Volume 2021, Issue 1 9410074

Research Article

Open Access

Doped Nanostructured Manganese Ferrites: Synthesis, Characterization, and Magnetic Properties

Corresponding Author

Sami-ullah Rather

[email protected]

orcid.org/0000-0001-5676-0728

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Usman Saeed,

Usman Saeed

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Abdulrahim Ahmad Al-Zahrani,

Abdulrahim Ahmad Al-Zahrani

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Hisham S. Bamufleh,

Hisham S. Bamufleh

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Hesham Abdulhamed Alhumade,

Hesham Abdulhamed Alhumade

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Aqeel Ahmad Taimoor,

Aqeel Ahmad Taimoor

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

O. M. Lemine,

O. M. Lemine

Physics Department, College of Sciences, Imam Mohammad Ibn Saud Islamic University (IMSIU), Riyadh, Saudi Arabia imamu.edu.sa

Search for more papers by this author

Arshid Mahmood Ali,

Arshid Mahmood Ali

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Belal Al Zaitone,

Belal Al Zaitone

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Muhammad Mahmud Alam,

Muhammad Mahmud Alam

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Sami-ullah Rather,

Corresponding Author

Sami-ullah Rather

[email protected]

orcid.org/0000-0001-5676-0728

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Usman Saeed,

Usman Saeed

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Abdulrahim Ahmad Al-Zahrani,

Abdulrahim Ahmad Al-Zahrani

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Hisham S. Bamufleh,

Hisham S. Bamufleh

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Hesham Abdulhamed Alhumade,

Hesham Abdulhamed Alhumade

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Aqeel Ahmad Taimoor,

Aqeel Ahmad Taimoor

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

O. M. Lemine,

O. M. Lemine

Physics Department, College of Sciences, Imam Mohammad Ibn Saud Islamic University (IMSIU), Riyadh, Saudi Arabia imamu.edu.sa

Search for more papers by this author

Arshid Mahmood Ali,

Arshid Mahmood Ali

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Belal Al Zaitone,

Belal Al Zaitone

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

Muhammad Mahmud Alam,

Muhammad Mahmud Alam

Department of Chemical and Materials Engineering, King Abdulaziz University, P.O. Box 80204 Jeddah 21589, Saudi Arabia kau.edu.sa

Search for more papers by this author

First published: 24 December 2021

https://doi.org/10.1155/2021/9410074

Citations: 5

Academic Editor: Filippo Giubileo

Share a link

Email
Wechat
Bluesky

Abstract

Nanocrystalline aluminum-doped manganese ferrite was synthesized by facile thermal treatment method. Nanostructure-doped ferrite with crystalline size that ranged between 3.71 and 6.35 nm was characterized via X-ray diffraction (XRD), scanning electron microscopy (SEM), X-ray photoelectron spectroscopy (XPS), and vibrating-sample magnetometry (VSM). The Scherrer and Williamson-Hall hypothesis techniques were utilized to determine lattice constants and strain. Various types of structural properties including octahedral and tetrahedral site radius, bond lengths and angles, hopping parameter, oxygen positional parameters, site bonds, and edge lengths were determined from XRD spectrum analysis. Discrepancy in the hypothetically expected angle indicates improvement of A-B superexchange intercommunication. Furthermore, magnetic-hysteresis (M-H) and XPS analysis support the claim of enhancement. The presence of the ionic nature of iron and manganese in ferrite is Fe^II, Fe^III, Mn^II, and Mn^IV as revealed by the results of XPS. Moreover, XPS assists in an excellent way to understand the properties such as configuration, chemical nature, and average inversion degree of doped ferrite samples. The spin noncollinearity and exquisite interaction amid the sublattice are responsible for the decrease in the saturation and remnant magnetization determined from the hysteresis loop at ambient temperature with maximum magnetic field of 1.8 T.

1. Introduction

The transition metal-oriented nanoferrites which consist of unique structural, electrical, thermal, and magnetic characteristics are utilized for various types of engineering and biomedical applications. Nanostructure ferrites are used in different types of biological applications such as X-ray diagnosis, drug delivery, hyperthermia, and magnetic resonance imaging (MRI) [1–4]. Moreover, nanocrystalline spinel ferrites possess a variety of characteristics which are applied in the field of electromagnetic interference (EMI), circuit-based electronic, pigments, sensors, radar systems, motors, and inductors [5–12]. Manganese ferrite (MnFe₂O₄) nanoparticles (NPs) with other ferrites are considered as a crucial tool for biomedical applications particularly for enhancing efficiency of magnetic resonance imaging, hyperthermia, and drug delivery [13]. The properties such as facile preparation, proper saturation magnetization, inflated Curie temperature, high coercivity, and redundant anisotropic constant make manganese NPs an exceptional contender for biological applications [14, 15].

Generally spinel-based ferrites are represented by the specification AB₂O₄, where A and B indicates divalent and trivalent cations. Ferrites exhibit different types of unit cell with eight formula units in each cell. The oxygen anions with larger size and metal cations with smaller size occupies face-centered cubic (fcc) and interstitial sites, respectively. The magnetite (Fe₃O₄), a form of iron oxide is the primary building block of most of the ferrites [16]. The (M²⁺_1-δFe³⁺_δ)[M²⁺_δFe³⁺_2-δ]O₄ formula provides general information related to sites and degree of inversion (δ). The () and [] bracket represents tetrahedral and octahedral sections and “δ” furnishes ferrite nature in terms of whether the structure is normal, inverse or random. When δ = 0, the formula is expressed as (M²⁺)[Fe₂³⁺]O₄, and the ferrite is called normal spinel ferrite. When δ = 1, the formula is expressed as (Fe³⁺)[M²⁺Fe³⁺]O₄, and the ferrite is called inverse spinel ferrite. When 0 < δ < 1, such as δ = 0.3, 0.6, or 0.9, the ferrite is called as mixed spinel ferrite. When δ = 0.3, the formula is expressed as (M_0.7²⁺Fe_0.3³⁺)[M_0.3²⁺Fe_1.7³⁺]O₄^2-[17]. Zinc ferrite (ZnFe₂O₄), a normal spinel, where Zn²⁺ cations represent as tetrahedral site and Fe³⁺ cations as octahedral sites leads to the formula as (Zn²⁺)[Fe₂³⁺]O₄ [18]. Cobalt ferrite (CoFe₂O₄) is an inverse ferrite, where Co²⁺ prefers octahedral and Fe³⁺ prefers uniform placement in octahedral and tetrahedral sites [19]. Manganese ferrite (MnFe₂O₄) is a mixed ferrite, where Mn²⁺ and Fe³⁺ prefer both tetrahedral and octahedral bonding sites [20]. Structural, magnetic, and optical characteristics of ferrites depends upon tetrahedral and octahedral sites occupied by divalent and trivalent cations [21, 22]. Furthermore, particle size distribution (PSD) also affects optical and magnetic characteristics of spinel ferrites [23, 24].

