|Paper-like graphene-Ag composite films with enhanced mechanical and electrical properties.|
|Jump to Full Text|
|PMID: 23324465 Owner: NLM Status: PubMed-not-MEDLINE|
|In this paper, we have reported that paper-like graphene-Ag composite films could be prepared by a facile and novel chemical reduction method at a large scale. Using ascorbic acid as a reducing agent, graphene oxide films dipped in Ag+ aqueous solutions can be easily reduced along with the decoration of different sizes of Ag particles distributed uniformly. The results reveal that the obtained films exhibit improved mechanical properties with the enhancement of tensile strength and Young's modulus by as high as 82% and 136%, respectively. The electrical properties of graphene-Ag composite films were studied as well, with the sheet resistance of which reaching lower than approximately 600 Ω/□. The graphene-Ag composite films can be expected to find interesting applications in the area of nanoelectronics, sensors, transparent electrodes, supercapacitors, and nanocomposites.|
|Rungang Gao; Nantao Hu; Zhi Yang; Qirong Zhu; Jing Chai; Yanjie Su; Liying Zhang; Yafei Zhang|
Related Documents :
|18806445 - Treatment parameters of high frequency electrical stimulation as established on the ele...
19735915 - Age-related changes in hand grip strength among rural and urban haryanvi jat females.
18489805 - The relationship between lower extremity strength and power to everday walking behavior...
23324465 - Paper-like graphene-ag composite films with enhanced mechanical and electrical properties.
18364325 - Iron status among australian adults: findings of a population based study in queensland...
9573795 - The effect of amalgam overhangs on alveolar bone height as a function of patient age an...
|Type: Journal Article Date: 2013-01-17|
|Title: Nanoscale research letters Volume: 8 ISSN: 1931-7573 ISO Abbreviation: Nanoscale Res Lett Publication Date: 2013|
|Created Date: 2013-03-20 Completed Date: 2013-03-21 Revised Date: 2013-04-18|
Medline Journal Info:
|Nlm Unique ID: 101279750 Medline TA: Nanoscale Res Lett Country: United States|
|Languages: eng Pagination: 32 Citation Subset: -|
|Key Laboratory for Thin Film and Microfabrication of Ministry of Education, Research Institute of Micro/Nano Science and Technology, Shanghai Jiao Tong University, Shanghai 200240, People's Republic of China. firstname.lastname@example.org.|
|APA/MLA Format Download EndNote Download BibTex|
Journal ID (nlm-ta): Nanoscale Res Lett
Journal ID (iso-abbrev): Nanoscale Res Lett
Copyright ©2013 Gao et al; licensee Springer.
Received Day: 2 Month: 1 Year: 2013
Accepted Day: 13 Month: 1 Year: 2013
collection publication date: Year: 2013
Electronic publication date: Day: 17 Month: 1 Year: 2013
Volume: 8 Issue: 1
First Page: 32 Last Page: 32
PubMed Id: 23324465
Publisher Id: 1556-276X-8-32
|Paper-like graphene-Ag composite films with enhanced mechanical and electrical properties|
|Rungang Gao1||Email: email@example.com|
|Nantao Hu1||Email: firstname.lastname@example.org|
|Zhi Yang1||Email: email@example.com|
|Qirong Zhu2||Email: firstname.lastname@example.org|
|Jing Chai1||Email: email@example.com|
|Yanjie Su1||Email: firstname.lastname@example.org|
|Liying Zhang1||Email: email@example.com|
|Yafei Zhang1||Email: firstname.lastname@example.org|
1Key Laboratory for Thin Film and Microfabrication of Ministry of Education, Research Institute of Micro/Nano Science and Technology, Shanghai Jiao Tong University, Shanghai 200240, People's Republic of China
2Instrumental Analysis Center, Shanghai Jiao Tong University, Shanghai 200240, People's Republic of China
Graphene, a two-dimensional single atomic layer of sp2-hybridized carbon arranged in a honeycomb structure, has generated tremendous interest due to its unique combination of electronic, mechanical, chemical, and thermal properties [1-4]. Many potential applications in various fields, including filler materials [5,6], field-emission devices , nanoscale electronic devices , sensors [8-10], transparent electrodes [11-14], and so on [15-18], have been reported.
