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

Rather, Sami-ullah; Saeed, Usman; Al-Zahrani, Abdulrahim Ahmad; Bamufleh, Hisham S.; Alhumade, Hesham Abdulhamed; Taimoor, Aqeel Ahmad; Lemine, O. M.; Ali, Arshid Mahmood; Al Zaitone, Belal; Alam, Muhammad Mahmud

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

Journal of Nanomaterials

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Abstract Introduction Experimental Results and Discussion Conclusions Data Availability Conflicts of Interest Acknowledgments References Copyright Related Articles

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Advanced Nano/Microporous Materials for Energy Storage

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Research Article | Open Access

Volume 2021 | Article ID 9410074 | https://doi.org/10.1155/2021/9410074

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

Sami-ullah Rather,¹Usman Saeed,¹Abdulrahim Ahmad Al-Zahrani,¹Hisham S. Bamufleh,¹Hesham Abdulhamed Alhumade,¹Aqeel Ahmad Taimoor,¹O. M. Lemine,²Arshid Mahmood Ali,¹Belal Al Zaitone,¹and Muhammad Mahmud Alam¹

Academic Editor: Filippo Giubileo

Received23 Aug 2021

Revised24 Nov 2021

Accepted30 Nov 2021

Published24 Dec 2021

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 , the formula is expressed as (M²⁺)[Fe₂³⁺]O₄, and the ferrite is called normal spinel ferrite. When , the formula is expressed as (Fe³⁺)[M²⁺Fe³⁺]O₄, and the ferrite is called inverse spinel ferrite. When , such as , the ferrite is called as mixed spinel ferrite. When , 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 () with 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 () 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 , 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 (). For clarity, hereafter, the Al-doped MnFe₂O₄ are referred to as , A graphic reaction design for the synthesis of is presented in Figure 1.

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 () 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 () 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 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 () are presented in Figure 2, and profiles a, b, c, and d refer to the content of , 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.

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

(a)

(b)

The Nelson-Riley function for each reflection of was calculated by using the following relation:

Figure 4(a) shows Nelson-Riley function of nanocrystalline . Diffraction angle from 10 to 80° was utilized to determine lattice parameters “” by extrapolating . True lattice value “” and average value “” variation is shown in Figure 4(b). It is visible from Figure 4(b) that little disparity between true value lattice constant “” and the average value lattice constant “” existed. Moreover, average value lattice constant “” is slightly more than true value lattice constant “.” 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 , , , , and 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].

(a)

(b)

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

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

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 “” verses “” 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.

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 () and octahedral bonding sites () were determined by Equations (11) and (12), where . The and site is the closest gap between A and B with oxygen ions. The higher compared to 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 and 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 ( and ), the shared tetrahedral edge length (), and shared and unshared octahedral edge lengths ( and ) 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].

(a)

(b)

The nanostructure characterization of 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.

(a)

(b)

(c)

(d)

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 () 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 . 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 () could be declared as follows:

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 (). The substitution formula of Al-doped manganese ferrite could be designated as follows:

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 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 , , , η_exp, and -squareness ratio are shown in Table 5. The magnetization evaluation was performed by using an additional field area of the calculated data by employing Langevin dependence [53]: where , , and are the effective values of the volume, density, and temperature, respectively, and the other values are related to their typical definitions.

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 and of the doped ferrite sample may be associated to reduced particle size. The reduction in 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 and 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 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 and of the A and B ferrite sublattices. The affiliation of – 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 () 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 () revealed in several places in the literature, the squareness ratio () 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 and are reduced as the Al content is elevated. This contraction was associated with spin noncollinearity and delicate interactions between sublattices.

Data Availability

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

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.

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Copyright © 2021 Sami-ullah Rather et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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