# Structural, Optical, Electrical, and Magnetic Properties of  PVA:Gd3+ and PVA:Ho3+ Polymer Films

Authors: M. Obula Reddy; B. Chandra Babu
Journal: Indian Journal of Materials Science
 (2015)

---

## Abstract

Polymer films of PVA:Gd3+ and PVA:Ho3+ have been synthesized by a solution casting method in order to study their structural, optical, electrical, and magnetic properties. The semicrystalline nature of the polymer films has been confirmed from XRD analysis. The FTIR analysis confirms the complex formation of the polymer with the metal ions. Dielectric studies of these films have also been carried out at various set temperatures in the frequency from 100 Hz to 1 MHz for carrying out impedance spectroscopy analysis to evaluate the electrical conductivity which arises due to a single conduction mechanism and thus to have a single semicircle pattern from these polymer films. The DC electrical conductivity increases with an increase in the temperature and it could be due to high mobility of free charges (polarons and free ions) at higher temperatures. The conductivity trend follows the Arrhenius equation for PVA:Gd3+ and for PVA:Ho3+ polymer films. PVA:Gd3+ polymer films show ferromagnetic nature, and PVA:Ho3+ polymer films have revealed paramagnetic nature based on the trends noticed in the magnetic characteristic profiles.


---

## Body

## 1. Introduction

In recent years energy conversion devices based on organic semiconductors are an emerging research field with substantial future prospects and it has attracted great attention due to the advantages of light weight, flexibility, and low cost of production with the possibility of fabricating large area devices based on solution processing. Polymeric materials have been the subject of intense scientific and technological research because of their potential applications. In particular, conducting polymers have been extensively investigated in the area of electronics and optoelectronics due to their attractive properties [1, 2]. Polymeric dielectric materials have been preferred because of their dielectric and physical properties over a wide range of temperatures and frequencies. Over the years, among various polymers, poly(vinyl alcohol) (PVA), as one of the most important polymers, has recently received considerable interest, owing to its numerous potential applications in electronic components. It has different internal structure that may be considered as amorphous or semicrystalline. The semicrystalline structure of PVA showed an important feature rather than of amorphous one. This is because semicrystalline PVA leads to formation of both crystalline and amorphous regions [3–5].PVA polymer is soluble in water and other solvents and is widely used in synthetic fiber, paper, contact lens, textile, coating, and binder industries, due to its excellent chemical and physical properties, nontoxicity, processability, good chemical resistance, high dielectric strength, good charge storage capacity, wide range of crystallinity, good film formation capacity, complete biodegradability, and high crystal modulus dopant-dependent electrical and optical properties [6–9]. PVA is comprised of carbon chain backbone with hydroxyl groups attached to methane carbons; these OH groups can be a source of hydrogen bonding and hence assist in the formation of polymer composite. Interestingly, semicrystalline materials have exhibited improvement in certain physical properties due to crystal-amorphous interfacial effect [9].The rare earth elements will exhibit ferromagnetism in addition to the unique luminescent nature. Luminescence from the RE3+ ions originates from the transitions between 4f orbitals, and these transitions are forbidden on symmetry grounds [10–12]. Among various rare earth activated systems, gadolinium and holmium materials emerged as promising candidates for such applications. In the present work, we prepared and characterized the PVA polymer with gadolinium Gd3+ (4f7) and holmium Ho3+(4f10) doping polymer films considered to investigate the features of optical, dielectric, and magnetic studies. Hence, these polymer films may be used in electrochemical display systems.


