1 Introduction

Conjugated conductive polymers have attracted great deal of attention during the last two decades because of their highly π-conjugated polymeric chains and metal like conductivity. Conjugated conducting polymers are widely studied because of their ease of fabrication, suitable nanostructures and remarkable electronic properties like low ionization potential, high electron affinity, low energy optical transitions and electrical conductivity [1]. Conductive polymers are increasingly desired for a growing number of sophisticated end-uses. These polymers are widely used in sensors [2, 3], supercapacitor [4], organic photovoltaics [5, 6], biofuel cells [7], biomedical engineering [8], drug delivery [9, 10], dye sensitized solar cells [11] etc. Currently fluorescent conducting polymers have been developed for various applications such as biological imaging and sensing [12], fluorescent polarizers [13], and light emitting diodes [14, 15]. They have significantly responded to interaction with number of analytes, including explosives [16, 17], metal ions and biological analytes [18], as a result of the fact that the fluorescent sensing probes have distinctive sensing capability.

Conjugated Schiff bases resulting from carbonyl and amino compound are one of the most important categories of organic compounds. The conjugated Schiff bases study has flourished in the last few years because of their wide applications in catalysis, biological modeling, design of molecular magnets [19, 20] and in the important drugs synthesis [21]. Schiff bases also plays an essential role as chelating ligands in coordination chemistry because of their easy proton donating property and flexible nature. Furthermore, Schiff base bonds provides suitable features such as; chelating effects to polymers, optoelectronic properties, liquid crystal properties, thermal stability and conductivity [22, 23].

Development of π-Conjugated polyazomethines polymers with conjugative bonds in the main chain has become an area of current research [24]. Major challenges in this field include the development of cheaper, thermally stable, solution-processable, fluorescent and high conducting materials [25]. Entirely aromatic polyazomethines have been recognized as an essential class of highly conjugated and thermally stable materials [26]. Polyazomethines with aromatic backbones are attractive highly efficient conducting polymers because of their good properties like thermal stability, optoelectronic, paramagnetism, fiber-forming, resistance and semiconductivity to high energy [27, 28]. Conjugated aromatic polyazomethines can be utilized in numerous areas as a result of their semi-conductive properties. Since conjugated polyazomethines have fluorescence characteristics, they may be utilized in the developement of light emitting devices, electrochromic materials and as hole transporting materials in solar cells [29].

In this communication, we have demonstrated the preliminary synthesis of solution processable conjugated polyazomethines based polymers derived from novel synthesized Schiff base monomers containing syringaldehyde unit, through condensation polymerization technique, concomitant with characterization by 1H-NMR and FT-IR. Thermal stability of the synthesized polymers has been explained by using TG–DTA. Optical absorption properties of the Schiff base monomers and its polymers containing azomethine bond have been studied using UV–Vis spectroscopic technique. Electrochemical behavior of the synthesized compounds has been examined using cyclic voltammetry (CV) technique. Morphological characteristics of the polyazomethines have been explained by SEM device. The electrical conductivity of polyazomethines was studied using impedance analyzer. The resulting aromatic conjugated polyazomethine is expected to exhibit high thermal stability and better semiconducting properties.

2 Experimental

2.1 Materials

3, 5-dimethoxy-4-hydroxy benzaldehyde (MHB) (99%, SRL, India), 4-amino benzene sulphonic acid (ABS) (99%, Merck, India), 2-amino thiophenol (AT) (99%, Aldrich, Germany), 1,5-diamino naphthalene (AN) (97%, Aldrich, Germany), p-xylene dibromide (XB) (97%, Aldrich, Germany) were used as received. Methanol, N, N-dimethylformamide (DMF) and Na2CO3 were supplied by SDFCL, Mumbai India.

2.2 Synthesis of monomers

Three novel Schiff base monomers were synthesized using condensation reaction between aromatic aldehydes and aromatic amines and they are shown in Scheme 1.

