Structural and Magnetic Studies of Cr 3 + Substituted Nickel Ferrite Nanomaterials Prepared by Sol-Gel Auto-Combustion

The present study envisages the preparation of chromium substituted Nickel ferrite NiCrxFe2−xO4 (x = 0~1.0) powders by a sol-gel auto-combustion method. X-ray diffraction analysis (XRD) showed that the specimens with x > 0.2 exhibited a single-phase spinel structure, and that more content of Cr within a specimen is favorable for the synthesis of pure Ni-Cr ferrites. The lattice parameter decreased with an increase in the Cr concentration. The sample without calcining exhibited a good crystallinity. Scanning Electron Microscopy (SEM) showed the formation of ferrite powders nano-particles, and that the substitution of Cr weakened the agglomeration between the particles. Mössbauer spectra of NiCrxFe2−xO4 showed two normal Zeeman-split sextets that displayed a ferrimagnetic behavior. Furthermore, the spectra indicated that iron was in the Fe3+ state, and the magnetic hyperfine field at the tetrahedral tended to decrease with an increase in the Cr substitution. The saturation magnetization decreased by the Cr3+ ions, and reached a minimum value (Ms = 4.46 emu/g). With an increase in the annealing temperature, the coercivity increased initially, which later decreased.


Introduction
Nickel ferrite (NiFe 2 O 4 ) is a typical soft magnetic ferrite, making it one of the most important spinel ferrites [1].It is widely used in electronic devices, due to its ability to remain permeable at high frequencies, high electrical resistivities, low eddy currents, and low dielectric losses, as well as its continuous chemical stability [2,3].NiFe 2 O 4 is an inverse spinel ferrite, in which the Ni 2+ ions occupy octahedral (B) sites, and Fe 3+ ions are distributed in tetrahedral (A) and octahedral (B) sites [2].The magnetic and electric properties of the spinel ferrites depend on the distribution of the cations among tetrahedral and octahedral sites.Chromium ions, with an antiferromagnetic nature, are known for achieving control over magnetic parameters, and in the development of technologically important materials.Patange et al. investigated the cation distribution and magnetic properties of chromium-substituted nickel ferrite, and found that Cr 3+ and Ni 2+ ions both have strong preference to occupy octahedral (B) site, and the magnetic saturation and Curie temperature all decrease by Cr 3+ ions substitution [1]. Lee et al. studied the electrical and magnetic properties of ferrite NiCr x Fe 2−x O 4 , which established that the magnetic moment and Curie temperature decreased with the chromium substitution, and that this system exhibited n-type semi-conductivity [4].Prasad et al. prepared nanoparticles NiCr x Fe 2−x O 4 by sol-gel, and concluded that the magnetization and coercivity decreased with an increase in the chromium ion concentration, due to the depletion of Fe 3+ ions at the octahedral (B) sites [5].Patange et al. obtained the cation distribution of nickel chromium ferrites by the IR spectra analysis [6].The current paper deals with structural and magnetic properties of ferrite NiCr x Fe 2−x O 4 (x = 0~1.0)powders that were prepared by a sol-gel auto-combustion method.The ferrite powders, prepared by this method exhibited a good sinterability with a homogeneous composition.The other advantages of the synthetic method include the requirement of relatively simple equipment, and low cost of the materials used.From previous studies [4][5][6], it is evident that increasing the substitution of Cr is favorable for the synthesis of pure Ni-Cr ferrites, and weakens the agglomeration between the particles.

Sample Preparation
Chromium-substituted Nickel ferrite NiCr x Fe 2−x O 4 (x = 0~1.0)powders were synthesized using the sol-gel auto-combustion process.The raw materials were analytical grade Ni(NO 3 ) 2 The molar ratio of metal nitrates to citric acid was taken as 1:1.The metal nitrates and citric acid were weighed and dissolved in deionized water to prepare the test solutions.The pH value of metal nitrate solution was adjusted from 7 to 9 by ammonia addition.The mixed solutions were heated in a thermostat water bath at 80 • C and stirred continuously to form the dried gel.Continuous dropwise addition of citric acid occurred in this process.The gels were dried in an oven at 120 • C for 2 h and were burnt in self-propagating combustion to form loose powder by being ignited in air at room temperature.The powders then were ground and sintered at temperatures of 400 • C and 800 • C.

