑅 = 1 µ𝑖𝑖 × 3 × 109 Hz (5) Snoek’s law represents the reciprocal relationship between resonance frequency and initial permeability (µi). Therefore, the permeability decreases rapidly in all substituted samples at a lower frequency while it becomes constant extremely near zero, consequently with further increment in frequency. The decrease in real permeability may be due to the porosity that arose during the sintering process of the ferrite samples. This porosity may hinder the domain-wall motion during magnetization, which leads to a decrease in the real part of the permeability. Moreover, this rapid reduction in permeability at higher frequencies might be due to the vibrational frequency that does not match the domains of the material with the applied magnetic field [22]. The decreasing behaviour of the imaginary part (µ'') of the complex permeability as a function of frequency can be observed in Figure 6. This behaviour of µ'' can be explained on the basis of Snoek’s law. According to the Snoek model, the relationship between µ'' and frequency (resonance frequency) is expressed as; 𝑓𝑓res = ϓM𝑠𝑠 4𝜋𝜋µ’’α (6) where α is the extinction coefficient, while Ms represents the saturation magnetisation. This model indicates the inverse relation between µ'' (loss factor) and fres. Various remarkable factors are involved in altering the (µ'') as well as the resonance frequency. Figure 5 demonstrated that Mg additives altered the maximum value of permeability for each sample, which also changed the characteristic frequencies as a consequence of both the respective relaxation of the domain wall and the ferromagnetic resonance. This relaxation process may cause to generate microwave dissipation, which leads to the creation of thermal energy. As a consequence, the value of µ'' starts to decrease rapidly with increasing frequency [22]. Moreover, the Mg doping leads in a decrease in magneto-crystalline anisotropy, which may lead to a drop in domain-wall hardness and a subsequent fall in resonance frequency. As a consequence, the contribution of these two mechanisms tends to increase the permeability levels with the Mg content. So, it may conclude that at lower frequency regions the u'' is reciprocal to magneto-crystalline anisotropy [23]. The complex imaginary part of the permeability (µ'') reveals the observed magnetic loss. The varying trend of tan loss with frequency can be clearly seen for all Mg-substituted samples with concentrations x = 0.1, 0.2, and 0.3 taken at 300 K, as shown in Figure 7. This may be due to the exchanging electron mechanism between Fe3+ and Fe2+ ions in the lower frequency zone, which requires more energy, representing high magnetic loss in the low frequency range. 170 Hassan et al. / European Journal of Chemistry 14 (2) (2023) 165-171 2023 – European Journal of Chemistry – CC BY NC – DOI: 10.5155/eurjchem.14.2.165-171.2359 Figure 6. Variation of the imaginary part µ'' of the complex permeability versus frequency for Sr1-xMgxFe4Sn2O11 (x = 0.1, 0.2, 0.3) R-type hexagonal ferrites. Figure 7. Graph of tan loss (magnetic loss) versus frequency of Mg-doped Sr1- xMgxFe4Sn2O11 R-type hexagonal ferrite at the concentration (x = 0.1, 0.2, 0.3). The frequency spectrum represents the observed resonant peak for x = 0.1 at about 2.83 MHz. These attributed peaks arose due to the matching behaviour of two frequencies, one the frequency of the applied field, while the other is the frequency between Fe3+ and Fe2+ ions, known as the hopping frequency. When both these frequencies, the hopping frequency of the electron and the frequency of the applied field, match each other, a phenomenon, known as resonance phenomena, occurs, which is responsible for generating these resonant peaks in higher-frequency regions. This is why these peaks are known as resonant peaks, as they come from frequency resonance phenomena [24]. Due to experimental restrictions, resonant peaks could not be demonstrated for the synthesized material at x = 0.2 and 0.3 which may also exist at higher range of frequencies. Generally, magnetic losses are required to examine the ferrite material’s magnetic permeability properties. The crystal defects as well as the impurities are responsible for the high resistance. At high frequencies, low-resistive grains become much more active, causing the dielectric constant to decrease [25]. The findings indicate that magnetic loss has increased, demonstrating greater alteration of the magnetic permeability features of ferrites [26]. 