Carbon Nanotube@MnO₂@Polypyrrole Composites: Chemical Synthesis, Characterization and Application in Supercapacitors

Abstract

Core/shell structures of carbon-based materials/ metal oxide have been considered as potential candidates for electrochemical devices due to their improved pseudocapacitance/electrical double layer capacitance and high conductivity/ superior surface area. The development of multiple core-shell structures of MWCNT@MnO₂@PPy was analyzed as a standard procedure for mass production of supercapacitor electrodes. The relative concentration of carbon nanotubes in the composite was varied to optimize the double layer capacitance contribution in overall response of device. Resulting structures presented capacitance in order of 272.7 Fg^-1 and reasonable cycling performance.

Keywords advanced energy systems; carbon nanotubes; smart materials

1. Introduction

Owing to the increasing demand for more efficient energy source and storage devices in our daily life (such as portable electronics and hybrid vehicles), increasing attention has been dedicated to producing energy storage flexible devices with improved cycle life- and charging/ discharging- rate.

The development of new electrochemical energy-related systems based on lithium-ion batteries (LIBs),^1,2 microbial fuel cells (MFCs)³ and supercapacitors requires the production of sustainable electrode materials with high energy density, high power density, good cycling performance in association with simple and low cost processability, due to the successive insertion/ exclusion of ions during successive cycles. The use of polymeric structures with a stable skeleton and large conjugated structure represents an important strategy to preserve charge transfer mechanisms.^1,2

Supercapacitors, also called electrochemical capacitors, present higher power- and energy- density.^4-6

Typical supercapacitors (standard symmetrical assembly) are composed by two electrodes separated by a solid membrane. The energy storage is due to the formation of double layer and redox reactions in carbon derivatives and conducting polymer/ metal oxide, respectively.^7-11

Non-Faradaic process dominates in the EDLC response and depends on specific surface area/ porosity of carbon-based materials.^12-14 Carbon derivatives (such as carbon nanotubes, reduced graphene oxide - rGO and modified graphene - Claisen Graphene)^15-19 have been considered as potential candidates for EDLC devices. Particularly, the chemical stability, strong mechanical resistance, superior electric conductivity, transparency in visible/ near infrared region and flexibility play a pivotal role for application of carbon nanotubes in new types of electronic devices such as flexible devices,²⁰ transparent electrode for dye-sensitized solar cell,^21-23 anode for microbial fuel cell ²⁴ and so on.

On the other side, pseudocapacitors (conducting polymers and metal oxide nanoparticles) contribute to charge storage mechanisms due to their characteristic fast redox reaction (Faradaic process). Conducting polymers (such as polypyrrole - PPy) introduce important advantages relative to environmental stability, high conductivity, high chemical stability and processability.^4,12,25-27 In addition, the chemical synthesis of free-standing polypyrrole nanotubes provides a potential candidate for thermoelectric application²⁸ and membrane for anode of microbial fuel cells.²⁹

Based on these aspects, it has been reported the use of carbon-based materials in association with pseudocapacitors to achieve the desired performance for energy storage devices.^30-33

In terms of pseudocapacitance, MnO₂ presents an extraordinary theoretical specific capacitance of 1370 F/g,^31,34 which is associated with poor electrical properties (low conductivity).

To circumvent this limitation, the combination with conducting polymers offers an interesting alternative directed to the production of hybrid conducting polymer/ metal oxide composite with improved electrical/ electrochemical properties.^31,35

The specific capacitance of polypyrrole nanotubes (reported by de Oliveira and de Oliveira)¹⁵ is in order of 47.83 F/g. The association of polypyrrole with modified graphene oxide returns capacitance in order of 277.8 F/g ¹⁷ while association of GO and PPy provides capacitance in order of 289 F/g.²⁵ The association of MnO₂ and graphene results in a capacitance of 192 F/g ¹⁹ while composites of MnO₂/GNS/CNTs returns a value in order of 132 F/g.¹⁹

The synthesis of polypyrrole on MnO₂ surface results in a porous composite with increasing surface area and reduced deterioration degree of PPy during charging/ discharging process.^34,36 The incorporation of carbon nanotubes improves the electrochemical- and mechanical- response of resulting highly flexible electrodes.³¹

Wang et al.³⁷ reported the production of MnO₂/PPy nanosheets (by chemical polymerization on carbon cloth) for symmetric supercapacitors. The combination of Li₄Ti₅O₁₂ nanowire with MWCNTs deposited on carbon cloth and copper-nickel oxide nanostructures³⁸ represent other interesting strategy in the direction to develop 3-d arrays with superior volumetric energy storage capabilitiy.³⁹ Li et al.⁴⁰ reported the combination of ferroferric oxide-carbon (Fe₃O₄-C) nanorod array as a convenient strategy for improvement in cyclability of electrodes. Alternatively, anodes based on core-shell structures such as TiO₂-MnO₂⁴¹circumvents the typical low cyclability of individual components. As we can see, the association of components (carbon nanotubes, polypyrrole and MnO₂) in hierarchical structures favors important applications due to the ion diffusion distance and available surface area for ionic reaction.