Characterization
The crystalline structure was analyzed using X-ray diffraction (D/max-2500V/PC, Rigaku, Tokyo, Japan), with Cu Kα radiation (λ = 0.15405 nm).The micrographs were obtained by scanning electron microscopy (NoVaTM Nano SEM 430, FEI Corporation, Hillsboro, OR, USA).The Mössbauer spectrum was performed at room temperature, using a conventional Mössbauer spectrometer (Fast Com Tec PC-mossII, Oberhaching, Germany), in constant acceleration mode.The γ-rays were provided by a 57 Co source in a rhodium matrix.Magnetization measurements were carried out with super conducting quantum interference device (MPMS-XL-7, Quantum Design, San Diego, CA, USA) at room temperature.

X-ray Diffraction (XRD) Analysis
Figure 1 shows the XRD patterns of NiCr x Fe 2−x O 4 (x = 0~1.0)ferrites calcined at 800 • C for 3 h.XRD results show that the specimens with x > 0.2 exhibited a single-phase spinel structure, while an impurity peak of Fe 2 O 3 was detected in the samples with x = 0 to 0.2.The results show that increasing the content of Cr was favorable for the synthesis of pure Ni-Cr ferrites.Similar results are evident in earlier studies [7].Table 1 indicates that the lattice parameter showed a decreased trend, with an increasing substitution of Cr 3+ ions.The decrease in the lattice parameter was likely due to the replacement of larger Fe 3+ ions (0.645 Å), by smaller Cr 3+ ions (0.63 Å) [4,8].The average crystallite size of the investigated samples that was estimated by the Scherrer's formula [5], were found to be between 25.5 and 57.5 nm (Table 1).It was observed that the average crystallite size decreased by increasing the Cr content, as evident with earlier reports [9].The X-ray density was calculated using the relation [10]: where M is relative molecular mass, N is the Avogadro's number and 'a' is the lattice parameter.
Table 1 shows that the x-ray density highlighted a decreasing trend for Cr 3+ concentration for all samples.The atomic weight of Fe is greater than Cr, so the relative molecular mass decreased with an increase in the Cr concentration.The decrease in the X-ray density is attributed to the fact that the relative molecular mass decreases significantly with a negligible decline in the lattice parameter.The X-ray patterns of NiCr0.2Fe1.8O4calcined at different temperature are shown in Figure 2. XRD patterns confirmed the formation of cubic spinel phase as the main phase along with traces of the secondary phase of Fe2O3.The intensity of Fe2O3 decreased with increasing heating temperatures.Furthermore, it was evident that the heat treatment was favorable for the synthesis of pure Ni-Cr ferrites.The lattice parameter and the X-ray density differed with a change in temperature for the samples.Average crystallite size of NiCr0.2Fe1.8O4increased with increasing the calcining temperature, as evident from Table 2.In earlier work [11], the diffraction peaks of Ni0.50Cu0.25Zn0.25CrxFe2-xO4calcined at low temperature were not very sharp, but our results indicate that the diffraction peaks of CoCr0.2Fe1.8O4without burning were very sharp.We prepared chromium substituted cobalt ferrite powders by the sol-gel auto-combustion method, whereas the samples without calcining showed a good crystallinity.The X-ray density was calculated using the relation [10]: where M is relative molecular mass, N is the Avogadro's number and 'a' is the lattice parameter.Table 1 shows that the X-ray density highlighted a decreasing trend for Cr 3+ concentration for all samples.The atomic weight of Fe is greater than Cr, so the relative molecular mass decreased with an increase in the Cr concentration.The decrease in the X-ray density is attributed to the fact that the relative molecular mass decreases significantly with a negligible decline in the lattice parameter.The X-ray patterns of NiCr 0.2 Fe 1.8 O 4 calcined at different temperature are shown in Figure 2. XRD patterns confirmed the formation of cubic spinel phase as the main phase along with traces of the secondary phase of Fe 2 O 3 .The intensity of Fe 2 O 3 decreased with increasing heating temperatures.Furthermore, it was evident that the heat treatment was favorable for the synthesis of pure Ni-Cr ferrites.The lattice parameter and the X-ray density differed with a change in temperature for the samples.Average crystallite size of NiCr 0.2 Fe 1.8 O 4 increased with increasing the calcining temperature, as evident from Table 2.In earlier work [11], the diffraction peaks of Ni 0.50 Cu 0.25 Zn 0.25 Cr x Fe 2−x O 4 calcined at low temperature were not very sharp, but our results indicate that the diffraction peaks of CoCr 0.2 Fe 1.8 O 4 without burning were very sharp.We prepared chromium substituted cobalt ferrite powders by the sol-gel auto-combustion method, whereas the samples without calcining showed a good crystallinity.

