BIBECHANA Vol. 21, No. 3, December 2024, 254-261 ISSN 2091-0762 (Print), 2382-5340 (Online) Journal homepage: http://nepjol.info/index.php/BIBECHANA Publisher: Dept. of Phys., Mahendra Morang A. M. Campus (Tribhuvan University) Biratnagar Composition optimization of Ni-Zn ferrites for magnetic hyperthermia: structural, morphological and spectroscopic study D. Parajuli1.2,∗, P. V. Ramana3, N. Murali4, S. Bista5, M. Sharma5, K. Samatha6 1Research Center for Applied Science and Technology, Tribhuvan University, Kathmandu -44613, Kirtipur, Nepal 2Tri-Chandra Multiple Campus, Ghantaghar, Kathmandu-44600, Nepal 3Sri DNR Government Degree College for Women Palakol-534260, West Godavari, Andhra Pradesh, India 4Department of Engineering Physics, AUCE, Andhra University, Visakhapatnam-530003, India 5College of Biomedical Engineering and Medical Science, Purbanchal University, Kupondole, Lalitpur, 44600, Nepal 6Department of Physics, Andhra University, Visakhapatnam-530003, India ∗Corresponding author: Email: deepenparaj@gmail.com Abstract The optimization of the appropriate composition is necessary for the characteristics suit- able for magnetic hyperthermia by varying the amount of iron in the ferrite composition. The NiZn ferrite with the composition Ni0.65Zn0.35Fe2O4, Ni0.65Zn0.40Fe1.95O4, and Ni0.60Zn0.35Fe2.05O4 indicated by IN, IE, and ID respectively were synthesized from sol-gel approach. XRD shows cubic spinel structure except for one extra peak in all three samples (IN 800℃; IE 800℃, and ID 900℃; 800℃, 900℃ and 1000℃) around 2= 40.9° is related to the iron oxide (Fe2O3) and is related to JCPDS 89-8104). The formation of the additional peak is due to the diffusion of atoms in the heating process. The variations in crystallite size and particle size are due to iron content. Their effect on magnetic properties and hence in hyperthermia are under study. Keywords Ni-Zn Ferrites, SEM-EDX, FTIR, Hyperthermia. Article information Manuscript received: May 7, 2024; Revised: June 20, 2024; Accepted: June 23, 2024 DOI https://doi.org/10.3126/bibechana.v21i3.65529 This work is licensed under the Creative Commons CC BY-NC License. https://creativecommons. org/licenses/by-nc/4.0/ 254 http://nepjol.info/index.php/BIBECHANA deepenparaj@gmail.com https://doi.org/10.3126/bibechana.v21i3.65529 https://creativecommons.org/licenses/by-nc/4.0/ https://creativecommons.org/licenses/by-nc/4.0/ D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 255 1 Introduction Hyperthermia, the application of heat to treat dis- ease, has ancient roots dating back to Egyptian, Indian, and Chinese civilizations. The therapeu- tic use of heat was historically limited to treating infections, improving circulation, and easing mus- cle pain. However, its scientific exploration be- gan in earnest in the 19th and 20th centuries. In 1866, German surgeon Carl Busch reported using heat to treat tumors, and in the 20th century, ad- vancements in technology facilitated more precise applications of hyperthermia [1]. This is highly ap- plicable in medical applications: 1) Cancer Treat- ment, 2) Enhanced Drug Delivery, 3) Immune Re- sponse Stimulation, 4) Pain management etc. In cancer treatment, there are three hyperthermia: Local Hyperthermia (Targets small areas, typically tumors, using external devices like microwave, ul- trasound, or radiofrequency to raise tissue temper- ature.), Regional Hyperthermia (treats larger ar- eas of the body, such as limbs or organs, often in combination with other treatments like chemother- apy.) and Whole-body Hyperthermia (used for metastatic cancer, raising the body's core temper- ature to enhance the effects of other cancer treat- ments.) [1] In enhanced drug delivery, hyperthermia increases cell membrane permeability, facilitating the uptake of chemotherapeutic drugs. It can en- hance the efficacy of drug-loaded nanoparticles and liposomes, targeting tumor sites more effectively. In immune response stimulation, heat can stimu- late immune responses by increasing the expression of heat shock proteins, which help the immune sys- tem recognize and attack cancer cells. In pain man- agement, it is used in physiotherapy to relieve mus- cle and joint pain, leveraging its ability to improve blood flow and reduce muscle stiffness [1]. Recent research focuses on magnetic nanoparticles that can be heated in an alternating magnetic field, provid- ing targeted hyperthermia with minimal damage to surrounding tissues [?]