4. Conclusions The autocombustion sol-gel procedure was used to synthesise the divalent element 'Mg successfully' substituted R- type hexagonal ferrites Sr1-xMgxFe4Sn2O11 (x = 0.0, 0.1, 0.2, 0.3). For all samples, the XRD graphs revealed a single R-type hexagonal ferrite phase. Because of the substitution of the Fe3+ ions, which perturbed the exchange interaction strength in the material, the maximum value of magnetization and remanence magnetization increased. The substitution of Mg content increased the coercivity of all samples. The particle size was calculated using the Langevin function and ranged from 4.7 to 6.5 nm. The M-H loops demonstrated that the synthesised samples were paramagnetic in nature. These ferrite materials are useful for super high-frequency devices due to their increased magnetic permeability (SHF). Acknowledgements Special thanks from the author to Director, Centre of Excellence in Solid State Physics, University of Punjab, Lahore, for providing all research facilities. Disclosure statement Conflict of interests: The authors declare that they have no conflict of interest. Ethical approval: All ethical guidelines have been adhered. Sample availability: Samples of the compounds are available from the author. CRediT authorship contribution statement Conceptualization: Zahoor Ul Hassan, Imran Sadiq; Methodology: Mishal Idrees; Software: Saira Riaz; Validation: Hassan mehmood Khan; Formal Analysis: Muhammad Sahahbaz Qureshi; Investigation: Samreen Saeed; Resources: Shahzad Naseem; Data Curation: Farhan Sadiq; Writing - Original Draft: Sajjad Hussain, Zahoor Ul Hassan, Imran Sadiq; Writing - Review and Editing: Sajjad Hussain; Muhammad Imran Visualization: Imran Sadiq; Funding acquisition: Saira Riaz; Supervision: Imran Sadiq Khan; Project Administration: Imran Sadiq. ORCID and Email Zahoor Ul Hassan zahoor507499@gmail.com https://orcid.org/0000-0003-0372-9502 Imran Sadiq imran.cssp@pu.edu.pk https://orcid.org/0000-0002-6583-8168 Hasan Mehmood Khan hmkhan@iub.edu.pk https://orcid.org/0000-0002-9440-5580 Sajjad Hussain sajjad.phd.cssp@pu.edu.pk https://orcid.org/0000-0001-6145-0484 Farhan Sadiq farhansadiq.khan@yahoo.com https://orcid.org/0000-0001-5487-3622 Mishal Idrees mishal.phd.cssp@pu.edu.pk https://orcid.org/0000-0001-8292-8926 Muhammad Shahbaz msq351@gmail.com https://orcid.org/0000-0002-8738-2851 Samreen Saeed samreensaeed489@gmail.com https://orcid.org/0000-0001-6871-7639 Muhammad Imran m.imran@ue.edu.pk https://orcid.org/0000-0003-1128-147X mailto:zahoor507499@gmail.com https://orcid.org/0000-0003-0372-9502 mailto:imran.cssp@pu.edu.pk https://orcid.org/0000-0002-6583-8168 mailto:hmkhan@iub.edu.pk https://orcid.org/0000-0002-9440-5580 mailto:sajjad.phd.cssp@pu.edu.pk https://orcid.org/0000-0001-6145-0484 mailto:farhansadiq.khan@yahoo.com https://orcid.org/0000-0001-5487-3622 mailto:mishal.phd.cssp@pu.edu.pk https://orcid.org/0000-0001-8292-8926 mailto:msq351@gmail.com https://orcid.org/0000-0002-8738-2851 mailto:samreensaeed489@gmail.com https://orcid.org/0000-0001-6871-7639 mailto:m.imran@ue.edu.pk https://orcid.org/0000-0003-1128-147X Hassan et al. / European Journal of Chemistry 14 (2) (2023) 165-171 171 2023 – European Journal of Chemistry – CC BY NC – DOI: 10.5155/eurjchem.14.2.165-171.2359 Saira Riaz saira.cssp@pu.edu.pk https://orcid.org/0000-0003-4720-1996 Shahzad Naseem shahzad.cssp@pu.edu.pk https://orcid.org/0000-0002-7814-7577 References [1]. 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Phys. 2012, 86, 024425. Copyright © 2023 by Authors. This work is published and licensed by Atlanta Publishing House LLC, Atlanta, GA, USA. The full terms of this license are available at http://www.eurjchem.com/index.php/eurjchem/pages/view/terms and incorporate the Creative Commons Attribution-Non Commercial (CC BY NC) (International, v4.0) License (http://creativecommons.org/licenses/by-nc/4.0). By accessing the work, you hereby accept the Terms. This is an open access article distributed under the terms and conditions of the CC BY NC License, which permits unrestricted non-commercial use, distribution, and reproduction in any medium, provided the original work is properly cited without any further permission from Atlanta Publishing House LLC (European Journal of Chemistry). No use, distribution, or reproduction is permitted which does not comply with these terms. Permissions for commercial use of this work beyond the scope of the License (http://www.eurjchem.com/index.php/eurjchem/pages/view/terms) are administered by Atlanta Publishing House LLC (European Journal of Chemistry). mailto:saira.cssp@pu.edu.pk https://orcid.org/0000-0003-4720-1996 mailto:shahzad.cssp@pu.edu.pk https://orcid.org/0000-0002-7814-7577 http://www.eurjchem.com/index.php/eurjchem/pages/view/terms http://creativecommons.org/licenses/by-nc/4.0 http://www.eurjchem.com/index.php/eurjchem/pages/view/terms 1. Introduction 2. Experimental 3. Results and discussion 3.1. Structural characterization 3.2. Grain morphology 3.3. Magnetic properties 3.4. Magnetic permeability analysis 4. Conclusions Acknowledgements Disclosure statement CRediT authorship contribution statement ORCID and Email References PrintField10: PrintField11: PrintField12: PrintField13: PrintField14: PrintField15: PrintField16: PrintField20: PrintField21: PrintField22: PrintField23: PrintField24: PrintField25: PrintField26: