# Structural, Dielectric, Optical and Magnetic Properties of Ti3+, Cr3+, and Fe3+: PVDF Polymer Films

Authors: M. Obula Reddy; L. Raja Mohan Reddy
Journal: Journal of Polymers
 (2013)

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## Abstract

Highly transparent and very clear nature of PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films of good quality have been synthesized by employing solution casting method. XRD profiles have confirmed semicrystalline structures in α-, β-, and γ-PVDF phases. IR spectra have confirmed these findings and revealed some structural defects such as monofluorinated alkenes. Emission spectra reveal that PVDF: Ti3+ has a blue emission, PVDF: Cr3+ has blue emission, and PVDF: Fe3+  red emission was observed. The conductivity and dielectric measurements have also been carried out as function of frequency and temperature changes. Due to the presence of the transition metal ions in these films, significant improvement in the ionic conductivity has been noticed. The dielectric behaviors of these films have been analyzed using dielectric permittivity (ε1), dissipation factor (tan δ), and impedance spectra (Z1 and Z11). VSM measurements have confirmed that the PVDF: Ti3+ exhibits antiferromagnetic nature, PVDF: Cr3+ film ferromagnetic nature, and PVDF: Fe3+ film strong paramagnetic nature. Thus, the present study has successfully explored the fact that these optical materials are also potential enough in both conductivity and magnetic properties for their use in applications suitably.


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## Body

## 1. Introduction

Polymer based magnetoelectric materials are promising materials such as conductive adhesives, supported catalysts, sensors, luminescent films, electrooptical devices, integrated optics, memory devices, and optical data processing technologies, and it is possible to achieve impressive enhancements of material properties as compared with the pure polymers, as being metal free and environmentally acceptable, due to the polymers unique characteristics such as flexibility, light weight, versatility, and low cost, and in some cases, biocompatibility can be taken to advantage [1–8].As a semicrystalline polymer, poly(vinylidene fluoride) (PVDF) is fit for membrane material due to its excellent chemical resistance, physical and thermal stability, high strength, high dielectric constant, and flexibility. Another feature that distinguishes PVDF from other polymers is its polymorphism; that is, it may present at least four crystalline phases ofα, β, δ, and γ. Moreover, an increasing interest has been devoted to PVDF in the development of electric or magnetic field sensors. For this application PVDF was added with transition metal (Ti3+, Cr3+ and Fe3+) ions to evaluate their electrical and magnetic properties.


## 2. Experimental Study

### 2.1. Sample Preparation and Characterization

The materials used in the present work are all high purity grade. PVDF, DMA, TiCl3, CrCl3, and FeCl3 are used for this study. Both the host polymer and dopant chemicals have been dissolved separately in 99.9% pure dimethylacetamide (DMA) in the proportion of 9 : 1 (Wt%) and such mixed solutions were stirred thoroughly using a magnetic stirrer at temperature 323 K for 24 hrs and each of these polymer solutions was cast onto Petri dishes and was kept in a vacuum oven at 333 K for two days in removing solvent traces while evaporation process takes place. The thickness of the films was in the range of ≈100 μm.The structures of the prepared polymers were characterized on XRD 3003 TT Seifert diffractometer withCukα radiation (λ=1.5406Å) at 40 KV and 20 mA and the 2θ range was varied between 10° and 70°. Perkin-Elmer FT-IR spectrophotometer was used for recording FTIR spectrum of the PVDF film in the region of 4000–400 cm−1. Both excitation and emission spectra of these polymer films were recorded on a SPEX FLUOROLOG (model-II) attached with a Xe-arc lamp (150 W). The dielectric constant, dielectric loss, and conductivity measurements were carried out on a Phase Sensitive Multimeter (PSM) Model-1700. The magnetic moment profile as function of applied magnetic field was measured on a Vibrating Sample Magnetometer (VSM) (Model-4500 magnet walker (model HF-20H)).