Scheme 1
scheme 1

Synthesis of MHBABS, MHBAT and MHBAN Schiff base monomer

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2.2.1 MHBABS monomer

In order to synthesis MHBABS monomer, initially in a 250 mL round bottom flask 4-amino benzene sulfonic acid (ABS) (2.25 g, 0.013 mol) was taken and then it was dissolved in 40 mL of methanol by continuous stirring on a magnetic stirrer at room temperature. To this, an aldehyde compound, 3, 5-dimethoxy-4-hydroxy benzaldehyde (MHB) (2.36 g, 0.013 mol) solution in 40 mL of methanol was added dropwise with continuous stirring. After that the reaction mixture was stirred for 10 min, 2 drops of glacial acetic acid were added. Then the mixture was again stirred for 6 h to form a Schiff base monomer, MHBABS at RT. Finally, the solvent was evaporated to obtain the solid product and then it was washed two times with cold methanol. The precipitated product was crystallized by using acetonitrile. Yield: 90%. 1H NMR (DMSO-d6): δ ppm, 9.73 (s, 1H, –SO3H), 9.13 (s, 1H, –OH), 8.51 (s, 1H, –CH=N), 7.60 (d, 2H, Ar-Hc), 7.17 (s, 2H, Ar-Ha), 7.13 (d, 2H, Ar-Hb) and 3.82 (s, 6H, -OCH3).

2.2.2 MHBAT monomer

MHBAT monomer was synthesized using a similar procedure to that employed for the synthesis of MHBABS monomer except that 2-amino thiophenol (AT) (1.63 g, 0.013 mol) was used instead of 4- amino benzene sulfonic acid (4ABS). Yield: 89%. 1H NMR (DMSO-d6): δ ppm, 9.24 (s, 1H, –OH), 8.53 (s, 1H, –CH=N), 7.50 (d, 1H, Ar-Hb), 7.30 (s, 2H, Ar-Ha), 7.25 (d, 2H, Ar-Hc), 7.20 (t, 1H, Ar-Hd), 4.10 (s, 1H,-SH), 3.82 (s, 6H, -OCH3).

2.2.3 MHBAN monomer

MHBAN monomer was synthesized by using 1, 5-diaminonaphthalene (AN) (0.95 g, 0.06 mol) in the same manner as described above. Yield: 82%. 1H NMR (DMSO-d6): δ ppm, 9.14 (s, 2H, -OH), 8.51 (s, 2H, -CH = N), 8.11 (d, 2H, Ar-Hb), 7.49 (t, 2H, Ar-Hc), 7.55 (s, 4H, Ar-Ha), 7.14 (d, 2H, Ar-Hd) and 3.8 (s, 6H, -OCH3).

2.3 Synthesis of polyazomethine based polymers

Three different types of polyazomethine based polymers, P-MHBABSXB, P-MHBATXB and P-MHBANXB containing syringaldehyde unit were synthesized by the action of Schiff base monomers, MHBABS, MHBAT and MHBAN containing different functional groups with aromatic dihalogen compound, p-xylenedibromide (XB) and they are represented in Scheme 2.

Scheme 2
scheme 2

Synthesis of P-MHBABSXB, P-MHBATXB and P-MHBANXB polymers

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2.3.1 P-MHBABSXB

The polymerization process was carried out as follows: 3.92 × 10−3 mol of MHBABS monomer was taken in a 250 mL of two neck round bottom flask equipped with a condenser and then it was dissolved in 40 mL of DMF. After that it was refluxed up to 130 °C under N2 environment followed by the addition of 0.4 g Na2CO3 into the flask and again stirred for 30 min. Then 4.2 × 10−3 mol p-xylenedibromide (XB) was dissolved in 5 mL of DMF and added dropwise into the flask and the mixture was again refluxed at 130 °C under a N2 atmosphere for 12 h. At the end of the reaction, a dark black-brown polymer was obtained. After the completion of reaction, the mixture was allowed to cool and precipitated by 250 mL of water. The synthesized polymer was filtered, washed with water to remove salt and dried in vacuum oven for 24 h. 1H NMR (DMSO-d6): δ ppm, 10.13 (s, 1H, –CH=N), 7.82 (d, 2H, Ar-Hc), 7.45-7.10 (m, 4H, Ar-Ha + Ar-Hb + Ar-He), 5.13(s, 2H, Hf), 4.97(s, 2H, Hd) and 3.97 (s, 6H, –OCH3).

