Superparamagentic Behaviour of MgFe2O4 Nano-ferrite
A. K. Srivastava*, Nishant Mongia
Department of Physics, Lovely Professional University, Phagwara, (Punjab)- 144411, India
Keywords: ferrite; superparamagnetic; VSM.
Nanosized magnesium ferrite (MgFe2O4 ) is synthesized using sol-gel method and then sintered at different sintering temperature. Chemicals required for synthesis of MgFe2O4 are: magnesium nitrate, Mg(NO3)2.6H2O with molecular weight 256.41 (AR grade) and ferric nitrate Fe(NO3)3.9H2O with molecular weight 404.00 (AR grade). Citric acid C6H6O7 with molecular weight 192.13 (AR grade) is taken as catalyst. Aqueous solutions of metal nitrates are prepared separately in stoichiometric proportion by dissolving the salts in distilled water. Aqueous solution of citric acid is added to the salt solution with cation to citric acid molar ratio of 1:1. The solution is then heated at 80°C with continuous stirring for about 2 hours with the help of magnetic stirrer until a viscous gel is formed. The viscous gel is dried in an oven by overnight heating for about 20 hours at 120°C to form the dried precursor powder. This precursor is sintered at different temperatures ranging from 300-800°C for 1 hour in a furnace. Samples prepared after sintering are gently crushed with mortar and pestle to get powder for characterization.
B. Characterization Tools
X-ray diffraction (XRD) patterns of thesamples are taken from PANALYTICAL instrument (X’pert pro) using Cu-Kα (λ= 1.54060 Å) radiation. FT-IR spectra are recorded in KBr medium in therange of 4000-375 cm-1 with a IR Prestige-21 FT-IR (Model SHIMADZU-8400S). Magnetization measurements are made through VSM (PAR 155 Model) at room temperature upto 8 KOe.
X-ray diffraction patterns of MgFe2O4 ferrite yield promising results in the synthesis of fine nanoparticles at fairly low temperature. The sol-gel method facilitates the formation of well-crystalline single phase structure of MgFe2O4 crystallites. XRD patterns of MgFe2O4 samples prepared at different sintering temperatures i.e.at 300, 600, 800 °C with pH less than 1, are shown in Fig. 1. It is clear that all the samples of the MgFe2O4 ferrites have FCC spinel structure due to the presence of (220), (311), (400), (422), (511), (440) and (533) reflection planes [10,11,12]. All the main peaks are indexed as the MgFe2O4in the standard data files of Joint Committee on Powder Diffraction Standards, (JCPDS no. 88-1937). Well resolved peaks in XRD pattern clearly indicate the single phase and polycrystalline nature of the samples. It can be seen that no change in the crystal structure occurs when nanoparticles are prepared at different sintering temperatures.
The lattice parameter ‘a’ is calculated using the formula  corresponding to prominent peak (311):
where 'a’ is the lattice parameter of the unit cell, ‘dhkl’ is the interplanar spacing and (h k l) are Miller indices of the plane.The required experimental values of interplanar distance dhkl for prominent peak (311) of different samples, needed for the calculation, are shown in Table 1. The calculated values of lattice parameter of all samples are also given in Table 1 which are in good agreement with the earlier reporters [14,15]. The lattice parameter ‘a’ which is determined as 8.386 Å matches well with JCPDS no. 88-1937. It is found that there is slight decrease in values of lattice constant with increase of sintering temperature. Similar trend was observed for copper zinc ferrites by P. Chand (2008) . This behaviour may be related to normal-inverse spinel transitions, as a consequence of temperature increase.
The crystallite size (D) of the particle of synthesized powder is determined from XRD peak broadening of (311) peak using Scherrer’s formula :
where D is the average particle size, β is full width at half maximum (FWHM) in radians, λ is the wavelength, and θ is the Braggs angle for the diffraction peak. The calculated values of particle size of the samples are given in Table 1. The required experimental values of peak position and FWHM for different samples, needed for the calculation, are also given in Table 1.
The bond length of tetrahedral (A-O) and octahedral (B-O) sites of cubic spinel structure have been estimated by using Standely’s equations .
where ‘a’ is the lattice constant and ‘u’ is oxygen ion parameter (u = 0.382 for MgFe2O4).The calculated values of the bond lengths of tetrahedral (A-O) and octahedral (B-O) sites of cubic spinel structure of the samples are given in Table1.The data shows complete relevance with the well known fact that bond length of octahedral site is greater than that of tetrahedral site.
TABLE 1: Peak position, dhkl-spacing and FWHM of MgFe2O4 system sintered at different temperatures for (311) plane.
|Sintering Temperature (°C)||Position (°2Th)||d311-spacing(Å)||FWHM (°2Th)||Particle size(nm)||Lattice-constant (Å)||Tetrahedral bond-length (Å)||Octahedral bond-length (Å)|
Fig.1:XRD patterns of MgFe2O4 ferrites sintered at different temperatures.
Slight variation observed in bond lengths is attributed to the respective values of lattice constant, higher values of lattice constant indicates decrease in covalent character .
It is found that that particle size remains almost constant as sintering temperature increases from 3000C to 800°C.This may be due to small pH value of the samples which is a controlling parameter of size for nanoparticles growth. It is observed that peaks get sharpen and intense with increasing sintering temperature, as expected for nanocrystalline materials. This is due to increase in crystallinity with increase in sintering temperature.