Large-scale preparation of paper-like graphene films has aroused much attention for their unique mechanical and electrical properties [15,16,19-22]. Some methods, including micromechanical exfoliation , chemical vapor deposition [12,23-25], and self-assembly [26-32] have been used to prepare this fascinating structure of the films, which have great potential for the applications in transparent electrodes , supercapacitors , biosensors , etc. Meanwhile, some noble metal nanoparticles have been added into the graphene films to improve the electronic and electrochemical properties of the composite films [31,32] using many methods, such as chemical reduction , electrochemical reduction , biochemical reduction , and in situ thermal reduction . As a result, the fabricated composite films have shown a tremendous potential in improving the electrochemical properties  and as an electrode of biosensors .
Although many efforts and applications have been achieved for these novel carbon films, it is still a great challenge to develop a novel method to prepare the films at a large scale. Herein, we report a new method to prepare graphene-Ag composite films with excellent and improved properties, which are fabricated by the large-scale assembly of graphene oxide films, followed by in situ reduction of graphene oxide films together with Ag+ by ascorbic acid. The mechanical and electrical properties of the obtained graphene-Ag composite films are also investigated.
The natural graphite powder (carbon content 99.999%) in the experiment was purchased from Qingdao Tianyuan Carbon Co. Ltd, Qingdao, China. Other solvents and reagents were of analytical reagent grade and used as received.
Graphene oxide was synthesized through the modified Hummers method  as stated in our previous reports [2,18,38]. Prior to reduction, the synthesized graphene oxide (0.15 g) was dispersed in 50 mL of deionized water by ultrasonic treatment (1,000 W, 40 kHz) for 2 h, and then, the yellow-brown dispersion was poured into a polytetrafluoroethylene (PTFE) plate with a diameter of 11.5 cm and heated at 80°C for 24 h. Finally, the brown-black films with a diameter of 10 to 11 cm and thickness of 10 μm could be obtained as shown in Figure 1a. In order to reduce the graphene oxide films, ascorbic acid was used as a reducing agent [38,39]. To obtain graphene films, 150 mg ascorbic acid was dissolved in water, followed by soaking the graphene oxide films into the solution for a certain time in order to determine an optimized period. In addition, to obtain graphene-Ag composite films, 150 mg ascorbic acid was dissolved into the AgNO3 aqueous solution (100 mL, 2 to 300 mg), and the graphene oxide films were soaked in the mixed solution for 5 h. The schematic illustration of two chemical synthesis routes is described in Figure 2. After washing with deionized water, the final black paper-like graphene films and graphene-Ag composite films (Figure 1b) were obtained after heated at 80°C for 2 h, respectively.
Atomic force microscope (AFM) image was taken with the Multimode Nanoscope V scanning probe microscopy system (Veeco Instruments Inc., Plainview, NY, USA) using tapping mode with Picoscan v5.3.3 software. The morphology of the films were observed using a scanning electron microscope (SEM) using a Carl Zeiss ULTRA 55 (Carl Zeiss, Oberkochen, Germany) with energy dispersive X-ray (EDX) spectrometry mode. The crystal structures of the films were examined by X-ray diffraction (XRD; D/MAX-2200, Rigaku, Tokyo, Japan) with Cu Kα (λ = 1.5418 Å) and 2θ from 5° to 85°. The Raman spectra were obtained using a Senterra R200-L Raman spectrometer (Bruker Optik GmbH, Ettlingen, Germany) with a 514-nm line of laser source. Fourier transform infrared (FTIR) spectra were recorded using a Vertex 70 vacuum FTIR spectrometer (Bruker Optik GmbH) and scanned from 4,000 to 400 cm−1 with KBr as background. Thermogravimetric analysis (TGA; Pyris 1, PerkinElmer, Waltham, MA, USA) was performed under a highly pure nitrogen atmosphere with a heating rate of 1°C to 10°C/min from 30°C to 700°C. The films with 5-mm width and 4- to 5-cm length were measured by dynamic mechanical analysis (DMA; TA-Q800, TA Instruments, Newcastle, DE, USA) at the room temperature. A four-probe detector (RTS-8, 4 PROBES TECH, Guangzhou, China) was used to measure the sheet resistance of the films.