Ferrite nanoparticles bearing new unique characteristics are prepared by different routes which include high-energy ball milling, solvothermal, coprecipitation, sol-gel method, thermal decomposition, hydrothermal, microemulsion, electrochemical, and laser ablation method [25–33]. It was reported that the crystal structure, size, and magnetic properties of ferrites including manganese ferrite are influenced by calcinations, reaction duration, capping reagent, and pH [34–36]. The preparation methods including thermal decomposition, microemulsion, and coprecipitation affect crystal structure and magnetic properties of ferrites as reported by Gyergyek et al. [37]. Furthermore, it was also reported that different types of the preparation method change cation distribution, composition, and crystallinity among tetrahedral and octahedral sites [37–39]. The lattice parameter and average strain of cobalt ferrites vary with doping of erbium. Furthermore, this variation is due to a large size of Er³⁺ cations as compared to Fe³⁺ ions [40]. Incorporation of Mg into ZnFe₂O₄ significantly affects the rearrangement of cation distribution at tetrahedral and octahedral sites [41]. The crystal size of nickel-cobalt spinel changes upon doping of rare-earth metals. Moreover, variation in crystal size is because of blocking of crystal expansion by large size metals. The crystal size and surface area of ferrite are influenced by changing the variation of different types of metals such as La, Zn, Cd, and Ni [27, 40–44].

In this research work, the preparation of mixed spinel ferrite MnFe_2−xAl_xO₄ (0 ≤ x ≤ 0.9) with (x) = 0.0, 0.3, 0.6, and 0.9 via a thermal method in association with capping agent polyvinylpyrrolidone is presented in detail. For mixed doped manganese spinel ferrite preparation, thermal disintegration route was chosen because of distinct accomplishments such as environmental acceptance, cheap, and persistent reproducibility; however, this process has a few drawbacks which include shape discrepancy and cluster of particles. Detailed characterization analysis of crystal structural parameter, nanostructure morphology, and quantitative assessment and magnetization characteristics of purified and Al-doped manganese mixed ferrite were also reported in this research work.

2. Experimental

2.1. Synthesis

Analytical precursors were used for the synthesis of pure and Al-doped manganese ferrite MnFe_2−xAl_xO₄ (x = 0.0, 0.3, 0.6, and 0.9) without repeating purification: polyvinylpyrrolidone (PVP) (Alfa Aesar), iron (III) nitrate nonahydrate [Fe(NO₃)₃·9H₂O] (min. 98%, Sigma-Aldrich), manganese (II) nitrate hexahydrate [Mn(NO₃)₂·6H₂O] (min. 98%, Sigma-Aldrich), and aluminum nitrate nonahydrate [Al(NO₃)₃·9H₂O] (min. 98%, Sigma-Aldrich).

In a thermal synthesis process of MnFe₂O₄, a solution containing 0.2 mmol (0.0808 g) Fe(NO₃)₃·9H₂O and 0.1 mmol (0.0179 g) Mn(NO₃)₂·6H₂O was vigorously stirred for 2 h, followed by inclusion of capping agent (PVP) solution. The capping agent solution was synthesized by adding 0.1 g of PVP into 50 ml of deionized water (DI) at 90°C. The mixed solution was vigorously stirred for 2 h at room temperature (RT). The pH of the above solution was determined by litmus paper which was followed by drying at 80°C for 24 h. The dried orange-colored sample was converted into powder and calcinated at 500°C for 4 h to eliminated PVP in order to form pristine MnFe₂O₄. A similar method was executed for the preparation of MnFe_2−xAl_xO₄ (x = 0.3, 0.6, and 0.9). For clarity, hereafter, the Al-doped MnFe₂O₄ are referred to as MnFe_1.7Al_0.3O₄, MnFe_1.4Al_0.6O₄, and MnFe_1.1Al_0.9O₄. A graphic reaction design for the synthesis of MnFe_2−xAl_xO₄ is presented in Figure 1.

Details are in the caption following the image — **Figure 1**
Open in figure viewer PowerPoint

Schematic design of the reaction arrangement of the synthesis of MnFe_2−xAl_xO₄.

2.2. Characterization

Structure of pristine and doped ferrite was determined by the XRD spectrum. The XRD spectrum was achieved using an INEL CPS 180 XRD Equinox 1000 diffractometer assembled with Co-Kα1 emission (λ = 1.789 Å) and regulated at 40 kV and 30 mA. The analysis was managed in the 2θ range of 10-80° at RT. The nanostructure behavior of samples was investigated by SEM. A wafer-delicate carbon film captivated inner side of a copper framework was used to install nanoparticles present in an ethanol solution. The XPS was operated by employing the SPEC GmbH (Germany) spectrometer at RT. The instrument is assembled with X-ray-bearing dual anode origin SPECS XR-50 Mg-Kα (hn = 1283.6 eV) in the presence of lift-off angle of photoelectrons of 90°. The ferrite samples were converted into pellets, before shifting to a high vacuum chamber. The vacuum was managed at 5 × 10⁻⁹ bar, during the operation. In order to perform surface quantification of the ferrite sample, a detailed operating method was employed containing high-resolution spectrum of O1s and C1s. To achieve a high quality XPS spectrum, calibration of the BE scale was performed by BE of C1s peak at 284.6 eV. The Lake Shore 7400 magnetometer VSM that was equipped with a 1.8 Tesla magnet was utilized to determine magnetic properties of ferrite samples at RT. The hysteresis loop of ferrite samples was obtained by plotting magnetization verses magnetic field. Furthermore, to measure remnant magnetization (Mr), saturation magnetization (Ms), and coercivity, magnetic hysteresis loops were utilized.

3. Results and Discussion

Powder XRD pattern results of MnFe_2−xAl_xO₄ (0 ≤ x ≤ 0.9) are presented in Figure 2, and profiles a, b, c, and d refer to the content of x = 0.0, 0.3, 0.6 and 0.9, respectively. The visibly strong peaks were found between 10 and 80°. The strong peaks shown in Figure 2 are contemplations from the (111), (220), (311), (222), (400), (422), (511), (440), (620), (533), and (444) planes of purified and Al-doped ferrites. All these prominent peaks are associated to Bragg’s contemplation of cubic ferrite with space group Fd3m. The nonexistence of other oxide peaks suggests that precursor is free from impurity. The inflation of Al content produces broadened diffraction peaks and simultaneously decreases intensity, which indicates development of nanostructured ferrites. The strong main peak (311) refers to crystallinity of the structure of ferrites. The decrease in crystallite size as the Al content elevates is shown in Table 1. The full width at half-maximum is utilized in the Scherer equation (Equation (1)) to determine crystal size (D). The main peak in the XRD spectrum was employed to calculate crystal size.

(1)

Table 1. XRD parameters of MnFe_2−xAl_xO₄ (x = 0.0, 0.3, 0.6, and 0.9).

