Singaram Vengatesan*,
Subramanyan Santhi,
Ganapathy Sozhan,
Subbiah Ravichandran,
D. Jonas Davidson and
Subramanyan Vasudevan
Electro-Inorganic Chemicals Division, CSIR – Central Electrochemical Research Institute, Karaikudi-630006, Tamilnadu, India. E-mail: svengatesan@cecri.res.in; Fax: +91 4565 227651; Tel: +91 4565 241295
First published on 6th March 2015
Hydroxide anion exchange membranes (HAEMs) are of recent research interest, since these membranes can potentially replace the noble metal catalysts used in electrochemical energy conversion systems such as fuel cells and electrolysers. The conductivity and stability of state-of-the-art anion exchange membranes are far below those required for real applications. Herein, we report a novel anion exchange membrane based on aminated and cross-linked poly(vinylbenzyl chloride) prepared by an easy, viable synthetic route. β-Hydrogen free, multi-nitrogen containing ‘hexamethylenetetramine’ was used and explored as an amination/cross-linking agent for the first time in this study. FT-IR and 1H-NMR analysis results confirmed the successful quaternization of poly(vinylbenzyl chloride) with hexamine. TGA results showed the degradation temperature of the quaternized polymer is as high as 160 °C. AFM analysis revealed that the membrane possesses phase separated morphology with hydrophobic and hydrophilic domains. The ionic conductivity of the membranes increased when the amine to polymer ratio was increased from 0.2 to 0.33, and the highest ionic conductivity achieved was 6.8 × 10−3 S cm−1. The membrane has good chemical and alkaline stability which strongly suggests that the membrane would be a promising material for electrochemical energy conversion systems.
Here, we report the preparation of anion exchange membranes with a cross-linked structure (Scheme 1) by a one-step synthetic route. It mainly involves the preparation of a quaternized poly(vinylbenzyl chloride) (PVBC) anion exchange polymer using an inexpensive amination/cross-linking reagent, hexamethylenetetramine (HMTA). HMTA, commonly known as ‘Urotropine’, is an amine base having a cage-like structure which finds various applications, especially in the plastic and rubber industries as a hardener/binder. In the literature, different amination/cross-linking agents such as ethylene diamine, hexamethylene diamine, tetramethylene pentamine, triethylene diamine have been used and most of them have a β-hydrogen in their structure.28–31 Pandey et al. prepared highly cross-linked anion exchange membranes using 1,4-diazabicyclo[2.2.2]octane as a cross-linker.31 Cao et al. prepared a novel alkaline anion exchange membrane using methylated melamine as an amination/cross-linking agent.32 Though the membrane afforded high ionic conductivity and stability, the methylation step described in their work is a particularly excessive pathway. However, the present work uses the amination agent HMTA, taking advantage of its β-hydrogen free structure which can circumvent the harmful elimination and/or substitution reactions. Moreover, this work involves a single step fabrication of the membrane by casting the viscous solution of the quaternization reaction mixture without further processing or modification.
For the solubility test, quaternized anion exchange polymers with HMTA:
PVBC ratios of 0
:
1, 0.2
:
1, 0.33
:
1, 0.5
:
1 and 1
:
1 were also synthesized in tetrahydrofuran (replacing NMP and methanol in the previous procedure) at 60 °C.
The oxidation stability of the membranes was also tested in Fenton’s solution. The Fenton’s solution was prepared using ferrous sulfate (FeSO4) and hydrogen peroxide (H2O2) in the weight ratio 1:
8 at the acidic pH of 3. A membrane sample with a known weight was immersed in the Fenton’s solution for 10 days at 30 °C. Then, the membrane sample was taken from the Fenton’s solution and rinsed with de-ionised water, followed by drying in a vacuum oven at 60 °C for 24 h. From the above experiments, the weight loss of the membrane was calculated.
The surface morphological features of the membrane were analysed using a TESCAN scanning electron microscope (model: S-3000H, Hitachi, Japan). The localization of hydrophilic domains in the membrane was analysed using an atomic force microscope (model: Picoscan 2100, Molecular imaging, USA).
The spectrum of PVBC has an absorption band at 1263 cm−1 that is attributed to CH2Cl wagging,36 and the region of 750–800 cm−1 is assigned to C–Cl stretching.37 The bands at 2921 and 2854 cm−1 are related to symmetric and asymmetric CH2 stretching, and the band at 1601 cm−1 is due to aromatic CC stretching. The quaternized PVBC polymer shows two major peaks at 1002 and 1304 cm−1, which are assigned to C–N stretching vibrations.36 Also, the C–Cl stretching vibration (800 cm−1) is not present in the quaternized PVBC spectrum, confirming the quaternization reaction. The broad peak which appears at 3430 cm−1 is due to O–H vibrations. Additionally, the intense peaks at 1461 and 1658 cm−1 indicate the presence of quaternary ammonium groups as reported in the literature.32 Notably, the intensity of the stretching band at 1658 cm−1 increased in the quaternized PVBC spectrum which might arise from the cross-linking of the PVBC polymer.