Structures and Grain Size
The Scanning Electron Microscopy (SEM) results of NiCrxFe2−xO4 (x = 0, 0.2) annealed at 800 °C for 3 h is shown in Figure 3.It can be observed that the distribution of grains was almost uniform in size, and were well crystallized for all samples.The substitution of Cr can weaken the agglomeration between the particles.The histogram of grain size distribution of NiCrxFe2−xO4 ferrites is shown in Figure 4 shows.The average grain size of NiFe2O4 and NiCr0.2Fe1.8O4estimated using a statistical method was approximately 69.51 and 52.63 nm, respectively.This shows that the ferrite powders were nano-particles, and the average grain size decreased significantly with an increase in the Cr content.The average grain size was slightly larger than the average crystallite size, as determined by XRD analysis.The data reveals that every particle was formed by a number of crystallites.

Structures and Grain Size
The Scanning Electron Microscopy (SEM) results of NiCr x Fe 2−x O 4 (x = 0, 0.2) annealed at 800 • C for 3 h is shown in Figure 3.It can be observed that the distribution of grains was almost uniform in size, and were well crystallized for all samples.The substitution of Cr can weaken the agglomeration between the particles.The histogram of grain size distribution of NiCr x Fe 2−x O 4 ferrites is shown in Figure 4 shows.The average grain size of NiFe 2 O 4 and NiCr 0.2 Fe 1.8 O 4 estimated using a statistical method was approximately 69.51 and 52.63 nm, respectively.This shows that the ferrite powders were nano-particles, and the average grain size decreased significantly with an increase in the Cr content.The average grain size was slightly larger than the average crystallite size, as determined by XRD analysis.The data reveals that every particle was formed by a number of crystallites.

Structures and Grain Size
The Scanning Electron Microscopy (SEM) results of NiCrxFe2−xO4 (x = 0, 0.2) annealed at 800 °C for 3 h is shown in Figure 3.It can be observed that the distribution of grains was almost uniform in size, and were well crystallized for all samples.The substitution of Cr can weaken the agglomeration between the particles.The histogram of grain size distribution of NiCrxFe2−xO4 ferrites is shown in Figure 4 shows.The average grain size of NiFe2O4 and NiCr0.2Fe1.8O4estimated using a statistical method was approximately 69.51 and 52.63 nm, respectively.This shows that the ferrite powders were nano-particles, and the average grain size decreased significantly with an increase in the Cr content.The average grain size was slightly larger than the average crystallite size, as determined by XRD analysis.The data reveals that every particle was formed by a number of crystallites.

Mössbauer Spectroscopy
The Mössbauer spectra for NiCrxFe2−xO4, recorded at room temperature, is shown in Figure 5.All samples were analyzed using the Mösswinn 3.0 program.The spectra exhibited two normal Zeeman-split sextets due to the presence of Fe 3+ at tetrahedral and octahedral sites, which indicated the ferromagnetic behavior of the samples [12].The sextet with the larger isomer shift was assigned to the Fe 3+ ions at the B site, and the one with the smaller isomer shift was assumed to arise from the Fe 3+ ions, occupying the A site.This may be attributed to the difference in Fe 3+_ O 2-internuclear separations.Since, the bond separation for the B site Fe 3+ ions, was larger in comparison with the A site ions, small overlapping of the orbits for Fe 3+ and O 2+ ions at B site occurred, resulting in the smaller covalency and large isomer shift for B site Fe 3+ ions [9].It is reported that the values of Isomer Shift (I.S.) for Fe 2+ ions lie in the range 0.6-1.7 mm/s, while for Fe 3+ they lie in the range 0.1-0.5 mm/s [13].From Table 3, the values for I.S. in our study indicate that iron is in Fe 3+ state.Table 3 shows that the magnetic hyperfine field at the tetrahedral A site, and octahedral B site, exhibited a decreasing trend with increasing Cr substitution.The decrease of magnetic hyperfine field with increasing Cr contents is attributed to the decrease of the A-B super-exchange interaction with the magnetic Fe 3+ ions replaced by magnetic Cr 3+ ions, which resulted in the decrease of the magnetic hyperfine field [9].Furthermore, the reduction of magnetic hyperfine field was related to the disappearance of the impurity Fe2O3.The decrease of Fe2O3 (with valence state − Fe 3+ ) led to the decrease of the superexchange interaction [14].The quadrupole shift of Mössbauer spectra was nearly zero in our study, which indicated that the ferrites exhibited a cubic symmetry.The decrease in the absorption area ration of B site can be attributed to the Fe 3+ ions decrease at B site, with the Cr 3+ ions doping.