2.3.2 P-MHBATXB

P-MHBATXB was synthesized using a similar method as described above by using MHBAT monomer (1.63 g, 0.013 mol) instead of MHBABS monomer. 1H NMR (DMSO-d6): δ ppm, 9.97 (s, 1H, –CH=N), 7.82 (d, 1H, Ar-Hb), 7.1–7.8 (m, Ar-Ha + Ar-Hc + Ar-Hd + Ar-Hf + Ar-Hg), 5.09 (s, 2H, Hh), 4.97(s, 2H, He) and 3.99 (s, 6H, –OCH3).

2.3.3 MHBANXBP

MHBANXB was also synthesized by using MHBAN monomer (0.95 g, 0.06 mol) in the same manner. 1H NMR (DMSO-d6): δ ppm, 9.93 (s, 2H, –CH=N), 8.11 (d, 2H, Ar-Hb), 7.9-7.1 (m, 2H, Ar-Hc + Ar-Ha + Ar-Hd + Ar-Hf), 5.33(s, 2H, He) and 3.8 (s, 6H, –OCH3).

2.4 Measurements

The solubility behavior of all the synthesized polyazomethines were tested qualitatively in a variety of solvents. It was found that all the polymers were insoluble in common organic solvents like acetone, CHCI3, THF and DCM. These synthesized polyazomethines were soluble in polar aprotic solvents such as DMF, DMAc, NMP, DMSO and pyridine. FT-NMR spectrometer (JEOL AL 500) was used to record the 1H NMR spectra by using DMSO-d6 as a solvent and tetramethylsilane (TMS) as an internal reference. IR spectra were acquired on Thermo Nicolet FT-IR spectrometer (Perkin-Elmer FT-IR spectrum two) within the range of 400–4000 cm−1 by using KBr pellets. Thermal analysis was performed by TGA-DTA analyzer (Perkin-Elmer STA 6000) with a heating rate of 10 °C per minute under N2 atmosphere. The sample analysis was carried out from 30 to 800 °C. The weight loss was recorded as a function of temperature. The number average molar weight (Mn), weight average molar weight (Mw), and polydispersity index (Mw/Mn) of P-MHBABSXB, P-MHBATXB, P-MHBANXB were measured by Youglin ACME 9000 GPC in DMF with a flow rate of 0.5 mL per minute at 40 °C on two polystyrene gel columns connected to a Younglin ACME 9000 RI detector and a Younglin ACME 9000 Gradient Pump. Ultraviolet–visible absorption spectra were recorded in DMSO by UV–Vis spectrophotometer (UV-1700 Pharma spec) at 25 °C. Cyclic voltammetry measurements were performed with a bipotentiostat (AFRDE 4E, Pine Instruments) together with an e-corder (201, eDAQ) at 80 mV/s scan rate under argon. Polymers were dissolved in dry DMSO at 10−3 M containing 0.1 M TBAPF6. A saturated Ag/AgCl electrode was employed as a reference electrode and a platinum electrode as an auxiliary electrode. Fluorescence measurements were performed on Varian Cary Eclipse fluorescence spectrometer in DMSO. Concentration of the compounds was 0.01 mg/mL and slit width was 5 nm. SEM images of the polymers were captured by an HRSEM Supra 40, Zeiss instrument. Wayne Karr impedance analyzer model 6500B made by Wayne Karr instrument used to determine impedance of sample film, data were recorded in the frequency range 20 Hz–10 MHz with applying potential of 100 mV. The temperature dependent impedance measurements were carried out by placing the polymeric samples between two stainless steel blocking electrodes inbuilt in sample holder and then the entire assembly was placed in furnace in the temperature range 30–100 °C with the accuracy of ± 1 °C. Altas constant thickness film maker model GS15810 made up by Specac limited UK was used for making polymer film with constant thickness. Instrument has specific dies ring for making specific thickness film, temperature set up (room temperature to 500 °C) and pressure control (0 to 15 tons). Whole set up shows accuracy of ± 1%.

