Poly (ionic liquid)-Based Breath Figure Films: A New Kind of Honeycomb Porous Films with Great Extendable Capability

In this work, we reported a new method for the convenient fabrication of various functional porous films, which cannot be directly generated using breath figures (BFs). A series of polystyrene-b-poly (ionic liquid) (PS-b-PIL) block copolymers were employed for BFs process for the first time. It was found that PS-b-PIL could form well-defined BFs porous structure. Remarkably, the described PS-b-PIL copolymers are prone to form hierarchical structure, and the formed pore structure is strongly dependent on the used experimental parameters. Importantly, we found that the anion exchange could provide as an effective means, by which the porous films could be further and facilely converted into other functional films. As a demonstration, in our case, porous films with different surface (hydrophilic and hydrophobic) property, porous polydopamine films decorated with Au nanoparticles or glutathione and porous SiO2 films were prepared by using different counteranions as well as further conversion. Due to the unlimited combination of cation and anion in ionic liquid moiety, all the results indicate that the BFs films generated by using PS-PIL could serve as a platform to access various functional porous films by a simple counteranion exchange, showing a great extendable capability.

by depositing silver on pincushion films. These periodically arranged structures of noble metals have proved to be good candidates as substrates for SERS 15 . Nevertheless, the strategy with great flexibility and expendability to access different BFs porous films, which cannot be directly generated using BFs process, is still limited.
In this work, based on a simple counteranion exchange reaction of ionic liquid moiety we developed a new approach for convenient fabrication of various functional porous films, particularly which cannot be directly generated using BFs process. Owing to their unique physical and chemical properties, polymerized ionic liquids (PILs) are emerging as a new type of materials showing great potential applications [16][17][18] . PILs combine the advantages of ionic liquid and polymers. One of the most distinct characteristics of PILs is that their properties can be facilely manipulated by a simple ion exchange reaction, providing a convenient and efficient means to access different polymeric materials. Additionally, block copolymer is an important type of amphiphilic molecules, which is suitable for BFs process and at the same time can form various nanostructures by self-assembly or micro-phase separation 17,18 . Thus, it is conceivable that the combination of both unique properties of IL and copolymer could enable the development of a new kind of BFs porous films, from which the fabrication of various other porous materials can be easily realized by simple ion-exchange or other followed reaction. To prove our concept, a series of polystyrene-b-poly (ionic liquid) (PS-b-PIL) block copolymers with various block ratios was synthesized and employed for BFs process for the first time (Fig. 1). Indeed, it was found that all of the synthesized amphiphilic PS-b-PIL block copolymers could stabilize water droplets during BFs process and produce well-defined BFs porous films. Remarkably, due to the salt feature of ionic liquid moiety and the resultant osmotic pressure, the described PS-b-PIL copolymers are prone to form hierarchical structure compared to the reported conventional polymers 11 , and the formed porous structure is strongly dependent on the used experimental parameters, including block ratio, solvent concentration, relative humidity, water pretreatment and post-treatment and salt solution pretreatment. The pore size and film morphology of honeycomb films could also be adjusted by post-treatment by swelling in hot water. Importantly, we found that the anion exchange could provide an effective means, by which the as-synthesized porous films from PS-b-PIL copolymers could be further and facilely converted into other functional films. As a demonstration, in our case, porous films with different surface (hydrophilic and hydrophobic) property, porous polydopamine films decorated with Au or glutathione and porous SiO 2 films were prepared by using different counteranions as well as further conversion. All the results described here indicate that owing to the unlimited combination of cation and anion in ionic liquid moiety, the BFs films generated by using PS-b-PIL could serve as a versatile platform to access various functional porous films by a simple counteranion exchange, showing great extendable capability. Therefore, the proposed method here is very attractive for the preparation of functional and scalable films by the use of polystyrene-b-poly (ionic liquid) block copolymers and the combination of BFs and ion exchange.

