Graphene is a 2-dimensional carbon material discovered by Professor Andre Geim et al. . It consists of a hexagonal array of
High-performance polymer composites can be fabricated by incorporating nano-fillers into polymer matrices [5,6]. Generally, carbon nanotubes (CNTs) have been used to fabricate high-performance polymer composites . However, graphene has already been experimentally shown to exhibit superior gas barrier and mechanical properties compared to CNTs .
The incorporation of graphene can reduce gas permeation through composite membranes by maximizing the gas-diffusion path-length . Various methods, such as Langmuir-Blodgtt film assembly, vacuum filtration and air-water interface collection, have been proposed for the fabrication of graphene films. However, the uniformity of the graphene films prepared by the methods mentioned above is inadequate to fabricate high barrier membranes. This is because of the incompletely interconnected networks between thin layer graphene sheets. The layer-by-layer (LBL) assembly method can be considered as a promising candidate for generating uniform graphene films.
LBL assembly, known as a nanofabrication technique most commonly using oppositely charged polyelectrolytes, has been used to prepare a variety of multifunctional thin films due to its simplicity, robustness and versatility [10,11]. LBL assembled films can be prepared by depositing alternately-charged polymer and nanoparticles onto a substrate with controlled
thickness via electrostatic attraction or hydrogen bonding. This precisely controlled deposition of ingredients has already been used to generate superior gas barrier films. LBL film properties providing high transparency and gas barrier properties can be precisely controlled by tailoring concentration, temperature, and pH of the polyelectrolyte solution [12-15].
Herein, we have presented a facile approach for preparing graphene composite films on polyimide (PI) membranes with effective gas barrier properties. Positively charged amino-phenyl functionalized grapheme oxide (APGO) is alternatively complexed with the negatively charged GO through an LBL assembly process. During this process, imidization can convert GO film to graphene film.
Natural Graphite powder (microcrystal grade, APS 2-15 μm, 99.9995% purity, metals basis) was purchased from Alfa Aesar. Nitrobenzene diazonium-tetrafluoroborates, phosphoric acid and ammonium hydroxide were purchased from Sigma- Aldrich (USA). The polyamic acid (PAA) was prepared via in situ polymerization. Pyromellitic dianhydride was purchased from Lonza (China); the 4, 4-oxidianiline, and 1-methyl-2-pyrrolidinone from Sigma-Aldrich (USA); and the 1,4-Diazabicyclo[2,2,2]octane from TCI (Japan). All chemicals were used as received; without further purification.
The oxidation of graphite was carried out following a modified Hummer’s method . GO (0.1 g) was immersed in H2SO4 (100 mL) and sonicated for 30 min; followed by the addition of 1.8 g of nitrobenzene diazonium-tetrafluoroborate. The mixture was magnetically stirred vigorously at 60℃ for 1 h. After cooling to room temperature, the mixture was diluted and washed with dimethylformamide. Finally, the product was washed with ethanol and dried at 60℃ for 24 h in a vacuum oven to get the nitro-phenyl functionalized GO (NPGO). Then, 0.1 g of dried NPGO was added to a solution of phosphoric acid (45 g) and DI-water (50 mL). The mixture was stirred at 115℃ for 6 h. After cooling to room temperature, the reactant mixture was transferred into a mixed solution of 200 mL of ammonium hydroxide and 100 mL of methanol. Next, the mixture was diluted with DI-water and stirred for 6 h for desalination. The APGO was washed with ethanol and dried at 60℃ for 24 h in a vacuum oven (Fig. 1).
Negatively charged GO and positively charged APGO solution were prepared using 18.2 MΩ DI-water at the concentration of 0.5 mg/mL. The pH value of each solution was maintained at approximately 10 using NaOH. Positively charged APGO solution was dropped on the PAA substrate the amount of water droplets sprayed through the spray gun, and then spin-coated at 3000 rpm for 40 s; followed by drying at 80℃. Negatively charged GO was deposited using the same methods. Ten deposition cycles of GO and AGPGO bi-layers were prepared on PAA films; followed by the buildup sequence of GO and APGO. The LBL-assembled reduced GO (rGO)/rAPGO/PI film was subjected to thermal curing of the PAA in an oven with steps of 100℃ and 200℃ for 1 h.