Mössbauer Spectroscopy
The Mössbauer spectra for NiCr x Fe 2−x O 4 , recorded at room temperature, is shown in Figure 5.All samples were analyzed using the Mösswinn 3.0 program.The spectra exhibited two normal Zeeman-split sextets due to the presence of Fe 3+ at tetrahedral and octahedral sites, which indicated the ferromagnetic behavior of the samples [12].The sextet with the larger isomer shift was assigned to the Fe 3+ ions at the B site, and the one with the smaller isomer shift was assumed to arise from the Fe 3+ ions, occupying the A site.This may be attributed to the difference in Fe 3+_ O 2− internuclear separations.Since, the bond separation for the B site Fe 3+ ions, was larger in comparison with the A site ions, small overlapping of the orbits for Fe 3+ and O 2+ ions at B site occurred, resulting in the smaller covalency and large isomer shift for B site Fe 3+ ions [9].It is reported that the values of Isomer Shift (I.S.) for Fe 2+ ions lie in the range 0.6-1.7 mm/s, while for Fe 3+ they lie in the range 0.1-0.5 mm/s [13].From Table 3, the values for I.S. in our study indicate that iron is in Fe 3+ state.

Mössbauer Spectroscopy
The Mössbauer spectra for NiCrxFe2−xO4, recorded at room temperature, is shown in Figure 5.All samples were analyzed using the Mösswinn 3.0 program.The spectra exhibited two normal Zeeman-split sextets due to the presence of Fe 3+ at tetrahedral and octahedral sites, which indicated the ferromagnetic behavior of the samples [12].The sextet with the larger isomer shift was assigned to the Fe 3+ ions at the B site, and the one with the smaller isomer shift was assumed to arise from the Fe 3+ ions, occupying the A site.This may be attributed to the difference in Fe 3+_ O 2-internuclear separations.Since, the bond separation for the B site Fe 3+ ions, was larger in comparison with the A site ions, small overlapping of the orbits for Fe 3+ and O 2+ ions at B site occurred, resulting in the smaller covalency and large isomer shift for B site Fe 3+ ions [9].It is reported that the values of Isomer Shift (I.S.) for Fe 2+ ions lie in the range 0.6-1.7 mm/s, while for Fe 3+ they lie in the range 0.1-0.5 mm/s [13].From Table 3, the values for I.S. in our study indicate that iron is in Fe 3+ state.Table 3 shows that the magnetic hyperfine field at the tetrahedral A site, and octahedral B site, exhibited a decreasing trend with increasing Cr substitution.The decrease of magnetic hyperfine field with increasing Cr contents is attributed to the decrease of the A-B super-exchange interaction with the magnetic Fe 3+ ions replaced by magnetic Cr 3+ ions, which resulted in the decrease of the magnetic hyperfine field [9].Furthermore, the reduction of magnetic hyperfine field was related to the disappearance of the impurity Fe2O3.The decrease of Fe2O3 (with valence state − Fe 3+ ) led to the decrease of the superexchange interaction [14].The quadrupole shift of Mössbauer spectra was nearly zero in our study, which indicated that the ferrites exhibited a cubic symmetry.The decrease in the absorption area ration of B site can be attributed to the Fe 3+ ions decrease at B site, with the Cr 3+ ions doping.Table 3 shows that the magnetic hyperfine field at the tetrahedral A site, and octahedral B site, exhibited a decreasing trend with increasing Cr substitution.The decrease of magnetic hyperfine field with increasing Cr contents is attributed to the decrease of the A-B super-exchange interaction with the magnetic Fe 3+ ions replaced by magnetic Cr 3+ ions, which resulted in the decrease of the magnetic hyperfine field [9].Furthermore, the reduction of magnetic hyperfine field was related to the disappearance of the impurity Fe 2 O 3 .The decrease of Fe 2 O 3 (with valence state − Fe 3+ ) led to the decrease of the superexchange interaction [14].The quadrupole shift of Mössbauer spectra was nearly zero in our study, which indicated that the ferrites exhibited a cubic symmetry.The decrease in the absorption area ration of B site can be attributed to the Fe 3+ ions decrease at B site, with the Cr 3+ ions doping.