2.5 Sample preparation for conductivity measurement

Initially 100 mg of polymer was taken in aluminium cup and covered by aluminium foil cap. Than it was placed inside film maker, and temperature was set at 100 °C. When temperature reached to 100 °C, 2 ton pressure was applied for 1 min. After that the polymeric film was cooled at room temperature. Film with aluminium foil was taken out from film maker and finally aluminium foil was separated out from the surface of polymeric film. Now polymeric film was ready for analysis of its electrical properties.

Doping of polymeric film was done by exposure of the thin film to iodine vapour for 6 h in desiccator. Then the film was taken out from the chamber and allowed to stabilize in open environment for 1 h. Doped polymeric film was ready for study of its electrical properties.

3 Results and discussion

3.1 NMR spectroscopy

1H NMR spectra of all the monomers and their polymers are given in Figure S1 (a) and (b). NMR spectra of monomers give sharp peaks as estimated. The hydroxyl, aromatic and azomethine proton peaks were observed at 9.2, 8.2–7.1 and 8.5 ppm respectively. In 1H NMR spectra of polymers, an enlargement of the peaks and an enhancement in the number of the peaks were examined. This peaks enlargement was appeared because of the presence of repetitive monomer units having different chemical environments. 1H NMR spectroscopic data showed the disappearance of thiol peak of thiophenol, hydroxyl peak of syringaldehyde and hydroxyl peak of sulphonic acid groups in the polymers that confirmed the formation of polymer with sulfonate ester, thioetheric and the etheric bridge.

3.2 Infrared spectroscopy

Figure S2 (a) and (b) gives the FT-IR spectra of the synthesized monomers and their polymers. The major FT-IR absorption bands observed in monomer and corresponding polymers, their assignments, and data are listed in Table 1. In the IR spectra (Figure S2 a), for MHBABS, MHBAT, and MHBAN, –OH peak was observed at 3515, 3422 and 3485 cm−1 respectively and the conversion of NH2 (amine) into N = CH (imine) by condensation was observed at 1659, 1623 and 1620 cm−1 respectively. The appearance of HC = N stretching frequency along with imine –CH stretching frequency and the methoxy stretching frequency confirmed the formation of the monomers. In the IR Spectra (Figure S2 b), for P-MHBABSXB, P-MHBATXB and P-MHBANXB, –C–OH peak of phenylene group was observed at 1209,1273 and 1208 cm−1 respectively. This proved that hydroxyl peak of the monomers at 3400–3500 cm − 1 disappeared in consequence of polymer formation. In the IR spectrum of P-MHBABSXB, –S=O peak of sulfonate ester was seen at 1358 cm−1. In IR spectra of polymers, an enlargement of the peak was because of the presence of repetitive monomer units. It was also observed that the N=CH bond in monomers shifted to lower wave number in polymers.

Table 1 FT-IR spectral data of Schiff base monomers and polyazomethines
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3.3 Thermal analysis

Thermal degradation patterns of the synthesized polymers have been displayed in Fig. 1a. Thermal degradation values for the polymers are given in Table 2. From the degradation pattern it is obvious that all the polymers follow a four-stage decomposition pattern. The initial weight loss, beginning from RT to 150.0 °C corresponded to removal of water molecules present in the polymer backbone. The second stage loss at around 270.0 °C is associated with a loss of ether, thioether and sulfonate ester linkage from the P-MHBABSXB, P-MHBATXB and P-MHBANXB, respectively. These weak bonds are easily broken at reasonable temperatures and make them thermally unstable. The third stage weight loss at around 360 °C corresponded to the elimination of imine group from the polymers backbone. Finally, the weight loss after 600.0 °C is observed due to decomposition and degradation of the polymer. In thermal analysis of all the polymers synthesized by condensation polymerization technique, the weight loss patterns are similar but the % of weight loss is dissimilar. From this study, it is observed that the synthesized polymers are thermally more stable.

Fig. 1
figure 1

a TGA of the polyazomethines. b GPC chromatograms of the polyazomethines

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Table 2 Molecular weights and thermal degradation values of polyazomethines
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3.4 GPC analysis

The polymer samples were subjected to GPC analysis and the results support polymer formation with a fairly high polydispersity index (PDI). The GPC (Fig. 1b) spectrum gives the molecular weight with polymerization time. The average molecular weight of polymers is shown in Table 2. According to this, the number of repeated monomer units in P-MHBABSXB, P-MHBATXB, P-MHBANXB are 126, 127 and 210 respectively.