FTIR spectrum is taken for the samples, prepared by grinding them with mortar and pestle into a mixture with KBr at approximately 1:10 mass ratio. The mixture is then pressed to make the thin pallets. The spectra of the samples are collected in the range of 4000-375cm-1 with IR Prestige-21 FTIR (model-8400S) of Shimadzu Corporation.
Figure 2 presents the infrared spectra of ferrite system MgFe2O4 prepared at different sintering temperature. The FTIR spectra are found to exhibit two major bands in the range 375-600 cm-1. The high frequency band (ν1) is in the range 560-580 cm-1 and the lower frequency band (ν2) is in the range 390 - 410 cm-1. These bands are common characteristics of spinel structure. The vibration of unit cell of the cubic spinel can be constructed in the tetrahedral (A) site and octahedral (B) site. The absorption band (ν1) is caused by stretching vibrations of the tetrahedral metal-oxygen bond and absorption band (ν2) is caused by the metal-oxygen vibrations in octahedral sites . The change in band position is expected because of the difference in the Fe3+– O2- distances for tetrahedral and octahedral complexes. It is found that Fe–O distance of A-site (1.89 Å) is smaller than that of the B-site (1.99 Å).This can be interpreted by more covalent bonding of Fe3+ ions at A-sites than B-sites.
Fig. 2: FTIR patterns of MgFe2O4 ferrites sintered at different temperatures.
There is slight variation in band frequency positions of tetrahedral and octahedral sites (ν1, ν2), for different samples. This is due to redistribution of cations among tetrahedral and octahedral sites, when samples are prepared as nanoparticles. More constructively, the increase in tetrahedral absorption frequency (ν1) for some samples may be accounted to the transition from normal to inverse spinel. In an inverse spinel ferrite the tetrahedral site is occupied by Fe3+ ions and octahedral site is occupied by Fe3+ and divalent ions. Due to charge imbalance the oxygen ion is likely to shift towards Fe3+ ions increasing the force constant between Fe and O. Hence we expect an increase in the tetrahedral band frequency (ν1), as we go from normal to inverse spinel.
One more thing is observed in some samples that there is splitting of octahedral absorption band as shown in Figure 2, which may be due to presence of different cations at B-site; Mg2+ and Fe3+ ions, showing inverse or partial inverse spinel structure.
FTIR spectra of MgFe2O4 samples show some additional bands with strong absorption around 3600-3200 cm-1, 1650-1560 cm-1 and 1390-1340 cm-1 which correspond to the stretching modes of O–H group, bending vibration of N–H bond in amine (–NH2) group and symmetrical stretching of N–O bond in nitro (C–NO2) group respectively. Also small absorption at nearly 2808 cm-1 is due to –CHO group. The presence of hydroxyl group is associated with water molecule, as water plays an important role in the formation of ferrites and their stabilization. No particular trend is observed in the absorption intensity due to functional groups in FTIR spectra of the samples. So, it appears that these groups are present in the samples during preparation of the spinel ferrites by sol-gel method and are not completely removed after sintering the samples at high temperature.
Hysteresis loops of different MgFe2O4 ferrite samples are analyzed at room temperature up to the applied magnetic field 8 kOe using VSM (Model PAR 155, from Princeton Applied Research USA). MgFe2O4 nanoparticles show typical hysteresis behaviour. Hysteresis loops are plotted for the measurements of magnetic parameters, particularly saturation magnetization (Ms) and coercivity (Hc) of the nanoferrite.
TABLE 2:Particle size, saturation magnetization (Ms), coercivity (Hc) and remanent magnetization (Mr) of MgFe2O4 system sintered at different temperatures.
|Sintering Temperature (°C)||Particle size(nm)||Saturation Magnetization Ms (emu/g)||Coercivity Hc (Oe)||Remanent Magnetization Mr (emu/g)|
Fig. 3: Room temperature hysteresis loops of MgFe2O4 ferrites sintered at different temperatures.
Figure 3 shows the hysteresis loops of MgFe2O4 samples sintered at temperatures 300 and 800°C for 1 hour. The sample exhibits vanished hysteresis as the sintering temperature is lowered. First, smaller value of saturation magnetization is observed. Second, coercivity approaches to zero with decrease in sintering temperature. The observed values of saturation magnetization and coercivity of MgFe2O4 ferrites sintered at 300 and 800°C are listed in Table 2. An appreciable decrease in the saturation magnetization (Ms) of the sample sintered at 300°C (≈7.40 emu/g) than one sintered at 800°C (≈37.40 emu/g) is found. It is found that the coercivity (Hc) decreases for the sample sintered at 300°C (≈0 Oe) as compared to sample sintered at 800°C (≈18.66 Oe).
The small value of coercivity may be attributed to the small size of the ferrite particle. Nanoparticles prepared are small enough that have reached single domain range and due to the randomizing effects of thermal energy, coercivity is very less.
A single domain particle of volume v has a uniform magnetization directed along the easy axis of magnetization. If v is small enough and the temperature is high enough that thermal energy will be sufficient to overcome the anisotropy energy causing a spontaneous reversal of magnetization. Coercivity (Hc) decreases due to thermal activation of magnetic spins below a critical volume and finally vanishes at superparamagnetic critical volume .
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