Magnetic Property of Particles
Figure 6 shows the hysteresis loops of NiCr x Fe 2−x O 4 at room temperature.The magnetization of all samples nearly reached a saturation point at the external field of 5000 Oe.As shown in Table 4, the saturation magnetization decreased with an increase in the Cr content.

Magnetic Property of Particles
Figure 6 shows the hysteresis loops of NiCrxFe2−xO4 at room temperature.The magnetization of all samples nearly reached a saturation point at the external field of 5000 Oe.As shown in Table 4, the saturation magnetization decreased with an increase in the Cr content.The saturation magnetization can be expressed by means of the following relation [4,14]: where nB is the magnetic moment with Bohr magneton as the unit, and M is the relative molecular mass.The relative molecular mass of NiCrxFe2−xO4 decreased as the Cr content in x increased.The change of magnetic moment nB can be explained with Néel's theory.The magnetic moment μ per ion for Cr 3+ , Ni 2+ and Fe 3+ ions was 3 μB, 2 μB and 5 μB [2,3,14], respectively.According to Néel's two sublattice model of ferrimagnetism, the cation distribution of (Fe)A[NiCrxFe1−x]BO4 was used, since Ni 2+ prefers to occupy the octahedral (B) site in NiFe2O4 ferrite of inverse spinel structure [1,2], and Cr 3+ ions have strong B-site preference [3,13,14].The magnetic moment nB is expressed as [3,4,10,14]: where MB and MA are the B and A sublattice magnetic moments.Formula (3) shows that the theoretical magnetic moment decreases when there is an increase in the Cr content.According to the relation of Formula (2), the theoretical saturation magnetization decreased with Cr content x.The variation of the experimental and theoretical saturation magnetization agreed with each other for all samples.The saturation magnetization can be expressed by means of the following relation [4,14]: where n B is the magnetic moment with Bohr magneton as the unit, and M is the relative molecular mass.
The relative molecular mass of NiCr x Fe 2−x O 4 decreased as the Cr content in x increased.The change of magnetic moment nB can be explained with Néel's theory.The magnetic moment µ per ion for Cr 3+ , Ni 2+ and Fe 3+ ions was 3 µ B , 2 µ B and 5 µ B [2,3,14], respectively.According to Néel's two sublattice model of ferrimagnetism, the cation distribution of (Fe)A[NiCr x Fe 1−x ]BO 4 was used, since Ni 2+ prefers to occupy the octahedral (B) site in NiFe 2 O 4 ferrite of inverse spinel structure [1,2], and Cr 3+ ions have strong B-site preference [3,13,14].The magnetic moment nB is expressed as [3,4,10,14]: where M B and M A are the B and A sublattice magnetic moments.Formula (3) shows that the theoretical magnetic moment decreases when there is an increase in the Cr content.According to the relation of Formula (2), the theoretical saturation magnetization decreased with Cr content x.The variation of the experimental and theoretical saturation magnetization agreed with each other for all samples.It is observed from Table 4 that the coercivity of NiCr x Fe 2−x O 4 initially decreased, then subsequently increased-with an increase in the Cr content x.The coercivity was found to decrease which can be attributed to the decrease of magnetocrystalline anisotropy, as Cr has a negative magnetocrystalline anisotropy [15].However, the coercivity increased when x ≥ 0.4, due to influence by many factors, such as impurity phase, crystallinity, microstrain, magnetic particle morphology and size distribution, anisotropy, and magnetic domain size [16][17][18].
The magnetic hysteresis loops at room temperature for unsintered NiCr 0.2 Fe 1.8 O 4 , and after annealing at 400 • C, 600 • C, and 800 • C, are shown in Figure 7. Table 5 indicates that NiCr 0.2 Fe 1.8 O 4 after annealing at 800 • C offered a maximum saturation magnetization value, since the particle size increased with an increase in the annealing temperature [17].The saturation magnetization of NiCr 0.2 Fe 1.8 O 4 decreased after annealing at 400 • C and 600 • C, which may be due to the presence of an impurity phase [19,20].Similar studies have been reported in the literature [21,22].It is observed from Table 4 that the coercivity of NiCrxFe2−xO4 initially decreased, then subsequently increased-with an increase in the Cr content x.The coercivity was found to decrease which can be attributed to the decrease of magnetocrystalline anisotropy, as Cr has a negative magnetocrystalline anisotropy [15].However, the coercivity increased when x ≥ 0.4, due to influence by many factors, such as impurity phase, crystallinity, microstrain, magnetic particle morphology and size distribution, anisotropy, and magnetic domain size [16][17][18].
The magnetic hysteresis loops at room temperature for unsintered NiCr0.2Fe1.8O4,and after annealing at 400 °C, 600 °C, and 800 °C, are shown in Figure 7. Table 5 indicates that NiCr0.2Fe1.8O4after annealing at 800 °C offered a maximum saturation magnetization value, since the particle size increased with an increase in the annealing temperature [17].The saturation magnetization of NiCr0.2Fe1.8O4decreased after annealing at 400 °C and 600 °C, which may be due to the presence of an impurity phase [19,20].Similar studies have been reported in the literature [21,22].The coercivity of NiCr0.2Fe1.8O4increased initially and subsequently decreased, with an increase in the annealing temperature.This can be explained by the variation of the grain size.The coercivity in the single domain region is expressed as HC = g − h/D 2 .In the multidomain region the variation of the coercivity with grain size can be expressed as in HC = a + b/D, where g, h, a, and b are constants and D is the diameter of the particle [17,18].Hence, in the single domain region, the coercivity increased with an increase in the grain size, while in the multidomain region the coercivity decreased as the particle diameter increased.In our earlier research, the grain size increased by increasing the sintered temperatures obtained by SEM.The grain size of NiCr0.2Fe1.8O4calcined at different temperature should be ideally from the single domain region to the multidomain region, so the coercivity increased initially and then decreased with an increase in the annealing temperature [19,20].Moreover, the impurity phases of Fe2O3 in the ferrite nanopowders is also the important factor that results in the decreases of coercivity [23][24][25].The coercivity of NiCr 0.2 Fe 1.8 O 4 increased initially and subsequently decreased, with an increase in the annealing temperature.This can be explained by the variation of the grain size.The coercivity in the single domain region is expressed as H C = g − h/D 2 .In the multidomain region the variation of the coercivity with grain size can be expressed as in H C = a + b/D, where g, h, a, and b are constants and D is the diameter of the particle [17,18].Hence, in the single domain region, the coercivity increased with an increase in the grain size, while in the multidomain region the coercivity decreased as the particle diameter increased.In our earlier research, the grain size increased by increasing the sintered temperatures obtained by SEM.The grain size of NiCr 0.2 Fe 1.8 O 4 calcined at different temperature should be ideally from the single domain region to the multidomain region, so the coercivity increased initially and then decreased with an increase in the annealing temperature [19,20].Moreover, the impurity phases of Fe 2 O 3 in the ferrite nanopowders is also the important factor that results in the decreases of coercivity [23][24][25].