3.5 Optical properties

The UV–Visible absorption spectra are valuable to recognize extent of conjugation in conducting polymers. In The UV spectrum given in Fig. 2a, two types of absorption peak were observed. The absorption peaks of n → π* transition of the azomethine groups and π → π* transitions of the aromatic ring were observed in all the synthesized monomers and their polymers. In monomers, these peaks were observed at lower wavelength whereas in polymer, it is evident that these peaks shifted to the right due to increase in degree of conjugation. For MHBABS, MHBAT, MHBAN, P-MHBABSXB, P-MHBATXB and P-MHBANXB n → π* electronic transitions were observed at 363, 355, 360, 420, 485, and 470 nm respectively and π → π* electronic transitions were observed at 300, 310, 320, 325, 335 and 365 nm respectively. The enhance degree of conjugation in polymers was confirmed by their absorbance spectra that are shifted bathochromically relative to their monomers. This is due to enhance degree of conjugation present in the polyazomethines.

Fig. 2
figure 2

Absorption spectra and cyclic voltammograms of Schiff base monomers and polyazomethines

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3.6 Electrochemical properties

Cyclic voltammetry technique is used to study the electrochemical characteristics of the monomers and their polymers. The current–potential voltammograms of all the monomers and their corresponding polymers are given in Fig. 2b–d as coincident. All the Schiff base monomers and their polymers possessed both oxidation and reduction peaks, confirming their p- and n-type behavior. The HOMO–LUMO energy levels as well as the electrochemical band gaps (E′g) were measured from the oxidation–reduction onset values according to known methods [30]. Electrochemical values of all the compounds are shown in Table 3. The large redox potentials calculated further confirmed the strength of the synthesized compounds. On the other hand, a less positive oxidation potential was observed for polymers represents its significant degree of conjugation. From the electrochemical data, it was confirmed that the polymers possesses smaller electrochemical band gaps than their monomers. The smaller band gap accelerates electronic transitions among HOMO–LUMO energy levels. Hence, the polymers become highly electrical conductive as compared to their monomers.

Table 3 Optoelectronic structure parameters of Schiff base monomers and polyazomethines
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3.7 Fluorescence measurements

The conjugated polymers emit light of different intensities at different wavelengths by showing fluorescence properties. When a substance emitted light in visible region, then the substance is appears to exhibit visible colored emission. Fluorescence spectra of the Schiff base monomers and their polymers are given in Fig. 3. From the Figure, it is observed that the emission spectra of all the polymers are shifted bathochromically comparative to those measured for their monomers. This is comparatively due to a greater degree of conjugation associated with electronic effects resulting from the electron withdrawing azomethine groups.

Fig. 3
figure 3

Fluorescence spectra of Schiff base monomers and polyazomethines

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3.8 SEM analysis

Morphological characteristics of the polymers were explained by SEM device. P-MHBABSXB, P-MHBATXB and P-MHBANXB were used in the form of powder. The SEM image has scan under 10 KX magnifications. Figure 4a–c shows the SEM images of P-MHBABSXB, P-MHBATXB and P-MHBANXB, respectively. The surface morphology of P-MHBABSXB was a non-uniform round shaped structure which was altered to a different shape and size (0.5 to 0.6 µm). P-MHBATXB showed uniform block morphology having different size varying from 02 to 20 µm. SEM image of P-MHBANXB showed globular structure having rough surface and varying the size from 0.2 to 20 µm.

Fig. 4
figure 4

SEM photographs of a P-MHBABSXB, b P-MHBATXB and c P-MHBANXB

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3.9 Study of electrical conductivity

Figure 5 shows the Nyquist plots (Z′ vs. Z′′) of three different polymeric films at different temperatures. The DC conductivity is determined from the semi-circular arc intercept on real part of impedance Z′ axis (i.e. bulk resistance, Rb) by using relation:

$$\sigma_{\text{dc}} = \left( { 1/{\text{R}}_{\text{b}} } \right) \times \left( {{\text{ l }}/{\text{A}}} \right)$$

where Ɩ = thickness of the sample film in cm, A = area of the sample holder in cm2 and Rb = bulk resistance.