Sample name	Lattice parameter a (Å)	Cell volume V (Å)³	Bulk density ρ_m (gm/cm³)	X-ray density ρ_x−ray (gm/cm³)	Porosity (%)	Crystal size (nm)
MnFe₂O₄	8.515	617.380	2.998	4.962	39.580	6.35
MnAl_0.3Fe_1.7O₄	8.512	613.910	2.885	4.775	39.581	5.99
MnAl_0.6Fe_1.4O₄	8.499	605.170	2.772	4.589	39.583	4.47
MnAl_0.9Fe_1.1O₄	8.458	601.120	2.660	4.403	39.586	3.71

X-ray wavelength, FWHM in radians, and Bragg’s angle, respectively, refer to λ, β, and θ.

Table 1 shows average crystal size data calculated from Equation (1) and was found to be 6.35, 5.99, 4.47, and 3.71 nm. The capping agent PVP was employed during the synthesis process to avert agglomeration of ferrite particles. The absence of PVP creates aggregation of particles owing to high energy of small particles as reported in the Ostwald ripening process [45]. Table 1 confirms the variation in lattice parameter, X-ray density, bulk density, cell volume, and porosity as the content of nonmagnetic Al changes. Furthermore, increasing Al concentration decreases lattice constant parameters, density, and particle size as shown in Figure 3. Dessai et al. also observed that increasing nonmagnetic Al³⁺ content in manganese ferrite decreases lattice parameter and density [46].

The Nelson-Riley function F(θ) for each reflection of MnFe_2−xAl_xO₄ was calculated by using the following relation:

(2)

Figure 4(a) shows Nelson-Riley function of nanocrystalline MnFe_2−xAl_xO₄. Diffraction angle from 10 to 80° was utilized to determine lattice parameters “a_o” by extrapolating F(θ). True lattice value “a_o” and average value “a” variation is shown in Figure 4(b). It is visible from Figure 4(b) that little disparity between true value lattice constant “a_o” and the average value lattice constant “a” existed. Moreover, average value lattice constant “a” is slightly more than true value lattice constant “a_o.” Both true and average value lattice constants reduces as the content of Al elevates. The reduction of both lattice constants may be due to change in ionic radius between Al³⁺ (0.51 Å) and Fe³⁺ (0.67 Å). According to the literature, it is obvious that replacement of highly magnetic Fe³⁺ ions by nonmagnetic Al³⁺ reduces lattice constant as Al content elevates [46, 47]. Lattice constant reduces from 8.515 Å to 8.458 Å as the Al content in the doped ferrite increases is shown in Figure 3 (right panel). The reduction in crystallite size from 6.35 nm to 3.71 nm presented in Figure 3 (left panel) may be due to substitution of larger size Fe³⁺ ions by smaller size Al³⁺ ions. High porosity and lattice constant shown in Table 1 are other reasons responsible for crystal size reduction. The parameters a, V, ρ_m, ρ_x−ray, and P presented in Table 1 were determined from Equations (3) to (7). These parameters decrease as the Al content increases except for porosity which is due to reduction of crystal size and lattice constant. High porosity as the Al content increases may be due to extra vacancies established by substitution of Fe³⁺ cations by Al³⁺ cations [48].

(3)

(4)

(5)

(6)

(7)

The strain created by crystal defects and distortions is due to addition of Al in manganese ferrites. The average strain <ε> of Al-doped manganese spinel was calculated by employing the following equation:

(8)

Addition of Equations (1) and (8) produces noticed line breadth in the form of Equation (9).

(9)

(10)

Williamson-Hall (W-H) calculations shown above in the form of Equations (9) and (10) were used to calculate crystallite size and average strain. The “β_hklcosθ” verses “4sinθ” presented in Figure 5 is employed to calculate both the particle size and the strain. The linear fit of the crystal size and strain follows the uniform deformation process, where the strain is assumed as homogeneous in all directions, a property of isotropy. The W-H and Scherer formulas used for the calculation of the average strain were in complete harmony with each other as shown in Table 2.

Table 2. Average strain of MnFe_2−xAl_xO₄ (x = 0.0, 0.3, 0.6, and 0.9).

Sample name	Scherrer method	W-H method
Sample name	〈ε〉 × 10⁻³	〈ε〉 × 10⁻³
MnFe₂O₄	10.90	27.10
MnFe_1.7Al_0.3O₄	7.99	6.50
MnFe_1.4Al_0.6O₄	10.75	21.50
MnFe_1.1Al_0.9O₄	11.44	23.60

The bond length of tetrahedral and octahedral sites was affected by the lattice constants which were created by crystal size reduction. The bond lengths shown in Table 3, associated to tetrahedral (R_A) and octahedral bonding sites (R_B) were determined by Equations (11) and (12), where δ = u − 0.375. The R_A and R_B site is the closest gap between A and B with oxygen ions. The higher R_B compared to R_A is the main reason that the Mn²⁺ cation capability is towards O^2- anions. The existence of Al³⁺ cations in ferrites reinforces the gap between Fe³⁺ and Al³⁺ cations. The L_A and L_B values shown in Table 3 determined from Equations (13) and (14) refer to hopping lengths and space between magnetic ions present in the tetrahedral and octahedral bonding sites. The change in hopping lengths of tetrahedral and octahedral sites is associated to change in crystal size which is exactly applicable to lattice constants [49]. The ionic radius alteration between Al³⁺ (0.51 Å) and Fe³⁺ (0.67 Å) ions is the other reason associated to change in hopping lengths. The tetrahedral and octahedral bond lengths (d_Ax and d_Bx), the shared tetrahedral edge length (d_AxE), and shared and unshared octahedral edge lengths (d_BxE and d_BxEU) shown in Table 3 were calculated from Equations (15) to (19). Furthermore, these values shown in Table 3 and Figure 6 suggest reduction as Al content in ferrites increases, therefore indicating complete dominance of the lattice constants and ionic radii [49].

(11)

(12)

(13)

(14)

(15)

(16)

(17)

(18)

(19)

Table 3. The bond lengths (R_A and R_B) and hopping lengths for tetrahedral and octahedral sites (L_A and L_B), tetrahedral and octahedral bond lengths (d_Ax and d_Bx), the shared tetrahedral edge length (d_AxE), and shared and unshared octahedral edge lengths (d_BxE and d_BxEU) of MnFe_2−xAl_xO₄ (0 ≤ x ≤ 0.9).

Sample name	Bond length (Å)		Hopping length (Å)		d_Ax (Å)	d_Bx (Å)	d_AxE (Å)	d_BxE (Å)	d_BxEU (Å)
Sample name	R_A	R_B	L_A	L_B	d_Ax (Å)	d_Bx (Å)	d_AxE (Å)	d_BxE (Å)	d_BxEU (Å)
MnFe₂O₄	1.9173	2.0871	2.0870	2.0870	1.9173	2.0870	3.1309	2.8901	3.0118
MnFe_1.7 Al_0.3O4	1.9166	2.0863	2.0863	2.0863	1.9167	2.0863	3.1298	2.8890	3.0107
MnFe_1.4 Al_0.6O4	1.9137	2.0831	2.0831	2.0831	1.9137	2.0831	3.1250	2.8846	3.0061
MnFe_1.1 Al_0.9O4	1.9045	2.0731	2.0731	2.0731	1.9045	2.0730	3.1100	2.8707	2.9916

The nanostructure characterization of MnFe_2−xAl_xO₄ performed by SEM is presented in Figure 7, where (a) corresponds to pure ferrite and (b–d) correlate to Al-doped manganese ferrites. The scale bar for all the samples is 100 nm. The agglomeration of smaller particles is visible in the nanostructured samples of ferrites. The EDX and elemental investigation averaged over different parts of the samples are presented in Table 4.

