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. 2013 May 13;3:1833. doi: 10.1038/srep01833

Polyoxometalate-based Supramolecular Gel

Peilei He 1, Biao Xu 1, Huiling Liu 1, Su He 1, Faisal Saleem 1, Xun Wang 1,a
PMCID: PMC3652265  PMID: 23666013

Abstract

Self-assemblyings of surfactant-encapsulated Wells-Dawson polyoxometalates (SEPs) nanobuilding blocks in butanone and esters yielded supramolecular gels showing thermo and photo responsive properties. The gels can be further polymerized if unsaturated esters were used and subsequently electrospinned into nanowires and non-woven mats. The as-prepared non-woven mats have a Young's modulus as high as 542.55 MPa. It is believed that this supramolecular gel is a good platform for polyoxometalates processing.

Polyoxometalates (POMs) are discrete molecular oxides of early transition metals1 and have obtained widespread application2,3,4,5,6 due to their advantageous properties, e.g., photochromism4,7, electrochromism4,8, magnetism9, catalysis5,10, chirality11. Till now, most of the studies have been focused on the growth of macrosized single crystals of POMs12,13,14,15 as their structures can be solved16. For all the success in the designs and findings of new type of POMs, these are still inherently large anions that are hard to process directly17. Great efforts have been made to build interfaces between POM anions and their surroundings to make them practically useful18,19,20,21,22. Most of the research centres are using covalent modification23,24,25,26,27 and non-covalent modification28,29,30 to build bridge between the POM and organic molecules. Compared with the covalent approach, non-covalent modification is easier to purify final system and get higher productivity.

Non-covalent surface modification uses the cation of quaternary ammonium salt to encapsulate POMs and transfer them from aqueous to nonaqueous phase. In the last few years, self-assemblyings of Keggin-type29,30 and Anderson-type31,32 POM clusters based on non-covalent modification have been explored. In addition, this modification strategy provides the possibilities for fast and controlled self-assembly of POMs into nanostructures33, which maybe have a great potential to become candidate materials. So far, many nanostructures of surfactants encapsulate polyoxometalates assemblies, such as microspheres29, nanofibers34, nanodisks30, nanoflowers35, nanocones and nanotubes30, have been achieved. Recently, we succeeded in the fabrication of nanocone that showed high-efficiency and selectivity toward the catalytic oxidation of sulphides when used as a nanoreactor36. Other than that, most of the assemblies failed to become available materials. A lot of efforts will be needed in the processing and applications of POMs materials.

Herein, we report the formation and response of a supramolecular gel by the self-assembly of surfactant encapsulated Wells-Dawson polyoxometalates which occurred in the butanone and ethyl acetate. In addition, ethyl acetate could be substituted by other unsaturated esters with carbon-carbon double bond or esters with other functional groups such as photofunctional groups. In this paper, we have tried the unsaturated ester. When the ester was substituted by unsaturated ester, the gel could be polymerized. In fact, it builds interface between the Wells-Dawson POM and the polymer. Photochromic hybrid polymer was obtained when the unsaturated ester was polymerized completely. Non-woven mats with greater mechanical stress were fabricated by electrospinning the partially polymerized gel. Therefore, we believe that supramolecular gel is a good platform for polyoxometalates processing.

Results

Firstly, the SEPs were synthesized by using the reported two-phase method29. The biggest difference was the use of two surfactants. Hexadecyl trimethyl ammonium bromide (CTAB) and tetrabutyl ammonium bromide (TBAB) were used to encapsulate the polyoxometalates with characteristic crystal structure of Wells-Dawson (K6P2W18O62·nH2O). In order to determine the component of SEPs, we took the SEPs for thermal gravimetric analysis (TGA) and NMR characterization. Figure 1a shows that the weight loss of SEPs is about 28.17% from 20 to 900°C. To combine the reference29 and TGA results, we think that the six potassium ions have been totally substituted by the cation of quaternary ammonium salt. There are six surfactants molecules in the SEPs. From the 1H NMR spectrum (Figure 1b, the whole 1H NMR spectra was shown in Figure S1), the integral area of H-a hydrogen (1.03 ppm) in TBAB is 1.5 and H-b hydrogen (0.89 ppm) in CTAB is 0.41. There are four H-a hydrogen in one TBAB molecule. We can calculate the ratio of CTAB and TBAB is 0.9:1 which is close to 1:1. So, we can conclude the chemical formula of SEPs is (CTA)3(TBA)3P2W18O62. In addition, Figure S2 shows the TEM images of SEPs which are dispersed in butanone. The diameter of SEPs is about 1~2 nm which is the limitation of resolution in TEM. Therefore, it is difficult to pick a particle of SEPs out.