Fig. 5
figure 5

Typical Nyquist plot of polyazomethines at different temperature and log σdc versus 1000/T plot for polyazomethines

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The DC conductivity of P-MHBABSXB, P-MHBATXB and P-MHBANXB was found out of range at without doping condition, However, I2 doped films of P-MHBABSXB, P-MHBATXB and P-MHBANXB showed higher DC conductivity 4.22 × 10−5 S/cm, 4.23 × 10−5 S/cm, and 1.02 × 10−5 S/cm respectively at 30 °C. This was due to the oxidation of I2 and enhanced amorphousness of polymeric film matrix. The DC conductivity increased up to 10−4 S/cm for all polymers at high temperature (100 °C) due to increase in chain flexibility at higher temperature.

The temperature reliant DC conductivity of I2 doped polymeric films shows the thermally activated process which is basically Arrhenius type (log σdc vs 1000/T given in Fig. 5) given as:

$$\sigma_{\text{T}} = \sigma_{0} { \exp }^{{ - {\text{Ea}}/{\text{ kT}}}}$$

where Ea = activation energy (eV), k = Boltzmann constant, T = temperature (K) and σ0 is the pre-exponential factor. Figure 5 reveals that the DC conductivity varies linearly as the temperature increases and follows the Arrhenius type thermally activated process with phase transition. The values of activation energy for P-MHBABSXB, P-MHBATXB and P-MHBANXB are 0.15 eV, 0.23 eV and 0.09 eV respectively before transition and 0.08 eV, 0.24 eV and 0.05 eV respectively after transition.

The frequency dependent conductivity study shows increase in conductivity with increasing frequency and shifting of the middle region towards higher conductance value in σac (S/cm) versus log f (Hz) plots with different temperatures (Figure S3) for P-MHBABSXB, P-MHBATXB and P-MHBANXB polymers. It indicates that the ion dynamics is thermally activated. σac (S/cm) versus log f (Hz) plots are probable to follow the Jonscher’s Power law (JPL) which is given by

$$\sigma = \sigma_{\text{dc}} + {\text{Af}}^{\text{n}}$$

where σdc DC conductivity of film, A = constant, n = power exponent.

In AC conductivity spectra of P-MHBABSXB, P-MHBATXB and P-MHBANXB polymer are shown in Fig. 6a. The value of power exponent is n < 1 for all 3 polymers (n ~ 0.87, n ~ 0.47 and n ~ 0.14 for P-MHBABSXB, P-MHBATXB and P-MHBANXB respectively) reveals the possible mechanism i.e. free hopping to correlated hopping type because of increased number of charge carries. [31, 32] Study of dielectric relaxation properties of polymer also performed to study the transport behavior and the polarization effect in polymeric film (Table 4). The loss tangent (ratio of loss factor (ε″) to dielectric constant (ε′), represented by tan δ) is calculated by applying relation;

$${ \tan }\delta = \frac{{\varepsilon^{\prime \prime } }}{{\varepsilon^{\prime } }}$$

where ε′ = Real parts of the dielectric constant and ε″ = Imaginary parts of the dielectric constant.

Fig. 6
figure 6

a AC conductivity spectra of P-MHBABSXB, P-MHBATXB and P-MHBANXB polymers at 30 °C (curves are fitted using relation σ = σo + Afn). b Loss tangent (tan δ) versus log f (Hz) plot for P-MHBABSXB, P-MHBATXB and P-MHBANXB at 30 °C

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Table 4 Electrical conductivity data of polyazomethines
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From tan δ versus log f (Hz) graph (Fig. 6b) it is observed that, up to certain value of frequency tan δ increases, the frequency where tan δ has maximum value is called the dielectric relaxation peak frequency (fr). With increasing temperature fr (Hz) increases (Fig S4), which indicate that the flexibility of polymeric chain increases with increasing temperature.