Table 4. Comparison of target and actual composition in MnFe_2−xAl_xO₄.

Target composition	Composition by EDX
Target composition	Mn	Fe	Al
MnFe₂O₄	0.88	2.35
MnFe_1.7Al_0.3O₄	0.98	2.20	0.42
MnFe_1.4Al_0.6O₄	0.99	1.80	0.71
MnFe_1.1Al_0.9O₄	1.03	1.20	1.06

The XPS measurements shown in Figure 8 were performed to estimate functionalization of ferrite surface with different active groups. Various chemical states A and B associated with ferrite surface states are presented in Figures 8(a)–8(d). The strong peaks existed in the ferrite spectrum of MnFe_2−xAl_xO₄ (x = 0.0, 0.3, 0.6, and 0.9) are correlated to Fe, Mn, O, and Al, respectively. The intense signal was adapted to different peaks including Mn 2p, doublet Fe 2p, O 1s, and Al 2p. The Mn 2p is a singlet based at a binding energy (BE) of 641.94 eV. The doublet signal of Mn 2p_3/2 Mn²⁺ octa and Mn 2p_3/2 Mn⁴⁺ tetra based at BE of 640.89 eV and 642.43 eV are related to Mn 2p_3/2 peak. Similarly, the same trend was detected for Al in the doped sample; however, a peak deviation of ±1 eV was visible. The doublet peak of Fe 2p was deviated from each other by BE 8.45 eV as a result of spin-orbit coupling. The iron 2p_3/2 signals were adapted into three different segments because of the multiplet splitting process. The prominent peaks located at BE 709.59 eV and 711.24 eV are related to Fe 2p_3/2 Fe²⁺ octa and Fe 2p_3/2 Fe³⁺ tetra. The doped samples follow a similar trend with a peak deviation of BE ± 2 eV. The strong peak located at BE 529.88 eV of O is in a multicomponent segment which belongs to the oxide lattice. The remaining less intense peaks of O is based at BE 529.44 eV, 538.99 eV, 533.74 eV, and 535.69 eV which are related to the oxygen bond formation with Fe, Mn, OH, and adsorbed H₂O, respectively. A similar trend for the oxygen peak was also observed in the ferrite doped samples. The Al 2p peak adapted into two prominent peaks located at BE 73.29 and 74.79 eV which are related to octahedral and tetrahedral sites. The Al peak intensity enhances as the Al concentration increases indicating expected substitution of Al³⁺ into manganese ferrite. The doping of Al into manganese ferrite responsible for structural and magnetic property variation is the main reason for peak deviation of Mn and Fe in the doped ferrites. The 45% Mn²⁺ ions are located at octahedral sites, and 55% Mn⁴⁺ ions are based at tetrahedral sites as far as unified intensity of the deconvoluted peaks is concerned. The Mn 2p_3/2 peaks are fitted into two intense peaks located at BE 640.89 eV and 642.43 eV. Moreover, the assessment of Fe²⁺ and Fe³⁺ based at BE 709.59 eV and 711.24 eV is 78% at the octahedral and 22% at tetrahedral bonding sites [50–52]. The substitution formula of MnFe_2−xAl_xO₄ (x = 0.0) could be declared as follows:

(20)

Similarly, the distribution of Mn²⁺, Mn⁴⁺, Fe²⁺, Fe³⁺, and Al³⁺ cations at the octahedral and tetrahedral was determined as reported by integrated intensity of deconvoluted strong peaks in MnFe_2−xAl_xO₄ (x = 0.3, 0.6, and 0.9). The substitution formula of Al-doped manganese ferrite could be designated as follows:

(21)

With regard to the assessment of cations among octahedral and tetrahedral, Al³⁺ cations choose tetrahedral sites, which deals with chances that Al³⁺ cations would substitute Fe³⁺ cations. The substitution of Fe³⁺ cations by Al³⁺ cations is in good compliance with preparation, XRD calculation analysis, EDX spectrum analysis, and magnetic characteristics.

Magnetic hysteresis loops of MnFe_2−xAl_xO₄ measured by vibrating sample magnetometer (VSM) at RT are presented in Figure 9. The pristine manganese ferrite sample displays ferromagnetic type nature bearing saturation magnetization of 47.32 emu/g when compared to the Al-doped sample (inset of Figure 9). The representative magnetic characteristics of purified and Al-doped ferrite samples calculated on the basis of the hysteresis loop including H_c, M_r, M_s, η_exp, and M_r/M_s-squareness ratio are shown in Table 5. The magnetization evaluation was performed by using an additional field area of the calculated M(H) data by employing Langevin dependence [53]:

(22)

where V_eff, ρ, and T are the effective values of the volume, density, and temperature, respectively, and the other values are related to their typical definitions.

Table 5. Coercive field (H_c), remnant magnetization (M_r), saturation magnetization (M_s), experimental molar magnetization (η_exp), and squareness ratio (M_r/M_s) determined from hysteresis loops of the ferrite samples.

Sample name	H_c (Oe)	M_r (emu/g)	M_s (emu/g)	η_exp	R = M_r/M_s
MnFe₂O₄	40	5.01	47.32	1.95	0.106
MnFe_1.7Al_0.3O₄	27	1.97	31.90	1.27	0.062
MnFe_1.4Al_0.6O₄	20	1.18	24.71	0.94	0.050
MnFe_1.1Al_0.9O₄	17	0.35	5.02	0.2	0.065