Results
Fabrication of hierarchically structured polymer films. We synthesized a variety of polymerized ionic liquid block copolymers by completely ionization of polystyrene-b-poly (chloromethyl styrene) (PS-b-PCMS) diblock copolymers synthesized by RAFT according to previously reported procedures [20][21][22][23][24] .  Four types of polymerized ionic liquid block copolymers named #1 PS252-b-PIL40, #2 PS264-b-PIL60, #3 PS557-b-PIL150 and #4 PS190-b-PIL95 were produced by RAFT and ionization (Fig. 2). Relative molecular weight and molecular weight distribution of PS-b-PCMS were determined by 1 H NMR and GPC. Relative molecular weight and molecular weight distribution of PS-b-PIL were calculated according the results described above after the ionization of PCMS, which are 35.0-93.0 kg/mol and 1.11-1.18, respectively (Table 1). These four types of PS-b-PIL with different ratios of PIL/PS (f comb = 0.2, 0.3, 0.4 and 0.5) were used in the following breath figures process. It is generally accepted that the honeycomb porous structures are generated in following three steps during breath figures process 6,7 . Firstly, the solution coated on a substrate is cooled through solvent evaporation, and surrounding water vapor is condensed, producing small and disordered water drops on the surface of the solution. Secondly, the water droplets growth and self-assemble to from a closely packed and regular droplet array on the surface of the solution. Finally, the solvent and water drops evaporate successively, affording regular porous honeycomb film. The same mechanism should be suitable for the interpretation of the formation of the porous structures observed in our case.
Morphological Characterization of honeycomb films. In this study, four types of PS-b-PIL with different PIL chain length were selected to prepare honeycomb porous membranes for the first time. PS-b-PIL block copolymers are quite unique since their distinct chemical structures are expected to have different performance during breath figures process, thus probably producing films with various interesting structures and morphologies. Due to the salt feature of ionic liquid moiety and the resultant osmotic pressure, the described PS-b-PIL copolymers are prone to form hierarchical structure which is different from the reported conventional polymers 11 .The introduction of PS-b-PIL in breath figures can give a micro honeycomb structure and a nano-scale suborder on the wall of honeycomb films. The formed porous structure is strongly dependent on many experimental parameters.
Breath figures process was generally performed in a chamber with steady temperature and relative humidity. During the breath figures process, solvent evaporated fast and water vapor condensed on the surface of the solution. The imprint of water drops on the solution and micelles of PS-b-PIL in the solution offered the films ordered honeycomb patterns and hierarchical structures. It is the first time to introduce imidazolium-functionalized poly (ionic liquid) block copolymer into breath figures. The obtained morphologies herein are quite different with that reported before 11 . The formation of a nano-scaled suborder was observed due to salt feature of ionic liquid moiety and the resultant osmotic pressure. The obtained honeycomb films with different ratios of PIL/PS showed different morphologies (Fig. 3) with the pore size of 0.8-2 μm in diameter.
For the morphology of #1 PS252-b-PIL40, the pore distribution is regular with pore size of 2 μm and only slight nano structures in the pores were found. However, we can find obvious nano structures (50-100 nm) on the wall and inside the pore of honeycomb films of #2 PS264-b-PIL60 while the pore size decreased to 0.8 μm.
From the cross section of #2, we can see layers of honeycomb films increased to 5 or 6 layers while for other three samples, only single layer were found. The pore sizes of #3 PS557-b-PIL150 and #4 PS190-b-PIL95 are about 2.4 um and 1 um, respectively. Nano structures on and inside the honeycomb films is about 20 nm. These structures are quite different from honeycomb films reported before 26 . We further compared the hierarchically structured honeycomb films generated from #2 PS264-b-PIL60 and #4 PS190-b-PIL95 (Fig. 4). The pore of #2 is more regular and nanostructures on and inside the honeycomb films is bigger than that of #4. The morphology and pore structure of PS-b-PIL honeycomb films were affected by many factors such as polymer concentration, block ratio, relative humidity, water saturation. The influence of these factors were systematically studied.
For the influence of polymer concentration on the pore structure and morphology of the porous BFs films, a series of #4 PS190-b-PIL95 solutions with different concentrations (0.1 wt%, 0.3 wt%, 0.5 wt% and 0.7 wt%) were used to fabricate films ( Fig. 5a-h). When the concentration is 0.3 wt%, we can get regular honeycomb film with rich and regular nanostructures. When the solution concentration is lower to 0.1 wt% or higher to 0.5 and 0.7 wt%, the honeycomb films are irregular. These phenomena can be explained by the interaction between water vapor and polymer. Low concentration of polymer in the solution cannot provide sufficient number amphiphilic molecules for the stabilization of water droplets while high concentration of polymer renders the lack of solvent to evaporate for reducing the temperature, leading to that there is not enough water droplet to condense and the water droplet cannot arrange well on the solution 27 .
