ライフサイエンスコーパス: graphene sheet

1 arbon black particles, carbon nanotubes, and graphene sheets).

2 amical screening of charge in a freestanding graphene sheet.

3 confined space between a metal surface and a graphene sheet.

4 ng wire has been embedded in another perfect graphene sheet.

5 ybridized carbon rings embedded in a perfect graphene sheet.

6 , experimental phonon dispersion of a single graphene sheet.

7 extending up to 30 A from both sides of the graphene sheet.

8 eties sufficient to enable the separation of graphene sheets.

9 ded graphite basal planes to give functional graphene sheets.

10 nd directly produce large, highly conductive graphene sheets.

11 3 J m(-2) for samples containing two to five graphene sheets.

12 place on the surface of exfoliated few-layer graphene sheets.

13 not ideal for the manufacture of processable graphene sheets.

14 the thermodynamic stability of free-standing graphene sheets.

15 ortions and flexible bending at the edges of graphene sheets.

16 es not readily exfoliate to yield individual graphene sheets.

17 rier by "locking in" favourable stackings of graphene sheets.

18 high-mobility semiconductor quantum wells or graphene sheets.

19 , or Al) nanoparticles encapsulated by large graphene sheets.

20 ut to study the morphology of functionalized graphene sheets.

21 ied with twist angle in bilayer and trilayer graphene sheets.

22 ensions of crystalline single- and few-layer graphene sheets.

23 spaces through folding and rearrangement of graphene sheets.

24 ovide evidence for the presence of monolayer graphene sheets.

25 lvated in a water monolayer confined between graphene sheets.

26 ng adsorption saturation of NaC molecules on graphene sheets.

27 i nanoparticles due to the highly conductive graphene sheets.

28 ween the guest molecules and the polarizable graphene sheets.

29 n, reduction or covalent modification of the graphene sheets.

30 hment of monodisperse Fe3O4 nanoparticles to graphene sheets.

31 e the nature of catalytic sites on ultrathin graphene sheets.

32 iform and open-networked array of aggregated graphene sheets.

33 ol the crumpling and unfolding of large-area graphene sheets.

34 shrinkage of giant fullerenes generated from graphene sheets.

35 l % of the solute is present as single-layer graphene sheets.

36 films corroborated the presence of monolayer graphene sheets.

37 nsional capillaries formed by closely spaced graphene sheets.

38 TEMPO-assisted exfoliation results in large graphene sheets (5-10 mum on average), which exhibit out

39 rammable photoactuation enabled by graphene: Graphene sheets aligned in liquid crystalline elastomers

40 lline Ni(OH)(2) nanoplates directly grown on graphene sheets also significantly outperform small Ni(O

41 croscopy imaging of water locked between two graphene sheets, an archetypal example of hydrophobic co

42 n of a nanohybrid by a combination of the 2D graphene sheet and 0D graphene quantum dots (GQDs).

43 e semiconducting channel between a monolayer graphene sheet and a metal thin film.

44 self-assembly over planar sp(2) carbons of a graphene sheet and furnishes the basis for fabrication o

45 ond to correlations between electrons in the graphene sheet and ions in the electrolyte.

46 etween the strain energy of curvature of the graphene sheet and the dangling-bond energy of the open

47 Ripples are an intrinsic feature of graphene sheets and are expected to strongly influence e

48 ing the preparation and functionalization of graphene sheets and carbon nanotubes to impart oxygen co

49 ve development of large-scale semiconducting graphene sheets and devices.

50 re effective reduction of chemically derived graphene sheets and graphite oxide than low-temperature

51 Carbon nanotube films, graphene sheets and metal-nanowire meshes can be both st

52 The findings on exfoliation of graphene sheets and related adsorption properties highli

53 of the dual signal amplification strategy of graphene sheets and the multienzyme labeling, the develo

54 formed by depositing alternating wafer-scale graphene sheets and thin insulating layers, then pattern

55 nar units (unbounded or bounded fragments of graphene sheets), and variable ratios of in-plane to edg

56 poly(acrylonitrile) at 1 wt% functionalized graphene sheet, and with only 0.05 wt% functionalized gr

57 e recently developed approaches to preparing graphene sheets, and then focus on the methods to assemb

58 erties arising from the nature of individual graphene sheets, and which assemble into monolithic thre

