Layer-by-layer assembled graphene oxide films and barrier properties of thermally reduced graphene oxide membranes
Layer-by-layer assembled graphene oxide films and barrier properties of thermally reduced graphene oxide membranes
Carbon letters. 2013. Oct, 14(4): 247-250
Copyright ©2013, Korean Carbon Society
This is an Open Access article distributedunder the terms of the Creative CommonsAttribution Non-Commercial License( which permits unrestrictednon-commercial use, distribution, andreproduction in any medium, providedthe original work is properly cited.
  • Received : August 15, 2013
  • Accepted : October 05, 2013
  • Published : October 31, 2013
Export by style
Cited by
About the Authors
Seon-Guk, Kim
Department of BIN Fusion Technology and Department of Polymer and Nano Science and Technology, Chonbuk National University, Jeonju, 561-759, Korea
Ok-Kyung, Park
Department of BIN Fusion Technology and Department of Polymer and Nano Science and Technology, Chonbuk National University, Jeonju, 561-759, Korea
Joong Hee, Lee
Department of BIN Fusion Technology and Department of Polymer and Nano Science and Technology, Chonbuk National University, Jeonju, 561-759, Korea
Bon-Cheol, Ku
Carbon Convergence Materials Research Center, Institute of Advanced Composites Materials, Korea Institute of Science and Technology, Wanju 565-905, Korea

In this study, we present a facile method of fabricating graphene oxide (GO) films on the surface of polyimide (PI) via layer-by-layer (LBL) assembly of charged GO. The positively charged amino-phenyl functionalized GO (APGO) is alternatively complexed with the negatively charged GO through an electrostatic LBL assembly process. Furthermore, we investigated the water vapor transmission rate and oxygen transmission rate of the prepared (reduced GO [rGO]/rAPGO) 10 deposited PI film (rGO/rAPGO/PI) and pure PI film. The water vapor transmission rate of the GO and APGO-coated PI composite film was increased due to the intrinsically hydrophilic property of the charged composite films. However, the oxygen transmission rate was decreased from 220 to 78 cm 3 /m 2 ·day·atm, due to the barrier effect of the graphene films on the PI surface. Since the proposed method allows for large-scale production of graphene films, it is considered to have potential for utilization in various applications.
1. Introduction
Graphene is a 2-dimensional carbon material discovered by Professor Andre Geim et al. [1] . It consists of a hexagonal array of sp 2 -bonded carbon atoms. The unique properties of graphene provide potential uses for a wide range of applications including nano-electronics, super-capacitors, hydrogen storage and nanocomposite [1 - 4] .
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 [7] . However, graphene has already been experimentally shown to exhibit superior gas barrier and mechanical properties compared to CNTs [8] .
The incorporation of graphene can reduce gas permeation through composite membranes by maximizing the gas-diffusion path-length [9] . 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
Lager Image
Schematic representation of amino-phenyl functionalized graphene oxide (APGO). NPGO: nitro-phenyl functionalized GO.
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.
2. Experimental
- 2.1. Materials
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.
- 2.2. Preparation of APGO
The oxidation of graphite was carried out following a modified Hummer’s method [16] . GO (0.1 g) was immersed in H 2 SO 4 (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 ).
- 2.3. LBL assembly film-fabrication
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.
- 2.4. Characterization
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).
3. Results and Discussion
Amino-phenyl groups are formed on the surface of GO through the diazonium-salt reaction, which was confirmed by the XPS analysis. Fig. 2 a 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 [17] . 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, -NH 2 , and Ar-NH 2 , respectively [18] . The peak intensity of the -NH 2 groups of APGO ( Fig. 2 d) is higher than that of NPGO ( Fig. 2 c), which reveals the reduction from -NO 2 of NPGO to NH 2 . This
Lager Image
X-ray photoelectron microscopy C1s spectra of GO (a), APGO (b), N1s spectra of NPGO (c) and APGO (d). GO: graphene oxide, APGO: amino-phenylfunctionalized GO, NPGO: nitro-phenyl functionalized GO.
Lager Image
Raman spectra and ID/IG ratio of graphite, graphene oxide (GO)and amino-phenyl functionalized GO (APGO).
clearly confirms the presence of Ar-NH 2 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 E 2g phonon of the sp 2 carbon-carbon bond; while the D-band represents the defect sites associated with vacancies and grain boundaries [19 , 20] . For the diazonium-salt reaction, the sp 2 of a carbon bond is converted to the sp 3 -hybridized carbon atom. Therefore, the intensity ratio of I D /I G provides direct evidence of the degree of functionalization [21 , 22] .
Barrier properties of pure PI and rGO/rAPGO/PIPI: polyimide, rGO: reduced graphene oxide, rAPGO: reduced aminophenyl functionalized GO.
Lager Image
Barrier properties of pure PI and rGO/rAPGO/PI PI: polyimide, rGO: reduced graphene oxide, rAPGO: reduced aminophenyl functionalized GO.
The ratio of I D /I G 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.
4. Conclusions
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.
This work was supported by a grant from the Korea Instituteof Science and Technology (KIST) Institutional Program, andby the Converging Research Center Program through the Ministryof Science, ICT & Future Planning.