Relative humidity that could be adjusted by humidity detector in the chamber also has a big impact on the morphology of the honeycomb film. The mutual effect between the PIL and the relative humidity was responsible for the subtle equilibrium during the BFs process, which led to regular pores at low humidity (35-45%) and prevented high pores regularity at high humidity (above 55%), as depicted in Fig. 5a1-h1. Honeycomb films generated using #4 PS190-b-PIL95 at humidity of 35% show regular pores of 1 μm. As the humidity increases to 45%, more regular pores of 1 μm were generated. When we further increased the relative humidity to 55% and 65%, the pores were extensively large and their size were no longer uniform, totally blemishing the honeycomb porous arrangement. During breath figures process, the pores generated in honeycomb films were due to water droplets template, and these water droplets came from the surrounding humid environment 7 . Hence, the relative humidity has a big influence on the morphology of the honeycomb film. At relative lower humidity (35-45%), these water droplets can increase in size before polymer precipitation into solid layers. The polymers around the droplets can stabilize the water droplets very well. As a result, regular porous structure in polymer film is formed. However, when the relative humidity was too high (for example above 55%), the water droplets condensed on the surface may become surplus. In such case, a large number of the formed droplets could easily and rapidly coalesce before the occurrence of the precipitation of the polymer around the droplets, thus leading to the formation of irregular and larger pore structure. In agreement with the observation in our work, the similar phenomenon was also found in literature 26 .
Since the honeycomb films were fabricated by PS-b-PIL, which owned the properties of ionic liquids, the morphology of the film was also considerably influenced by water content and osmotic pressure, which could be adjusted by adding different amounts of deionized water and saturated sodium chloride solution. During the process of breath figures of PS-b-PIL, different water contents in the solution and the differences of osmotic pressure between the inner and outer water phase have played an important role during the formation of honeycomb films. From Fig. 6a-d, various honeycomb films were obtained from precursor solution by adding 0 μL, 3 μL, 6 μL and 9 μL water. We can obviously see that water content has an important impact on the structure and morphology of honeycomb film. When we adding 3 μL and 6 μL deionized water, the films are more regular, and the pore size is about 1.2 μm. However, when we adding 9 μL deionized water, film morphology is irregular and the pore sizes are non-uniform. These result proved the water content has a big influence on honeycomb films fabricated by breath figures. Besides water content, we also studied the influence of osmotic pressure by adding different amount of saturated sodium chloride solution. From Fig. 6e-f, honeycomb films were obtained from precursor solution with adding 0 mg, 3 mg, 6 mg and 9 mg sodium chloride solution. We find that solutions without adding saturated sodium chloride solution yield breathe figures structures with single layer honeycomb films, as shown in Fig. 6e. On the contrary, PS-b-PIL solutions containing salt yield a multi-layer film with obvious hierarchical pore structure on the wall of honeycomb films (Fig. 6f-h). We tried to figure out why adjusting the above two effects can exhibit such morphologies of the films. Chloroform solution of polymer is usually employed for breath figures process. In our case, the used polymer is a poly(ionic liquid) containing block copolymer (PS-b-PIL), which shows distinct amphiphilic feature and can be used as a polymeric surfactant to form stable W/O emulsions. Thus, in our work, besides the chloroform solution of PS-b-PIL, the PS-b-PIL stabilized emulsions of water-chloroform and saturated NaCl solution-chloroform were also used for breath figures process with the expectation of creating new pore structure. Interestingly, we found that the water content in the used water-chloroform emulsions has an important influence on the formation of the pore structure in the resulting PS-b-PIL polymer films. When the water content is relatively small, the pore structure formed is generally irregular. Upon the increase of the amount of water, the pore structure became uniform at first, and then the further increase of water amount resulted in the destruction of the water droplets template arrangement, affording relative large and irregular pore structure. In the case of saturated NaCl-chloroform emulsion, it was found that the amount of saturated sodium chloride solution in the used emulsion has significant influence on the formation of the pore structure in the resulting PS-b-PIL polymer films. Different from the BFs process of using normal PS-b-PIL chloroform solution, probably due to the presence of osmotic pressure between the inner NaCl water phase and outer condensed water, the addition of saturated NaCl solution in PS-b-PIL chloroform could lead to dramatic increase of the pores in the formed polymer films. Especially, when increased amount of saturated NaCl solution was used, the polymer films with interconnected pore structure were obtained. The exact mechanism underlying for the evolution of pore structure is still not clear, and further more experiments are required.