The Fe²⁺ and Fe³⁺ cation saturation magnetization and coercivity are changed by embedding Al³⁺ cations into manganese ferrite. As a result of integrated intensity of deconvoluted peaks, visible saturation magnetization and coercivity addiction to Mn²⁺ and Mn⁴⁺ ions were negligibly afflicted by the doping of Al³⁺ cations into manganese ferrite. The moderate saturation magnetization contraction and coercivity escalation as the Al content is elevated is shown in Figure 10. The decreased value of M_s and M_r of the doped ferrite sample may be associated to reduced particle size. The reduction in M_s after addition of nonmagnetic Al³⁺ in ferrite is also confirmed by the literature date reported by Dessai et al. [46]. Furthermore, there is a decrease in the average crystallite size control existence of spin inclination and spin canting, which appear by virtue of a defined size and surface-related effects. The reduction in M_s and M_r of doped samples as the Al content is elevated may be due to cation diffusion among the host and embedded groups. The substitution of Fe²⁺ and Fe³⁺ ions by Al³⁺ ions at the octahedral and tetrahedral decreases the bond stability of Fe³⁺-O-Fe³⁺. The decrease in the amount of Fe²⁺ and Fe³⁺ cations in the A- and B-sites decreases the magnetic dipole moment of the B-sublattice and consequently decreases the magnetic moment of ferrites. The exchange of Fe³⁺ cations bearing magnetic moment 5 μ_B with nonmagnetic Al³⁺ cations carrying magnetic moment 0 μ_B decreases the superexchange bonding that balances adjacent magnetic dipoles in an antiparallel form. Moreover, the decrease in overall magnetization is possible because of reinforced spin noncollinearity. The elevation of Al³⁺ ions which decreases the lattice parameter is due to smaller ionic radius (0.55 Å) of Al³⁺ cations as compared to Fe³⁺ cations (0.67 Å). The decrease in magnetization in embedded ferrite is also associated with exchange of cations in the A- and B-sites. The fact is that M_s builds upon the number and type of cation based at different sites in tetrahedral and octahedral bonding sites in the ferrite. The exchange influences the magnetization M_A and M_B of the A and B ferrite sublattices. The affiliation of M_B – M_A produces magnetization in spinel ferrites. In manganese-based ferrite, Mn⁴⁺ ions choose tetrahedral sites and are emphasized as the Al concentration is elevated. The Mn²⁺ ion location in the octahedral sites fades away as the Al content increases. Generally, tetrahedral and octahedral sites in ferrites engaged by Fe³⁺ cations are partially substituted by Al³⁺ cations. The substitution of Fe³⁺ by Al³⁺ cations in the B-sites decides magnetization of manganese ferrites. The reduction of magnetization of the Al-doped ferrite samples is due to substitution of Al³⁺ ions. The squareness ratio (R) less than 0.5 indicates a multidomain structure of ferrite materials while greater than 0.5 signifies a single-domain structure of manganese ferrite. According to the recent investigation carried out related to squareness ratio (R) revealed in several places in the literature, the squareness ratio (R) observed between 0.01 and 0.1 suggests a multidomain structure of ferrite materials [54–56].

4. Conclusions

The significance of Al³⁺ cations as a dopant in nanocrystalline manganese ferrite prepared through the thermal treatment method was discussed. The nanostructured samples were characterized by different methods to examine nanocrystallinity, thermal stability, chemical stability, distribution, and morphological properties. The representative Scherrer formula and Williamson-Hall extrapolation equations were employed to determine the crystallite size and lattice strain parameters. The parameters including ionic radii of tetrahedral and octahedral bonding sites, oxygen positional constants, hopping and bond lengths, bond angles and sites, and edge lengths were determined from the XRD spectrum. The characterization such as XPS and M-H analysis explains the inconsistency in the theoretically anticipated bond angles which implied beefing up of the A-B superexchange synergy. Distribution, chemical form, and degree of inversion were determined from the XPS spectrum. The characteristic magnetic hysteresis loop attained from VSM at RT displays that both M_r and M_s are reduced as the Al content is elevated. This contraction was associated with spin noncollinearity and delicate interactions between sublattices.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This project was funded by the Deanship of Scientific Research (DSR) at King Abdulaziz University, Jeddah, under grant no. (G: 191-135-1442). The authors, therefore, acknowledge with thanks the DSR for the technical and financial support.

Open Research

Data Availability

The data used to support the findings of this study are included within the article.