## 2. Experimental Studies

### 2.1. Sample Preparation

Spectral pure host matrix chemical of polyvinyl alcohol (PVA) (with MW = 1, 30,000) and dopant chemicals of GdCl3·6H2O and HoCl3·6H2O were used in the present work. Development of transparent PVA:Gd3+ and PVA:Ho3+ polymer films was done for obtaining Gd3+:PVA and Ho3+:PVA films upon gadolinium chloride/holmium chloride by using the solution casting method. Both the host polymer and dopant chemicals were dissolved separately in double distilled water (DDW) in the proportion of 1 : 9 and such mixed solutions were stirred thoroughly using a magnetic stirrer at temperature 60°C for 12 hrs and thus the homogenously mixed solution was poured on to Petri dish for obtaining transparent polymer films through slow evaporation method after 48 hrs from those dishes, and those neatly formed transparent polymer films were collected into appropriate containers for measurement purposes. All the obtained polymer films were in 150 μm thickness in good transparencies. These prepared PVA:Gd3+and PVA:Ho3+ polymer films were cut into 2 cm × 1 cm sizes for undertaking the experimental studies on them.


### 2.2. Characterization Techniques

The structures of the prepared polymers were characterized on XRD 3003 TT Seifert diffractometer with Cukα radiation (λ=1.5406 Å) at 40 KV and 20 mA and the 2θ range between 10° and 70°. Perkin-Elmer FT-IR spectrophotometer was used for recording FT-IR spectra of the host PVA, and the doped PVA:Gd3+ and PVA:Ho3+ polymer films in the region of 4000–400 cm−1. The absorption spectra of the above prepared films were measured on Varian-Cary-Win. Spectrometer (JASCO V-570), and 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). Dielectric measurements carried out using Phase Sensitive Multimeter (PSM) (Model-1700). The magnetic moment profile as function of applied magnetic field was measured on a Vibratory Sample Magnetometer with a range of ±20 KOer.


## 2.1. Sample Preparation

Spectral pure host matrix chemical of polyvinyl alcohol (PVA) (with MW = 1, 30,000) and dopant chemicals of GdCl3·6H2O and HoCl3·6H2O were used in the present work. Development of transparent PVA:Gd3+ and PVA:Ho3+ polymer films was done for obtaining Gd3+:PVA and Ho3+:PVA films upon gadolinium chloride/holmium chloride by using the solution casting method. Both the host polymer and dopant chemicals were dissolved separately in double distilled water (DDW) in the proportion of 1 : 9 and such mixed solutions were stirred thoroughly using a magnetic stirrer at temperature 60°C for 12 hrs and thus the homogenously mixed solution was poured on to Petri dish for obtaining transparent polymer films through slow evaporation method after 48 hrs from those dishes, and those neatly formed transparent polymer films were collected into appropriate containers for measurement purposes. All the obtained polymer films were in 150 μm thickness in good transparencies. These prepared PVA:Gd3+and PVA:Ho3+ polymer films were cut into 2 cm × 1 cm sizes for undertaking the experimental studies on them.


## 2.2. Characterization Techniques

The structures of the prepared polymers were characterized on XRD 3003 TT Seifert diffractometer with Cukα radiation (λ=1.5406 Å) at 40 KV and 20 mA and the 2θ range between 10° and 70°. Perkin-Elmer FT-IR spectrophotometer was used for recording FT-IR spectra of the host PVA, and the doped PVA:Gd3+ and PVA:Ho3+ polymer films in the region of 4000–400 cm−1. The absorption spectra of the above prepared films were measured on Varian-Cary-Win. Spectrometer (JASCO V-570), and 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). Dielectric measurements carried out using Phase Sensitive Multimeter (PSM) (Model-1700). The magnetic moment profile as function of applied magnetic field was measured on a Vibratory Sample Magnetometer with a range of ±20 KOer.


## 3. Results and Discussion

### 3.1. XRD Analysis

The XRD patterns of the host matrix PVA and 10 wt% of Gd3+ and Ho3+:PVA polymer films are shown in Figures 1(a)–1(c). The XRD pattern of pure PVA shows a characteristic peak at 2θ ≈ 19.80 which confirms the semicrystalline nature of orthorhombic structure. Even after the doping of La3+ ion by Gd3+ and Ho3+ ion the matrix semicrystalline nature does not change, but intensity of the peak decreases gradually, suggesting a decrease in the degree of crystallinity of PVA. They observed that the intensity of XRD peak decreases as the amorphous nature increases with the addition of dopant [13, 14].Figure 1
(a–c) XRD profiles of PVA, PVA:Gd3+, and PVA:Ho3+ polymer films.