The modified Hummers method had been used to prepare graphene oxide. By sonicating the graphene oxide in water, graphene oxide sheet aqueous solution was obtained. From the tapping-mode AFM image as shown in Figure 3, it is observed that the thickness of the obtained graphene oxide sheet is approximately 1.05 nm, which indicates that the graphene oxide can be easily exfoliated into single layer by the oxidation and sonication treatment . The graphene oxide films with a large area were fabricated by casting method. The graphene oxide sheets can be easily assembled into graphene oxide films by volatizing water in the oven at 80°C. PTFE, a hydrophobic substrate, is used to make sure that the films are easily peeled off and the large-area free-standing films fabricated. As shown in Figure 1a, the yellow-brown paper-like films with a semitransparent characteristic are obtained. In order to obtain the graphene films, ascorbic acid, as an excellent reducing agent, has been used here to reduce the graphene oxide films . As a result of the reduction process, the opaque graphene films with black color (Figure 1b) are obtained. Excitingly, the morphology of the graphene films can be perfectly maintained after the reduction process (Figure 4a,b), which suggests that this facile and novel method is suitable for the large-scale production of graphene films. For the improvement of the conductivity of the films, Ag particles have been in situ introduced during the process of the reduction reaction. The morphology of the graphene-Ag composite films has been observed by SEM, as shown in Figure 4. It can be found that the films are decorated with Ag particles with an average particle size from approximately 20 nm to approximately 1 μm (Figure 4c,d,e,f,g). When the mass ratio of AgNO3/graphene oxide is 1:75, these Ag particles with a size of about 20 nm were distributed uniformly at the surface of the composite films (Figure 4c). When the mass ratio is increased to 1:30, the Ag particles with the same size as shown in Figure 4c disperse well while the intensity of Ag particles distributed on the surface of the films increase (Figure 4d). As the mass ratio is increased to 1:15, the size of Ag particles is remarkably increased along with partial particles deposited together to form bigger spheres with a diameter of approximately 1 μm (Figure 4e). With the increase of the mass ratio to 1:7.5, Ag particles further aggregate but still disperse well (Figure 4f). Finally, with the mass ratio of 2:1, the morphology of those Ag particles becomes bigger and irregular (Figure 4g).
EDX is used to qualitatively determine the variation of relative ratio of each element. The results in Figure 5 and Table 1 show that the atomic ratios of C/O of the graphene films and graphene-Ag composite films are various from 2.2 to 2.5, lower than those in a previous study . Compared with the graphene oxide films (the atomic ratio of C/O is approximately 1.5), the increased atomic ratio of C/O of the composite films means that the reduction progress has occurred. Simultaneously, the weight percentages of the Ag element may influence the reaction in some way. When the amount of AgNO3 reaches to 300 mg, the atomic ratio of C/O is far lower, indicating that the reduction process may be affected when the amount of AgNO3 is excessive. As for EDX results, the appropriate amount of AgNO3 is around 5 to 10 mg.