Conclusions
XRD analysis of the NiCr x Fe 2−x O 4 ferrite reveals that the specimens with x > 0.2 exhibit a single-phase spinel structure, while the impurity peak of Fe 2 O 3 was detected in the samples with x = 0 or 0.2.The decrease in the lattice parameter was probably due to the replacement of the larger Fe 3+ ions by smaller Cr 3+ ions.The XRD patterns of NiCr 0.2 Fe 1.8 O 4 calcined at different temperature indicate the intensity of Fe 2 O 3 decreased with increasing the heat treatment temperatures, and the diffraction peaks of the sample without burning were very sharp along with a good crystallinity.SEM results indicate that the grains were distributed homogeneously, and the ferrite powers were nano-particles; the average grain size was slightly larger than the average crystallite size determined by XRD, which shows that every particle is formed by a number of crystallites.Room temperature Mössbauer spectra of NiCr x Fe 2−x O 4 calcined at 800 • C showed the presence of two normal Zeeman-split sextets, and that it exhibited a ferrimagnetic behavior for the all samples.The decrease in the magnetic hyperfine field with increasing Cr contents was attributed to the decrease of the A-B super-exchange interaction.The saturation magnetization decreased with an increase in the Cr content x, which could be explained by Néel's theory.Furthermore, with an increase in the annealing temperature, the coercivity increased initially and subsequently decreased for NiCr 0.2 Fe 1.8 O 4 , since the particle size increased with increasing the annealed temperature.

Table 5 .
Magnetic data for NiCr 0.2 Fe 1.8 O 4 calcined at different temperatures.