References

1 Valenzuela R., Novel applications of ferrites, Physics Research International. (2012) 2012, 9, 591839, https://doi.org/10.1155/2012/591839, 2-s2.0-84859732304.
10.1155/2012/591839
Google Scholar
2 Latorre-Esteves M., Cortés A., Torres-Lugo M., and Rinaldi C., Synthesis and characterization of carboxymethyl dextran-coated Mn/Zn ferrite for biomedical applications, Journal of Magnetism and Magnetic Materials. (2009) 321, no. 19, 3061–3066, https://doi.org/10.1016/j.jmmm.2009.05.023, 2-s2.0-67650113938.
10.1016/j.jmmm.2009.05.023
CAS Web of Science® Google Scholar
3 Nigam A. and Pawar S. J., Structural, magnetic, and antimicrobial properties of zinc doped magnesium ferrite for drug delivery applications, Ceramics International. (2020) 46, no. 4, 4058–4064, https://doi.org/10.1016/j.ceramint.2019.10.243.
10.1016/j.ceramint.2019.10.243
Google Scholar
4 Kefeni K. K., Msagati T. A. M., Nkambule T. T. I., and Mamba B. B., Spinel ferrite nanoparticles and nanocomposites for biomedical applications and their toxicity, Materials Science and Engineering: C. (2020) 107, article 110314, https://doi.org/10.1016/j.msec.2019.110314, 31761184.
10.1016/j.msec.2019.110314
PubMed Web of Science® Google Scholar
5 Wang X., Gong L., Zhang D., Fan X., Jin Y., and Guo L., Room temperature ammonia gas sensor based on polyaniline/copper ferrite binary nanocomposites, Sensors and Actuators B: Chemical. (2020) 322, article 128615, https://doi.org/10.1016/j.snb.2020.128615.
10.1016/j.snb.2020.128615
Web of Science® Google Scholar
6 Sukmarani G., Kusumaningrum R., Noviyanto A., Fauzi F., Habieb A. M., Amal M. I., and Rochman N. T., Synthesis of manganese ferrite from manganese ore prepared by mechanical milling and its application as an inorganic heat-resistant pigment, Journal of Materials Research and Technology. (2020) 9, no. 4, 8497–8506, https://doi.org/10.1016/j.jmrt.2020.05.122.
10.1016/j.jmrt.2020.05.122
CAS Web of Science® Google Scholar
7 Ott G., Wrba J., and Lucke R., Recent developments of Mn-Zn ferrites for high permeability applications, Journal of Magnetism and Magnetic Materials. (2003) 254-255, 535–537, https://doi.org/10.1016/S0304-8853(02)00961-7, 2-s2.0-0037211741.
10.1016/S0304-8853(02)00961-7
CAS Web of Science® Google Scholar
8 Kumar Chakradhary V. and Akhtar M. J., Absorption properties of CNF mixed cobalt nickel ferrite nanocomposite for radar and stealth applications, Journal of Magnetism and Magnetic Materials. (2021) 525, article 167592, https://doi.org/10.1016/j.jmmm.2020.167592.
10.1016/j.jmmm.2020.167592
Web of Science® Google Scholar
9 Hernandez M., Messagie M., Hegazy O., Marengo L., Winter O., and van Mierlo J., Environmental impact of traction electric motors for electric vehicles applications, JLCA. (2017) 22, no. 1, 54–65, https://doi.org/10.1007/s11367-015-0973-9, 2-s2.0-84944707422.
10.1007/s11367-015-0973-9
Google Scholar
10 Agrafiotis C. C. and Zaspalis V. T., Self-propagating high-temperature synthesis of MnZn-ferrites for inductor applications, Journal of Magnetism and Magnetic Materials. (2004) 283, no. 2-3, 364–374, https://doi.org/10.1016/j.jmmm.2004.06.054, 2-s2.0-9344249055.
10.1016/j.jmmm.2004.06.054
CAS Web of Science® Google Scholar
11 Caltun O., Dumitru I., Feder M., Lupu N., and Chiriac H., Substituted cobalt ferrites for sensors applications, Journal of Magnetism and Magnetic Materials. (2008) 320, no. 20, e869–e873, https://doi.org/10.1016/j.jmmm.2008.04.067, 2-s2.0-47649108656.
10.1016/j.jmmm.2008.04.067
CAS Web of Science® Google Scholar
12 Ranga R., Kumar A., Kumari P., Singh P., Madaan V., and Kumar K., Ferrite application as an electrochemical sensor: a review, Materials Characterization. (2021) 178, article 111269, https://doi.org/10.1016/j.matchar.2021.111269.
10.1016/j.matchar.2021.111269
Web of Science® Google Scholar
13 Javed F., Abbas M. A., Asad M. I., Ahmed N., Naseer N., Saleem H., Errachid A., Lebaz N., Elaissari A., and Ahmad N. M., Gd³⁺ doped CoFe₂O₄ nanoparticles for targeted drug delivery and magnetic resonance imaging, Magnetochemistry. (2021) 7, no. 4, https://doi.org/10.3390/magnetochemistry7040047.
10.3390/magnetochemistry7040047
PubMed Web of Science® Google Scholar
14 Adeela N., Maaz K., Khan U., Karim S., Nisar A., Ahmad M., Ali G., Han X. F., Duan J. L., and Liu J., Influence of manganese substitution on structural and magnetic properties of CoFe₂O₄ nanoparticles, Journal of Alloys and Compounds. (2015) 639, 533–540, https://doi.org/10.1016/j.jallcom.2015.03.203, 2-s2.0-84926649075.
10.1016/j.jallcom.2015.03.203
CAS Web of Science® Google Scholar
15 Nekvapil F., Bunge A., Radu T., Cinta Pinzaru S., and Turcu R., Raman spectra tell us so much more: Raman features and saturation magnetization for efficient analysis of manganese zinc ferrite nanoparticles, Journal of Raman Spectroscopy. (2020) 51, no. 6, 959–968, https://doi.org/10.1002/jrs.5852.
10.1002/jrs.5852
CAS Web of Science® Google Scholar
16 Fleet M. E., The structure of magnetite: symmetry of cubic spinels, Journal of Solid State Chemistry. (1986) 62, no. 1, 75–82, https://doi.org/10.1016/0022-4596(86)90218-5, 2-s2.0-0022677455.
10.1016/0022-4596(86)90218-5
CAS Web of Science® Google Scholar
17 Pradhan S. K., Bid S., Gateshki M., and Petkov V., Microstructure characterization and cation distribution of nanocrystalline magnesium ferrite prepared by ball milling, Materials Chemistry and Physics. (2005) 93, no. 1, 224–230, https://doi.org/10.1016/j.matchemphys.2005.03.017, 2-s2.0-20444499475.
10.1016/j.matchemphys.2005.03.017
CAS Web of Science® Google Scholar
18 Puspitasari P., Rizkia U. A., Sukarni S., Permanasari A. A., Taufiq A., and Putra A. B. N. R., Effects of various sintering conditions on the structural and magnetic properties of zinc ferrite (ZnFe2O4), Materials Research. (2020) 24, no. 1, 1–5, https://doi.org/10.1590/1980-5373-mr-2020-0300.
10.1590/1980-5373-mr-2020-0300
Web of Science® Google Scholar
19 Rani B. J., Ravina M., Saravanakumar B., Ravi G., Ganesh V., Ravichandran S., and Yuvakkumar R., Ferrimagnetism in cobalt ferrite (CoFe₂O₄) nanoparticles, Nano-Structures and Nano-Objects. (2018) 14, 84–91, https://doi.org/10.1016/j.nanoso.2018.01.012, 2-s2.0-85044648614.
10.1016/j.nanoso.2018.01.012
CAS Google Scholar
20 Ju Y. W., Park J. H., Jung H. R., Cho S. J., and Lee W. J., Electrospun MnFe₂O₄ nanofibers: preparation and morphology, Composites Science and Technology. (2008) 68, no. 7-8, 1704–1709, https://doi.org/10.1016/j.compscitech.2008.02.015, 2-s2.0-42249108849.
10.1016/j.compscitech.2008.02.015
CAS Web of Science® Google Scholar