## 2.1. Sample Preparation and Characterization

The materials used in the present work are all high purity grade. PVDF, DMA, TiCl3, CrCl3, and FeCl3 are used for this study. Both the host polymer and dopant chemicals have been dissolved separately in 99.9% pure dimethylacetamide (DMA) in the proportion of 9 : 1 (Wt%) and such mixed solutions were stirred thoroughly using a magnetic stirrer at temperature 323 K for 24 hrs and each of these polymer solutions was cast onto Petri dishes and was kept in a vacuum oven at 333 K for two days in removing solvent traces while evaporation process takes place. The thickness of the films was in the range of ≈100 μm.The structures of the prepared polymers were characterized on XRD 3003 TT Seifert diffractometer withCukα radiation (λ=1.5406Å) at 40 KV and 20 mA and the 2θ range was varied between 10° and 70°. Perkin-Elmer FT-IR spectrophotometer was used for recording FTIR spectrum of the PVDF film in the region of 4000–400 cm−1. Both excitation and emission spectra of these polymer films were recorded on a SPEX FLUOROLOG (model-II) attached with a Xe-arc lamp (150 W). The dielectric constant, dielectric loss, and conductivity measurements were carried out on a Phase Sensitive Multimeter (PSM) Model-1700. The magnetic moment profile as function of applied magnetic field was measured on a Vibrating Sample Magnetometer (VSM) (Model-4500 magnet walker (model HF-20H)).


## 3. Results and Discussion

### 3.1. XRD Analysis

XRD diffraction reveals that the PVDF polymer films under investigation are characterized by semicrystalline structure and it has three crystal structures includingα-, β- and γ-phases [9, 10]. From Figures 1(a)–1(c), the spectra of the (a) PVDF: Ti3+, (b) PVDF: Cr3+, and (c) PVDF: Fe3+ polymer films present peaks at 2θ  ≈ 20.25°, 39.64°, 42.06° and 46.21° and labeled to the diffractions in planes of (110), (002), (042) and (114), respectively; those could be due to the characteristic peaks of α, β, and γ crystalline phases, and are confirmed by FTIR analysis as well. The results is shown in Table 1 and in good agreement with the reports made available in the literature [11, 12].Table 1
X-ray diffraction peaks semi-crystalline PVDF phases.
Values of 2 and respectived spacing observed in the X-Ray Diffraction
2θ (in degrees)
d (Å)
Assignment
Plane
20.25
4.30
β
110
39.64
2.28
α
002
42.06
2.13
α
042
46.21
2.06
γ
114Figure 1
((a)–(c)) XRD profile of PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.


### 3.2. FTIR Analysis

Figures2(a)–2(c) show the plots of IR transmission spectra of the PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films in the spectral range of 4000–400 cm−1 and all the spectra are found to be more similar in nature. The main PVDF characterizing frequencies are observed, where β phase occurs mostly at 440 cm−1, 510 cm−1 and 840 cm−1 and, for α phase at 430 cm−1, 610 cm−1, 765 cm−1, and 1420 cm−1. However, the peaks at 880 cm−1 and 950 cm−1 were identified as belonging to the γ-phase. Couple bands that are identified at 1665 cm−1 and 1629 cm−1 have been assigned to the C=C stretching as was reported earlier [13, 14] and this indicates the presence of polarons in the polymeric matrix. The band at 748 cm−1 which refers to the head to head (h-h) and tail to tail (t-t) defects [15]. The change of the intensities of these IR bands indicates a change of the chelation mode of Ti3+, Cr3+, and Fe3+ in PVDF matrix. It is interesting to notice that the C=C mode and the h-h defects are suitable sites for polarons and bipolarons formation in the PVDF matrix.Figure 2
((a)–(c)) FTIR spectra of PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.


### 3.3. Photoluminescence Analysis

Figures3(a)–3(f) show both excitation and emission spectra of PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films. For PVDF: Ti3+, the emission spectrum has been obtained with λexci = 387 nm, the emission spectrum displays emissions at 413 nm (could not be assigned) 435 nm (3T1(F)→3A2(F)), and 457 nm (also could not be assigned to a transition). For PVDF: Cr3+, the emission spectrum has been measured with λexci = 385 nm, strong emission bands are observed at 421 nm (Eg2→T42g) and 435 nm (T42g→A42g). For PVDF: Fe3+ emission spectrum has been recorded with λexci = 329 nm, strong emission bands are observed at 588 nm and 625 nm (4A2→4T1 (4P)). All assignments that are made on the measured emission bands are in agreement with the literature reported results [16].((a)-(b)) Excitation and emission of PVDF: Ti3+ polymer films. ((c)-(d)) Excitation and emission of PVDF: Cr3+ polymer films. ((e)-(f)) Excitation and emission of PVDF: Fe3+ polymer films.
(a)
(b)
(c)
(d)
(e)
(f)