. Integrating hyperther- mia with radiation and immunotherapy has shown promising results, enhancing treatment efficacy and reducing side effects. Advances in imaging and ther- mal dosimetry have improved hyperthermia's preci- sion, allowing for real-time non-invasive treatment monitoring and adjustments [2]. The extensive research conducted on the Ni-Zn ferrite system [3–6] has demonstrated that Ni-Zn bulk ferrite emerges as the optimal core material for high-frequency applications. This is due to its advantageous properties, such as high saturation magnetization, elevated Curie temperature, favor- able magnetic permeability, low power loss, and high DC resistivity [7, 8]. Transforming bulk Ni- Zn ferrite into nanostructures offers significant po- tential for enhancing specific properties like satu- ration magnetization, initial permeability, particle size, and DC resistivity. Consequently, this mate- rial holds promise for various applications, includ- ing magnetic data storage, targeted drug delivery systems, MRI contrast enhancement, and serving as a heating agent in magnetic fluid hyperther- mia [9, 10]. Achieving desired variations in mul- tiple parameters tailored for each application re- quires meticulous control over the synthesis process to produce the material in nano form. It is known that tailoring the chemical compo- sition allows control of magnetic properties [11–13]. These properties depend primarily on the exchange interactions, which depend upon the types and concentrations of different cations present in the composition [14, 15]. Numerous researchers have made efforts [16–18] to obtain the least-sized parti- cles with superior magnetic properties in nano Ni1- xZnxFe2O4 ferrites by choosing an appropriate zinc concentration (x). On the other hand, research has revealed that studies involving varied iron content in bulk or nano Ni-Zn ferrites are severely inade- quate [19–21]. In any ferrite system, the arrangement of sub- stituted ions within the structure plays a crucial role in altering the electromagnetic properties [22]. To develop a suitable material with desired char- acteristics, it's essential to thoroughly comprehend how different cations occupy positions within the A and B sub-lattices [23]. For instance, achiev- ing magnetic hyperthermia necessitates materials exhibiting high saturation magnetization, low co- ercivity, and a significant Curie temperature [24]. Enhancing processing conditions and focusing on consequent magnetic properties can lead to the fab- rication of superior materials for magnetic hyper- thermia applications [25]. The study undertakes a methodical examina- tion aimed at obtaining a nano ferrite composi- tion. It aims to significantly enhance specific satu- ration magnetization through a comprehensive un- derstanding of how cation distribution varies with different levels of iron content in the ferrite composi- tion. Here, we present and analyze their structural, morphological, and spectroscopic data. 2 Method of preparation The sol-gel process was adopted in preparing the Ni-Zn nanoferrites with varying amounts of iron in the composition. The nitrates of nickel, zinc, and iron are mixed in stoichiometric proportion along with deionized water and stirred for 2 hrs and then mixed with a chelating agent polyethylene glycol (PEG) (10g of PEG mixed in 100mL deionized wa- ter) in 1:1 ratio and dehydrated