### 3.2. FTIR Analysis

Figures2(a)–2(c) show an FTIR spectra pure PVA and 10 wt% of Gd3+ and Ho3+:PVA polymers. All the spectra exhibit the characteristic bands of virgin PVA which are stretching and bending vibrations of O-H, C-O, C=C, and C-H groups. Abroad and strong band is observed at 3333 cm−1 which arises from (OH) stretching frequency and indicates the presence of hydroxyl group and 2940 cm−1 corresponds to the anti-symmetric. A weak band observed at 2168 cm−1 has been attributed to the combination frequencies of the rocking and the stretching vibrations. A moderate absorption peaks at 1730 cm−1 and 1655 cm−1 have been attributed to the C=O, C=C stretching mode. The FT-IR data along with the band assignments [15, 16] are presented in Table 1. From spectra, it can be noticed that the doping with Gd3+ and Ho3+ causes some observable changes in the spectrum of PVA in the range 1000–400 cm−1. It induces some new bands and slight changes in the intensities of some bands. The new bands may be correlated likewise to defects induced by the charge transfer reaction between the polymer chain and the dopant [15–17].Table 1
Assignments of FTIR bands of pure PVA and 10 wt% of Gd3+and Ho3+:PVA polymer films.
Pure PVA (cm−1)
Gd3+:PVA (cm−1)
Ho3+:PVA (cm−1)
Assignment
3101–3524
2813–3573
2873–3560
O-H stretching
1706
1709
1711
C=C stretching
1530
1541
1541
C-H bending
1480
1465
1468
CH2 bending
1230
1238
1243
CH + OH bending
1115
1118
1125
CO stretching
847
854
856
C-C stretching
668
675
675
O-H wagging
562
565
565
CO bending
489
489
489
C-Cl bendingFigure 2
(a–c) FT-IR profile of PVA, PVA:Gd3+, and PVA:Ho3+ polymer films.
(a)
PVA
(b)
PVA:Gd3+
(c)
PVA:Ho3+


### 3.3. Optical Properties

Figure3(a) shows a strong absorption band located at 271 nm (8S7/2→6I7/2) besides a weak absorption band at 315 nm (8S7/2→6P7/2), respectively [18]; these bands can be ascribed to the 4f-4f intraconfigurational transitions between 8S7/2 ground state and 6P7/2 and 6I7/2. Emission spectrum of this polymer film is shown in Figure 3(b), which demonstrates a sharp line 311 nm (6P7/2→8S7/2) and an intense peak at about 324 nm with λexci=275 nm [19]. From Figure 4(a), it is observed that there exists a strong absorption band at 380 nm for Ho3+: PVA polymer films besides five weaker absorption bands at 416 nm, 450 nm, 485 nm, 537 nm, and 641 nm respectively, and those have appropriately been assigned to the electronic transitions such as (5I8→5G4) at 380 nm, (5I8→ (5G,3G)5) at 416 nm, (5I8→5G5) at 450 nm, (5I8→5F3) at 485 nm, (5I8→5F4) at 537 nm, and (5I8→5F5) at 641 nm, which are also agreeing with the reported values [20]. From Figure 4(b), a strong blue emission at 433 nm (5G5→5I8) can be observed with λexci=380 nm and two weak emission bands are observed at 412 nm and 460 nm (5G6→5I8), respectively, which are also agreeing with the reported value [21].Figure 3
(a, b) Absorption (a) and (b) emission spectra of PVA:Gd3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Gd3+Figure 4
(a, b) Absorption (a) and emission spectra of PVA:Ho3+ polymer films.
(a)
PVA:Ho3+
(b)
PVA:Ho3+