Figure 1.

Figure 1

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(a) TGA of SEPs in the nitrogen atmosphere with a scanning rate of 10°C min−1. (b) 1H NMR spectra of the pure SEPs in C3D6O.

After that we studied the self-assembly behaviour of SEPs. The butanone solution of SEPs changed from transparent to opaque with ester added to it. When the ratio of butanone to ethyl acetate is 2:1, we can get a transparent gel. Originally, the solution was opaque when the ethyl acetate was added. But, the opaque solution became a transparent gel in three minutes. We can see that the formation of gel is very fast. TEM and SEM images (Figure 2a, b, c, d, f) show the gel consists of nanowires. The length of nanowires is nearly dozens of micrometres. Furthermore, the nanowires have a lamellar structure which can be seen from the magnified TEM image (Figure 2b). The same result can be obtained from HADDF-STEM images (Figure 2c). By measuring the interlayer space in TEM image (Figure 2b), we found that the interlayer space is about 3 nm. X-ray energy dispersive spectroscopy (EDS) with HRTEM indicates the existence of nitrogen and tungsten all over the nanowires, which shows that the nanowires are composed of SEPs (Figure S3).

Figure 2.

Figure 2

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(a–b) TEM images of nanowires which were made up of (CTA)3(TBA)3P2W18O62. The inset shows the photo of gel formed by nanowires. (c–d) TEM images of nanowires which were made up of (CTA)3(TBA)3P2Mo18O62. The inset shows the photo of gel. (e) (high-angle annular dark-field scanning TEM) HAADF-STEM image of nanowires. (f) SEM image of nanowires.

To verify the structure of the nanowires, we slice them to observe the cross section of the nanowires under TEM characterization. We selected epoxy resin as embedding medium. Then curing process proceeded at 60°C. The slice process carried out under room temperature and cryoprocess wasn't needed. Figure 3a shows that the nanowires are circular. X-ray diffraction pattern (Figure 3c) of dried assemblies showed a layer spacing 3.27 nm which is in accordance with the result of TEM (Figure 2b). When the ethyl acetate was replaced by other esters, the sol could also be transformed into gel. And the structure of nanowires could be maintained. The photo of some typical gels is shown in Figure S4. When the esters were unsaturated esters having carbon-carbon double bond or esters with other functional groups, the gel would have more functionality. Thus this supramolecular gel is a good platform for POMs processing.

Figure 3.

Figure 3

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(a) TEM image of the cross section of the nanowires. (b) Magnified TEM images of the cross section. (c) Small Angle X-ray Diffraction of the nanowires. (d) Schematic drawing of the nanoroll.

The thermo and photo responsive behavior of the gel have been also studied. As demonstrated in Figure 4, we found that the gel transformed into sol when the gel was shaken, suggesting that the gel has a poor stability. Then we heated the sol to 70°C, which is close to the boiling point of the solvents, for one hour. The sol was again transformed into gel. Therefore, the hybrid gel was thermally stable. This behavior of the gel is similar to that of the copolymer gel37. Figure S5 shows the photochromic process of the gel. When the gel was irradiated for two hours, some blue dots occurred in the gel. With an increase in the irradiation time, the gel became dark blue and part of the gel shrunk to sol. The color of gel faded when it stayed for three hours in the air. The photochromic process is caused by the photo reduction of tungsten7.

Figure 4. Photo of the thermo responsive behavior of the gel.

Figure 4

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Then we used methyl methacrylate instead of ethyl acetate to form the gel, and a little amount of polymerization initiator was added into the methyl methacrylate. Then the polymerization of the gel occurred in the oven at 70°C. Afterwards we got the hybrid polymer (the inset photo of Figure S6) with POMs. Figure S6 shows the cross section of the hybrid polymer. The bright dots should be the cross section of the nanowires (Figure S6) and the hybrid polymer could keep the good reversible photochromism. Figure 5 shows the photochromic property of the hybrid polymer. As shown in the Figure 5a, when the hybrid polymer was irradiated for three hours, it became dark blue. The transmittance spectrum of the hybrid polymer before and after irradiation is shown in Figure 5c. When the blue polymer was stored in dark, the color of the polymer faded after 24 hours. It is obvious that the decoloration of gel is much faster than the polymer and the color change is reversible (Figure 5c). When the blue polymer was put into nitrogen atmosphere, the decoloration was much slower. On the basis of above results, we believe that oxygen is the key factor in decoloration. The much more oxygen in the gel than in the polymer leads to the much faster decoloration of the gel7.