In this work, we have chemically synthesized dual core-shell organic-inorganic devices for application as supercapacitor electrodes. Corresponding systems (reported in the literature)^42,43 were typically synthesized by electropolymerization. The relative concentration of carbon nanotubes in composites was varied in order to establish the best ratio of EDLC/pseudocapacitance in hierarchical structures.

2. Experimental Procedure

Multi-walled carbon nanotubes (MWCNT), KMnO₄, MnSO₄, ammonium persulfate (APS), HCl and KCl were of analytical grade, produced by Aldrich and used as received, while pyrrole (Aldrich) was distilled before polymerization.

Dual core-shell coaxial composites were prepared according a two-step procedure: the synthesis of MWCNT@MnO₂ complex and the preparation of coaxial MWCNT@MnO₂@PPy.

2.1. Synthesis of MnO ₂ nanorods (α-MnO ₂)

Nanorods of MnO₂ were synthesized according procedure reported by Sen et al.:⁴⁴ KMnO₄ aqueous solution (0.1M in 10 mL) was mixed with an aqueous solution of MnSO₄ (0.15 M in 10 mL) and vigorously stirred for 6 hours. The resulting dark-brown precipitate was separated by centrifugation and dried at 100 °C.

2.2. Synthesis of composite MWCNT@MnO₂

MWCNT@MnO₂ composite was synthesized according procedure reported by Li et al.:³⁰ KMnO₄ (100 mg) was dispersed in milli-Q water (50 mL) at 80^{( )}°C with variable amount of MWCNT viz. 0 mg, 100 mg, 200 mg, 300 mg, 400 mg and 500 mg. Resulting solution was acidified with aliquots of HCl (2 M) until reaches pH 3. Continuous stirring for 10 h at ambient temperature completed the reaction. The resulting powder was rinsed with milli-Q water and filtered (under vacuum) followed by drying procedure (100 °C). It is noteworthy that relative concentration of MnO₂ in the composite remains fixed while relative concentration of MWCNT is varied, in order to identify the influence of carbon derivatives on overall response of device.

2.3. Synthesis of dual core/ shell composite MWCNT@MnO₂@polypyrrole

According procedure described by Li et al.,³⁰ MWCNT@MnO₂ complex (50 mg) was introduced in 30 mL of SDS aqueous solution (5 mM). The resulting material was vigorously stirring stirred for 20 minutes. Pyrrole (0.21 mL) was added to the final product, which was kept at 2 °C under stirring for 5 minutes. After this step, APS aqueous solution - 0.06 M (50 mL) was slowly dropwised into the previous solution (kept at 2 °C) under continuous stirring for 2 hours. The resulting powder was filtered (under vacuum) and dried at 70 °C overnight. Resulting powder (50 mg) was pressed in pellets of 13mm-diameter under 20 kN and soaked into standard electrolyte (KCl aqueous solution - 1M) overnight for incorporation of electrolyte into composites and separator. For comparison, samples of PPy@MnO₂ were prepared considering the corresponding mass of MnO₂ (50 mg).

2.4. Characterization techniques

The morphology of nanostructures was explored from images of scanning electron microscopy (SEM) using a Quanta 200 FEG microscopy (voltage of 20 kV) and transmission electron microscopy (TEM) by TEM FEI Tecnai 20-200 kV. Fourier Transform Infrared (FTIR) spectrum of material was performed in an IR-Prestige-21 FTIR Shimadzu.

The electrochemical responses (cyclic voltammetry - CV), impedance spectrum and galvanostatic charge-discharge cycling (GCD) curves were performed by potentiostat/galvanostat Autolab PGSTAT 302N. DC conductivity of composite was determined using a Keythley 2002 multimeter connected to a 12962 Solartron Sample Holder.

Specific surface area of devices was performed according Brunauer-Emmett-Teller (BET) technique using a Micromeritics ASAP 2420 surface area analyzer.

Symmetric assembly of pellets of composites separated by commercial ion exchange membrane (Celgard) was introduced between two electrodes of 12962 Solartron Sample Holder, while the electrochemical characterization was provided by potentiostat. GCD curves were performed with charging-discharging curves acquired at 6 mA/ -6mA, respectively. Specific capacitance (C) in a symmetrical two-electrodes is given by Eq. 1.⁴⁵

(1) $\mathit{C}=\frac{4\mathit{I}}{\mathit{m}\left(\frac{\mathit{dV}}{\mathit{dt}}\right)}$

where m represents the total mass of electrodes and dV/dt is slope of discharge curve established at fixed current.