at 100oC. The in- volved reactions are: (a) 0.65 Ni (NO3)2.6H2O + 0.35 Zn D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 256 (NO3)2.6H2O + 2 Fe (NO3)3.9H2O + PEG → Ni0.65Zn0.35Fe2O4 + 8NO2 + 2O2 + 24H2O (b) 0.65 Ni(NO3)2.6H2O + 0.40 Zn(NO3)2.6H2O + 1.95 Fe(NO3)3.9H2O + PEG → Ni0.65Zn0.40Fe1.95O4 + 7.95NO2 + 1.975O2 + 23.85H2O (c) 0.60 Ni(NO3)2.6H2O + 0.35 Zn(NO3)2.6H2O + 2.05 Fe(NO3)3.9H2O + PEG→ Ni0.60Zn0.35Fe2.05O4 + 8.05NO2 + 2.025O2 + 24.15H2O The drying resulted in a reddish gel along with reddish brown fumes of NO2 [26] which further con- verted into fluffy ferrite mass. The water content was removed with the use of a hot air oven for 10 hours. Each ferrite composition's as-prepared pow- der has been annealed at 400 ℃ for one hour and then allowed to cool naturally by turning off the fur- nace. The annealed powder was extensively crushed and made into pellets and toroids using polyvinyl alcohol as a binder. All the pellets and toroids have been heated for one hour at optimum temperatures (800 ℃ to 1050 ℃ @ 5℃/min) before being sub- jected to natural cooling to room temperature. The samples were further designated as IE-1000, IN- 1050, and ID-1000, where 1000 and 1050 indicate the optimum annealing temperatures. Flowchart 1: Preparation and characterization of Ni-Zn Ferrites The preparation and characterization of Ni-Zn Ferrites are shown in flowchart 1 which ensuring clarity and reproducibility for future researchers. Characterization The samples have been characterized PANalytical X’Pert PRO was used for determining the crystal- lographic structure. SUPRA 55 Zeiss FESEM with attached EDX and working with a primary e-beam at an energy of 25 keV was used for morphological study. Nicolet-MAGNA-550 IR spectrometer was used for the compositional study. Detailed analy- sis and discussion about the observed variations in various parameters like lattice constant, and parti- cle size, have been described as a function of iron content to finalize a composition with the desired characteristics of the magnetic hyperthermia appli- cation. 2.1 Materials All the chemicals (Sulphuric acid, Buffer tablets, Potassium dichromate, 1,5-diphenyl carbazide, Ni- tric acid, Sodium hydroxide, etc) of analytical grade were purchased from Thermo Fisher Scientific In- dia. 1000ppm stock solution of potassium dichro- mate, 0.1 N nitric acid, 5N sulphuric acid, 2N nitric acid, 0.1M & 2N sodium hydroxide, 0.25% DCPI so- lution and buffer solutions (pH-4.0,7.0 & 9.2) were prepared in different volumes. 3 Results and Discussion 3.1 XRD study The spinel structure was tested and the lattice pa- rameter of samples was been computed from the observed Bragg angles of the XRD in the range 15°– 85° with 1.5406 Å wavelength X-rays. The XRD patterns of the samples IN, ID, and IE, Ni-Zn nano- ferrite from 800 ℃ to 1050 ℃ are shown in Figures 1 to 3. The wider peaks indicate the smaller crystallite size. The signs of nascent iron oxides are observed in the material. The intensity is increasing slowly with temperature indicating the enhancement of the crystallization. The estimated lattice parame- ters corresponding to the IN-1050, ID-1000, and IE- 1000 samples were 8.3746 Å, 8.3774 Å, and 8.3806 Å respectively depending on the iron content from 50% to 51.25%. The marginal increase in the case of IE-1000 has been associated with the formation of Fe2+ ions in the material processed at a higher annealing temperature and the larger ionic radius of Fe2+ ions (0.78 Å). The peaks (111), (220), (311), (222), (400), (422), (511), (440), (620), (533), (622) corresponds to JCPDS- 08-0234 and are cubic spinel structure. There is one extra peak in all three samples (IN 800℃; IE 800℃, and ID 900℃; 800℃, 900℃ and 1000℃) around 2= 40.9° is related to the iron ox- ide (Fe2O3) and is related to JCPDS 89-8104). The formation of the additional peak is due to the dif- fusion of atoms in the heating process [10,27]. 