### 3.4. Dielectric Properties

Figures5(a) and 5(b) show the variation of the dielectric constant (ε′) with frequency at different constant temperatures for Gd3+:PVA and Ho3+:PVA polymer films. From the figures, it is clear that the values of the (ε′) are very high at low frequency. Such high value of dielectric constant at low frequencies has been explained by the presence of space charge effects, which is contributed by the accumulation of charge carriers near the electrodes. At higher frequencies, dielectric constant has been found to be relatively constant with frequency. This is because periodical reversal of the field takes place so rapidly that the charge carriers will hardly be able to orient themselves in the field direction resulting in the decrease in dielectric constant [22, 23]. The dielectric loss tangent as a function of frequency at various temperatures for Gd3+:PVA and Ho3+:PVA polymer films is shown in Figures 6(a) and 6(b). From the figures, it is clear that the variation of tan δ with frequency gives an evidence for a distinct dipolar peak which is temperature dependent. A distribution of molecular weights or cooperation movement of adjacent chains could give the spread of relaxation times. The existence of a peak at relatively lower frequencies is an indication of the longer relaxation time pertinent to polymers composed of macromolecules. It can be seen that as the temperature increases the tan δ maximum shifts towards higher frequencies indicating the main dielectric relaxation character of dielectric loss in these polymer films [24].Figure 5
(a, b) Dielectric constant varies with frequency for PVA:Gd3+ and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+Figure 6
(a, b) Dielectric loss varies with frequency for PVA:Gd3+ and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+


### 3.5. Conductivity Analysis

The ionic conductivity of the polymer electrolytes mainly depends on the concentration of conducting dopant and their mobility. The conductivity values can be calculated from the relationσDC=d/RbA, where d is the thickness of the film, A is the area of the film, and Rb is the bulk resistance of the bulk material which is obtained from the intercept of real part of complex impedance plot. Impedance diagrams of PVA: Gd3+ and PVA: Ho3+ polymer films as shown in Figures 7(a) and 7(b) in temperature range 303–373 K. The plots consist of a high frequency depressed semicircle represented by a parallel combination of a capacitor, which is due to the mobile ions inside the polymer matrix. The bulk resistance has been calculated from the low frequency intercept of the semicircle or high frequency intercept of the spike on the real axis. The bulk resistance Rb decreases with increase in temperature. This may be due to increase in the mobile charge carriers with increasing temperature related increase in the amorphousness of the polymer electrolyte, which has been confirmed by XRD analysis [25, 26]. The conductivity increased with increase in temperature but the rate of increase was different in different temperature regions as shown in Table 2. From, Figures 8(a) and 8(b) show a typical 1000/T versus log(σDC) plot for Gd3+:PVA and Ho3+:PVA polymer films. From the slopes of these plots, the activation energies were calculated using the Arrhenius relation:(1)σDC=σoexp⁡-EKBT,where σDC is the conductivity at temperature T, σo is a constant, E is the activation energy, and KB is the Boltzmann constant. Arrhenius plots show nonlinearity which suggest that the ion transport in polymer electrolytes depends on the polymer segmental motion [27].Table 2
Dc conductivity values for PVA:Gd3+ and  PVA:Ho3+ polymer films.
Temperature(K)
PVA:Gd3+ (×10−6 S/cm)
PVA:Ho3+  (×10−6 S/cm)
313
1.234
3.173
323
1.465
3.354
333
2.843
3.975
343
4.965
6.453
353
10.563
8.234
363
15.876
10.453
373
26.124
15.543Figure 7
(a, b) Cole-Cole plots for PVA:Gd3+and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+Figure 8
(a, b) Arrhenius plots for PVA:Gd3+ and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+


