*3.2.2 Ps ~ fBaTiO3 for different fields*

**Figure 6** give you an idea about the variation of *P*s as a function of *f*BaTiO3 for all the PF, at changed electric fields from 5 kV/cm to 8 kV/cm. It is practical that on increasing the concentration of *n*-BaTiO3, and also on rising the electric fields, the value of *P*s raises up to *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *P*s decreases, due to the aggregation of *n*-BaTiO3 causing poor improvement of the ferroelectric properties. At 5 kV/cm, the value of *P*s increases from 0.1 μC/cm<sup>2</sup> for *f*BaTiO3 = 0.2 up to 0.24 μC/ cm<sup>2</sup> for *f*BaTiO3 = 0.30, but when *f*BaTiO3 > 0.30, *P*s decreases to 0.24 μC/cm<sup>2</sup> .

## *3.2.3 Pr ~ fBaTiO3 for different fields*

The variation of *P*r as a function of *f*BaTiO3 for all the PF (**Figure 7**), at different electric fields from 5 kV/cm to 8 kV/cm. It can be seen that on increasing the concentration of *n*-BaTiO3, *P*r increases up to *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30,

**95**

**Figure 5.**

increases from 0.10 μC/cm<sup>2</sup>

much less than 3.5 kV/cm.

*3.2.4 Ec ~ fBaTiO3 for different fields*

*Ferroelectric, Piezoelectric and Dielectric Properties of Novel Polymer Nanocomposites*

*P*r decreases, i.e. a parallel behavior as observed in the case of variation of *P*s ~ *f*BaTiO3, is also observed which is attributed to the same origin. At 8 kV/cm, *P*<sup>r</sup>

*(color online) the variation of (a) ɛeff and (b) tan* δ *as a function of frequency at 300 K for the PF.*

for *f*BaTiO3 > 0.30, *P*r decreases and approaches to much less than 0.20 μC/cm<sup>2</sup>

The variation of *E*c as a function of *f*BaTiO3 for all the PF, at different electric fields from 5 kV/cm to 8 kV/cm is shown in **Figure 8**. The value of *E*c is preserved higher up to *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *E*c decreases, i.e. a similar conduct as observed in the case of variation of *P*s ~ *f*BaTiO3, is also observed endorsed to the same origin. At 6 kV/cm, the value of *E*c increases from 2.5 kV/cm for *f*BaTiO3 = 0.2 up to 3.5 kV/cm for *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *E*c decreases and becomes

for *f*BaTiO3 = 0.2 up to 0.20 μC/cm<sup>2</sup>

for *f*BaTiO3 = 0.30, but

.

*DOI: http://dx.doi.org/10.5772/intechopen.96593*

*Ferroelectric, Piezoelectric and Dielectric Properties of Novel Polymer Nanocomposites DOI: http://dx.doi.org/10.5772/intechopen.96593*

*P*r decreases, i.e. a parallel behavior as observed in the case of variation of *P*s ~ *f*BaTiO3, is also observed which is attributed to the same origin. At 8 kV/cm, *P*<sup>r</sup> increases from 0.10 μC/cm<sup>2</sup> for *f*BaTiO3 = 0.2 up to 0.20 μC/cm<sup>2</sup> for *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *P*r decreases and approaches to much less than 0.20 μC/cm<sup>2</sup> .

## *3.2.4 Ec ~ fBaTiO3 for different fields*

The variation of *E*c as a function of *f*BaTiO3 for all the PF, at different electric fields from 5 kV/cm to 8 kV/cm is shown in **Figure 8**. The value of *E*c is preserved higher up to *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *E*c decreases, i.e. a similar conduct as observed in the case of variation of *P*s ~ *f*BaTiO3, is also observed endorsed to the same origin. At 6 kV/cm, the value of *E*c increases from 2.5 kV/cm for *f*BaTiO3 = 0.2 up to 3.5 kV/cm for *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *E*c decreases and becomes much less than 3.5 kV/cm.

*Multifunctional Ferroelectric Materials*

the ordered structure of the PF.

