A0310106

IOSR Journal of Applied Physics (IOSR-JAP)
e-ISSN: 2278-4861. Volume 3, Issue 1 (Jan. - Feb. 2013), pp 01-06
www.iosrjournals.org
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Study of Dielectric Properties of Nano-crystalline Mn-Zn Ferrite
Sunita Bhagwat*
, Pratibha Rao
Department of Physics, Abasaheb Garware College, Karve Road, Pune – 411 004, India
Abstract: The ac conductivity σ and dielectric properties (dielectric constant ’, dielectric loss ’’ and loss
tangent tan δ) were measured as a function of frequency between 100 Hz and 20 MHz for the mixed ferrites
ZnxMn1-xFe2O4 (where x = 0.2 to 0.8), synthesized by solid-state route. The ac conductivity σ below 1 MHz
seems to be nearly frequency independent for all compositions; and above these frequency ranges, σ sharply
increases until it reaches a maximum value. The relaxation time (τ) was found to be in the range 0.3x10-5
–
1.5x10-5
sec from the hopping frequency. The dielectric constant for these ferrites is approximately inversely
proportional to the square root of the resistivity. The electrical conduction mechanism was explained in terms of
the electron hopping model. The formation of spinel structure and crystalline size was confirmed using X-ray
diffraction (XRD) technique. Morphology of the samples was studied using Scanning Electron Microscopy
(SEM).
Keywords: Solid-state route; spinel ferrite; dielectric properties; ac conductivity
I. INTRODUCTION
Polycrystalline spinel ferrites are known for their sensing applications [1-2] apart from their ever
increasing demand in the technological applications in microwave and radio wave devices. These ferrites are
widely used for manufacturing transformers and inductors in power supplies [3]. They are mainly classified in
two categories: the high permeability ferrites which are used for filtering applications and the low core loss
ferrites used for power transformers and inductors in switching mode power supplies. Mn-Zn ferrites are known
for magnetic sensors [4]. However, they have not been explored much for microwave applications. The ferrite
resonator antennas (FRAs) have the ability to change their characteristics as a function of the applied magnetic
field. The low dielectric behaviour makes ferrite materials useful in high frequency applications. Some of the
properties of dielectric resonator antennas (DRAs) can be actively controlled using low-loss ferrite materials [5].
In the present work polycrystalline samples of ZnxMn1-xFe2O4 (x ranges from 0.2 to 0.8) were prepared
by solid-state route. The structural characterization was studied using XRD. The morphological studies were
carried out using SEM.
II. EXPERIMENTAL
2.1 Synthesis Technique
Polycrystalline samples of ZnxMn1-xFe2O4 (x ranges from 0.2 to 0.8) were prepared by solid-state route
using high purity ZnO, Fe2O3 and MnCO3 respectively in stoichiometric proportions. The ZnO/Fe2O3 and
MnCO3/Fe2O3 powders were grounded separately for 30 min using an agate mortar. Each mixture was
transferred to a ball mill for 6h using 50 ml vials and 12 mm diameter balls made of stainless steel and a ball-to-
powder mass ratio of 20. A rotation speed of 240 rpm was used. The milling was done in air atmosphere without
any additives. The powder is calcinated at 1000o
C for 1h with a heating rate of 2o
C/min followed by cooling at
room temperature in air. The pre-sintered samples were crushed again and mixed for another 30 min. with
acetone, to be reduced into small crystallites of uniform size. The mixture was air dried and a proper proportion
of each powder was again ball milled by adding few drops of 2-propanol. The milling was done with the
intention of producing a homogenous mixture of both solid components, without provoking significant
structural damage. Finally, the milled reactive powders were dried at 80o
C in a furnace for 30 min. The powder
was compressed uniaxially under a pressure of 1x107
N/m2
into pellet form of diameter 10 mm and thickness
about 2 mm. The pellets were sintered at 1000o
C for 3 h in air atmosphere and cooled to room temperature to
make them rigid and impart ceramic properties.
2.2 Characterization Techniques
The structural characterization of the ferrite samples was carried out using Philips diffractometer, with
CuK radiation. The average crystallite size, t, was determined using the Scherrer formula [6]:
t = 0.9 / B1/2 cos b (1)
where B1/2 is the angular line width at half maximum intensity and b is the Bragg angle for the actual peak.