The XRD patterns also support the results from SEM and EDX. Only when the amount of AgNO3 is 300 mg, the final weight percentage of Ag is more than 7%, so the crystal structure and ordering of Ag particles can be characterized by XRD. As shown in Figure 6 (i), the characteristic peaks at 38.02°, 44.24°, and 64.56° correspond with the (111), (200), and (220) planes of the cubic Ag crystal (JCPDS no. 04–0783), respectively, which indicates that the metallic Ag particles are formed after being reduced. According to the Bragg spacing equation, the characteristic peak of carbon (002) changes from 26.6° (Figure 6 (j), pristine graphite powder) to 9.6° (Figure 6 (a), graphene oxide) and sharply weakens, showing that the layer-to-layer distance (d-spacing) from 0.67 to 1.84 nm, which means the structure of sp2 carbon has been deformed after the introduction of some oxygen functional groups. At the same time, the layer-to-layer distance of the graphene-Ag composite films has also been changed from 1.20 to 1.61 nm, indicating that some of the oxygen functional groups have been reduced. As shown, the graphene-Ag composite films have a shorter distance from 1.20 to 1.34 nm than the graphene films from 1.56 to 1.61 nm, suggesting that AgNO3 is beneficial to the reduction process and the suitable amount of AgNO3 is 10 mg.
The Raman scattering signals were measured on the graphite powder (Figure 7 (a)), graphene oxide films (Figure 7 (b)), the graphene films (Figure 7 (c to e)), and the graphene-Ag composite films (Figure 7 (f to j)). The Raman spectra exhibit two main characteristic peaks, the D band (approximately 1,345 cm−1) and G band (approximately 1,590 cm−1). The G band represents the plane vibrations with E2g symmetry and is mainly sensitive to the configuration of sp2 sites, while the D band is related to the breathing mode of κ-point phonon of A1g symmetry. As the graphite was oxidized into graphene oxide, the G band is broadened and the D band increases substantially, indicating the decrease in size of the in-plane sp2 sites, possibly because of the extensive oxidation and ultrasonic exfoliation . When graphene oxide is reduced by ascorbic acid for 5 h, the increase of the ID/IG intensity ratio of graphene is observed compared to that of the graphene oxide. Finally, when AgNO3 was used, the increase of D band also occurred. This change suggests an increase in the average size of the sp2 sites upon reduction of graphene oxide, which indicates that the reduction reaction has taken place and agrees well with the Raman spectrum of the graphene oxide reduced by hydrazine as reported by Stankovich et al. .
FTIR is used to characterize the functional groups in the films shown in Figure 8. When the pristine graphite powder (sample j) is oxidized, many functional groups can be introduced in the graphene oxide films (sample a), which have a peak at approximately 3,410 cm−1 arising from the -OH stretching vibrations and peak at approximately 1,730 cm−1 of carboxyl C=O, approximately 1,620 cm−1 of C-C groups, approximately 1,400 cm−1 of O-H, and 1,100 cm−1 of alkoxy C-O. After the reduction treatment, most of the absorption peaks are weakened or disappeared, mainly leaving the C-C vibration peaks [11,16]. As far as samples b to d with the reduction time of 1 h (as shown in Figure 8 (b)) are concerned, the peaks remain almost as strong as that of sample a, suggesting that the reduction of sample b has not completely occurred. Meanwhile, the peaks of samples c and d do not have a significant difference, indicating that the period time of 5 h is enough to reduce the graphene oxide. When the amount of AgNO3 is added from 2 to 10 mg (samples e to g), the peaks seem to be similar with those of samples c and d since a few existing Ag particles do not block the reaction. However, when the amount of AgNO3 is excessive as 20 mg (sample h) and 300 mg (sample i), all peaks become stronger again, which means that the side effects will arise gradually as the amount of AgNO3 increases.