Figure 5.

Figure 5

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(a) Reversible photochromism property of the hybrid polymer when irradiated with UV light (The hybrid polymer got from the polymerization of gel).(b) Transmittance spectra of the hybrid polymer before (black line) and after (blue line) irradiation. (c) The photochromic switching of the transmittance change (monitored at 715 nm) during consecutive cycles of UV irradiation and storage in the dark.

Since the gel can be polymerized when unsaturated ester replaced ethyl acetate, we tried to use electrospinning to process the gel. Although the immediately-formed gel has a low viscosity, it cannot be used for electrospinning directly. But we can still get a sticky hybrid polymer gel by polymerizing the gel.

According to the responsive behavior of gel, it can be transformed into sol when it is shaken. Then we got a spinnable feeding solution. After electrospinning, we got non-woven mats (optical images in Figure 6a,b) which consisted of ribbon-like fibers (Figure 6a,b). The possible reason for the formation of ribbon-like structure (Figure 6c) is that the concentration of polymer is too high38. Because of our good platform, it is much easier to get other morphologies of fiber through adjusting the time of polymerization. To characterize the mechanical properties of the non-woven mats, we used a wheel-shaped collector to get parallel fibers (Figure 6d) at 1600 rpm39. We studied the stress-strain behavior of the parallel fibers. In the tests, the orientation of the applied stress is parallel to the fiber arrangement direction. The loading speed is 1 mm/min. The tests were carried out at the room temperature which is about 20°C. The stress-strain curves of the fibrous membranes are shown in Figure 6. Young's modulus of the two membranes is 427.18 MPa (Figure 6e) and 542.55 MPa (Figure 6f). The Young's modulus values are all the average values within the elastic range. From these results it seems very clear that the good platform of supramolecular gel provides many advantages in the electrospinning.

Figure 6. SEM images and photographs of the fiber mats with different polyoxometalates gel.

Figure 6

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(a) CTA3TBA3P2W18O62 (b) CTA3TBA3P2Mo18O62. (c) Magnified SEM images of the fibers. (d) SEM image of parallel fibers. Stress-strain curves of fibrous membrane prepared by polymethyl methacrylate with (e) CTA3TBA3P2W18O62 (f) CTA3TBA3P2Mo18O62.

Discussion

In order to find out the gel formation process, we carried a time control experiment. During the formation of gel, we took the samples for TEM characterization at different times. Figure S7a was the TEM image when ethyl acetate had been added into butanone for 20 s. Many spheres and a few nanowires occurred. Ethyl acetate as a poor solvent resulted in the aggregation of SEPs. And this can explain why many spheres occurred in the opaque solution. After 40 s, the amount of nanowires increased and the amount of spheres decreased slowly (as shown in Figure S7b) and the flowability of the solution decreased. When ethyl acetate had been added for 60 s, more and more nanowires occurred. When the time was increased to 2 min, we could see the sample was constituted of nanowires and spheres in the TEM image (Figure S7d). After 3 min, the transparent gel (the inset photo of Figure 2a) formed and the TEM image was the same as Figure 2a. These results indicate the aggregations or assemblies in the solution change from spheres to nanowires. It is corresponding to the change from opaque solution to transparent gel. This process was caused by the rearrangement or self-assembly of SEPs. The diameter of nanowires is less than 100 nm, so the gel is transparent.

Moreover, other polyoxometalates have been tried to form gel. First of all, Wells-Dawson phosphomolybic acid (H6P2Mo18O62) was used to do the self-assembly. In the same condition, we got a yellow gel (the inset of Figure 2c) and TEM images (Figure 2c, d) show that the gel consists of nanorolls. But all attempts to Keggin POMs ended in failure. The results revealed that the structure of Wells-Dawson POM played a very important role in forming gel. We also tried to use monolacunary Wells-Dawson (K10P2W17O61·nH2O)40 and monosubstituted Wells-Dawson (K7P2W17VO62·nH2O)41 to form gel. Unfortunately, no gel was formed. So in the formation of gel, ideal Wells-Dawson POMs is essential. An alternative explanation is that the surface charge of monolacunary and monosubstituted Wells-Dawson POMs changed. We believe that all ideal Wells-Dawson POMs can be used to form gel besides phosphotungstate and phosphomolybic acid.