### 3.6. Magnetic Behavior Analysis

Figure9(a) shows the measured room temperature magnetization curve for Gd3+ doped PVA 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 857.59 Oer, 5.75 × 10−3 emu/gm, and 228.42 × 10−6 emu, respectively. This can be explained by RKKY theory; that is, 4f states are highly localized with negligible overlap, and the 4f moments are coupled via RKKY-type exchange, which is mediated by the valence electrons. The 4f moments lead to an induced polarization of the 6s and 5d valence electrons, resulting in a measured magnetic moment. Therefore, it is reasonable to suggest that the observed ferromagnetism is due to oxygen vacancies and/or defects in the polymer film. Figure 9(b) shows the results of PVA:Ho3+ polymer film, indicating strong paramagnetic nature. From the loop coercive field, saturation magnetization (Ms) and remnant magnetization (Mr) were estimated to be 41.42 Oer, 11.83 × 10−3 emu/gm, and 32.07 × 10−6 emu, respectively, which reveals the existence of defects and impurities, and we believe that the observed strong paramagnetism is caused both by the defects (such as oxygen vacancies) and with Ho ions incorporation. From the graphs PVA:Gd3+ shows ferromagnetism and PVA:Ho3+ shows paramagnetic nature [28, 29].Figure 9
(a, b) Magnetization dependence of the applied field for (a) PVA:Gd3+ and (b) PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+


## 3.1. XRD Analysis

The XRD patterns of the host matrix PVA and 10 wt% of Gd3+ and Ho3+:PVA polymer films are shown in Figures 1(a)–1(c). The XRD pattern of pure PVA shows a characteristic peak at 2θ ≈ 19.80 which confirms the semicrystalline nature of orthorhombic structure. Even after the doping of La3+ ion by Gd3+ and Ho3+ ion the matrix semicrystalline nature does not change, but intensity of the peak decreases gradually, suggesting a decrease in the degree of crystallinity of PVA. They observed that the intensity of XRD peak decreases as the amorphous nature increases with the addition of dopant [13, 14].Figure 1
(a–c) XRD profiles of PVA, PVA:Gd3+, and PVA:Ho3+ polymer films.


## 3.2. FTIR Analysis

Figures2(a)–2(c) show an FTIR spectra pure PVA and 10 wt% of Gd3+ and Ho3+:PVA polymers. All the spectra exhibit the characteristic bands of virgin PVA which are stretching and bending vibrations of O-H, C-O, C=C, and C-H groups. Abroad and strong band is observed at 3333 cm−1 which arises from (OH) stretching frequency and indicates the presence of hydroxyl group and 2940 cm−1 corresponds to the anti-symmetric. A weak band observed at 2168 cm−1 has been attributed to the combination frequencies of the rocking and the stretching vibrations. A moderate absorption peaks at 1730 cm−1 and 1655 cm−1 have been attributed to the C=O, C=C stretching mode. The FT-IR data along with the band assignments [15, 16] are presented in Table 1. From spectra, it can be noticed that the doping with Gd3+ and Ho3+ causes some observable changes in the spectrum of PVA in the range 1000–400 cm−1. It induces some new bands and slight changes in the intensities of some bands. The new bands may be correlated likewise to defects induced by the charge transfer reaction between the polymer chain and the dopant [15–17].Table 1
Assignments of FTIR bands of pure PVA and 10 wt% of Gd3+and Ho3+:PVA polymer films.
Pure PVA (cm−1)
Gd3+:PVA (cm−1)
Ho3+:PVA (cm−1)
Assignment
3101–3524
2813–3573
2873–3560
O-H stretching
1706
1709
1711
C=C stretching
1530
1541
1541
C-H bending
1480
1465
1468
CH2 bending
1230
1238
1243
CH + OH bending
1115
1118
1125
CO stretching
847
854
856
C-C stretching
668
675
675
O-H wagging
562
565
565
CO bending
489
489
489
C-Cl bendingFigure 2
(a–c) FT-IR profile of PVA, PVA:Gd3+, and PVA:Ho3+ polymer films.
(a)
PVA
(b)
PVA:Gd3+
(c)
PVA:Ho3+


