- Open Access
- Total Downloads : 6
- Authors : Naveen Kumari, Vinod Kumar, S. K. Singh
- Paper ID : IJERTCONV1IS02047
- Volume & Issue : NCEAM – 2013 (Volume 1 – Issue 02)
- Published (First Online): 30-07-2018
- ISSN (Online) : 2278-0181
- Publisher Name : IJERT
- License: This work is licensed under a Creative Commons Attribution 4.0 International License
Investigations on Transition Metal Doped Pure Ferrite Nanoparticles
Investigations on Transition Metal Doped Pure Ferrite Nanoparticles
1Naveen Kumari, 2Vinod Kumar, 3S. K. Singh
Abstract FeCr0.2Fe1.8O4 nano-particles were synthesized by chemical co precipitation method. The developed particles were characterized by powder X-ray diffraction technique for crystalline properties. The diffraction peaks shows the single crystalline phase of the developed spinel ferrite particles. Effect of Cr3+ ion doping on dielectric properties was studied as a function of frequency in the range 100Hz-5MHz, using impedance analyzer. Electrical conductivity was found to increase with doping of Cr3+ ions. Activation energy found to decrease with Cr3+ ion doping. An exponential increase in ac conductivity was observed with increase in frequency. Increase in conductivity was explained on the basis of Maxwell- Wagner two layer model. Conductivity was found to increase with temperature. The developed particles were further utilized for ferrofluid preparation.
Index TermsStructural parameters; Electrical resistivity; activation energy; Dielectric parameters.
Much increasing interest of nanoparticle ferrites is the discovery of their unusual properties such as structural, electronic, optical and magnetic when their microstructure is reduced to nano region . Polycrystalline ferrites are supposed to be very good dielectric material with high resistivity and vide range of technical applications in wide frequency range. As nanoparticle size, shape, crystallnity, particle size distribution play important role on physical, chemical, electrical properties of particles . The properties and size of nanoparticle are very sensitive to preparation technique . The spinel nanoparticle ferrites have been synthesized by various techniques [4-6]. The distribution of cations over tetrahedral and octahedral sites in ferrites has remarkable effect on electrical and magnetic properties . In present report to investigate the effect of transition metal(Cr3+) doping on structural and electrical properties in nano dimension we have synthesized nanoparticle FeCr0.2Fe1.8O4 via chemical co-precipitation method using oleic acid as surfactant. Reduction in agglomeration of particles was observed when nanoparticles were caped with oleic acid .Results of investigation were analyzed in terms of crystalline size, X-ray density(x), measured density, effect of temperature and frequency on dielectric parameters of ferrite sample.Experimental
Transition metal (Cr3+) doped ferrite nano particle FeCr0.2Fe1.8O4 were prepared by Chemical Co-precipitation method, Analytical grade chemical reagents used in this work were Ferrous chloride FeCl2 and Ferric nitrate Fe(NO3)3.9H2O and Cr(NO3)3.9H2O.0.25M aqueous solution of all the reagents in specific amount were mixed using stirring. The reaction temperature was kept 70oC for approximately 40 min. The precipitated reagent ammonia (NH3) was mixed to homogeneous aqueous solution with constant stirring A specific amount of oleic acid in 1:2 ratio as a surfactant was added to prevent agglormation of precipitated particles and to protect from atmospheric oxygen. The PH of reaction temperature was constantly monitored and was achieved at 7.5.The precipitated particles were repeatedly washed with distilled water until the solution was free from Nitrate and Chloride ions. The product was dried in air at 100oC to remove water contents. The dried powder mixed homogeneously in cleaned mortar and pestle. The prepared material was analyzed for crystalline phase, various structural and physical properties using XRD. XRD pattern was taken at room temperature using Cuk (=1.54060Ao) radiation in 2 range 20o-70o.Crystalline size (D) of synthesized particle was calculated using Scherrer formula .