Poly (ionic liquid) block copolymer owned the properties of block copolymers and thus the morphology of the film was also considerably affected by micro-phase separation of block copolymer. Hot water was chosen as solvent to swell the honeycomb films because of the different interactions of blocks with hot water. After the process of breath figures, the honeycomb films of PS-b-PIL were put into hot water at 90 °C for different times. For further study the effects of block ratio, water pretreatment and post-treatment on the films, we selected films with and without water pretreatment to carry out the next treatment. From Fig. 7, porous honeycomb films prepared by BFs from sample #2 PS264-b-PIL60 and #4 PS190-b-PIL95 were pretreated without or with water saturation and swelled in hot water for different time. Honeycomb films of #2 PS264-b-PIL60 were pretreated without and with water saturation after swelling in hot water for 0 to 4 h (Fig. 7a1-e2). The films without water saturation showed a big change on nanostructure than films with water saturation. When films swelled for 3 and 4 hours, their nanostructure became soft. As time increased to 5 hours, the nanostructure disappeared and only cracked texture was found on the wall of honeycomb films (Fig. 8a,b). Honeycomb films of #4 PS190-b-PIL95, which is pretreated without and with water saturation after swelling in hot water for 0 to 4 h (Fig. 7a3-e3). The films without and with water saturation both showed big changes on nanostructure. When swelling time is 4 hours for films without water pretreatment and 3 or 4 hours for films with water pretreatment, the honeycomb structure also cracked. With swelling time for 3 hours, the nanostructure cracked. We can see the details in Fig. 8c,d. These results can be understood that the different length of the poly (ionic liquid) segments led to different interaction when swelling in hot water. A more thorough mechanism will continue to be studied in our future work.
The generation of membrane containing desired pore and pore distribution by BFs is a multi-factor process. Many parameters can adjust the pore size, such as different chain length, polymer concentrations, relative humidity water pre or post treatment and salt pretreatment and osmotic pressure.  Fig. 9. After the complete exchange, honeycomb films of PS-b-PIL-OH changed little and the nanostructure kept well on the film. However, for honeycomb films of PS-b-PIL-BF 4 and PS-b-PIL-Tf 2 N, nanostructure on their films disappeared. After ionic exchange reaction for 24 hours, the ion may be not exchanged completely. While for 48 hours, the ionic exchange reaction is obviously completed, ATR-FTIR and EDS can further prove this (Fig. 10A,B). All the membranes show the absorption peaks at 1447 cm −1 and 1656 cm −1 , which are the vibrational mode of the benzene ring and imidazolium cations. Line b in Fig. 10A shows a wide peak between 3700-3150 cm −1 , which is due to the stretching  Fig. 10B, all the polymerized ionic liquids contained elements of corresponding anions, which further confirms the successful anion exchange of the PS-b-PIL block copolymers [29][30][31][32][33][34] . The hydrophilic and hydrophobic property of the films can be determined by contact angle (Fig. 10C). After anion exchange from Cl − to OH − , the contact angle changed from 101° to 55° and the hydrophilic property greatly increased. When the counteranions were BF 4 − and Tf 2 N − , the honeycomb films were more hydrophobic.   Fig. 11a-f. The changing of morphology of honeycomb films confirm the above findings (Fig. 11b,c). From the TEM images, we can see that the size of gold nanoparticles is about 5 nm ± 0.8 nm with no obvious aggregation.
The coating of GSH altered little to the pore structure (Fig. 11g,h). The introduction of GSH on the film was confirmed by ATR-FITR and EDX analysis of PS-b-PIL-OH, PS-b-PIL-OH@PDA, PS-b-PIL-OH@PDA@GSH and GSH membranes (Fig. 12). The formation of PDA on PS-b-PIL-OH can be corroborated by the appearance of absorption peak at 1630 cm −1 , attributed to the stretching vibration of the C=C indole group, which is generated after polymerization reaction (Fig. 12A). In the 3500 cm −1 region, a broad absorption peak belonged to the O-H groups. Introduction of glutathione (GSH) on the films was also confirmed by ATR-FTIR spectroscopy. The characteristic peaks of 2930 cm −1 (C-H stretching), 1648 cm −1 (cysteine-carbonyl), and 1605 cm −1 (glutamic acid-carbonyl) proved the coating of GSH on PS-b-PIL-OH@PDA films. Thiol groups tightly anchored GSH. The ATR-FTIR peak at 2532 cm −1 for S-H stretching disappearing. EDX in Fig. 12B can be seen that all the functionalized of polymerized ionic liquids films are composed of desired characteristic element, which further confirms the successful modification GSH on PS-b-PIL-OH@PDA films 35,36 .