## 3.3. Optical Properties

Figure3(a) shows a strong absorption band located at 271 nm (8S7/2→6I7/2) besides a weak absorption band at 315 nm (8S7/2→6P7/2), respectively [18]; these bands can be ascribed to the 4f-4f intraconfigurational transitions between 8S7/2 ground state and 6P7/2 and 6I7/2. Emission spectrum of this polymer film is shown in Figure 3(b), which demonstrates a sharp line 311 nm (6P7/2→8S7/2) and an intense peak at about 324 nm with λexci=275 nm [19]. From Figure 4(a), it is observed that there exists a strong absorption band at 380 nm for Ho3+: PVA polymer films besides five weaker absorption bands at 416 nm, 450 nm, 485 nm, 537 nm, and 641 nm respectively, and those have appropriately been assigned to the electronic transitions such as (5I8→5G4) at 380 nm, (5I8→ (5G,3G)5) at 416 nm, (5I8→5G5) at 450 nm, (5I8→5F3) at 485 nm, (5I8→5F4) at 537 nm, and (5I8→5F5) at 641 nm, which are also agreeing with the reported values [20]. From Figure 4(b), a strong blue emission at 433 nm (5G5→5I8) can be observed with λexci=380 nm and two weak emission bands are observed at 412 nm and 460 nm (5G6→5I8), respectively, which are also agreeing with the reported value [21].Figure 3
(a, b) Absorption (a) and (b) emission spectra of PVA:Gd3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Gd3+Figure 4
(a, b) Absorption (a) and emission spectra of PVA:Ho3+ polymer films.
(a)
PVA:Ho3+
(b)
PVA:Ho3+


## 3.4. Dielectric Properties

Figures5(a) and 5(b) show the variation of the dielectric constant (ε′) with frequency at different constant temperatures for Gd3+:PVA and Ho3+:PVA polymer films. From the figures, it is clear that the values of the (ε′) are very high at low frequency. Such high value of dielectric constant at low frequencies has been explained by the presence of space charge effects, which is contributed by the accumulation of charge carriers near the electrodes. At higher frequencies, dielectric constant has been found to be relatively constant with frequency. This is because periodical reversal of the field takes place so rapidly that the charge carriers will hardly be able to orient themselves in the field direction resulting in the decrease in dielectric constant [22, 23]. The dielectric loss tangent as a function of frequency at various temperatures for Gd3+:PVA and Ho3+:PVA polymer films is shown in Figures 6(a) and 6(b). From the figures, it is clear that the variation of tan δ with frequency gives an evidence for a distinct dipolar peak which is temperature dependent. A distribution of molecular weights or cooperation movement of adjacent chains could give the spread of relaxation times. The existence of a peak at relatively lower frequencies is an indication of the longer relaxation time pertinent to polymers composed of macromolecules. It can be seen that as the temperature increases the tan δ maximum shifts towards higher frequencies indicating the main dielectric relaxation character of dielectric loss in these polymer films [24].Figure 5
(a, b) Dielectric constant varies with frequency for PVA:Gd3+ and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+Figure 6
(a, b) Dielectric loss varies with frequency for PVA:Gd3+ and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+