59 Monolayer graphene sheets are employed to preserve and template mo

60 The large voids in the graphene sheets are occupied by chloride ions with an eq

61 The graphene sheets are self-assembled and deeply crumpled i

62 most of the observed transport properties of graphene sheets at zero magnetic field can be explained

63 ng of such composites requires not only that graphene sheets be produced on a sufficient scale but th

64 rit some of the key properties of individual graphene sheets, but also develop additional functions t

65 ate the solublization/suspension of pristine graphene sheets by an equimolar mixture of benzene and h

66 n selectively remove monolayers in few-layer graphene sheets by means of electron-beam-induced sputte

67 were fabricated from single- and multilayer graphene sheets by mechanically exfoliating thin sheets

68 od for the scalable synthesis of few-layered graphene sheets by the microwave-assisted functionalizat

69 idized sp(3) carbon atoms and vacancies in a graphene sheet can degrade its mechanical strength, they

70 Amyloid protein fibrils and graphene sheets can be combined to make a material that

71 ns of graphene with clean and well-separated graphene sheets can be obtained in both aqueous and orga

72 pproaches, unfunctionalized and non-oxidized graphene sheets can be produced; among them an inexpensi

73 Single-atom-thick graphene sheets can now be produced by chemical vapour d

74 (2)/g, the maximum surface area for infinite graphene sheets, carried mainly by edge sites; we call t

75 raphite flakes to single-layer and few-layer graphene sheets combined with functionalization of the g

76 to ripples in the membrane that stiffen the graphene sheets considerably, to the extent that gamma i

77 The graphene sheets contain extremely small amounts of irons

78 Moreover, the graphene sheets dampen capillary waves such that rotatio

79 associated with the moire corrugation of the graphene sheet due to local variations in the graphene-s

80 tion sites might be realized across a single graphene sheet, facilitating the development of graphene

81 d dispersing small amounts of functionalized graphene sheets (FGSs) in liquid NM.

82 ed arrangement intercalated with small-sized graphene sheets filling the space and microvoids.

83 4.2 A [(12,12) to (3,3)] as well as a C(2)F graphene sheet fluorinated on one side only.

84 Whereas the graphene sheets formed from the unzipped part of the out

85 nner fiber structure consists of large-sized graphene sheets forming a highly ordered arrangement int

86 ITO) nanocrystals directly on functionalized graphene sheets, forming an ITO-graphene hybrid.

87 of the exfoliated accompanying carboxylated graphene sheet from pristine is achieved via Friedel-Cra

88 synthesized by the controlled reassembly of graphene sheets; from their initial stacked morphology,

89 The existence of layered structures based on graphene sheets gives rise to an electronic structure re

90 Electrical measurements on graphene sheets, graphene nanoribbons, and large graphen

91 ing is opened and attaches covalently to the graphene sheet (Gs) to form exfoliated graphene with gra

92 wth behaviors were observed on low-oxidation graphene sheets (GS) and highly oxidized graphite oxide

93 on lightly oxidized, electrically conducting graphene sheets (GS) exhibit a high specific capacitance

94 nd recent studies have shown that individual graphene sheets have extraordinary electronic transport

95 In-situ TEM shows that graphene sheets help maintain the capacity even in the c

96 supported on N-doped carbon black or N-doped graphene sheets, highlighting the importance of the 3D m

97 on lattice are detected, indicating that the graphene sheets host the ideal charge density wave.

98 oes beyond the traditional model of parallel graphene sheets hosting layers of physisorbed hydrogen i

99 mical functionalization by doping a pristine graphene sheet in a certain pattern with hydrogen atoms

100 sheet, and with only 0.05 wt% functionalized graphene sheet in poly(methyl methacrylate) there is an

101 ies for applications would be to incorporate graphene sheets in a composite material.

102 of the chemical composition of the edges of graphene sheets in both flat and curved sp(2)-hybridized

103 ates, and also holds together the individual graphene sheets in multilayer samples.

104 of stabilization of liquid-phase-exfoliated graphene sheets in N-methylpyrrolidone (NMP), N,N'-dimet

105 orphology that reflects the structure of the graphene sheets in solution.

106 loid aggregation to model the aggregation of graphene sheets in the liquid phase in order to predict

107 enhanced through the excellent dispersion of graphene sheets in the matrix material and the strong gr

108 The highly ordered graphene sheets in the plane of the membrane make organi

109 However, the graphene sheets in these devices have irregular shapes a

110 r since the first isolation of free-standing graphene sheets in year 2004.