Dielectric measurements were carried out at room temperature using 4192A impedance analyzer over a
wide range of frequency from 100 Hz up to 20 MHz. The dielectric constant ’ were calculated using the
formula:
’ = Cd / oA (2)
where o the permittivity of the free space, C is the capacitance, d the thickness and A the cross-sectional area of
the pellet.
The dielectric loss factor ’’ has been calculated from the relation:
’’ = ’ tan  (3)
where tan  is the loss tangent.
The ac conductivity σ of the sample was determined from dielectric parameters using the relation
ac = ’’ (4)
where  is the angular frequency.
III. RESULTS AND DISCUSSION
3.1 X-ray diffraction Studies
Fig.1 shows the typical X-ray diffraction pattern for ZnxMn1-xFe2O4 compact disk sintered at 1000o
C in
air for 3 h. The XRD pattern exhibits all the peaks indicative of single phase spinel crystal structure. The non-
occurrence of the other phases suggests there is no solubility limit to Zn2+
ions in the manganese ferrite spinel
lattice. It is known that the degree of replacement of the host cations by the other ions in the host lattice depends
on the cation radius of the substituent [7]. The crystallite size of all the samples was calculated using the
Scherrer formula and it was found to be between 40 and 50 nm.
20 30 40 50 60 70 80
(440)
(511)
(422)
(400)
(220)
Intensity(Arbitaryunits)
2 (deg)
(311)
Figure 1: Typical XRD pattern of ZnxMn1-xFe2O4
3.2 Dielectric Constant Behaviour
The dielectric behaviour of ferrite nanoparticles are influenced mainly by the synthesis technique, grain
size, cation distribution etc [8]. The behavior of both ’, ’’ and σ at RT versus frequency are shown in Fig.2 (a-
e). The general trend for all composition is that ’ and ’’ decrease with increasing frequency. The decrease in
dielectric constant with increasing frequency is attributed to the fact that electron exchange between Fe2+
and
Fe3+
ions cannot follow the change of the external applied field beyond certain frequency [9]. At lower
frequencies the grain boundaries are more effective than grain electrical conduction. This behavior of a
dielectric constant, with Zn ions substitution can be explained qualitatively on the basis of the mechanism of the
polarization process in ferrite which is similar to that in the conduction process. The whole polarization in
ferrites is mainly contributed by the space charge polarization, which is governed by the number of space charge
carriers. The conductivity in the material and the hopping exchange of charges between two localized states
governed by density of the localized state and resultant displacement of charges w.r.t. the external field. As the
frequency increases ionic and orientation sources of polarizability decrease and finally disappear due to inertia
of the molecules and ions. The high value of the dielectric constant in the present ferrite for x = 0.2 may be
attributed to space charge polarization [10]; or it could be due to an increase in crystallite size and
morphologically clean microstructure as seen in Fig. 3(a).