3.2 FESEM study At the nanoscale, the size of particles becomes cru- cial due to the significant variations in material properties compared to larger micron-sized coun- terparts. Nano-sized ferrite particles, as they ap- proach a critical diameter, display distinctive mag- netic characteristics such as single domain behav- ior, superparamagnetism, and a lowered Curie tem- perature. Moreover, in nanoparticles with a high surface-to-volume ratio, surface spin disorder can alter magnetic properties over time. In single- domain particles, the absence of domain wall res- D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 257 onance shifts the operational frequency to higher ranges, making them valuable for high-frequency applications. Conversely, single-domain particles of sufficiently small size may demonstrate superpara- magnetism, a property crucial for applications like magnetic hyperthermia treatment. (a) (b) (c). Figure 1: XRD of the (a) IN sample (b) ID sam- ple and (c) IE sample subjected to various heating temperatures. FESEM micrographs of these three samples sup- port the observed microstructural changes in terms of increased porosity and compaction of reduced grains (Figure 2). Figure 2: FESEM images of (a) IN-1050 (b) ID- 1000 and (c) IE-1000 pellet samples. Archimedes' principle has been used to deter- mine the experimental (or) bulk density of all the samples. The bulk density of the sample, dbulk = w1 w1−w2 (1) where W1 = the sample weight in air (g) W2 = the sample weight in water (g) The X-ray density is often more than the macro- scopic density of a specimen which is influenced by the weight and volume of the specimen. This is because the macroscopic specimen, in contrast, ex- hibits minute cracks and pores. Determining the X-ray density, also known as ''theoretical density'', is essential because it may be used to evaluate ac- tual porosity by comparing it to the macroscopic density of the sintered compacts. The theoretical density or X-ray density (dx-ray) has been calcu- lated from the lattice parameter values using the expression below [28], dX−ray = 8M Na3 (2) where, M is the molecular weight of the ferrite sample, N is the Avogadro number and a is the lat- tice parameter of the unit cell. From the values of X-ray and experimental den- sities, the percentage of porosity of the samples was calculated using the relation, The percentage of porosity, dX−ray − dbulk dX−ray × 100 (3) The experimental density, X-ray density, and porosity of the samples have been presented in Ta- ble 1. D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 258 Table 1: Optimum firing temperatures, bulk density, X-ray density, and percentage of porosity of IN- 1050, ID-1000, and IE-1000 samples Composition Optimum firing temperature (°C) Bulk density (g/cm3) X-ray density (g/cm3) Porosity (%) Ni0.65Zn0.35Fe2.05O4 1050 4.498 5.355 16.0 Ni0.65Zn0.40Fe1.95O4 1000 4.516 5.360 15.8 Ni0.60Zn0.35Fe2.05O4 1000 4.577 5.340 14.3 It is speculated that the production of Fe2+ ions in the sample processed at greater annealing tem- peratures is the cause of the higher bulk density of the IE-1000 composition. The larger sintering tem- peratures facilitate the reduction of Fe3+ ions into Fe2+ ions creating oxygen vacancies in the material which promotes the formation of larger grains with higher densities [27]. 3.3 EDX spectra Energy-dispersive X-ray spectroscopy (EDX) is used to record the elemental composition of the sin- tered samples. Figures 3 to 5 illustrate EDX spec- tra for the ID-1000, IE-1000, and IN-1050 samples. The observed presence of the elements, nickel (Ni), zinc (Zn), iron (Fe), and oxygen (O) in the spec- tra confirms that the nanoparticles belong to Ni-Zn ferrite material with no impurities. 