### 3.4. Impedance Analysis

Impedance analysis reflects the collective response of microscopic polarization process under an external electric field. Under an alternating field, frequency dispersion or dielectric relaxation is observed due to different polarization mechanisms within a dielectric. Typical spectroscopic plots of dielectric constant (ε1) versus frequency (f) for the three polymer (PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+) films are shown in Figures 4(a)–4(c). It is observed that the ε1 decreases rapidly with increasing frequency. The rapid fall of dielectric constant (ε1) in their frequency range shows that space charge polarization contributes significantly to the total polarization observed in these films. Space charge polarization (interfacial polarization) arises whenever phases of different conductivities are present in the same material. When an electric field is applied, the charges more through a conducting phase but are interrupted as they come across a high resistivity phase. This leads to a buildup of charge at the interface, which is manifested as enhanced polarization. These builtup charges cannot follow the applied field rapidly at high frequencies and hence, the resultant loss. The dielectric loss (tanδ) versus frequency (f) for the three polymer (PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+) films are shown on Figures 5(a)–5(c). A single relaxation peak was observed. The loss peak maximum shifts to a lower frequency with decreasing temperature, and the peak intensity decreases and the distribution broadens. This may be due to the result of a dominant effect of the polarization by migrating charges at low frequency. The dispersion observed at low frequencies could be attributed to the interfacial polarization mechanism and the dispersion observed at high frequencies could be attributed to the dipolar relaxation [15, 17].((a)–(c)) Dielectric constant as function of frequency for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)((a)–(c)) Dielectric loss as function of frequency for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)Complex plane plots (Z1 versus Z11) for a typical polymer films are shown in Figures 6(a)–6(c). The behaviour of films and at different temperatures is similar. The Cole-Cole plots showed two well-defined regions. semi circle pattern indicating the involvement of a single conduction mechanism in the composite system. The single mechanism is attributed to grain size or due to the mobility of free charges (polaron or free ions) induced by the increment of temperature. The bulk dc resistance (Rb) of the electrolyte was determined as the point where the high frequency semicircle in the plots cuts the Z1 axis. The ionic conductivity (σ) is calculated
(1)σdc=d(Rb·A),
where d = thickness of the film and A = area of the electrodes. It has been observed in polymer films that σdc values first increased with increased temperature; this can be explained with the help of free volume theory. As the temperature increases, the polymer can expand easily and produce free volume. Thus ions, solvated molecules, or polymer segments can move to the free volume and hence the increase in conductivity. At higher temperatures σdc values decrease due to that metal halide cations act as transient crosslinker, resulting in progressive immobilization of the polymer chain segments thereby decreasing the conductivity. Figures 7(a)–7(c) shows the temperature dependence of ionic conductivity for the PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films. The conductivity values of these polymer films are shown in Table 2. These results suggest that Arrhenius phenomenological relationship can be used to describe the conductivity behaviour for the aforementioned polymer films. Indicating Arrhenius type thermally activated process given by the relation σ=σ0exp(-Ea/KT), where σ0 is the preexponential factor, Ea the activation energy, and K is the Boltzmann constant.Table 2
Theσdc conductivity values of PVDF: Ti3+/Cr3+/Fe3+ polymer films.
Temperature(K)
PVDF: Ti3+ (×10−4 S/cm)
PVDF: Cr3+ (×10−4 S/cm)
PVDF: Fe3+ (×10−4 S/cm)
303
1.667
0.1183
0.1625
313
1.782
0.1235
0.1735
323
1.891
0.1335
0.2114
333
1.983
0.1747
0.2684
343
2.054
0.1938
0.3273
353
2.243
0.2170
0.3827
363
2.592
—
0.4672
373
3.673
—
0.6063((a)–(c)) Cole-Cole plots for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)((a)–(c)) Conductivity with temperature change for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)The activation energies are calculated from the slopes of logσdc versus 1000/T plots as shown in Figures 8(a)–8(c) and it has been found that the activation energy decreases from region I to region II. The activation energy of PVDF: Ti3+ is 0.452 eV, PVDF: Cr3+ is 0.460 eV, and for PVDF: Fe3+1.16 eV. It is noteworthy that the films with low activation energies are desirable for practical applications [18].((a)–(c)) Arrhenius plots for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)