The complex dielectric permittivity is given as ɛ* = ɛ′ − jɛ″. ɛ′ and ɛ″ are associated with the charge capacity and loss of energy by movement of charge respectively. ɛ′ and ɛ″ are given as follows;

$$\varepsilon^{\prime } = \frac{C l }{{\varepsilon_{o} A}}\quad {\text{and}}\quad \varepsilon^{\prime \prime } = \varepsilon_{o} { \tan }\delta$$

where C = capacitance of sample, εo = permittivity of free space.

The complex electric modulus study is performed to study the electrode polarization effect and relaxation in polymeric electrolyte systems. The electric modulus given as (M* = M′ + jM′′) is related to complex dielectric permittivity by relation;

$${\text{M}}* = \frac{1}{{\varepsilon^{*} }}$$

M′ and M″ are calculated by relation;

$${\text{M}}^{\prime } = \frac{{\varepsilon^{\prime } }}{{\left( {\varepsilon^{\prime 2} + \varepsilon^{\prime \prime 2} } \right)}}\quad {\text{and}}\quad {\text{M}}^{\prime \prime } = \frac{{\varepsilon^{\prime \prime } }}{{\left( {\varepsilon^{\prime 2} + \varepsilon^{\prime \prime 2} } \right)}}$$

where M′ = Real part of the complex modulus M* and M″ = Imaginary part of the complex modulus M*.

Frequency dependent ɛ′ and ɛ″ at different frequencies are shown in Fig. 7 for different polymers at 30 °C. There is sharp increment of ɛ′ and ɛ″ at lower frequency range in plot of dielectric permittivity ɛ′ and ɛ″ versus log f (Hz) due to electrode polarization. In higher frequency region this polarization effect is suppressed for polymeric films as a result of decrease in fast periodic reversal of electric field [33]. Temperature dependent dielectric permittivity study of polymers confirmed that there is increase in electrode polarization, capacitance of polymeric system and losses energy by displacment of charge with increasing temperature (Figure S5).

Fig. 7
figure 7

ɛ′ and ɛ″ versus log f (Hz) plot for polyazomethines at 30 °C

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In electric modulus M′ and M″ versus log f (Hz) plot, Fig. 8 shows that large capacitance associated with polymer at lower frequency resulting to a constant line in graph which is approaches to zero. It also indicates the minimum contribution of electrode polarization, the thermally activated relaxation and charge carrier hopping is taking place in polymer system. With increasing temperature M″ peak maximum shifted towards higher frequencies (Figure S6) confirms that thermally activated conduction [34, 35].

Fig. 8
figure 8

M′ and M″ versus log f (Hz) plot for polyazomethines at 30 °C

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4 Conclusions

In this study, three novel π-conjugated Schiff base type monomers containing syringaldehyde unit were successfully prepared and characterized. Stable and conjugated azomethine polymers soluble in standard organic solvents were synthesized by condensation polymerization. The synthesized conducting polymers were characterized by 1H NMR, IR, TGA, GPC, fluorescence, UV–Vis, CV and SEM techniques. The NMR and IR spectroscopic analysis confirmed the formation of Schiff base monomers and their corresponding polymers. Thermal degradation behaviours of the synthesized polymers were also examined. TGA results showed that the synthesized polymers were thermally more stable up to 300 °C. Consequently, due to high thermal stabilities the synthesized polymers may be valuable candidates to produce temperature-stable materials. Polymer synthesis was further confirmed by GPC analysis. The enhance degree of conjugation of polymers was explained by their absorbance and fluorescence spectra that were shifted bathochromically relative to their monomers. According to electrochemical properties, electrochemical band gaps (E′g) values of the monomer and polymer differ depending on enhance of conjugation. Optical and electrochemical analysis results indicated that polymers possess smaller band gaps than their monomers. The calculated band gaps make the polymers highly suitable for photovoltaic, electronic and optoelectronic applications. The electrical conductivity calculated by iodine doping show good results. Conductivity study showed that the maximum conductivity for all polymers at 100 °C to be ~ 10−4 S/cm. The temperature dependent DC conductivity values followed Arrhenius type behavior with low activation energy which confirms the semiconducting nature of polymers. AC conductivity curves followed the Jonscher’s Power law with power exponent n < 1 that support the DC free hopping for all three polymers. Dielectric properties suggested that the dielectric relaxation was thermally activated with charge carrier hopping.