Thermogravimetric analysis has also been performed. Figure 9 exhibits TGA curves of (a) graphite; (b) graphene oxide; (c to e) graphene films reduced for 1, 5, and 12 h; and (f to j) graphene-Ag composite films with the amount of AgNO3 from 2 to 300 mg under nitrogen atmosphere. In the left image of Figure 9, graphene oxide (Figure 9 (b)) and the graphene reduced for only 1 h (Figure 9c) have an inferior thermal stability, while the pristine graphite is quite stable below 600°C. The decomposition of graphene oxide begins at 200°C, which is probably due to the loss of the acidic functional groups and residues. When reduction time is more than 5 h (Figure 9 (d) and (e)), the TGA curves of graphene only exhibit a slight mass loss at a temperature lower than 600°C, which suggests that the enhancement of thermal stability is achieved after the oxygen-containing functional groups are removed during reduction [18,28]. In addition, Ag particles can also affect the thermal stability of graphene. If the amount of AgNO3 is appropriate (no more than 10 mg), the TGA curves of graphene-Ag composite films exhibited a mass loss at a temperature lower than 600°C, slightly lesser than that of graphene reduced only by ascorbic acid. However, when the amount of AgNO3 is 20 mg and 300 mg, the TGA curves of the composite films turned out to have the same trend as that of graphene oxide. The right image of Figure 9 exhibits the weight loss of partial samples at a temperature from 690°C to 700°C; it can be seen that the residue weight increases as the amount of AgNO3 is increased, and more than 15% weight is left at 690°C as the AgNO3 is excessive up to 300 mg. We can also find that the residue weight of samples i and j has a little difference with the EDX results. It may be due to the excessive Ag particles which aggregated and deposited nonuniformly on the surface of the graphene-Ag composite films.
The mechanical properties of graphene oxide films and graphene films have also been studied, as shown in Figure 10 and Table 2. Compared with graphene oxide films, graphene films exhibit enhanced mechanical behaviors. After being reduced for 5 h, the stress of the obtained graphene films increases from 33 to 60 MPa (increased by 82%), and the strain decreases from 1.3% to 0.9%. The preliminary results, a considerable improvement in the Young's modulus of graphene films increased by 136% (up to 7.8 MPa), are encouraging. From Table 2, it can be also observed that the optimal reduction period for the preparation of graphene films is 5 h. Moreover, after Ag particles are decorated, there is little change in the mechanical properties of graphene-Ag composite films compared with the corresponding graphene films.
Finally, the sheet resistance of these films was measured using the four-probe detector as shown in Figure 11. The electrical properties can be tuned by the addition of a given amount of Ag particles. When the amount of AgNO3 is no more than 10 mg, the sheet resistance decreases; on the other hand, when the amount of AgNO3 is 20 mg, the sheet resistance increases. When the optimal amount of AgNO3 is 10 mg, a minimum sheet resistance of approximately 600 Ω/□ for graphene-Ag composite films is obtained. It can be found that the conductivity of the resultant graphene-Ag composite films can be improved greatly via the uniform decoration of Ag particles.
In summary, we have demonstrated that graphene-Ag composite films are fabricated in a large scale using a facile chemical reduction method. The graphene oxide sheets can be easily assembled to form free-standing graphene oxide films during the volatilization process on PTFE hydrophobic substrate. After dipping the graphene oxide films into the Ag+ aqueous solution, Ag particles can be uniformly distributed on the surface of graphene films using ascorbic acid as a reducing agent. The morphology of the composite films can be maintained during the reduction process. The obtained films have been characterized by AFM, SEM, XRD, Raman, FTIR, TGA, DMA, and a four-probe detector. The results show that the obtained films exhibit improved mechanical properties with the enhancement of tensile strength and Young's modulus by as high as 82% and 136%, respectively. The electrical properties of the graphene-Ag composite films were studied as well, with the sheet resistance of which reaching lower than approximately 600 Ω/□. The composite films hold a great potential for applications in the fields of nanoelectronics, sensors, transparent electrodes, supercapacitors, and nanocomposites.
The authors declare that they have no competing interests.
RGG carried out the sample preparation, participated on its analysis, performed all the analyses except AFM and FTIR analyses, and wrote the paper. NTH also wrote the paper and analyzed the samples. JC performed the FTIR analysis. QRZ participated on the AFM analysis and proof corrections. ZY, YJS, LYZ, and YFZ participated in the study guidance and paper correction. All authors read and approved the final manuscript.