## 3.5. Conductivity Analysis

The ionic conductivity of the polymer electrolytes mainly depends on the concentration of conducting dopant and their mobility. The conductivity values can be calculated from the relationσDC=d/RbA, where d is the thickness of the film, A is the area of the film, and Rb is the bulk resistance of the bulk material which is obtained from the intercept of real part of complex impedance plot. Impedance diagrams of PVA: Gd3+ and PVA: Ho3+ polymer films as shown in Figures 7(a) and 7(b) in temperature range 303–373 K. The plots consist of a high frequency depressed semicircle represented by a parallel combination of a capacitor, which is due to the mobile ions inside the polymer matrix. The bulk resistance has been calculated from the low frequency intercept of the semicircle or high frequency intercept of the spike on the real axis. The bulk resistance Rb decreases with increase in temperature. This may be due to increase in the mobile charge carriers with increasing temperature related increase in the amorphousness of the polymer electrolyte, which has been confirmed by XRD analysis [25, 26]. The conductivity increased with increase in temperature but the rate of increase was different in different temperature regions as shown in Table 2. From, Figures 8(a) and 8(b) show a typical 1000/T versus log(σDC) plot for Gd3+:PVA and Ho3+:PVA polymer films. From the slopes of these plots, the activation energies were calculated using the Arrhenius relation:(1)σDC=σoexp⁡-EKBT,where σDC is the conductivity at temperature T, σo is a constant, E is the activation energy, and KB is the Boltzmann constant. Arrhenius plots show nonlinearity which suggest that the ion transport in polymer electrolytes depends on the polymer segmental motion [27].Table 2
Dc conductivity values for PVA:Gd3+ and  PVA:Ho3+ polymer films.
Temperature(K)
PVA:Gd3+ (×10−6 S/cm)
PVA:Ho3+  (×10−6 S/cm)
313
1.234
3.173
323
1.465
3.354
333
2.843
3.975
343
4.965
6.453
353
10.563
8.234
363
15.876
10.453
373
26.124
15.543Figure 7
(a, b) Cole-Cole plots for PVA:Gd3+and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+Figure 8
(a, b) Arrhenius plots for PVA:Gd3+ and PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+


## 3.6. Magnetic Behavior Analysis

Figure9(a) shows the measured room temperature magnetization curve for Gd3+ doped PVA 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 857.59 Oer, 5.75 × 10−3 emu/gm, and 228.42 × 10−6 emu, respectively. This can be explained by RKKY theory; that is, 4f states are highly localized with negligible overlap, and the 4f moments are coupled via RKKY-type exchange, which is mediated by the valence electrons. The 4f moments lead to an induced polarization of the 6s and 5d valence electrons, resulting in a measured magnetic moment. Therefore, it is reasonable to suggest that the observed ferromagnetism is due to oxygen vacancies and/or defects in the polymer film. Figure 9(b) shows the results of PVA:Ho3+ polymer film, indicating strong paramagnetic nature. From the loop coercive field, saturation magnetization (Ms) and remnant magnetization (Mr) were estimated to be 41.42 Oer, 11.83 × 10−3 emu/gm, and 32.07 × 10−6 emu, respectively, which reveals the existence of defects and impurities, and we believe that the observed strong paramagnetism is caused both by the defects (such as oxygen vacancies) and with Ho ions incorporation. From the graphs PVA:Gd3+ shows ferromagnetism and PVA:Ho3+ shows paramagnetic nature [28, 29].Figure 9
(a, b) Magnetization dependence of the applied field for (a) PVA:Gd3+ and (b) PVA:Ho3+ polymer films.
(a)
PVA:Gd3+
(b)
PVA:Ho3+


## 4. Conclusions

In summary, it could be concluded that we have successfully developed highly transparent and stable Gd3+ and Ho3+:PVA polymer films were prepared by solution casting method. The XRD studies reveal the amorphous nature of the polymer that produces greater ionic diffusion. FTIR reveals the complexation between polymer and dopants. The conductivity is found to exhibit increasing trend with increasing temperature. The maximum conductivity of PVA:Gd3+ film is 2.621 × 10−5 S/cm at 373 K and for PVA:Ho3+ film is 15.564 × 10−5 S/cm at 353 K. From magnetic profile PVA:Gd3+ shows ferromagnetic nature and PVA:Ho3+ shows the paramagnetic nature. Hence, these polymer films can be used in electrochemical display systems.



---

*Source: 927364-2015-05-27.xml*