3.4 FTIR spectra Figure 6 represents the room temperature FTIR spectra recorded in the range from 3000 cm-1 to 300 cm-1 on the Nicolet-MAGNA-550 spectrome- ter using the KBr pellet for IN-1050, IE-1000, and ID-1000 samples. Each spectrum has two significant absorption bands corresponding to Fe2+ O2- vibrations at tetrahedral and octahedral sites, respectively, be- tween 592-595 cm-1 and 414-420 cm-1 [29]. The absorption band 2363 cm-1 corresponds to the at- mospheric carbon dioxide absorbed on the surface of the particles during sample preparation [30]. A weak band was observed at around 470 cm-1, at- tributed to the splitting of the octahedral band due to the Jahn-Teller distortion, confirming the pres- ence of the Fe2+- O2- vibration band in the fer- rite [31]. Table 2 shows the band positions that cor- respond to tetrahedral and octahedral metal com- plexes. Figure 3: EDX spectra of ID-1000 sample. Figure 4: EDX spectra of IE-1000 sample. Figure 5: EDX spectra of IN-1050 sample. Table 2: Band positions and Fe3+ - O2- bond force constants for the samples. Sample (Tetrahedral) cm-1 (Octahedral) cm-1 Fe3+-O2- Bond force constant (105 dyne/cm) Tetrahedral (Kt) Octahedral (Ko) IN 1050 592 414 227 133 ID 1000 595 417 223 135 IE 1000 593 420 228 137 D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 259 In comparison to the corresponding bands of IN- 1050, the tetrahedral band (v1) of ID-1000 and oc- tahedral band (v2) of IE-1000 exhibit a shift to- wards the higher wave numbers. The tetrahedral band shift suggests that Zn2+ (0.60 Å) ions prefer to occupy tetrahedral sites and push Fe3+ ions to- wards oxygen ions due to the larger ionic radius of Zn2+ than Fe3+ (0.49 Å) ion. This is expected to result in a decrease in the distance between Fe3+ - O2- ions. The presence of a weak absorption band, 668 cm-1 could be attributed to the presence of the Zn2+ ions at the tetrahedral sites [32] correspond- ing to the Zn2+ - O2- tetrahedral complexes. An increase in zinc concentration resulted in a corre- sponding increase in band intensity (Figure 7) in the ID-1000 sample. Figure 6: FTIR spectra of Ni-Zn ferrites. Figure 7: Magnified pictures of absorption bands of Ni-Zn ferrite samples. Due to a change in bond length at B-sites, there is a shift of the octahedral absorption band in the IE-1000 sample causing an increase in the force con- stant of the octahedral site when compared to the normal sample. The force constant for the Fe3+ - O2- bond has been estimated with the help of the formula shown below [33], K = 42c22 (4) (all values are in CGS), where c is the speed of light, is the wave number and is the reduced mass for Fe3+ and O2- ions. Table 2 shows the esti- mated force constants for the tetrahedral and octa- hedral sites. Generally, there is a decrease in bond length and an increase in force constant for either site if the radius of the impurity ion is lower than the displaced ion. The concentration of displaced nickel ion and the excess iron ion is the same in the IE-1000 sample. The rise in iron concentration at octahedral sites could improve the reduced mass, besides substituting the nickel ions at octahedral sites and the process is in charge of the variations noticed in band position and force constant. To have the quantitative distribution of ions on tetrahedral and octahedral sites, effective cation distribution is needed. Further, the distribution helps to discuss the changes taking place in the peak position of the absorption bands with the amount of iron content in the Ni-Zn system. For this purpose, the cation distribution has been proposed based on experimentally obtained saturation magnetization measurements. 