The introduction of chemical bonds and functional groups onto the graphene surface was confirmed by X-ray photoelectron microscopy (XPS, AXIS-NOVA, Kratos Inc., USA) and Raman spectroscopy (Lab RAM HR, Horiba, Japan).The barrier properties of the bare and coated PI films were also examined. The water-vapor transmission rat of bare-PI and coated-PI film was measured using a water vapor transmission analyzer (AQUATRAN Model 1, Mocon, USA). The oxygen transmission rate of the bare and coated PIs at 25℃ was measured using a gas transmission-rate tester (Toyoseiki, Japan). A flow of oxygen at 100 KPa was fed to one side of a 2.5 cm diameter film sample. The fractured cross-section was observed for analysis using scanning electron microscopy (NOVA NanoSEM, FEI, USA).
Amino-phenyl groups are formed on the surface of GO through the diazonium-salt reaction, which was confirmed by the XPS analysis. Fig. 2a shows the spectra of the XPS C1s original and fitted curves of GO. GO had four major peaks, with positions at 284.6, 286.6, 288.0 and 289.5 eV; which are attributed to the C=C, C-O, C=O and O-C=O species, respectively; which indicate that the oxidation of graphite intended by using Hummer’s method, occurred successfully. In the case of APGO, a new peak at 285.7 eV was observed, which is the C1s attributed to a C-N bond . This result demonstrates the formation of covalent bonds between amino-phenyl groups and GO. N1s also showed three peaks at 397.7, 399.2, and 405.2 eV, corresponding to C-N, -NH2, and Ar-NH2, respectively . The peak intensity of the -NH2 groups of APGO (Fig. 2d) is higher than that of NPGO (Fig. 2c), which reveals the reduction from -NO2 of NPGO to NH2. This
[Fig. 2.] X-ray photoelectron microscopy C1s spectra of GO (a), APGO (b), N1s spectra of NPGO (c) and APGO (d). GO: graphene oxide, APGO: amino-phenyl functionalized GO, NPGO: nitro-phenyl functionalized GO.
clearly confirms the presence of Ar-NH2 groups on the surface of graphene via the diazonium-salt reaction.
Fig. 3 shows the Raman spectra of Gr, GO and APGO. The Raman spectrum of APGO displays two strong peaks at 1580 and at 1350 cm-1, corresponding to the D and G-bands, respectively. The G-band is attributed to the first order scattering of the E2g phonon of the
Barrier properties of pure PI and rGO/rAPGO/PI
The ratio of ID/IG of APGO was increased from 0.86 to 1.05 after amino-phenyl functionalization. This result also clearly indicates that the amino-phenyl functional group was covalently bonded onto the surface of the GO after surface functionalization.
Combining graphene with the polymer matrix made it possible to produce barrier polymer-composite films. The 2-dimensional structure of the graphene can improve the barrier properties of the polymer matrix. Herein, we investigated the water vapor transmission rate (WVTR) and oxygen transmission rate (OTR), of the prepared (rGO/rAPGO)10 deposited PI film (rGO/rAPGO/PI) and of the pure PI film. The WVTR and OTR of these samples are summarized in Table 1. In the case of WVTR, the transmission rate of the rGO/rAPGO/PI-composite film is higher than that of pure PI film. The WVTR depends mainly on the hydrophilic or hydrophobic characteristics of materials. The oxygen groups of GO and APGO cannot be completely removed during the imidization process. The remaining oxygen groups can still make membranes hydrophilic, compared to that of pure PI. Therefore, the WVTR of rGO/rAPGO/PI is higher than that of PI. However, OTR is strongly dependent on the barrier effect of the fillers. The OTR of the rGO/rAPGO/PI composite showed about 60% decrease compared that of pure PI. The large aspect-ratio of graphene multilayers can maximize the diffusion length of gaseous molecules through the composites; in what is called a “tortuous path” [23,24]. Therefore, PI composites with rGO and rAPGO should exhibit lower OTR values than that of pure PI due to the barrier effect of the graphene film on the PI surface.
PI-graphene composite films were produced using a LBL assembly technique. The water-vapor barrier property of the composite membranes was not enhanced due to the hydrophilic nature of the graphene layers; while the oxygen barrier property was improved by 60% compared to pure PI membranes. This result indicates that water vapor transmission rate is strongly affected by the hydrophilic quality of the materials, and that the oxygen barrier property is affected by the barrier effect of fillers.