*3.2.2 Ps ~ fBaTiO3 for different fields*

*3.2.3 Pr ~ fBaTiO3 for different fields*

At 5 kV/cm, the value of *P*s increases from 0.1 μC/cm<sup>2</sup>

the ferroelectric polarization) as evident from **Figure 4**. Conversely the dielectric properties, such as the effective dielectric constant (εeff) and loss tangent (Tan δ) of all the PF becomes a linear dependence of *f*BaTiO3 (**Figure 5**), i.e. the static εeff enhances from 10 for pure PVDF to 400 for *f*BaTiO3 = 0.6, whereas the loss tangent increases from 0.09 for pure PVDF to 0.9 for *f*BaTiO3 = 0.6 [14]. The variation in the dielectric and ferroelectric behavior is credited to the different types of structures responsible for the two altered electrical properties respectively. The dielectric properties are connected with the more interfaces in the PF, hence εeff & Tan δ enhances linearly with *f*BaTiO3 and the ferroelectric properties are associated with

*(color online) polarization (P) vs. applied electric field (E) hysteresis loop measured at a frequency of 1 Hz* 

*with different fBaTiO3 for different fields (a) 5 kV/cm (b) 6 kV/cm (c) 7 kV/cm (d) 8 kV/cm.*

**Figure 6** give you an idea about the variation of *P*s as a function of *f*BaTiO3 for all the PF, at changed electric fields from 5 kV/cm to 8 kV/cm. It is practical that on increasing the concentration of *n*-BaTiO3, and also on rising the electric fields, the value of *P*s raises up to *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30, *P*s decreases, due to the aggregation of *n*-BaTiO3 causing poor improvement of the ferroelectric properties.

for *f*BaTiO3 = 0.30, but when *f*BaTiO3 > 0.30, *P*s decreases to 0.24 μC/cm<sup>2</sup>

The variation of *P*r as a function of *f*BaTiO3 for all the PF (**Figure 7**), at different electric fields from 5 kV/cm to 8 kV/cm. It can be seen that on increasing the concentration of *n*-BaTiO3, *P*r increases up to *f*BaTiO3 = 0.30, but for *f*BaTiO3 > 0.30,

for *f*BaTiO3 = 0.2 up to 0.24 μC/

.

**94**

cm<sup>2</sup>

**Figure 4.**

**Figure 6.** *Ps ~ fBaTiO3 at different electric fields (a) 5 kV/cm (b) 6 kV/cm (c) 7 kV/cm (d) 8 kV/cm.*

**97**

*Ferroelectric, Piezoelectric and Dielectric Properties of Novel Polymer Nanocomposites*

**Figure 9** gives the explanation of change in piezo- electric coefficient (d33) of the PF as a function of *f*BaTiO3. On increasing the concentration of *n*-BaTiO3, the piezoelectric nature of composite also increases and when the amount of *n*-BaTiO3 filler content increases much, the value of d33 becomes constant. The value of d33 increases from 2.10 pC/N for *f*BaTiO3 = 0.0 up to 2.20 pC/N for *f*BaTiO3 = 0.20 and remains constant, beyond *f*BaTiO3 = 0.20 up to *f*BaTiO3 = 1.0 because of the aggregated filler (*n*-BaTiO3) causes poor improvement in the peizo- electric nature of the PF.

*Ec ~ fBaTiO3 at different electric fields (a) 5 kV/cm (b) 6 kV/cm (c) 7 kV/cm (d) 8 kV/cm.*

The variation of dielectric properties of the PCC as a function of frequency at 300 K are shown in **Figure 10a** and **b**, respectively. The value of ɛeff at 50 Hz for the 0.0 sample is 16 while this value increases up to 120 linearly up to the PCC with *f*BaTiO3 = 0.5 & after that it raises up to the value of 330 & 420 for the samples with *f*BaTiO3 = 0.55 & *f*BaTiO3 = 0.60 respectively. The higher value of ɛeff for the *f*BaTiO3 = 0.55 & *f*BaTiO3 = 0.60 are attributed to the large interfacial polarization arising due to the occurrence of spherulites and created large interface like structures(during cold pressing), while the spherulites are lost for the hot molded

The static dielectric constant (εr) of the cold pressed pure PVDF is ~16 i.e. higher

than the εr of hot molded pure PVDF (~10) due to the loss of spherulites (Inset, **Figure 11**) of the polymer. ɛeff decreases with increase of frequency due to the

*DOI: http://dx.doi.org/10.5772/intechopen.96593*

**3.3 Piezoelectric properties**

**Figure 8.**

**3.4 Dielectric properties**

samples (**Figure 11**).

**Figure 7.** *Pr ~ fBaTiO3 at different electric fields (a) 5 kV/cm (b) 6 kV/cm (c) 7 kV/cm (d) 8 kV/cm.*

*Ferroelectric, Piezoelectric and Dielectric Properties of Novel Polymer Nanocomposites DOI: http://dx.doi.org/10.5772/intechopen.96593*

**Figure 8.** *Ec ~ fBaTiO3 at different electric fields (a) 5 kV/cm (b) 6 kV/cm (c) 7 kV/cm (d) 8 kV/cm.*