4 Conclusions The sol-gel process was adopted in preparing the Ni-Zn nanoferrites with varying amounts of iron in the composition. XRD shows cubic spinel struc- ture except for one extra peak in all three samples (IN 800℃; IE 800℃, and ID 900℃; 800℃, 900℃ and 1000℃) around 2= 40.9° is related to the iron oxide (Fe2O3) and is related to JCPDS 89-8104). In comparison to the IN-1050 bands, the ID-1000 and IE-1000 samples exhibit shifts towards higher wave numbers in the tetrahedral and octahedral bands, respectively. A weak band was observed at around 470 cm-1 in FTIR spectroscopy, attributed to the splitting of the octahedral band due to the Jahn-Teller distortion, confirming the presence of the Fe2+- O2- vibration band in the ferrite. There is a decrease in bond length and an increase in force constant for either site if the radius of the impurity ion is lower than the displaced ion. The iron content explicitly affect the magnetic and hence hyperther- mial phenomena. D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 260 References [1] P. Gas. Essential facts on the history of hyperthermia and their connections with electromedicine. Przeglad Elektrotechniczny, 87(12B):37–40, 2011. [2] H. Fatima, T. Charinpanitkul, and K. S. Kim. Fundamentals to apply magnetic nanoparti- cles for hyperthermia therapy. Nanomaterials, 11(5), 2021. [3] D. Parajuli, N. Murali, and K. Samatha. Cor- relation between the magnetic and dc resistiv- ity studies of cu substituted ni and zn in ni- zn ferrites. BIBECHANA, 19(1–2):61–67, Sep 2022. [4] D. Parajuli, P. Taddesse, N. Murali, and K. Samatha. Study of structural, electromag- netic and dielectric properties of cadmium sub- stituted ni–zn nanosized ferrites. Journal of the Indian Chemical Society, 99(3):100380, Mar 2022. [5] D. Parajuli and K. Samatha. Structural anal- ysis of cu substituted ni\zn in ni-zn ferrite. BIBECHANA, 18(1):128–133, Jan 2021. [6] D. Parajuli and K. Samatha. Morphological analysis of cu substituted ni\zn in ni-zn fer- rites. BIBECHANA, 18(2):80–86, May 2021. [7] A. M. Kumar, M. C. Varma, C. L. Dube, K. H. Rao, and S. C. Kashyap. Develop- ment of ni–zn nanoferrite core material with improved saturation magnetization and dc re- sistivity. Journal of Magnetism and Magnetic Materials, 320(14):1995–2000, Jul 2008. [8] A. Verma, T. C. Goel, R. G. Mendiratta, and M. I. Alam. Dielectric properties of nizn ferrites prepared by the citrate precursor method. Materials Science and Engineering: B, 60(2):156–162, Jun 1999. [9] X. Jia, D. Chen, X. Jiao, T. He, and H. Wang. Monodispersed co, ni-ferrite nanoparticles with tunable sizes: controlled synthesis, mag- netic properties, and surface modification. Journal of Physical Chemistry C, 2008. Ac- cessed: Nov. 07, 2023. [10] R. M. Mohamed, M. M. Rashad, F. A. Haraz, and W. Sigmund. Structure and magnetic properties of nanocrystalline cobalt ferrite powders synthesized using organic acid precur- sor method. Journal of Magnetism and Mag- netic Materials, 322(14):2058–2064, Jul 2010. [11] M. Atif, M. W. Asghar, M. Nadeem, W. Khalid, Z. Ali, and S. Badshah. Synthesis and investigation of structural, magnetic and dielectric properties of zinc substituted cobalt ferrites. Journal of Physics and Chemistry of Solids, 123:36–42, Dec 2018. [12] A. V. Raut, R. S. Barkule, D. R. Shengule, and K. M. Jadhav. Synthesis, structural in- vestigation and magnetic properties of zn2+ substituted cobalt ferrite nanoparticles pre- pared by the sol–gel auto-combustion tech- nique. Journal of Magnetism and Magnetic Materials, 358–359:87–92, May 2014. [13] T. Zeeshan, S. Anjum, S. Waseem, and L. Mustufa. Tailoring of structural and mag- netic properties by substitution of copper in cobalt chromium ferrites. Ceramics Interna- tional, 44(15):17709–17715, Oct 2018. [14] G. Kumar et al. Superparamagnetic behaviour and evidence of weakening in super-exchange interactions with the substitution of gd3+ ions in the mg–mn nanoferrite matrix. Materials Research Bulletin, 63:216–225, Mar 2015. [15] P. Appa Rao et al. A systematic study of cobalt-zinc ferrite nanoparticles for self- regulated magnetic hyperthermia. Journal of Alloys and Compounds, 794:60–67, Jul 2019. [16] T. J. Shinde, A. B. Gadkari, and P. N. Vasam- bekar. Magnetic properties and cation distri- bution study of nanocrystalline ni–zn ferrites. Journal of Magnetism and Magnetic Materials, 