This work was supported by the National High-Tech R & D Program of China (863, no. 2011AA050504), National Natural Science Foundation of China (no. 51102164), Program for New Century Excellent Talents in University, Shanghai Science and Technology Grant (12JC1405700 and 12nm0503800), Shanghai Pujiang Program (no. 11PJD011), the Program for Professor of Special Appointment (Eastern Scholar) at Shanghai Institutions of Higher Learning, Medical-Engineering Crossover Fund (YG2012MS40 and YG2012MS37), and Science-Engineering Crossover Fund (X198052) of Shanghai Jiao Tong University. We also acknowledge the analysis support from the Instrumental Analysis Center of Shanghai Jiao Tong University.
|Novoselov K,Geim A,Morozov S,Jiang D,Zhang Y,Dubonos S,Grigorieva I,Firsov A,Electric field effect in atomically thin carbon filmsScienceYear: 200430666666810.1126/science.110289615499015|
|Su Y,Wei H,Gao R,Yang Z,Zhang J,Zhong Z,Zhang Y,Exceptional negative thermal expansion and viscoelastic properties of graphene oxide paperCarbonYear: 2012502804280910.1016/j.carbon.2012.02.045|
|Cheng P,Yang Z,Wang H,Chen W,Chen M,Shangguan W,Ding G,TiO2-graphene nanocomposites for photocatalytic hydrogen production from splitting waterInt J Hydrogen EnergyYear: 2012372224223010.1016/j.ijhydene.2011.11.004|
|Raza M,Westwood A,Brown A,Hondow N,Stirling C,Characterisation of graphite nanoplatelets and the physical properties of graphite nanoplatelet/silicone composites for thermal interface applicationsCarbonYear: 2011494269427910.1016/j.carbon.2011.06.002|
|Yan J,Wei T,Shao B,Fan Z,Qian W,Zhang M,Wei F,Preparation of a graphene nanosheet/polyaniline composite with high specific capacitanceCarbonYear: 20104848749310.1016/j.carbon.2009.09.066|
|Hu N,Meng L,Gao R,Wang Y,Chai J,Yang Z,Kong E,Zhang Y,A facile route for the large scale fabrication of graphene oxide papers and their mechanical enhancement by cross-linking with glutaraldehydeNano-Micro LettYear: 2011321522210.2174/1876402911103030215|
|Geim A,Novoselov K,The rise of grapheneNat MaterYear: 2007618319110.1038/nmat184917330084|
|Huang X,Hu N,Gao R,Yu Y,Wang Y,Yang Z,Kong E,Wei H,Zhang Y,Reduced graphene oxide–polyaniline hybrid: preparation, characterization and its applications for ammonia gas sensingJ Mater ChemYear: 201222224882249510.1039/c2jm34340a|
|Reed J,Zhu H,Zhu A,Li C,Cubukcu E,Graphene-enabled silver nanoantenna sensorsNano LettYear: 2012124090409410.1021/nl301555t22793868|
|Hu N,Wang Y,Chai J,Gao R,Yang Z,Kong E,Zhang Y,Gas sensor based on p-phenylenediamine reduced graphene oxideSensors Actuat B-ChemYear: 201216310711410.1016/j.snb.2012.01.016|
|Tang L,Wang Y,Li Y,Feng H,Lu J,Li J,Preparation, structure, and electrochemical properties of reduced graphene sheet filmsAdv Funct MaterYear: 2009192782278910.1002/adfm.200900377|
|Zhang K,Zhang L,Zhao X,Wu J,Graphene/polyaniline nanofiber composites as supercapacitor electrodesChem MaterYear: 2010221392140110.1021/cm902876u|
|Jo G,Choe M,Cho C,Kim J,Park W,Lee S,Hong W,Kim T,Park S,Hong B,Kahng Y,Lee T,Large-scale patterned multi-layer graphene films as transparent conducting electrodes for GaN light-emitting diodesNanotechnologyYear: 20102117520110.1088/0957-4484/21/17/17520120368676|