### 3.5. Magnetic Properties

Figures9(a)–9(c) show the room temperature magnetization (M-H) hysteresis loops of PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films with a maximum field of 20 kOe. Figure 9(a) shows the results of PVDF: Ti3+ polymer film and depicts the reverse-S-type curve, indicating the intrinsic diamagnetism. From the loop the coercive field (Hc), saturation magnetization (Ms), and remanent magnetization (Mr) were estimated to be 839.57 Oer, 1.01 × 10−3 emu/gm and 75.96 × 10−6 emu, respectively. Figure 9(b) shows the results of PVDF: Cr3+ polymer film, indicating the existence of RT ferromagnetism nature. From the loop coercive field, saturation magnetization (Ms) and remnant magnetization (Mr) were estimated to be 38.19 Oer, 1.211 × 10−3 emu/gm and 61.156 × 10−6 emu respectively, we conform that the observed ferromagnetism is intrinsic. Therefore it is reasonable to suggest that the observed ferromagnetism is due to oxygen vacancies and/or defects in the polymer film. Figure 9(c) shows the results of PVDF: Fe3+ polymer film, indicating weak ferromagnetic nature. From the loop coercive field, saturation magnetization (Ms) and remnant magnetization (Mr) were estimated to be 118.84 Oer, 5.875 × 10−3 emu/gm and 114.04 × 10−6 emu respectively, which reveals the existence of defects and impurities; we believe that the observed weak ferromagnetism is caused both by the defects (such as oxygen vacancies) and with Fe ions incorporation [19, 20]. From the graphs PVDF: Ti3+ shows antiferromagnetism, PVDF: Cr3+ shows ferromagnetism, and PVDF: Fe3+ shows weak ferromagnetic nature.((a)–(c)) Hysteresis loops for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)


## 3.1. XRD Analysis

XRD diffraction reveals that the PVDF polymer films under investigation are characterized by semicrystalline structure and it has three crystal structures includingα-, β- and γ-phases [9, 10]. From Figures 1(a)–1(c), the spectra of the (a) PVDF: Ti3+, (b) PVDF: Cr3+, and (c) PVDF: Fe3+ polymer films present peaks at 2θ  ≈ 20.25°, 39.64°, 42.06° and 46.21° and labeled to the diffractions in planes of (110), (002), (042) and (114), respectively; those could be due to the characteristic peaks of α, β, and γ crystalline phases, and are confirmed by FTIR analysis as well. The results is shown in Table 1 and in good agreement with the reports made available in the literature [11, 12].Table 1
X-ray diffraction peaks semi-crystalline PVDF phases.
Values of 2 and respectived spacing observed in the X-Ray Diffraction
2θ (in degrees)
d (Å)
Assignment
Plane
20.25
4.30
β
110
39.64
2.28
α
002
42.06
2.13
α
042
46.21
2.06
γ
114Figure 1
((a)–(c)) XRD profile of PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.


## 3.2. FTIR Analysis

Figures2(a)–2(c) show the plots of IR transmission spectra of the PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films in the spectral range of 4000–400 cm−1 and all the spectra are found to be more similar in nature. The main PVDF characterizing frequencies are observed, where β phase occurs mostly at 440 cm−1, 510 cm−1 and 840 cm−1 and, for α phase at 430 cm−1, 610 cm−1, 765 cm−1, and 1420 cm−1. However, the peaks at 880 cm−1 and 950 cm−1 were identified as belonging to the γ-phase. Couple bands that are identified at 1665 cm−1 and 1629 cm−1 have been assigned to the C=C stretching as was reported earlier [13, 14] and this indicates the presence of polarons in the polymeric matrix. The band at 748 cm−1 which refers to the head to head (h-h) and tail to tail (t-t) defects [15]. The change of the intensities of these IR bands indicates a change of the chelation mode of Ti3+, Cr3+, and Fe3+ in PVDF matrix. It is interesting to notice that the C=C mode and the h-h defects are suitable sites for polarons and bipolarons formation in the PVDF matrix.Figure 2
((a)–(c)) FTIR spectra of PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.