PS-b-PIL-OH@SiO 2 composite films were successfully fabricated in our work (Fig. 13b). Attributed to the ionic exchange by OH − , the films were grafted with base catalytic groups. Afterwards, we got the regular SiO 2 honeycomb structured films. (Fig. 13c). The well-kept honeycomb structure proved that it is a very convenient and extendible approach to extend honeycomb films. ATR-FITR clearly confirms the successful hydrolysis of TEOS (Fig. 13d). For the PS-b-PIL-OH@SiO 2 composite films and SiO 2 honeycomb films, the characteristic peak of Si-O-Si asymmetric stretching vibration appeared at 1066 cm −1 . And the characteristic peaks of -OH absorption peak of Si-OH appeared at 3000 cm −1 to 3600 cm −1 . The characteristic peak of Si-O-Si symmetric stretching vibration and SiO 2 tetrahedron also appeared at 960 cm −1 and 784 cm −1 .
Due to common commercial use of Congo red as a colorant in dyeing industry, the research of its degradation is necessary 37,38 . Herein honeycomb films decorated with Au nanoparticles were used to photocatalytic degradation of Congo red dye. After 10 min, the concentration of Congo red significantly decreased, showing an obvious degradation (Fig. 14a). From Fig. 14b, the degradation of CR by our functional films fast reached maximum value with high efficiency while the degradation in the control experiment without adding films is almost zero. In order to research the stability of the films, we studied degradation efficiency of membrane for six consecutive cycles. The photocatalytic efficiency keeps well after six cycles (Fig. 14c). The photographs of original CR solution and CR solution after photocatalytic degradation in the absences or presences of gold films are shown in Fig. 14d, and the difference is obvious.

Conclusions
In summary, a series of polystyrene-b-poly (ionic liquid) (PS-b-PIL) block copolymers were synthesized by us, and their formation behaviour of honeycomb films by BFs approach under different conditions were systematically studied for the first time. It was found that all the synthesized PS-b-PIL copolymers could form well-defined honeycomb porous films, but their morphologies are strongly dependent on the using experimental conditions, including block ratio, solvent concentration, relative humidity, water and salt solution pretreatment. Remarkably, due to the salt feature of ionic liquid moiety and the resultant osmotic pressure as well as the micro-phase separation of block copolymer, the described PS-b-PIL are prone to form unique hierarchical structure compared to the conventional polymers. Importantly, we found that the anion exchange could provide an effective means, by which the as-synthesized BFs porous films from PS-b-PIL copolymers could be further converted to conveniently and facilely access other films. As a demonstration, a series of ordered porous films with different surface (hydrophilic and hydrophobic) property, porous SiO 2 film, porous polydopamine films with decorated Au or glutathione was successfully prepared by using different counteranions as well as further conversion. Due to the unlimited combination of cation and anion in ionic liquid moiety, all the results described here indicate that the BFs films generated by using PS-b-PIL could serve as a platform to access various functional porous films by a simple counteranion exchange. Especially, based on the concept of "task-specific" ionic exchange, we can introduce varieties of functional anions into PS-b-PIL BFs porous films by anion-exchange reactions, leading to a broad spectrum of new porous films with desired functions. Thus, we believe the method reported here would provide a new strategy  with a great flexibility and expendability to access different BFs porous films, which cannot be directly generated by using BFs approach.

Methods
Materials and methods. Styrene, vinyl benzyl chloride, 2,2-azobisisobutyronitrile (AIBN), ethanol, glutathione (GSH), dopamine, chloroauric acid, sodium hydroxide, TEOS, Congo red, deionized water, chloroform and DMF were bought from the chemical suppliers. Unless otherwise stated, all the chemicals were used without further purification. Vinyl benzyl chloride and styrene were distilled under reduced pressure before use. AIBN was purified by recrystallization three times from ethanol. Glass substrates were cut to 1 × 1 cm 2 and were cleaned prior to use in piranha solution (7:3 v/v of H 2 SO 4 /H 2 O 2 ) and washed three times with deionized water and ethanol, then dried with N 2 .
Synthetic procedures. Synthesis of PS-b-PIL block copolymer. The synthesis of a variety of poly (ionic liquid) block copolymers with imidazolium-functionalization was carried out according to reported procedures, denoted PS-b-PIL 19 . Firstly, polystyrene-b-poly (chloromethyl styrene) (PS-b-PCMS) block copolymers created by the stepwise RAFT of styrene and chloromethyl styrene (CMS) [20][21][22][23] . Secondly, PS-b-PCMS were quaternized here to get an imidazolium-functionalized charged block with a certain concentration of methylimidazole in DMF at 80 °C 24,25 . The characterization of M n value and polydispersity for these samples was performed by 1 H NMR and GPC.