3. Results

The morphology of resulting material is shown in the TEM images of Figure 1. Nanorods of MnO₂ ((69.00±4.64) nm of length - as shown in the Figure 1a) resulted from synthesis described in the Section 2.1.

Figure 1
TEM images of (a) MnO₂ nanorods - scale bar of 50 nm, (b) MWCNT (100 mg)@MnO₂ - scale bar of 100 nm, (c) MWCNT (100 mg) @MnO₂@PPy - scale bar of 500 nm and (d) polypyrrole aggregates - scale bar of 200 nm.

Composites of MWCNT@MnO₂ (Figure 1b) are characterized by tubular morphology. The increase in the diameter of nanotubes can be attributed to the covering of MnO₂ on MWCNT surface.

TEM image of composite MWCNT@MnO₂@PPy (Figure 1c) shows partial covering of PPy on hybrid structure (polypyrrole grains are shown in the Figure 1d). The polymerization of PPy on the surface of MWCNT@MnO₂ complex affects the fiber diameter, as clearly indicated in the SEM images - by comparison with Figure 2a (MWCNT)/ Figure 2b (MWCNT@MnO₂ structure) with Figure 2c / Figure 2d (MWCNT@MnO₂@PPy). The identification of components is shown in the EDS overlaid image (Figure 2e) with corresponding distribution of O and Mn (Figure 2f and Figure 2g, respectively).

Figure 2
SEM images of MWCNT (a), MWCNT(500 mg)@MnO₂ complex (b), MWCNT (500 mg)@MnO₂@PPy composite (c and d), overlaid EDX image of MWCNT@MnO₂@PPy composite (500 mg) (e) and identification of oxygen (f) and Mn (g) - values indicated in the Figs. 2b and 2d correspond to measured diameter of indicated fiber.

The diameter of pristine carbon nanotubes (6- 9 nm, length 5 mm and BET of 253.0 m²/g, according supplier) increases to (47.05±5.12) nm after incorporation of MnO₂ (composite MWCNT@MnO₂) and to (143.15±6.59) nm with successive covering of polypyrrole (MWCNT@MnO₂@PPy).

The measured value BET surface area of composite MWCNT@MnO₂@PPy was in order of 82.22 m²/g, as a consequence of covering of conducting polymer on coaxial structure of MWCNT@MnO₂ (corresponding surface area of α−MnO₂ is in order of 78.40 m²/g).

3.1. Structure analysis

FTIR spectra of α−MnO₂, polypyrrole, MWCNT@MnO₂ and MWCNT@MnO₂@polypyrrole are shown in the Figure 3. Bands at 3434 and 1630 cm^-1 are attributed to O-H stretching. Mn-O vibration modes are identified from broad band between 500 cm^-1 and 800 cm^-1.^44,46

Figure 3
FTIR spectrum of α-MnO₂, polypyrrole, MWCNT@MnO₂ and MWCNT@MnO₂@PPy coaxial nanostructures.

Characteristic bands of polypyrrole are identified at 1547 and 1464 cm^-1 (C=C and C-C vibrations), 1184 cm^-1 (C-C breathing vibration)⁴⁷ and 908 cm^-1 (out of plane vibration of =C-H).⁴⁸ The peak at 1042 cm^-1 is assigned to C−H in-plane vibration bands of the pyrrole ring.¹⁷

The coaxial nanostructure (MWCNT@MnO₂@PPy) presents band at 3434 cm^-1 (MnO₂) while bands at 1547, 1449, 1174, 1039 and 908 cm^-1 are assigned to the presence of polypyrrole in coaxial composite, in analogy with previously reported peaks. It is noteworthy that some of these peaks are shifted to lower energies, as result of interaction between polypyrrole/MWCNT and polypyrrole/MnO₂.

3.2. Electrical and electrochemical characterization of composites MWCNT@MnO₂@Polypyrrole

The conductivity of pellets prepared at different relative concentration of MWCNT@MnO₂ is strongly affected by increase in the relative concentration of MWCNT/MnO₂ complex in the resulting MWCNT@MnO₂@PPy composite, as shown in the Figure 4.

Figure 4
DC conductivity of coaxial composites of MWCNT@MnO₂@PPy prepared using increasing rate of MWCNT/MnO₂.

The progressive incorporation of MWCNT on coaxial nanostructures improves the conductivity of resulting composite, with direct implication on reduction of IR drop during charge/ discharge procedure.

