A. Yusmar et al./ Materials Today: Proceedings 5 (2018) 14955–14959
14957
Fig. 1. (a) X-ray diffraction pattern of Mn
1-
x
Zn
x
Fe
2
O
4
ferrite synthesized by coprecipitation method (a)
x = 0.2, (b)
x = 0.3, (c)
x = 0.4, (d)
x = 0.5,
(e)
x = 0.6, (f)
x = 0.7, and (g)
x = 0.8, (b) Variation of average crystal sizes (■) and lattice constant (▼) as a function of Zn concentration.
The morphology of Mn
1-
x
Zn
x
Fe
2
O
4
spinel ferrite was observed by TEM analysis.
TEM image of Mn
1-
x
Zn
x
Fe
2
O
4
spinel ferrite is shown in Fig. 2. TEM image shows Mn
1-
x
Zn
x
Fe
2
O
4
as prepared experience agglomeration due to
small particle size producing high surface energy and surface tension of ferrites. The SEAD pattern confirms that
Mn
1-
x
Zn
x
Fe
2
O
4
spinel ferrite was polycrystalline materials.
Fig. 2 (a) TEM image of Mn
1-
x
Zn
x
Fe
2
O
4
(b).SAED image of Mn
1-
x
Zn
x
Fe
2
O
4
.
Figure 3 shows the variation of real dielectric constant (
ε’) and imaginary dielectric constant (
”)
as a function of
frequency for the all samples Mn
1-
x
Zn
x
Fe
2
O
4
spinel ferrite at room temperature in the frequency range from 5-120 kHz.
For all samples, the value of
ε’ and
ε” is high at low frequency and then it decreases as the frequency increases,
and finally becomes saturated at high frequency. This is a normal behavior observed in most of the ferrite material
[3]. The frequency dependent behaviors of dielectric constants in ferrite follow the Maxwell-Wagner’s interfacial
polarization is in agreement with Koop’s theory [8]. The high values of dielectric constant
at low frequency are
caused by the predominance of species like Fe
2+
ions, interfacial dislocation pile-ups, oxygen vacancies,
grain
boundaries and different kind of polarizations (electronic, atomic, interfacial, and ionic etc.) [9]. In the other hand at
high frequency, the dielectric constant decreases due to the electronic exchange between the ferrous and ferric ions
a
b
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