|Choi B,Hong J,Hong W,Hammond P,Park H,Facilitated ion transport in all-solid-state flexible supercapacitorsACS NanoYear: 201157205721310.1021/nn202020w21823578|
|Xu Z,Gao H,Hu G,Solution-based synthesis and characterization of a silver nanoparticle–graphene hybrid filmCarbonYear: 2011494731473810.1016/j.carbon.2011.06.078|
|Zheng L,Zhang G,Zhang M,Guo S,Liu Z,Power J,Preparation and capacitance performance of Ag–graphene based nanocompositeJ Power SourcesYear: 2012201376381|
|Hu N,Wei L,Wang Y,Gao R,Chai J,Yang Z,Kong E,Zhang Y,Graphene oxide reinforced polyimide nanocomposites via in situ polymerizationJ Nanosci NanotechnolYear: 20121217317810.1166/jnn.2012.514422523962|
|Hu N,Gao R,Wang Y,Wang Y,Chai J,Yang Z,Kong E,Zhang Y,The preparation and characterization of non-covalently functionalized grapheneJ Nanosci NanotechnolYear: 2012129910410.1166/jnn.2012.513922523951|
|Wang D,Li F,Zhao J,Ren W,Chen Z,Tan J,Wu Z,Gentle I,Lu G,Cheng H,Fabrication of graphene/polyaniline composite paper via in situ anodic electropolymerization for high-performance flexible electrodeACS NanoYear: 200931745175210.1021/nn900297m19489559|
|He L,Yao L,Sun J,Wu W,Yang J,Cai L,Song R,Hao Y,Ma Z,Huang W,In-site mineralization of amorphous calcium carbonate particles: a facile and efficient approach to fabricate poly(L-lactic acid) based hybridsPolym Degrad StabilYear: 2011961187119310.1016/j.polymdegradstab.2011.04.018|
|Fuentes-Cabrera M,Rhodes B,Fowlkes J,López-Benzanilla A,Terrones H,Simpson M,Rack P,Molecular dynamics study of the dewetting of copper on graphite and graphene: implications for nanoscale self-assemblyPhys Rev EYear: 201183041603|
|Geim A,Graphene: status and prospectsScienceYear: 20093241530153410.1126/science.115887719541989|
|Li X,Wang X,Zhang L,Lee S,Dai H,Chemically derived, ultrasmooth graphene nanoribbon semiconductorsScienceYear: 20083191229123210.1126/science.115087818218865|
|Berger C,Song Z,Li X,Wu X,Brown N,Naud C,Mayou D,Li T,Hass J,Marchenkov A,Conrad E,First P,de Heer W,Electronic confinement and coherence in patterned epitaxial grapheneScienceYear: 20063121191119610.1126/science.112592516614173|
|Kim K,Zhao Y,Jang H,Lee S,Kim J,Kim K,Ahn J,Kim P,Choi J,Hong B,Large-scale pattern growth of graphene films for stretchable transparent electrodesNatureYear: 200945770671010.1038/nature0771919145232|
|Lafkioti M,Krauss B,Lohmann T,Zschieschang U,Klauk H,von Klitzing K,Smet J,Graphene on a hydrophobic substrate: doping reduction and hysteresis suppression under ambient conditionsNano LettYear: 2010101149115310.1021/nl903162a20218633|
|Yu D,Dai L,Self-assembled graphene/carbon nanotube hybrid films for supercapacitorsJ Phys Chem LettYear: 2010146747010.1021/jz9003137|
|Choi B,Park H,Park T,Yang M,Kim J,Jang S,Heo N,Lee S,Kong J,Hong W,Solution chemistry of self-assembled graphene nanohybrids for high-performance flexible biosensorsACS NanoYear: 201042910291810.1021/nn100145x20377244|
|Xu Y,Sheng K,Li C,Shi G,Self-assembled graphene hydrogel via a one-step hydrothermal processACS NanoYear: 201044324433010.1021/nn101187z20590149|
