Abstract
The spinel ferrite system is prepared by coprecipitation method. XRD analysis confirms the formation of ferrite phase in all the samples. The FTIR spectra of all the samples show two main absorption bands below 1000 cm−1. FTIR studies reveal cationic exchange between A site and B site. The magnetic moment calculated from EPR studies is lower when compared to the theoretical values. This confirms the existence of noncollinear magnetic structure arising due to spin canting at B site.
1. Introduction
Manganese zinc ferrite is technologically important class of materials because of its unusual magnetic properties and is extensively used in electronic applications such as transformers, coils, and recording heads. Ferrites crystallize into spinal type which has tetrahedral A site and octahedral B site. The properties of the ferrites can be tuned by varying the cation and their distribution among tetrahedral A site and octahedral B site. Further bulk properties of ferrite change as its dimensions are changed to nanoscale [1–4]. Superparamagnetism, spin canting, and metastable cation distribution are some of the phenomena which have been observed in nanoparticles of various ferrites.
The method of preparation plays an important role in the properties of the ferrite nanoparticles. Varieties of experimental methods like sol-gel method, coprecipitation method, hydrothermal method, reverse micelle method, and autocombustion method are carried out for the production of ferrite nanoparticles. Among these methods coprecipitation method is an attractive method for producing nanoferrites because of increased homogeneity, purity, and reactivity. Singh et al. [5] have reported the EPR studies of nanostructured zinc ferrites heat treated at different temperature. Priyadharsini et al. [6] have reported the FTIR studies of nanostructured NiZn ferrite. In the present investigation we report the FTIR, EPR studies of the Ni substituted MnZn ferrite nanoparticles prepared by coprecipitation method.
2. Experimental Details
Nanoparticles of with varying from 0.0 to 0.3 were prepared by coprecipitation method. Aqueous solutions of MnCl2, ZnSo4, NiCl2, and FeCl3 in their respective stoichiometry were thoroughly mixed at 80°C. This mixture was then transferred immediately into a boiling solution of NaOH at 100°C. Precipitation takes place and the solution was stirred for about 60 minutes until the reaction is complete. The pH of the solution was maintained at 12 throughout the reaction. Conversion of metal salts into hydroxides and subsequent transformation of metal hydroxide to nanoferrites takes place. The nanoparticles thus formed were isolated by centrifugation and washed several times with deionized water followed by acetone and then dried at room temperature. The dried powder was grounded thoroughly in a clean agate mortar. Obtained powders were used for all of the measurements. X-ray diffraction (XRD) was carried out using a PANanalytical X’pert PRO diffractometer using CuKα as radiation source. Data were collected for every 0.02° in the angle range 20°–70° of 2θ. Scanning electron microscope imaging was carried out using the FEI Quanta FEG 200 (HR-SEM) equipment for the surface morphology analysis. The particle size was determined by subjecting the samples to transmission electron microscopy (TEM) using a Phillips CM20 microscope. The Fourier transform infrared (FTIR) spectra were recorded in the range 400 cm−1 to 4000 cm−1 using a FTIR spectrometer (Bruker). Electron paramagnetic resonance (EPR) spectra were taken by using an X-band CW EPR (EMX 102.7) spectrometer.
3. Results and Discussion
3.1. Structural Analysis
Figure 1 shows the X-ray diffraction pattern for (with = 0.0, 0.1, 0.2, 0.3). The diffraction pattern confirmed the formation of cubic ferrite phase for all the samples. The broad XRD line indicates that the ferrite particles are of nanosize. The average crystalline size for each composition is calculated from XRD line width of (311) peak using Scherrer formulae [7] and is given in Table 1. Figure 2 shows the TEM image of . It is observed that all the samples are highly homogeneous and nearly spherical in shape. Figure 3 shows the SEM image of . A clear SEM image reveals that there are no secondary phases. This is supported by the absence of additional peaks in the XRD pattern.