21 Slimani Y., Almessiere M. A., Sertkol M., Shirsath S. E., Baykal A., Nawaz M., Akhtar S., Ozcelik B., and Ercan I., Structural, magnetic, optical properties and cation distribution of nanosized Ni_0.3Cu_0.3Zn_0.4Tm_xFe_2−xO₄ (0.0 ≤ x ≤ 0.10) spinel ferrites synthesized by ultrasound irradiation, Ultrasonics Sonochemistry. (2019) 57, 203–211, https://doi.org/10.1016/j.ultsonch.2019.05.001, 2-s2.0-85065394626, 31085087.
10.1016/j.ultsonch.2019.05.001
CAS PubMed Web of Science® Google Scholar
22 Hossain A., Sarker M. S. I., Khan M. K. R., and Rahman M. M., Spin effect on electronic, magnetic and optical properties of spinel CoFe₂O₄: a DFT study, Materials Science and Engineering: B. (2020) 253, article 114496, https://doi.org/10.1016/j.mseb.2020.114496.
10.1016/j.mseb.2020.114496
Web of Science® Google Scholar
23 Ramaprasad T., Jeevan Kumar R., Naresh U., Prakash M., Kothandan D., and Chandra Babu Naidu K., Effect of pH value on structural and magnetic properties of CuFe2O4nanoparticles synthesized by low temperature hydrothermal technique, Materials Research Express. (2018) 5, no. 9, article 095025, https://doi.org/10.1088/2053-1591/aad860, 2-s2.0-85052283392.
10.1088/2053-1591/aad860
PubMed Web of Science® Google Scholar
24 Ateia E. E., el-Bassuony A. A., Abdelatif G., and Soliman F. S., Novelty characterization and enhancement of magnetic properties of Co and Cu nanoferrites, Journal of Materials Science: Materials in Electronics. (2017) 28, no. 1, 241–249, https://doi.org/10.1007/s10854-016-5517-y, 2-s2.0-84981485820.
10.1007/s10854-016-5517-y
CAS Web of Science® Google Scholar
25 Zhang Z., Yao G., Zhang X., Ma J., and Lin H., Synthesis and characterization of nickel ferrite nanoparticles via planetary ball milling assisted solid-state reaction, Ceramics International. (2015) 41, no. 3, 4523–4530, https://doi.org/10.1016/j.ceramint.2014.11.147, 2-s2.0-84922931187.
10.1016/j.ceramint.2014.11.147
CAS Web of Science® Google Scholar
26 Wang J., Ren F., Yi R., Yan A., Qiu G., and Liu X., Solvothermal synthesis and magnetic properties of size-controlled nickel ferrite nanoparticles, Journal of Alloys and Compounds. (2009) 479, no. 1-2, 791–796, https://doi.org/10.1016/j.jallcom.2009.01.059, 2-s2.0-67349088424.
10.1016/j.jallcom.2009.01.059
CAS Web of Science® Google Scholar
27 Gul I. H., Ahmed W., and Maqsood A., Electrical and magnetic characterization of nanocrystalline Ni-Zn ferrite synthesis by co-precipitation route, Journal of Magnetism and Magnetic Materials. (2008) 320, no. 3-4, 270–275, https://doi.org/10.1016/j.jmmm.2007.05.032, 2-s2.0-35448958167.
10.1016/j.jmmm.2007.05.032
CAS Web of Science® Google Scholar
28 Chen D. H. and He X. R., Synthesis of nickel ferrite nanoparticles by sol-gel method, Materials Research Bulletin. (2001) 36, no. 7-8, 1369–1377, https://doi.org/10.1016/S0025-5408(01)00620-1, 2-s2.0-0035815779.
10.1016/S0025-5408(01)00620-1
CAS Web of Science® Google Scholar
29 Singh G. and Chandra S., Electrochemical performance of MnFe₂O₄ nano-ferrites synthesized using thermal decomposition method, International Journal of Hydrogen Energy. (2018) 43, no. 8, 4058–4066, https://doi.org/10.1016/j.ijhydene.2017.08.181, 2-s2.0-85029660365.
10.1016/j.ijhydene.2017.08.181
CAS Web of Science® Google Scholar
30 Huo J. and Wei M., Characterization and magnetic properties of nanocrystalline nickel ferrite synthesized by hydrothermal method, Materials Letters. (2009) 63, no. 13-14, 1183–1184, https://doi.org/10.1016/j.matlet.2009.02.024, 2-s2.0-62849118242.
10.1016/j.matlet.2009.02.024
CAS Web of Science® Google Scholar
31 Pillai V., Kumar P., Multani M. S., and Shah D. O., Structure and magnetic properties of nanoparticles of barium ferrite synthesized using microemulsion processing, Colloids and Surfaces: Physicochemical and Engineering Aspects. (1993) 80, no. 1, 69–75, https://doi.org/10.1016/0927-7757(93)80225-4, 2-s2.0-0027702101.
10.1016/0927-7757(93)80225-4
CAS Web of Science® Google Scholar
32 Mazarío E., Herrasti P., Morales M. P., and Menéndez N., Synthesis and characterization of CoFe₂O₄ ferrite nanoparticles obtained by an electrochemical method, Nanotechnology. (2012) 23, no. 35, article 355708, https://doi.org/10.1088/0957-4484/23/35/355708, 2-s2.0-84865156821, 22894928.
10.1088/0957-4484/23/35/355708
PubMed Web of Science® Google Scholar
33 Nawathey-Dikshit R., Shinde S. R., Ogale S. B., Kulkarni S. D., Sainkar S. R., and Date S. K., Synthesis of single domain strontium ferrite powder by pulsed laser ablation, Applied Physics Letters. (1996) 68, no. 24, 3491–3493, https://doi.org/10.1063/1.115768, 2-s2.0-5944227147.
10.1063/1.115768
CAS Web of Science® Google Scholar
34 Naseri M. G., Halimah M. K., Dehzangi A., Kamalianfar A., Saion E. B., and Majlis B. Y., A comprehensive overview on the structure and comparison of magnetic properties of nanocrystalline synthesized by a thermal treatment method, Journal of Physics and Chemistry of Solids. (2014) 75, no. 3, 315–327, https://doi.org/10.1016/j.jpcs.2013.11.004, 2-s2.0-84891624424.
10.1016/j.jpcs.2013.11.004
CAS Web of Science® Google Scholar
35 Naseri M., Optical and magnetic properties of monophasic cadmium ferrite (CdFe₂O₄) nanostructure prepared by thermal treatment method, Journal of Magnetism and Magnetic Materials. (2015) 392, 107–113, https://doi.org/10.1016/j.jmmm.2015.05.026, 2-s2.0-84929313785.
10.1016/j.jmmm.2015.05.026
CAS Web of Science® Google Scholar
36 Naseri M. G., Saion E. B., Hashim M., Shaari A. H., and Ahangar H. A., Synthesis and characterization of zinc ferrite nanoparticles by a thermal treatment method, Solid State Communications. (2011) 151, no. 14-15, 1031–1035, https://doi.org/10.1016/j.ssc.2011.04.018, 2-s2.0-79958280145.
10.1016/j.ssc.2011.04.018
CAS Web of Science® Google Scholar
37 Gyergyek S., Makovec D., Kodre A., Arčon I., Jagodič M., and Drofenik M., Influence of synthesis method on structural and magnetic properties of cobalt ferrite nanoparticles, Journal of Nanoparticle Research. (2010) 12, no. 4, 1263–1273, https://doi.org/10.1007/s11051-009-9833-5, 2-s2.0-77955091341.
10.1007/s11051-009-9833-5
CAS Web of Science® Google Scholar
38 Jauhar S., Kaur J., Goyal A., and Singhal S., Tuning the properties of cobalt ferrite: a road towards diverse applications, RSC Advances. (2016) 6, no. 100, 97694–97719, https://doi.org/10.1039/C6RA21224G, 2-s2.0-84992193985.
10.1039/C6RA21224G
CAS Web of Science® Google Scholar
39 Chakrapani K., Bendt G., Hajiyani H., Schwarzrock I., Lunkenbein T., Salamon S., Landers J., Wende H., Schlögl R., Pentcheva R., Behrens M., and Schulz S., Role of composition and size of cobalt ferrite nanocrystals in the oxygen evolution reaction, ChemCatChem. (2017) 9, no. 15, 2988–2995, https://doi.org/10.1002/cctc.201700376, 2-s2.0-85020388322.
10.1002/cctc.201700376
CAS Web of Science® Google Scholar