Nair RR , Blake P , Grigorenko AN , Novoselov KS , Booth TJ , Stauber T , Peres NMR , Geim AK (2008) Fine structure constant defines visualtransparency of graphene. Science 320 1308 -    DOI : 10.1126/science.1156965
Pham VH , Cuong TV , Nguyen-Phan T-D , Pham HD , Kim EJ , Hur SH , Shin EW , Kim S , Chung JS (2010) One-step synthesis of superior dispersionof chemically converted graphene in organic solvents. Chem Commun 46 4375 -    DOI : 10.1039/c0cc00363h
Huang W , Ouyang X , Lee LJ (2012) High-performance nanopapers basedon benzenesulfonic functionalized graphenes. ACS Nano 6 10178 -    DOI : 10.1021/nn303917p
Huang P , Zhu H , Jing L , Zhao Y , Gao X (2011) Graphene covalently bindingaryl groups: conductivity increases rather than decreases. ACS Nano 5 7945 -    DOI : 10.1021/nn2023232
Huang X , Qi X , Boey F , Zhang H (2012) Graphene-based composites. Chem Soc Rev 41 666 -    DOI : 10.1039/C1CS15078B
Chae BJ , Kim DH , Jeong IS , Hahn JR , Ku BC (2012) Electrical andthermal properties of poly(p-phenylene sulfide) reduced graphiteoxide nanocomposites. Carbon Lett 13 221 -    DOI : 10.5714/CL.2012.13.4.221
Koerner H , Price G , Pearce NA , Alexander M , Vaia RA (2004) Remotely actuated polymer nanocomposites?stress-recovery of carbonnanotube-filled thermoplastic elastomers. Nat Mater 3 115 -    DOI : 10.1038/nmat1059
Kim H , Miura Y , Macosko CW (2010) Graphene/polyurethane nanocompositesfor improved gas barrier and electrical conductivity. Chem Mater 22 3441 -    DOI : 10.1021/cm100477v
Huang HD , Ren PG , Chen J , Zhang WQ , Ji X , Li ZM (2012) High barriergraphene oxide nanosheet/poly(vinyl alcohol) nanocomposite films. J Membr Sci 409-410 156 -    DOI : 10.1016/j.memsci.2012.03.051
Ku BC , Kumar J , Blumstein A , Kim DW , Samuelson LA (2004) Barrierproperties of ordered multilayer polymer nanocomposites. In:Schwarz JA, Contescu CI, Putyera K, eds. Dekker Encyclopedia ofNanoscience and Nanotechnology Marcel Dekker New York 213 -    DOI : 10.1201/9781439834398.ch9.
Decher G (1997) Fuzzy Nanoassemblies: toward layered polymeric multicomposites. Science 277 1232 -    DOI : 10.1126/science.277.5330.1232
Yang YH , Bolling L , Priolo MA , Grunlan JC (2013) Super gas barrier andselectivity of graphene oxide-polymer multilayer thin films. Adv Mater 25 503 -    DOI : 10.1002/adma.201202951
Qu Q , Gu C , Gu Z , Shen Y , Wang C , Hu X (2013) Layer-by-layer assemblyof polyelectrolyte and graphene oxide for open-tubular capillaryelectrochromatography. J Chromatogr A 1282 95 -    DOI : 10.1016/j.chroma.2013.01.055
Park JS , Cho SM , Kim WJ , Park J , Yoo PJ (2011) Fabrication of graphenethin films based on layer-by-layer self-assembly of functionalizedgraphene nanosheets. ACS Appl Mater Interfaces 3 360 -    DOI : 10.1021/am100977p
Lee DW , Hong TK , Kang D , Lee J , Heo M , Kim JY , Kim B-S , Shin HS (2011) Highly controllable transparent and conducting thinfilms using layer-by-layer assembly of oppositely charged reducedgraphene oxides. J Mater Chem 21 3438 -    DOI : 10.1039/c0jm02270e
Hummers WS, Jr. , Offeman RE (1958) Preparation of graphitic oxide. J Am Chem Soc 80 1339 -    DOI : 10.1021/ja01539a017
Shang J , Ma L , Li J , Ai W , Yu T , Gurzadyan GG (2012) The origin offluorescence from graphene oxide. Sci Rep 2 792 -    DOI : 10.1038/srep00792
Park OK , Hwang JY , Goh M , Lee JH , Ku BC , You NH (2013) Mechanicallystrong and multifunctional polyimide nanocomposites usingamimophenyl functionalized graphene nanosheets. Macromolecules 46 3505 -    DOI : 10.1021/ma400185j
Kim NH , Kuila T , Lee JH (2013) Simultaneous reduction, functionalizationand stitching of graphene oxide with ethylenediamine for compositesapplication. J Mater Chem A 1 1349 -    DOI : 10.1039/C2TA00853J
Park OK , Hahm MG , Lee S , Joh HI , Na SI , Vajtai R , Lee JH , Ku BC , Ajayan PM (2012) In situ synthesis of thermochemically reducedgraphene oxide conducting nanocomposites. Nano Lett 12 1789 -    DOI : 10.1021/nl203803d
Ferrari AC , Meyer JC , Scardaci V , Casiraghi C , Lazzeri M , Mauri F , Piscanec S , Jiang D , Novoselov KS , Roth S , Geim AK (2006) Ramanspectrum of graphene and graphene layers. Phys Rev Lett 97 187401 -    DOI : 10.1103/PhysRevLett.97.187401
Park OK , Lee S , Joh HI , Kim JK , Kang PH , Lee JH , Ku BC (2012) Effectof functional groups of carbon nanotubes on the cyclizationmechanism of polyacrylonitrile (PAN). Polymer 53 2168 -    DOI : 10.1016/j.polymer.2012.03.031
Priolo MA , Gamboa D , Holder KM , Grunlan JC (2010) Super gas barrierof transparent polymer?clay multilayer ultrathin films. Nano Lett 10 4970 -    DOI : 10.1021/nl103047k
Tseng IH , Liao YF , Chiang JC , Tsai MH (2012) Transparent polyimide/graphene oxide nanocomposite with improved moisture barrierproperty. Mater Chem Phys 136 247 -    DOI : 10.1016/j.matchemphys.2012.06.061