333:152–155, May 2013. [17] H. Kavas, A. Baykal, M. S. Toprak, Y. Köseoǧlu, M. Sertkol, and B. Aktaş. Cation distribution and magnetic properties of zn doped nife2o4 nanoparticles synthesized by peg-assisted hydrothermal route. Journal of Alloys and Compounds, 479(1–2):49–55, Jun 2009. [18] P. Gao et al. Structural and magnetic proper- ties of ni1xznxfe2o4 (x=0, 0.5 and 1) nanopow- ders prepared by sol–gel method. Journal of Magnetism and Magnetic Materials, 348:44– 50, Dec 2013. [19] H. Su, H. Zhang, X. Tang, Y. Jing, and Y. Liu. Effects of composition and sintering tempera- ture on properties of nizn and nicuzn ferrites. Journal of Magnetism and Magnetic Materials, 310(1):17–21, Mar. 2007. [20] K. Sun, Z. Lan, Z. Yu, X. Jiang, and J. Huang. Phase formation, grain growth and magnetic properties of nicuzn ferrites. Journal of Mag- netism and Magnetic Materials, 323(7):927– 932, Apr. 2011. D. Parajuli et al./ BIBECHANA 21 (2024) 254-261 261 [21] X. He, G. Song, and J. Zhu. Non- stoichiometric nizn ferrite by sol-gel process- ing. Materials Letters, 59(14–15):1941–1944, Jun. 2005. [22] D. Parajuli, S. Uppugalla, N. Murali, A. Ramakrishna, B. Suryanarayana, and K. Samatha. Synthesis and characterization mxene-ferrite nanocomposites and its applica- tion for dying and shielding. Inorganic Chem- istry Communications, 148:110319, Feb. 2023. [23] D. Parajuli and K. Samatha. Structural and cation distribution analysis of nickel- copper/nickel-magnesium substituted lithium ferrites. BIBECHANA, 21(1):74–82, Mar. 2024. [24] D. Parajuli, N. Murali, and K. Samatha. Cr3+ substitution effect on co-cu and cu-co nano fer- rites on structural and morphological proper- ties. BIBECHANA, 20(3):275–284, Nov. 2023. [25] D. D. Andhare, S. R. Patade, M. V. Khed- kar, A. A. Nawpute, and K. M. Jadhav. Inten- sive analysis of uncoated and surface modified co-zn nanoferrite as a heat generator in mag- netic fluid hyperthermia applications. Applied Physics A: Materials Science and Processing, 128(6), Jun. 2022. [26] J. S. Ghodake, R. C. Kambale, T. J. Shinde, P. K. Maskar, and S. S. Suryavanshi. Mag- netic and microwave absorbing properties of co2+ substituted nickel–zinc ferrites with the emphasis on initial permeability studies. Jour- nal of Magnetism and Magnetic Materials, 401:938–942, Mar. 2016. [27] C. Sujatha, K. V. Reddy, K. S. Babu, A. R. Reddy, and K. H. Rao. Effects of heat treat- ment conditions on the structural and mag- netic properties of mgcuzn nano ferrite. Ce- ramics International, 38(7):5813–5820, Sep. 2012. [28] S. B. Singh et al. Structural, thermal and magnetic studies of mgxzn1xfe2o4 nanofer- rites: Study of exchange interactions on mag- netic anisotropy. Ceramics International, 42(16):19179–19186, Dec. 2016. [29] M. M. Mallapur, P. A. Shaikh, R. C. Kambale, H. V. Jamadar, P. U. Mahamuni, and B. K. Chougule. Structural and electrical proper- ties of nanocrystalline cobalt substituted nickel zinc ferrite. Journal of Alloys and Compounds, 479(1–2):797–802, Jun. 2009. [30] M. Sangmanee and S. Maensiri. Nanostruc- tures and magnetic properties of cobalt ferrite (cofe 2o4) fabricated by electrospinning. Ap- plied Physics A: Materials Science and Pro- cessing, 97(1):167–177, Oct. 2009. [31] N. Singh, A. Agarwal, S. Sanghi, and P. Singh. Effect of magnesium substitution on dielectric and magnetic properties of ni–zn ferrite. Phys- ica B: Condensed Matter, 406(3):687–692, Feb. 2011. [32] A. Pradeep and G. Chandrasekaran. Ftir study of ni, cu and zn substituted nano-particles of mgfe2o4. Materials Letters, 60(3):371–374, Feb. 2006. [33] P. A. Shaikh, R. C. Kambale, A. V. Rao, and Y. D. Kolekar. Structural, magnetic and electrical properties of co–ni–mn ferrites syn- thesized by co-precipitation method. Journal of Alloys and Compounds, 492(1–2):590–596, Mar. 2010. Introduction Method of preparation Materials Results and Discussion XRD study FESEM study EDX spectra FTIR spectra Conclusions