Fig. 2 represents the NMR spectra of the PVBC, HMTA and quaternized PVBC. From the NMR spectra, the aliphatic protons (–CH2 and –CH) of PVBC appear at around 1 to 2 ppm, whereas the aromatic ring protons appear at 6.5 and 7.2 ppm. The peak at around 4.6 ppm is assigned to the CH2Cl group. On the other hand, the hexamine spectrum shows a single peak at 4.55 ppm which corresponds to six equivalent methylene (–CH2) protons. The peaks appearing at around 2.5 and 3.3 ppm in all three spectra are the signals from the DMSO-d6 and moisture present in DMSO-d6, respectively. In the case of the quaternized PVBC spectrum, a new peak appears at 5.0 ppm in addition to the peak at 4.6 ppm. The new peak which appears in the downfield region is assigned to the quaternized CH2Cl group. This result confirms the quaternization of the PVBC with hexamine.
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Fig. 2 1H-NMR spectra of (a) HMTA, (b) PVBC and (c) quaternized PVBC in Cl− form (HMTA/PVBC = 0.5![]() ![]() |
Fig. 3 shows a photograph of the anion exchange polymers synthesized with different amine/polymer ratios in THF solvent. The solution opacity changes as the amine content is increased in the PVBC polymer, and it converts into a viscous gel (0.5:
1 ratio) and a solid precipitate (1
:
1 ratio) at high amine concentrations. This reveals that the PVBC was aminated and cross-linked by HMTA which increased the solution viscosity and reduced the solubility of the quaternized polymer. Besides, cross-linking of the polymer chains would also increase the molecular weight and reduce the solubility of the quaternized polymer. The degree of quaternization of PVBC with various amounts of HMTA was calculated from the chloride content of the membrane. The calculated DQ (%) of the membrane with HMTA/PVBC ratios of 0.2, 0.25, 0.33, and 0.5 are 27.2, 36.3, 47.2 and 61.6%, respectively. From these results, it is clear that the degree of quaternization increases with increasing amounts of HMTA.
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Fig. 3 Photograph of the quaternized anion exchange polymers with different HMTA/PVBC ratios (a) 0![]() ![]() ![]() ![]() ![]() ![]() ![]() ![]() ![]() ![]() |
Thermo-gravimetric analysis was performed to estimate the thermal stability of the quaternized anion exchange polymer. The TGA curves of the PVBC and quaternized PVBC polymer are shown in Fig. 4. The PVBC polymer shows two major degradation steps: the polymer backbone degradation from 310 °C to 410 °C, and carbonization from 420 °C to 700 °C. However, the quaternized PVBC polymer shows three distinct degradation steps: the quaternary ammonium group degradation from 160 °C to 250 °C, polymer degradation from 310 °C to 400 °C, and carbonization from 410 °C to 700 °C. The TGA results are in good agreement with the literature results reported for anion exchange polymers containing quaternary ammonium groups.32
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Fig. 4 Thermo-gravimetric curves of (a) PVBC and (b) quaternized PVBC in Cl− form (HMTA/PVBC = 0.25![]() ![]() |
The membranes with different HMTA/PVBC ratios were fabricated using the quaternized PVBC (Cl− form) in NMP solution, except for the ratio of 1:
1. The 1
:
1 membrane could not be achieved due to the formation of a solid precipitate before casting the reaction mixture. The optical image of the anion exchange membrane is depicted in Fig. 5a which displays a yellowish membrane with a smooth surface. Fig. 5b and c are the SEM illustrations of the surface and cross-sectional morphological features of the membrane. The membrane shows no signs of cracks and/or voids. The cross-section of the membrane (Fig. 5c) appears smooth without any perforations or defects.