According to the XRD result, we can conclude the nanowires have a lamellar structure. To combine with the lamellar structure and the circular shape (Figure 3a, b), we think that nanorolls are more exact to describe the structure of assemblies than nanowires. And Figure 3d is a brief scheme of nanoroll.

We have proposed a hypothesis to explain why the SEPs can form gel by self-assembly. First, the SEPs self-assemble into long nanorolls. Then the nanorolls' entanglement subsequently leads to gel formation. This hypothesis could be supported by the time control experiments. As shown in Figure 7, the three-dimensional network in the gel was made up of nanorolls. The nanorolls were obtained from the self-assembly of the SEPs. As we mentioned above, one Wells-Dawson POM cluster was encapsulated by three CTAB molecules and three TBAB molecules. CTAB and TBAB molecules spaced at regular intervals. This kind of distribution leads to the SEPs rolls up to form nanorolls. The interaction between nanorolls may be the van der Waals force. However, this is difficult to test and verify.

Figure 7. A schematic representation of the possible formation of the transparent gel.

Figure 7

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In summary, by self-assembly we got a hybrid gel which was made up of nanorolls with lamellar structure. The gel was formed in 3 minutes, and it had thermo-responsive and photochromic properties as well. At the same time, the esters in this system could be substituted by unsaturated esters. So, the gel was very easy to be polymerized. Based on the fast formation and polymerizable properties of the gel, we got hybrid polymer. At the same time, the photochromic property and structure could also be preserved. Non-woven mats with greater mechanical stress were fabricated by electrospinning of the partially polymerized gel. Therefore, we believe that this supramolecular gel is a good platform for polyoxometalates processing.

Methods

Synthesis of SEPs

CTAB (0.91 g, 2.5 mmol) and TBAB (0.81 g, 2.5 mmol) were added into CHCl3 (20 mL), either K6P2W18O62·nH2O or H6P2W18O62·nH2O (0.8 mmol, synthesized according to reference42,43) was added into water (10 mL). After that, the organic phase was added into the solution of polyoxometalates with stirring. After one hour, the mixture was centrifuged at 10000 rpm for 8 min. Then the precipitates were washed 2 times by deionized water. In the end, the precipitates were dried at room temperature. The product was obtained as some powder.

Self-assembly

The product (20 mg) was dispersed in butanone (2 mL). Then ethyl acetate or other esters (1 mL) was added into the solution of butanone at room temperature. The ratio of butanone and esters changed when we used different esters in self-assembly.

Polymerization

First, benzoyl peroxide (BPO, 20 mg) was added into methyl methacrylate (1 mL). It was added into the butanone solution (1 mL) of SEPs. Methyl methacrylate was substituted for ethyl acetate to do the self-assembly. Then the assemblies were kept in the oven at 70°C for several hours.

Electrospinning

The gel with partial polymerization was shaken to become sol and it was loaded into a plastic syringe with a stainless steel needle. A piece of flat aluminium foil was used as an acceptor. The distance between the needle and the acceptor was 10 cm. And the voltage was 13 kV. The flow rate was about 1 mL/h. The electrospinning process was conducted in air. A wheel-shaped collector was used to get parallel fibers at 1600 rpm. The voltage and distance didn't change.

Author Contributions

P.L.H. carried out the experimental work, analyzed the data and wrote the paper. B.X., H.L.L., S.H., and F.S. helped with the design and experiments. X.W. conceived the whole experimental project, analyzed the data and wrote the paper.

Supplementary Material

Supplementary Information

Supporting information

srep01833-s1.pdf (1.9MB, pdf)

Acknowledgments

This work was supported by NSFC (91127040, 20971078, 21221062), and the State Key Project of Fundamental Research for Nanoscience and Nanotechnology (2011CB932402).

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Supplementary Materials

Supplementary Information

Supporting information

srep01833-s1.pdf (1.9MB, pdf)

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