Fabrication of hierarchically structured polymer films. The synthesized PS-b-PIL here was dissolved in mixed solvent (chloroform/methanol (20:1, v/v)), and magnetic stirred to get 0.3 wt% homogeneous solution. The solutions were filtered by 0.1 μm Millipore membrane before use. The preparation procedure of BFs process was carried out in a constant temperature and a built-in electric fan was used to adjust the humidity. About 30 μL solution was dropped on glass substrate under certain relative humidity conditions at 25 °C. After solvent evaporate completely, the regular porous honeycomb films were removed from the chamber. The films were allowed to air-dry in the oven overnight at room temperature. To the PS-b-PIL solution was added a certain amount of deionized water or sodium chloride saturated solution to yield 0.3 wt% polymer solutions with different water content and osmotic pressure after magnetic stirring for several hours. The following steps are the same as above. Fabrication of hierarchically structured polymer films with different counter anions. Honeycomb PS-b-PIL films with different counter anions were obtained via anion exchange. Original films with chloride form were soaked in the corresponding salt aqueous solution such as potassium hydroxide solution (0.1 mol/L), sodium tetrafluoroborate solution (0.1 mol/L) and bistrifluoromethanesulfonimide lithium solution (0.1 mol/L) at ambient temperature for 24 h or 48 h. The converted films were washed with deionized water for three times. After washing, films were put into oven at 40 °C overnight and then films with OH − , BF 4 − and Tf 2 N − were gotten.
Fabrication of functional honeycomb structured films. PIL with OH − honeycomb porous films were put into 0.2 mg/mL dopamine aqueous solution overnight. Then these films were washed with deionized for three several times. Honeycomb films coated with polymerized dopamine (PDA) were put into 0.02 mol/L chloroauric acid aqueous solution overnight. The pH value was adjusted to 8 with the use of triethylamine. The obtained films were washed several times with water, and then dried in the oven. Honeycomb films coated with PDA were put into 0.02 mol/L glutathione aqueous solution overnight. The pH value was also adjusted to 8 with the use of triethylamine. The obtained films were washed several times with water, and then dried in the oven.
Fabrication of ordered SiO 2 honeycomb structures. The ordered SiO 2 honeycomb structures were fabricated by a simple process. Tetraethyl orthosilicate (0.52 g) was dissolved in absolute ethyl alcohol (5 g), and then deionized water (1.08 g) was dripped into the above mixture solution. After mixing uniformly, honeycomb films of PS-b-PIL-OH were immersed in the above solution. After 48 h, the films were taken out and washed with absolute ethyl alcohol for three times. The SiO 2 /PS-b-PIL-OH composite films were immersed in CH 2 Cl 2 solution to remove the PS-b-PIL. The obtained SiO 2 honeycomb structures were washed with CH 2 Cl 2 for three times, and then dried in oven.
Degradation of azo dyes. The photocatalytic application of the honeycomb films coated with gold nanoparticles was used for Congo red degradation. Films coated with gold nanoparticles (10 mg) and excess NaBH 4 (110 mg) were put in 200 mL CR solution (100 mg/mL) in conical flask with magnetic stirring. After uniform mixing, put the above sample under ultraviolet light. The control experiments were performed in the group without the addition of the catalytic films. The degradation rate of CR was calculated by the absorbance at 498 nm (maximum characteristic absorption peak of Congo red).
Characterization. 1 H NMR spectra were obtained using a JEOL JNM-ECA300 at 300 MHz with CDCl 3 .
Gel permeation chromatography (GPC) was performed by a set of a Waters 515 HPLC pump. The surface pore structure and morphologies of the honeycomb films were detected by a field emission scanning electron microscopy (FE-SEM, 10 kV, SU-8010) with energy dispersive X-ray spectrometry (EDS, 15 kV). Film samples were pre-coated with platinum before observed. The elements on the films were determined by SEM-EDS. Membrane morphologies and structures were studied by transmission electronic microscope (TEM, 80 KV, JEM 2010). The chemical structures of the coated polymer films were characterized by attenuated total reflection-Fourier transform infrared spectra in the range of 600-4000 cm −1 (ATR-FTIR, Bruker VERTEX70). The films were pre-treated in oven at 80 °C all-night before use. UV-Vis spectra were observed on PerkinElmer Lambda35 spectrometer.