An examination of Table I reveals that the values of dielectric constant ’, dielectric loss ’’ and loss
tangent tan δ are maximum for x = 0.2. It also can be seen that among these mixed Mn–Zn ferrites, the one with
the compositions Zn0.8Mn0.2Fe2O4 exhibits the lowest dielectric constant, the lowest dielectric loss, the lowest
loss tangent and the lowest electrical conductivity. This might be due the presence of macro-agglomerations
containing very fine particles which can be clearly seen in Fig. 3(b).
From Table I it can be seen that the composition Zn0.2Mn0.8Fe3O4 has the maximum dielectric constant
(47.9). This high value can be explained as it has maximum number of ferrous ions whose exchange between
Fe2+
and Fe3+
gives rise to maximum dielectric polarization, that could be due to the availability of ferrous ions
on octahedral B - site. It is also pertinent to mention that the variation of electrical conductivity runs parallel to
the variation in dielectric constant as shown in Fig.2. Thus, it is the number of ferrous ions on octahedral sites
that play a dominant role in the processes of conduction as well as dielectric polarization. The electrical
conduction mechanism can be explained by the electron hopping model of Heikes and Johnston [11]. One
obtains local displacements of electrons in the direction of the applied electric field; these displacements
determine the polarization of the ferrite.
Table I. Dielectric data of ZnxMn1-xFe2O4 at 100 kHz
3.3 Dielectric Loss Factor
All dielectric materials have two types of losses. One is a conduction loss, representing the flow of
actual charges through the dielectric material. The other dielectric loss is due to the movement or rotation of the
atoms in an alternating field. The dielectric loss factor ’’ with variation in frequency is as shown in Fig.2. It is
considered to be the most important part of the total core loss in ferrites. The dielectric loss pattern is seen to be
similar to that of dielectric constant. This dielectric loss factor is attributed to domain wall resonance. At higher
frequencies, losses are found to be low, if domain wall motion is inhibited and magnetization is forced to change
by rotation. The dielectric loss obtained for the present nano-ferrites synthesized by solid-state method possess
lower value for x = 0.8 which makes this ferrite to be useful in the higher frequency applications like DRAs.
3.4 Dielectric Loss Tangent
Fig. 2(f) shows the variation of the loss tangent tan δ with frequency for the investigated composition.
It is known that loss tangent tan δ is defined as ’’/’. The occurrence of peaks in the variation of loss tangent
with frequency can observed when the hopping frequency of localized charge carriers is approximately equal to
that of the externally applied electric field; i.e., resonance phenomena. From the Fig.2 (f) it can be seen that
between x = 0 and 0.8 tan shows a maximum at frequency between 10 and 50 kHz. Iwauchi [12] reported a
strong correlation between the conduction mechanism and the dielectric behaviour of the ferrites. The
conduction mechanism in n-type ferrites is considered as due to hopping of electrons between Fe2+
and Fe3+
resulting in local displacements which determines the polarization behaviour of the ferrites [13]. The condition
for observing a maximum in tan δ of a dielectric material is given by [14]:
τ ~1 (4)
where  is the relaxation time.
And  = 2πfmax, where fmax is proportional to the hopping probability p. The relaxation time  is related
to the hopping probability per unit time, p, by an equation p or fmax α p. It was found to be in the range
0.3x10-5
– 1.5x10-5
sec. A decrease of fmax with increasing zinc content indicates that the hopping probability per
unit time decreases continuously except for x = 0.65.
3.5 AC Conductivity
The ac conductivity σ and dielectric properties (’ and ’’) as a function of frequency at RT for the
above mentioned composition are shown in Fig.2 (a–e). It can be seen that below 1 MHz, σ seems to be nearly
frequency independent for all compositions. Above these frequency ranges, σ sharply increases until it reaches a
maximum value. The dispersion in σ with frequency has been explained by Koop’s theorem [15] which
suggested that the ferrite compact acts as multilayer capacitor. In this model, the ferrite grains and grain
x ' ''  [/-cm] tan   [-cm] sqrt () '*sqrt()
0.2 4.79E+01 8.82E+01 5.04E-06 1.84E+00 1.98E+05 445.4354 2.13E+04
0.35 1.27E+01 1.06E+01 6.06E-07 7.77E-01 1.65E+06 1284.174 1.63E+04
0.5 2.38E+01 1.86E+01 1.06E-06 7.82E-01 9.41E+05 969.8687 2.31E+04
0.65 1.07E+01 4.14E+00 2.37E-07 3.86E-01 4.23E+06 2055.508 2.20E+04
0.8 5.45E+00 3.59E-01 2.05E-08 6.58E-02 4.88E+07 6986.689 3.81E+04
a

boundaries have different properties. The effect of the multilayer condenser rise with frequency as a result the
conductivity increases.
2 3 4 5 6 7
0
20
40
60
80
100

log f
Conductivityx10-6(/Ohm-cm)
0
500
1000
1500
2000
2500
3000
'and''
''
'
x = 0.2 a
2 3 4 5 6 7
0
20
40
60
80
log f
x = 0.35 b
0
200
400
600
800
1000
1200

'and''
''
'
2 3 4 5 6 7
0
20
40
60

log f
0
200
400
600
800
1000
'and''
x = 0.5
''
'
c
2 3 4 5 6 7
0
20
40
60

log f
0
10
20
30
40
'and''
'
''
x = 0.65 d
2 3 4 5 6 7
0
20
40
60
log f
x = 0.8
0
2
4
6
8
10
12
14

Conductivityx10
-6
(/Ohm-cm)
'and''
'
''
e
2 3 4 5 6 7
0.0
0.4
0.8
1.2
1.6
2.0
tan
log f
x = 0.2
x = 0.5
x = 0.65
x = 0.8
x = 0.35
f
Figure 2: (a-e) plot of ’,’’ and σ vs. frequency and (f) tan  vs. frequency at room temperature
Figure 3: SEM micrographs of ZnxMn1-xFe2O4 samples for (a) x = 0.2 and (b) x = 0.8
ba

3.6 Relation Between the Dielectric Constant and the Resistivity
The values of resistivity 
and '
are shown in Table 1. It can be seen from the table that the ’
is roughly inversely proportional to the square root of resistivity and the product '
remains nearly constant
as shown in the Table 1. A similar relationship between ’ and 
was found by Ravinder [16] for different
ferrites. The dielectric losses in ferrites are generally reflected in the resistivity measurements, materials with
low resistivity exhibiting high dielectric losses and vice versa [17]. Fig. 4 shows that the plot of dielectric
constant ’ vs. zinc content x is an inverse image of that of log of resistivity vs. zinc content. This is a
confirmation of the correlation between dielectric constant and resistivity [13].
0.2 0.3 0.4 0.5 0.6 0.7 0.8
0
20
40
60
Zn content (x)
Dielectricconstant'