|Wang D,Kou R,Choi D,Yang Z,Nie Z,Li J,Saraf L,Hu D,Zhang J,Graff G,Liu J,Pope M,Aksay I,Ternary self-assembly of ordered metal oxidegraphene nanocomposites for electrochemical energy storageACS NanoYear: 201041587159510.1021/nn901819n20184383|
|Giovannetti G,Khomyakov P,Brocks G,Karpan V,van den Brink J,Kelly P,Doping graphene with metal contactsPhys Rev LettYear: 200810102680318764212|
|Khomyakov P,Giovannetti G,Rusu P,Brocks G,van den Brink J,Kelly P,First-principles study of the interaction and charge transfer between graphene and metalsPhys Rev BYear: 200979195425|
|Dai Y,Cai S,Yang W,Gao L,Tang W,Xie J,Zhi J,Ju X,Fabrication of self-binding noble metal/flexible graphene composite paperCarbonYear: 2012504648465410.1016/j.carbon.2012.05.053|
|Zhou Y,Yang J,Cheng X,Zhao N,Sun L,Sun H,Li D,Electrostatic self-assembly of graphene–silver multilayer films and their transmittance and electronic conductivityCarbonYear: 20125043444350|
|Shan C,Yang H,Han D,Zhang Q,Ivaska A,Niu L,Electrochemical determination of NADH and ethanol based on ionic liquid-functionalized grapheneBiosens BioelectronYear: 2010251504150810.1016/j.bios.2009.11.00920007014|
|Zhou X,Huang X,Qi X,Wu S,Xue C,Boey F,Yan Q,Chen P,Zhang H,In situ synthesis of metal nanoparticles on single-layer graphene oxide and reduced graphene oxide surfacesJ Phys Chem CYear: 2009113108421084610.1021/jp903821n|
|Hummers W,Offema R Jr,Preparation of graphitic oxideJ Am Chem SocYear: 1958801339134110.1021/ja01539a017|
|Yang Z,Gao R,Hu N,Chai J,Cheng Y,Zhang L,Wei H,Kong E,Zhang Y,The prospective two-dimensional graphene nanosheets: preparation, functionalization, and applicationsNano-Micro LettYear: 201241910.2174/1876402911204010001|
|Zhang J,Yang H,Shen G,Cheng P,Zhang J,Guo S,Reduction of graphene oxide via L-ascorbic acidChem CommunYear: 2010461112111410.1039/b917705a|
|Lui C,Liu L,Mak K,Flynn G,Heinz T,Ultraflat grapheneNatureYear: 200946233934110.1038/nature0856919924211|
|Ferrari A,Meyer J,Scardaci V,Casiraghi C,Lazzeri M,Mauri F,Piscanec S,Jiang S,Novoselov K,Roth S,Geim A,Raman spectrum of graphene and graphene layersPhys Rev LettYear: 20069718740117155573|
|Stankovich S,Dikin D,Dommett G,Kohlhaas K,Zimney E,Stach E,Piner R,Nguyen R,Ruoff R,Graphene-based composite materialsNatureYear: 200644228228610.1038/nature0496916855586|
Elements of all films measured by EDX
Atomic ratio (C/O)
0 stands for the graphene film reduced for 5 h.
Mechanical properties of graphene oxide films and graphene films reduced for different times
|Sample||Strain (%)||Stress (MPa)||Modulus (GPa)|
||1.3 ± 0.2
||33.0 ± 1.3
||3.3 ± 0.3
|(b) 1 h
||0.8 ± 0.1
||49.3 ± 0.9
||6.8 ± 0.1
|(c) 5 h
||0.9 ± 0.1
||60.2 ± 0.6
||7.8 ± 0.1
|(d) 12 h||0.9 ± 0.1||32.5 ± 1.4||3.9 ± 0.2|
Keywords: Graphene, Ag particles, Composite films, Graphene oxide, In situ reduction, Graphene paper, Electrical properties, Mechanical properties.
Previous Document: Prenatal micronutrient supplementation and postpartum depressive symptoms in a pregnancy cohort.
Next Document: Experiences with a simple laparoscopic gastric tube construction.