Here K is Scherrer constant, is X-ray wavelength, is full width at half maximum and is diffraction angle. Lattice constant (a), X-ray density (x), measured density (m), porosity (P), specific surface area(S) [16-17] were estimated using following relations
a=d/sqrt (p+k2 +l2) in Ã… 2)
Where d is interlplaner spacing
x=8M/Na3 in gm/cm2 3)
Where M is molecular weight of sample, N is Avogadros number
m=m/r2h in gm/cm2 4) Where m is mass, r is radius, h is height of sample. P=1-(m/x) 5)
The fine powder was palletized in form of a pellet of 13mm in dia. and thickness (t) =2.628mm under a pressure of 37.5N/m2 for 5min.using hydraulic press .Then pallet was used for the measurement of various dielectric parameters using impedance analyzer in frequency range from 100Hz to 5MHz.The real () and imaginary part () of dielectric constant, dielectric loss tangent (tan) and ac conductivity (ac) were calculated using following standard relations.
= tan 8) because of increase in drift mobility of charge carriers as
=02f tan 9)
electron hoping between ferrous (Fe2+) and ferric (Fe3+) ions
Where C is capacitance in farad (F) A is X-sectional area of pallet in m2
0 is constant of permittivity in free space, 8.85*10-14 Fcm-1 f is frequency of applied field in Hz
RESULTS AND DISCUSSION
Fig.1 shows the X-ray diffraction pattern of the prepared ferrite sample .Analysis of XRD diffraction pattern shows strong diffraction from the (220), (311), (400), (422), (511) and (440) planes confirm the formation of cubic spinel structure of ferrite sample. The average crystalline size (D) of ferrite is calculated using Scherrer formula using most intense peak, i.e., (311) .The average crystalline size comes out to be 16.54nm.
Fig.1 XRD pattern of FeCr0.2Fe1.8O4 sample at room temperature.
Fig.2 shows frequency dependence of real part of dielectric constant () at different temperatures. Analysis shows that there is decrease in dielectric constant () with increase in frequency and there is increase in dielectric constant () with increase in temperature. It is being observed that, this increase is quite significant at lower frequencies and as frequency increases this increase in dielectric constant() becomes quite insignificant. At higher frequency electron exchange between Fe2+/Fe3+ ions cannt follow with applied alternating electric field, which causes a decrease in contribution of space charge polarization in dielectric constant and we observe a decrease in dielectric constant .The sharp decrease in with increase in frequency can also be explained on the basis of Maxwell- Wagner two layer model , according to which ferrite are consisted of well conducting grains followed by thin layer of poorly conducting grain boundaries . The decrease in dielectric constant with increase in frequency is normal dielectric behavior was observed by several investigators [11- 13] and was explained by Rezlescu and Rezlescu .This increase in dielectric constant with temperature could be
present at octahedral site is thermally enhanced by increasing temperature which causes local displacement of charge carriers in the direction of applied electric field which in turn enhance their contribution to the space charge polarization
.This ,in turn, lead to increase in the value of dielectric constant() . It is known that dielectric constant of ferrite materials is due to interfacial, dipolar(alignment of permanent dipoles molecules), electronic(due to displacement of centre of negatively charged electron cloud relative to positive nucleus of ato by electric field) and ionic polarization(due to displacement of cations and anions in opposite direction when electric field is applied)  .Dipolar and interfacial polarization play dominant role at lower frequencies and both are temperature dependent . At higher frequencies electronic and ionic polarization are main contributors and both these does not depend upon significantly upon temperature.So significant increase in dielectric constant with temperature at lower frequencies arises from the combined effect of dipolar and interfacial polarization. At high frequencies dielectric constant () is almost constant due the dominant effect of ionic and electronic polarization.
Fig. 2 Frequency dependence of Dielectric constant() at different temperatures i.e 373K,423K,473K.