'
g
5.0
5.5
6.0
6.5
7.0
7.5
8.0
log
Figure 4: Plot of dielectric constant and resistivity vs Zn concentration
IV. CONCLUSION
The dielectric properties of Mn-Zn ferrites were investigated in this study and the results are
summarized as follows:
1. The general trend for all composition is that ’ and ’’ decrease with increasing frequency.
2. The value of the dielectric constant for the sample when x = 0.2 is found to be high due to space charge
polarization mechanism or could be due to morphologically clean grain structure.
3. The value of the dielectric constant for the sample when x = 0.8 is found to be low which makes this ferrite
to be useful in the higher frequency applications like DRAs.
4. The frequency dependence of dielectric loss tangent (tanδ) shows the existence of broad peaks at low
frequency range.
5. The ’ is roughly inversely proportional to the square root of resistivity and the product  
remains
nearly constant.
ACKNOWLEDGEMENT
Author (SMB) is thankful to University Grants Commission (UGC), New Delhi for providing financial
assistance. Authors are grateful to Dr. Jyoti Jog and Mr. Chetan Chanmal, National Chemical Laboratory, Pune
for providing the dielectric data of the samples.
REFERENCES
[1] Y. Chen, J. E. Snyder, C. R. Schwichtenberg, K. W. Dennis, R. W. McCallum, D. C. Jiles, Metal bonded Co-ferrite for torque sensor
applications, IEEE Transactions on Magnetics, 35, 1999, 3652-3654.
[2] N. Iftimie, E. Rezlusu, P. D. Popa, N. Reslescu, Gas sensitivity of nano-crystalline nickel ferrite, Journal of Optoelectronics and
Aadvance Materials, 8, 2006, 1016-1018.
[3] M. Sugimoto, The past, present and future of ferrites, Journal of American Ceramics Society, 82, 1999, 269-280.
[4] R. Lebourgeois, C. Coillot, Mn-Zn ferrites for magnetic sensor in space application, Journal of Applied Physics, 103, 2008, 07E510-
513.
[5] P. B. A. Fechine, R. S. T. Moretzsohn, R. C. S. Costa, J. Derov, J. W. Stewart, A. J. Drehman, C. Junqueira, A. S. B. Sombra,
Dielectric ferrite resonator antennas, Microwave and Optical Technology Letters, 50, 2008, 2852–2857.
[6] H. P. Klug and L. E. Alexander, X-ray Diffraction Procedures for Polycrystalline and Amorphous Materials ( John Wiley, New York,
1974) 491.
[7] D. J. Kim, Lattice parameters, ionic conductivities and solubility limits in fluorite-structure MO2 oxide [M = Hf4+
, Zr4+
, Ce4+
, Th4+
,
U4+
] solid solutions, Journal of American Ceramics Society, 72, 1989, 1415-16.
[8] H.M. Abdelmoneim, Dielectric properties of TixLi1-xLa0.1Fe1.9O4 ferrite thin films, Indian Jornal of Pure and Appied. Physics, 48,
2010, 562-570.
[9] G. Ranga Mohan, D. Ravinder, A.V. Ramana Reddy and B.S. Boyanov, Dielectric properties of polycrystalline mixed nickel–zinc
ferrites, Materials Letters, 40, 1999, 39-45.

[10] D.El. Kony, Dielectric Relaxation in Al-substituted Ni-Cd spinel ferrites, Egyptcian Journal of Solids, 27, 2004, 285-297.
[11] R.R. Heikes and D. Johnston, Jornal of Chemical Physics, 26, 1957, 582.
[12] K. Iwauchi, Journal of Applied Physics, 10, 1960, 1520.
[13] L.I. Rabinkin and Z.I. Novika (Ferrites Minsk, 1960) 146.
[14] M. B. Reddy and P.V. Reddy, Journal of Physics D: Applied Physics, 24, 1991, 975.
[15] C.G. Koops, On the dispersion of resistivity and dielectric constant of some semiconductors at audio frequencies, Physical Review, 83,
1951, 121-124.
[16] D. Ravinder, Dielectric behaviour of lithium-cadmium ferrites, Physica Status Solidi A, 129, 1992, 549-554.
[17] A.S. Hudson, Marconi Review, 37, 1968, 43.

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