## 3.3. Photoluminescence Analysis

Figures3(a)–3(f) show both excitation and emission spectra of PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films. For PVDF: Ti3+, the emission spectrum has been obtained with λexci = 387 nm, the emission spectrum displays emissions at 413 nm (could not be assigned) 435 nm (3T1(F)→3A2(F)), and 457 nm (also could not be assigned to a transition). For PVDF: Cr3+, the emission spectrum has been measured with λexci = 385 nm, strong emission bands are observed at 421 nm (Eg2→T42g) and 435 nm (T42g→A42g). For PVDF: Fe3+ emission spectrum has been recorded with λexci = 329 nm, strong emission bands are observed at 588 nm and 625 nm (4A2→4T1 (4P)). All assignments that are made on the measured emission bands are in agreement with the literature reported results [16].((a)-(b)) Excitation and emission of PVDF: Ti3+ polymer films. ((c)-(d)) Excitation and emission of PVDF: Cr3+ polymer films. ((e)-(f)) Excitation and emission of PVDF: Fe3+ polymer films.
(a)
(b)
(c)
(d)
(e)
(f)


## 3.4. Impedance Analysis

Impedance analysis reflects the collective response of microscopic polarization process under an external electric field. Under an alternating field, frequency dispersion or dielectric relaxation is observed due to different polarization mechanisms within a dielectric. Typical spectroscopic plots of dielectric constant (ε1) versus frequency (f) for the three polymer (PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+) films are shown in Figures 4(a)–4(c). It is observed that the ε1 decreases rapidly with increasing frequency. The rapid fall of dielectric constant (ε1) in their frequency range shows that space charge polarization contributes significantly to the total polarization observed in these films. Space charge polarization (interfacial polarization) arises whenever phases of different conductivities are present in the same material. When an electric field is applied, the charges more through a conducting phase but are interrupted as they come across a high resistivity phase. This leads to a buildup of charge at the interface, which is manifested as enhanced polarization. These builtup charges cannot follow the applied field rapidly at high frequencies and hence, the resultant loss. The dielectric loss (tanδ) versus frequency (f) for the three polymer (PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+) films are shown on Figures 5(a)–5(c). A single relaxation peak was observed. The loss peak maximum shifts to a lower frequency with decreasing temperature, and the peak intensity decreases and the distribution broadens. This may be due to the result of a dominant effect of the polarization by migrating charges at low frequency. The dispersion observed at low frequencies could be attributed to the interfacial polarization mechanism and the dispersion observed at high frequencies could be attributed to the dipolar relaxation [15, 17].((a)–(c)) Dielectric constant as function of frequency for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)((a)–(c)) Dielectric loss as function of frequency for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)Complex plane plots (Z1 versus Z11) for a typical polymer films are shown in Figures 6(a)–6(c). The behaviour of films and at different temperatures is similar. The Cole-Cole plots showed two well-defined regions. semi circle pattern indicating the involvement of a single conduction mechanism in the composite system. The single mechanism is attributed to grain size or due to the mobility of free charges (polaron or free ions) induced by the increment of temperature. The bulk dc resistance (Rb) of the electrolyte was determined as the point where the high frequency semicircle in the plots cuts the Z1 axis. The ionic conductivity (σ) is calculated
(1)σdc=d(Rb·A),
where d = thickness of the film and A = area of the electrodes. It has been observed in polymer films that σdc values first increased with increased temperature; this can be explained with the help of free volume theory. As the temperature increases, the polymer can expand easily and produce free volume. Thus ions, solvated molecules, or polymer segments can move to the free volume and hence the increase in conductivity. At higher temperatures σdc values decrease due to that metal halide cations act as transient crosslinker, resulting in progressive immobilization of the polymer chain segments thereby decreasing the conductivity. Figures 7(a)–7(c) shows the temperature dependence of ionic conductivity for the PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films. The conductivity values of these polymer films are shown in Table 2. These results suggest that Arrhenius phenomenological relationship can be used to describe the conductivity behaviour for the aforementioned polymer films. Indicating Arrhenius type thermally activated process given by the relation σ=σ0exp(-Ea/KT), where σ0 is the preexponential factor, Ea the activation energy, and K is the Boltzmann constant.Table 2
Theσdc conductivity values of PVDF: Ti3+/Cr3+/Fe3+ polymer films.
Temperature(K)
PVDF: Ti3+ (×10−4 S/cm)
PVDF: Cr3+ (×10−4 S/cm)
PVDF: Fe3+ (×10−4 S/cm)
303
1.667
0.1183
0.1625
313
1.782
0.1235
0.1735
323
1.891
0.1335
0.2114
333
1.983
0.1747
0.2684
343
2.054
0.1938
0.3273
353
2.243
0.2170
0.3827
363
2.592
—
0.4672
373
3.673
—
0.6063((a)–(c)) Cole-Cole plots for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)((a)–(c)) Conductivity with temperature change for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)The activation energies are calculated from the slopes of logσdc versus 1000/T plots as shown in Figures 8(a)–8(c) and it has been found that the activation energy decreases from region I to region II. The activation energy of PVDF: Ti3+ is 0.452 eV, PVDF: Cr3+ is 0.460 eV, and for PVDF: Fe3+1.16 eV. It is noteworthy that the films with low activation energies are desirable for practical applications [18].((a)–(c)) Arrhenius plots for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)