Corresponding electrochemical impedance spectrum of MWCNT@MnO₂@PPy (shown in the Nyquist plots of Figure 5a) is composed by two specific regions viz. a semicircle (which corresponds to faradaic reactions) and a straight line due to the interfacial effects at low frequency excitation. The results reveal that incorporation of carbon nanotubes (above 100 mg) affects the slope of linear branch (low frequency) and the diameter of characteristic semicircle.

Figure 5
(a) Nyquist plots of supercapacitors prepared using increasing rate of MWCNT/ MnO₂. In the inset are shown the corresponding equivalent circuit (right) and dependence of double layer capacitance (C_dl) with amount of MWCNT and (b) C-V curves of coaxial composite MWCNT (500 mg) @MnO₂@PPy and corresponding calculated capacitance, (c) corresponding dependence of capacitance vs. scan rate and (d) cycling performance of supercapacitor.

The complete response in the Nyquist diagram has been simulated by corresponding equivalent circuit (shown in the inset of Figure 5a) obtained by association of bulk solution resistance (R_s), charge transfer resistance (R_ct), a constant phase element (CPE) that characterizes pseudocapacitance (C_P) and a double layer capacitor (C_dl). Overlaid lines on impedance spectrum of Figure 5a represent the best fitting from equivalent circuit (modified Randles circuit). From corresponding parameters (returned from fitting of curves), C_dl presented an interesting behavior in terms of dependence with MWCNT concentration. As shown in the inset of Figure 5a, the maximum in the C_dl is verified for samples prepared with 300 mg of MWCNT, indicating that morphology of resulting sample prepared at specific concentration favors the charge accumulation at the interface carbon derivative/ electrolyte. The corresponding C-V curves profile is shown in the Figure 5b, which considers samples prepared using 500 mg of MWCNT. The corresponding values of capacitance (shown in the legend of Figure 5b) varies inversely with scan rate of voltage, as expected - corresponding curves are shown in the Figure 5c. Cycling performance is indicated in the Figure 5d.

GCD curves (shown in the Figure 6a) indicated that capacitance in order of 76.67 F/g is obtained for composites of MnO₂@PPy.

Figure 6
(a) GCD curves of coaxial composite MWCNT (0 mg, 100 mg, 200 mg) @MnO₂@PPy and (b) GCD curves of coaxial composite MWCNT (300 mg, 400 mg and 500 mg) @MnO₂@PPy.

The incorporation of MWCNT/ metal oxide as support for polymer growth improved the electrochemical response of material. The inclusion of MWCNT (100 mg of carbon nanotubes during preparation of MWCNT@MnO₂) results in a capacitance of 91.25 F/g. while 200 mg of MWCNT improves the specific capacitance to value in order of 133.25 F/g.

Specific capacitance reaches a maximum (272.72 F/g) for samples prepared using 300 mg of MWCNT (as shown in the Figure 6b). The corresponding cycling performance test returned a value of capacitance retention in order of 60% after 300 cycles of charge/discharge for this sample (as shown in the Figure 5d).

Progressive incorporation of MWCNT (above 300 mg) reduced the specific capacitance (211.05 F/g - 400 mg of MWCNT and 139.77 F/g - 500 mg of MWCNT). The dependence of specific capacitance of devices with amount of MWCNT is in agreement with corresponding dependence of double layer capacitance (inset of Figure 5a), confirming that electrochemical performance of device depends on relative concentration of carbon nanotubes.

In spite of continuous increase in the conductivity level in response of progressive incorporation of MWCNT in complex, the charge accumulation on double layer reaches an optimal condition at intermediate concentration of MWCNT (300 mg).

As consequence, the best condition for application of composites as supercapacitors was dominated by performance of EDLC in complex.

4. Conclusions

The improved electrical conductivity of electrodes and available surface area for charge accumulation in composites of MWCNT@MnO₂@PPy play a pivotal role to achieve the adequate condition for optimal performance of corresponding electrochemical device.

The relative concentration of MWCNT in coaxial MWCNT@MnO₂ complex covered by polypyrrole affects charge transfer mechanisms and dielectric response of resulting composite.

The dependence of double layer capacitance with relative concentration of carbon nanotubes in the composite is in agreement with response of specific capacitance of resulting devices, which reaches optimal value in order of 272.72 F/g, characterizing an adequate condition for device implementation.

5. Acknowledgement

The authors wish to thank FACEPE, FINEP, CNPq, FAPESB, and CAPES for financial support.

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Publication Dates

• Publication in this collection
  11 Aug 2016
• Date of issue
  Sep-Oct 2016

History

• Received
  03 May 2016
• Accepted
  25 July 2016