3.2. FTIR Studies
Figure 4 shows the room temperature IR spectrum of the above mentioned samples. The spectra are recorded in the range 400 to 4000 cm−1. The spectra show two main absorption band below 1000 cm−1 which is a common feature of ferrites. The high frequency band lies in the range 560–600 cm−1 while the low frequency band lies in the range 474–436 cm−1. These bands are assigned to the vibrations of the metal ion-oxygen complexes in tetrahedral and octahedral sites, respectively [8, 9]. It is observed that the high frequency band increases with increase in Ni substitution, whereas the low frequency band is found to decrease. Waldron [9] attributed the high frequency band to the intrinsic vibrations of the tetrahedral groups and the low frequency band to the octahedral groups. Puri and Varshney [10] have reported that Zn2+ showed a strong preference for tetrahedral A site and Ni2+ ion showed preference for B site, while Mn2+ ions showed preference for A site and B site. We have also observed from our earlier studies [11] that Ni2+ ions occupy the B site and force some of the Fe3+ ions from B site to A site. Ni2+ ions in the octahedral site have larger ionic radius and higher atomic weight than Fe3+ ions. This affects the Fe3+-O− stretching vibration resulting in the decrease of octahedral vibrational frequency. This may be the reasons for the increase in the octahedral peak intensity. The increase in the concentration of Fe3+ ions having lower ionic radius and lower atomic weight in the tetrahedral site increases the tetrahedral frequency vibration. All our samples show a split in the octahedral frequency band. Priyadarsini et al. [6] have obtained similar split in the octahedral frequency band.
3.3. EPR Spectral Studies
The EPR of ferrite is important for investigating the magnetic properties of magnetic materials at high frequency because the resonance originates from the interaction between spin and electromagnetic waves. The powder EPR spectra of Zn0.5Fe2O4 (with = 0.0, 0.1, 0.2, 0.3) were measured at 9.3 GHz at room temperature and are shown in Figure 5. The resonance line width , the position corresponding to zero signal , and the effective factor are determined from [12–14] where is the planck’s constant, is the frequency of the microwave, is the magnetic field occurring, and is the Bohr magneton. From Table 2 it was observed that the value decreased with increasing Ni substitution up to and then increases for . This decrease in the value of may be due to superexchange interaction between Ni2+ and Fe3+ ions through nonmagnetic O2− ions. Due to decrease in the superexchange interaction there may be rise in the value of for the substitution . The superexchange interaction in ferrite is responsible for magnetic ordering within each sublattice. The interaction between A and B site is strongest in ferrites. As the AB interaction predominate, the spins of A and B site ions in ferrites will be opposite with a resultant magnetic moment equal to the difference between those of A and B site ions [15–17].
The theoretical values of the magnetic moment per formula unit and the experimental values of the magnetic moment are given in Table 2. According to the cation distribution estimated from our earlier studies, it was observed that the net magnetic moment of Zn0.5Fe2O4 is but the experimental value of the total magnetic moment is . This low value of experimental values may be due to the occupation of Ni2+ ions in the B site. This forces some of the Fe3+ ions from B site to A site. As a result of this migration of ions between A and B site, the magnetization at B site decreases resulting in overall decrease in the magnetization of the samples. In addition to this rearrangement of cation between A site and B site, the other reasons reported in literature are due to significant canting existing in B site [18, 19]. Surface effects and the occurrence of a glassy state were also reported to be playing an active role in the decline of magnetic value [20].
Figure 6 shows the relation between magnetic moment and the resonance field as a function of Ni substitution. The resonance field increases with increase in the Ni content and reaches a maximum for the sample , whereas the magnetic moment decreases with increasing Ni content. This can be attributed to the reason that as the magnetic moment decreases the internal field also decreases. So to satisfy the relation , the resonance field should be high.
Figure 7 shows the variation of line width with Ni content. The line width decreases with increase in the Ni content upto . This is due to occupation of Ni2+ ion in the octahedral B site. The presence of Ni2+ ions in the octahedral B site causes a decrease in the magnetic moment of the B sublattice. This causes an overall decrease in the total magnetic moment. This decrease in the magnetic moment of the samples may be the reason for the decrease in the line width of the samples up to .
4. Conclusion
Ni substituted MnZn nanoferrites were prepared by coprecipitation method. The X-ray diffraction pattern shows the formation of ferrite phase in all the samples. FTIR studies reveal cationic exchange between A site and B site. The line width decreases with increase in Ni content. Low experimental value of magnetic moment calculated from EPR spectra compared to the theoretical value confirms the existence of spin canting in B site which results in a noncollinear magnetic structure.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.