## 3.5. Magnetic Properties

Figures9(a)–9(c) show the room temperature magnetization (M-H) hysteresis loops of PVDF: Ti3+, PVDF: Cr3+, and PVDF: Fe3+ polymer films with a maximum field of 20 kOe. Figure 9(a) shows the results of PVDF: Ti3+ polymer film and depicts the reverse-S-type curve, indicating the intrinsic diamagnetism. From the loop the coercive field (Hc), saturation magnetization (Ms), and remanent magnetization (Mr) were estimated to be 839.57 Oer, 1.01 × 10−3 emu/gm and 75.96 × 10−6 emu, respectively. Figure 9(b) shows the results of PVDF: Cr3+ polymer film, indicating the existence of RT ferromagnetism nature. From the loop coercive field, saturation magnetization (Ms) and remnant magnetization (Mr) were estimated to be 38.19 Oer, 1.211 × 10−3 emu/gm and 61.156 × 10−6 emu respectively, we conform that the observed ferromagnetism is intrinsic. Therefore it is reasonable to suggest that the observed ferromagnetism is due to oxygen vacancies and/or defects in the polymer film. Figure 9(c) shows the results of PVDF: Fe3+ polymer film, indicating weak ferromagnetic nature. From the loop coercive field, saturation magnetization (Ms) and remnant magnetization (Mr) were estimated to be 118.84 Oer, 5.875 × 10−3 emu/gm and 114.04 × 10−6 emu respectively, which reveals the existence of defects and impurities; we believe that the observed weak ferromagnetism is caused both by the defects (such as oxygen vacancies) and with Fe ions incorporation [19, 20]. From the graphs PVDF: Ti3+ shows antiferromagnetism, PVDF: Cr3+ shows ferromagnetism, and PVDF: Fe3+ shows weak ferromagnetic nature.((a)–(c)) Hysteresis loops for PVDF: Ti3+, PVDF: Cr3+ and PVDF: Fe3+ polymer films.
(a)
(b)
(c)


## 4. Conclusion

In summary, it is concluded that we have successfully synthesized both undoped (reference) and doped PVDF films containing transition metal ions such as Ti3+, Cr3+, and Fe3+, respectively, and analyzed their structural, electrical and magnetic properties from the measurements of their XRD, FTIR spectra, photoluminescent spectra, dielectric constant, dielectric loss, and magnetic properties. XRD results have revealed that these polymer films possess monoclinic, α-, β-, and γ-phases. Conductivity σdc in the place of electrical conductivity. From magnetic profile measurements, PVDF: Ti3+ film has shown antiferromagnetic nature, PVDF: Cr3+ film has revealed ferromagnetic nature, and PVDF: Fe3+ has displayed strong paramagnetic nature.



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