Fig.3 shows variation of dielectric loss tangent (tan) with frequency at different temperature. The dielectric loss arises when polarization lags behind applied ac electric field .Fig shows that the dielectric loss decreases rapidly in low frequency region because at lower frequencies due to high resistivity of grain boundaries, more energy is required for electron exchange between the Ferrous and ferric ions at octahedral site as a result of which loss is high .While it becomes almost frequency independent at higher frequencies because at higher frequencies jumping frequency of ions can not follow applied electric field. Also there is increase in dielectric loss wi th increase in temperature due to the increased conduction of thermally activated electrons.
Fig.3 Frequency dependence of dielectric loss tangent(tan) at different temperature i.e 373K,423K,473K.
The total conductivity can be approximated as
(, T)=dc(T) + ac(, T) = dc(T) + A(T)s(T) 10)
Here dc is temperature dependent dc conductivity and ac is temperature and frequency dependent ac conductivity.A(T) is temperature dependent term and s(T) is universal power law exponent value lying in the range from 0 to 1. Fig.4 shows variation of log() with frequency at different temperature. Conductivity increases with temperature which is due to increased hopping of thermally activated charge carriers. Variation shows that total conductivity almost remains constant in lower frequency region and shows dispersion for higher frequency which is in accordance with eq.(10).
Fig.4 Frequency dependence of ac conductivity(ac) at different temperature i.e 373K,423K,473K.
It is being observed from plot that with increase in temperature this dispersion in frequency shifts towards higher frequency. In the low frequency region, grain boundaries are more effective with high resistance due to which we obtain constant plateau region (dc). At higher frequencies, the
increase in conductivity is due to increased hoping of charge carriers (ferrous and ferric) at octahedral site and also due to grain effect . s(T) universal power law exponent is being calculated from the variation of logac with logw at different temperatures which shows decreasing behavior with increasing temperature which is in accordance with CBH(correlated barrier hopping)model .
D.C electrical conductivity of transition metal doped ferrite system was recorded as a function of temperature is shown in fig.5. From graph it is being observed that dc(D.C. electrical conductivity) increases with increase in temperature which revels the semiconducting nature of ferrite sample. The plot shows an Arrhenius-type temperature dependence i.e. =
oexp(-E/kBT), where E is activation energy, kB is Boltzmann constant and T is absolute temperature. Activation energy (E) was calculated from slope of 1000/T vs log dc in two different temperature ranges. E =0.42 in temperature range 333K- 503K and E =2.34 in temperature range 568K- 618K. In most ferrite samples, a straight line is found in these plots in a wide temperature range but in this ferrite sample a change in slope is being observed which points to two parallel conductivity mechanism with different activation energies.
Fig.5 Arrhenius plot for dc conductivity.
Transition metal doped FeCr0.2Fe1.8O4 nanoparticles were successfully synthesized using chemical co-precipitation technique. XRD pattern confirm the formation of spinel structure of prepared sample. Dielectric constant() increases with increase in temperature and decreases with increase in frequency of applied field which shows significant increase with temperature at low frequencies and becomes approximately temperature independent at higher frequencies. Dielectric loss tangent (tan) decreases with increase in frequency which shows fast decrease at low frequency and becomes approximately frequency independent at higher frequencies because at higher frequencies hoping of electron between Ferrous and ferric ions could not synchronize with applied electric field. AC conductivity increases with increase in frequency and temperature.
Table 1: Table showing crystalline properties viz. crystalline size (D(311)), lattice constant (a), lattice volume (V), X-ray density (x), measured density (m), porosity (P), and electrical properties viz. electrical resistivity (dc), activation energy (E), and dielectric constant (), universal power
law exponent s(T), relaxation time ( ,,).
dc at 373k
583.83 (Ã…) 3
Conductivity is approximately constant in lower frequency region and shows dispersion at higher frequency region. Calculated values of s(T) universal power law exponent shows decreasing behavior with increasing temperature which is in accordance with CBH(correlated barrier hopping)model. Relaxation time(M,, ) decreases with increase in temperature which ensure the increase in conductivity with increase in temperature.
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