40 Prathapani S., Vinitha M., Jayaraman T. V., and Das D., Effect of Er doping on the structural and magnetic properties of cobalt-ferrite, Journal of Applied Physics. (2014) 115, no. 17, 17A502–A7A5023, https://doi.org/10.1063/1.4854915, 2-s2.0-84893146206.
10.1063/1.4854915
Web of Science® Google Scholar
41 Pendyala S. K., Thyagarajan K., GuruSampath Kumar A., and Obulapathi L., Effect of Mg doping on physical properties of Zn ferrite nanoparticles, Journal of the Australian Chemical Society. (2018) 54, no. 3, 467–473, https://doi.org/10.1007/s41779-018-0173-8, 2-s2.0-85050499119.
10.1007/s41779-018-0173-8
CAS Google Scholar
42 Mariosi F. R., Venturini J., da Cas Viegas A., and Bergmann C. P., Lanthanum-doped spinel cobalt ferrite (CoFe₂O₄) nanoparticles for environmental applications, Ceramics International. (2020) 46, no. 3, 2772–2779, https://doi.org/10.1016/j.ceramint.2019.09.266, 2-s2.0-85072997935.
10.1016/j.ceramint.2019.09.266
CAS Web of Science® Google Scholar
43 Paulsen J. A., Ring A. P., Lo C. C. H., Snyder J. E., and Jiles D. C., Manganese-substituted cobalt ferrite magnetostrictive materials for magnetic stress sensor applications, Journal of Applied Physics. (2005) 97, no. 4, article 044502, https://doi.org/10.1063/1.1839633, 2-s2.0-13744258231.
10.1063/1.1839633
Web of Science® Google Scholar
44 Kaur H., Singh A., Kumar V., and Ahlawat D. S., Structural, thermal and magnetic investigations of cobalt ferrite doped with Zn²⁺ and Cd²⁺ synthesized by auto combustion method, Journal of Magnetism and Magnetic Materials. (2019) 474, 505–511, https://doi.org/10.1016/j.jmmm.2018.11.010, 2-s2.0-85056625970.
10.1016/j.jmmm.2018.11.010
CAS Web of Science® Google Scholar
45 Mou F. Z., Guan J. G., Sun Z. G., Fan X. A., and Tong G. X., In situ generated dense shell-engaged Ostwald ripening: A facile controlled- preparation for BaFe₁₂O₁₉ hierarchical hollow fiber arrays, Journal of Solid State Chemistry. (2010) 183, no. 3, 736–743, https://doi.org/10.1016/j.jssc.2010.01.016, 2-s2.0-77649187600.
10.1016/j.jssc.2010.01.016
CAS Web of Science® Google Scholar
46 Gauns Dessai P. P., Meena S. S., and Verenkar V. M. S., Influence of addition of Al³⁺ on the structural and solid state properties of nanosized Ni-Zn ferrites synthesized using malic acid as a novel fuel, Journal of Alloys and Compounds. (2020) 842, article 155855, https://doi.org/10.1016/j.jallcom.2020.155855.
10.1016/j.jallcom.2020.155855
Web of Science® Google Scholar
47 Kumar K. V., Paramesh D., and Reddy P. V., Effect of Aluminium doping on structural and magnetic properties of Ni-Zn ferrite nanoparticles, World Journal of Nano Science and Engineering. (2015) 5, no. 3, 68–77, https://doi.org/10.4236/wjnse.2015.53009.
10.4236/wjnse.2015.53009
CAS Google Scholar
48 Waghmare S. P., Borikar D. M., and Rewatkar K. G., Impact of Al doping on structural and magnetic properties of Co-ferrite, Materials Today. (2017) 4, 11866–11872.
Google Scholar
49 Rather S. U. and Lemine O. M., Effect of Al doping in zinc ferrite nanoparticles and their structural and magnetic properties, Journal of Alloys and Compounds. (2020) 812, 152058–152068, https://doi.org/10.1016/j.jallcom.2019.152058.
10.1016/j.jallcom.2019.152058
CAS Web of Science® Google Scholar
50 Kumar G., Kotnala R. K., Shah J., Kumar V., Kumar A., Dhiman P., and Singh M., Cation distribution: a key to ascertain the magnetic interactions in a cobalt substituted Mg–Mn nanoferrite matrix, Physical Chemistry Chemical Physics. (2017) 19, no. 25, 16669–16680, https://doi.org/10.1039/C7CP01993A, 2-s2.0-85024133638, 28621366.
10.1039/C7CP01993A
CAS PubMed Web of Science® Google Scholar
51 Naik S. R. and Salker A. V., Change in the magnetostructural properties of rare earth doped cobalt ferrites relative to the magnetic anisotropy, Journal of Materials Chemistry. (2012) 22, no. 6, 2740–2750, https://doi.org/10.1039/C2JM15228B, 2-s2.0-84855946046.
10.1039/C2JM15228B
CAS Web of Science® Google Scholar
52 Yadav R. S., Kuřitka I., Vilcakova J., Havlica J., Masilko J., Kalina L., Tkacz J., Švec J., Enev V., and Hajdúchová M., Impact of grain size and structural changes on magnetic, dielectric, electrical, impedance and modulus spectroscopic characteristics of CoFe₂O₄ nanoparticles synthesized by honey mediated sol-gel combustion method, Advances in Natural Sciences: Nanoscience. (2017) 8, article 045002.
Google Scholar
53 Raghavender A. T., Shirsath S. E., Pajic D., Zadro K., Milekovic T., Jadhav K. M., and Kumar K. V., Effect of Al doping on the cation distribution in copper ferrite nanoparticles and their structural and magnetic properties, Journal of the Korean Physical Society. (2012) 61, no. 4, 568–574, https://doi.org/10.3938/jkps.61.568, 2-s2.0-84866093837.
10.3938/jkps.61.568
CAS Web of Science® Google Scholar
54 Assar S. T. and Abosheiasha H. F., Effect of Ca substitution on some physical properties of nano-structured and bulk Ni-ferrite samples, Journal of Magnetism and Magnetic Materials. (2015) 374, 264–272, https://doi.org/10.1016/j.jmmm.2014.08.011, 2-s2.0-84907346009.
10.1016/j.jmmm.2014.08.011
CAS Web of Science® Google Scholar
55 Chaudhari H. N., Dhruv P. N., Singh C., Meena S. S., Kavita S., and Jotania R. B., Effect of heating temperature on structural, magnetic, and dielectric properties of magnesium ferrites prepared in the presence of Solanum lycopersicum fruit extract, Journal of Materials Science: Materials in Electronics. (2020) 31, 18445–18463.
10.1007/s10854-020-04389-1
Web of Science® Google Scholar
56 Kagdi A. R., Solanki N. P., Carvalho F. E., Meena S. S., Bhatt P., Pullar R. C., and Jotania R. B., Influence of Mg substitution on structural, magnetic and dielectric properties of X-type barium![single bond](https://sdfestaticassets-us- east-1.sciencedirectassets.com/shared-assets/55/entities/sbnd.gif)zinc hexaferrites Ba₂Zn_2-xMg_xFe₂₈O₄₆, Journal of Alloys and Compounds. (2018) 741, 377–391, https://doi.org/10.1016/j.jallcom.2018.01.092, 2-s2.0-85041134946.
10.1016/j.jallcom.2018.01.092
CAS Web of Science® Google Scholar

Citing Literature

All articles

Doped Nanostructured Manganese Ferrites: Synthesis, Characterization, and Magnetic Properties

Abstract

1. Introduction

2. Experimental

2.1. Synthesis

2.2. Characterization

3. Results and Discussion

4. Conclusions

Conflicts of Interest

Acknowledgments

Open Research

Data Availability

References

Citing Literature

Figures

References

Information

About Wiley Online Library

Help & Support

Opportunities

Connect with Wiley

Doped Nanostructured Manganese Ferrites: Synthesis, Characterization, and Magnetic Properties

Abstract

1. Introduction

2. Experimental

2.1. Synthesis

2.2. Characterization

3. Results and Discussion

4. Conclusions

Conflicts of Interest

Acknowledgments

Open Research

Data Availability

References

Citing Literature

Figures

References

Related

Information