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Fig. 5 (a) Optical image, (b) surface and (c) cross-sectional SEM images of the quaternized PVBC membrane (HMTA/PVBC = 0.33![]() ![]() |
Fig. 6 shows the ionic conductivity and ion-exchange capacity of the membranes in their OH− form. The PVBC only membrane exhibits very low ionic conductivity in the order of 10−7 S cm−1 (data not shown here). A quantum jump in conductivity is observed once the PVBC is quaternized with HMTA, i.e. 10−7 S cm−1 to 10−3 S cm−1. The conductivity rises exponentially as the HMTA/PVBC ratio is increased from 0.2 to 0.33 which reflects the vital role of the amination agent in the quaternization of the PVBC polymer. However, a further increase in the HMTA/PVBC ratio from 0.33 to 0.5 produces a decrease in conductivity. This observed phenomenon is due to the high level of polymer cross-linking as the amine content was increased to a greater extent. As reported by Xiong et al.,38 a high level of cross-linking reduces the membrane conductivity due to the formation of a membrane compact structure that narrows the anion transfer channels. From the figure, the ion exchange capacity of the membranes also shows a linear increasing trend with the increase in amine/polymer ratios. The IEC increases from 0.99 to 3.42 meq. g−1 (Table 1) as the amine/polymer ratio is increased from 0.2 to 0.5. It is apparent that a greater number of ion exchange groups can be introduced during the quaternization process, since the amination agent HMTA possesses multi-nitrogen centres in its structure. The nitrogen content of the membranes obtained from elemental analysis (Table 1) shows that the membrane acquires a significant amount of nitrogen in its composition, and it increases as the amine to polymer ratio is increased.
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Fig. 6 Ionic conductivity (![]() ![]() |
In general, ion exchange membranes have the tendency to absorb water, since they possess a high density of hydrophilic ionic groups. Moreover, the water content of the membrane also plays a vital role in the ion conduction process. Therefore, the water uptake of the prepared anion exchange membranes was measured in the OH− form and the results are given in Table 1. The water uptake data of the membranes show that the uptake increases as the amine to polymer ratio is increased. This is mainly attributed to the high level of quaternization as the amine content is increased. The high level of quaternization is likely to introduce a higher number of ionic groups in the anion exchange polymer and increase the water absorption capacity of the membrane.
The chemical stability of a membrane is crucial for long term operations, and the stabilities of the anion exchange membranes were measured under strong alkaline and oxidizing conditions. The membranes were immersed in 5 M KOH and Fenton’s solution separately for 10 days at 30 °C and the stability test results are shown in Table 2. The alkaline stability of the membranes was evaluated in terms of IC and IEC values. From the table, the membrane IC and IEC values decreased very marginally compared to the untreated membranes (Table 1). Notably, the membranes with a high amine concentration (0.33 and 0.5) exhibit low alkaline stability compared to those with a low amine concentration (0.2 and 0.25). Also, after immersing in Fenton’s solution the membranes showed negligible weight loss (∼1%). Fenton’s test was performed especially to see the oxidation stability of the anion exchange membranes in the presence of sensitive OH radicals. These results reveal that the membranes are chemically stable.
To observe the morphological features of the membrane thoroughly, AFM analysis was performed in tapping mode and the results are shown in Fig. 7. The topography image (Fig. 7a) of the membrane shows microphase separated morphology and the microphase separation mainly occurs between the hydrophobic backbone and the hydrophilic graft chains.39 The 3D phase image (Fig. 7b) of the membrane shows the distribution of peak and valley regions. Earlier, Luo et al. studied the poly(vinylbenzyl chloride–methylmethacrylate) copolymer based anion exchange membrane using AFM and identified that the peak regions mostly arise from the hydrophobic domains and the valley regions from the hydrophilic ionic domains.40 It can be predicted from the above results that the membrane developed in the present work possesses the phase separated morphology which is typically found in Nafion® based membranes.41
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Fig. 7 AFM tapping mode: (a) topography image and (b) 3D phase image of the anion exchange membrane (HMTA/PVBC = 0.33![]() ![]() |
The quaternization of alkyl halides with HMTA was reported earlier by Vidal et al.,42 in the preparation of QA functionalised silica sorbents for solid-phase extraction. However, we report for the first time the simultaneous amination and cross-linking of a chloropolymer using HMTA, and explored the applicability of the QA functionalized polymer as an anion exchange membrane. Moreover, this work is also unique as it involves the preparation an anion exchange membrane in a single step using an inexpensive amination/cross-linking agent. Further, the absence of any β-hydrogen in the amination agent eliminates the possible degradation of the anion exchange membranes by Hoffman elimination and/or substitution reactions. Though the developed membranes were chemically stable, their mechanical flexibility is poor due to the high cross-linking and the rigidity of the aromatic polymer which hampers the application in real systems.
TGA results showed the thermoplastic behaviour of the quaternized polymer which mainly occurred due to the incorporation of hydrophilic QA groups into the hydrophobic aromatic polymer backbone. AFM analysis revealed the presence of well defined hydrophobic and hydrophilic phase separation within the membrane. The chemical stability of the membranes was superior in alkaline and oxidizing environments, whereas the mechanical properties have to be improved for practical application of the membranes in real electrochemical systems.
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