111 al reduction removed oxygen and defects from graphene sheets, increased the size of sp(2) domains, an

112 The rolling up of a graphene sheet into a tube is a standard visualization t

113 scalable self-assembly of randomly oriented graphene sheets into additive-free, essentially homogeno

114 port a prompt electrochemical exfoliation of graphene sheets into aqueous solutions of different inor

115 However, the actual processes of rolling up graphene sheets into CNTs in laboratory syntheses have n

116 Processing graphene sheets into nanoribbons with widths of less tha

117 zable approach for fashioning one-atom-thick graphene sheets into resilient and movable parts with mi

118 Here we develop a method to incorporate graphene sheets into vanadium pentoxide nanoribbons via

119 ergy gaps that are sometimes observed when a graphene sheet is placed on a hexagonal boron nitride su

120 The self-assembly of graphene sheets is driven thermodynamically, as graphite

121 Mass production of high-quality graphene sheets is essential for their practical applica

122 The bonding between adjacent graphene sheets is investigated by molecular dynamics si

123 on between two model hydrophobic plates, and graphene sheets, is reduced when urea is added to the so

124 rowth enlarged, over one hour, the nuclei to graphene sheets larger than one hundred nm(2) in area.

125 transfer from the electron beam to few-layer graphene sheets leads to unique structural transformatio

126 d identification of the fluence at which the graphene sheet loses long-range order.

127 ectrical behaviour of both doped and undoped graphene sheets maintain excellent properties, with low

128 graphene surface, the carrier equilibrium in graphene sheet might be altered, and manifested by the c

129 ional (3D) hybrid material of nitrogen-doped graphene sheets (N-RGO) supporting molybdenum disulfide

130 Surfactant-wrapped chemically converted graphene sheets obtained from reduction of graphene oxid

131 the role of surface mediators on the buckled graphene sheets of acid-microwaved CNTs.

132 Synthesis of large-scale graphene sheets of high quality and at low cost has been

133 and scalable approach produces high-quality graphene sheets of low oxygen content, enabling a broad

134 Graphene sheets--one-atom-thick two-dimensional layers o

135 ctrical-circuit model is established and the graphene-sheet pattern is designed optimally for maximiz

136 R selectivity, we treated partially oxidized graphene sheets (po-Gr) with NR to obtain po-Gr-NR dispe

137 imilar trend, with values for functionalized graphene sheet- poly(methyl methacrylate) rivaling those

138 ur bottom-up chemical approach of tuning the graphene sheet properties provides a path to a broad new

139 anchorage, pi-stacking interactions with the graphene sheets provide further pi-delocalization that i

140 we characterize the hydrophobicity of curved graphene sheets, self-assembled monolayers (SAMs) with c

141 a-fetoprotein (AFP) is described that uses a graphene sheet sensor platform and functionalized carbon

142 perating at room temperature, where a single graphene sheet serves simultaneously as the plasmonic me

143 of pre-synthesized Ni(OH)(2) nanoplates and graphene sheets shows lower specific capacitance, highli

144 been observed on all suspended and supported graphene sheets studied so far.

145 However, the finite curvature of the graphene sheet that forms the nanotubes and the broken s

146 With the protection of graphene sheets, the large and freestanding LixM/graphen

147 ain metal atoms are intercalated between its graphene sheets, the same has not been achieved in a sin

148 on-neighboring carbon atoms across an entire graphene sheet, thereby producing only a minimum concent

149 In contrast to the graphene sheet, they are chemically versatile.

150 e may therefore apply ideas from kirigami to graphene sheets to build mechanical metamaterials such a

151 pathways used so far for modification of 2-D graphene sheets to make is three-dimensional.

152 Second, functionalized graphene sheets used for the biosensor platform increase

153 discrete electronic domains within a single graphene sheet using scanning transmission X-ray microsc

154 potential of mean force between two solvated graphene sheets using molecular dynamics (MD) simulation

155 wo-dimensional periodic ripples in suspended graphene sheets, using both spontaneously and thermally

156 Decorating Fe3O4 nanoparticles on graphene sheets was performed via a facile one-step chem

157 ring descending local curvatures) and a flat graphene sheet, we confirm that adsorption capacity is i

158 y electrically tuning the Fermi level of the graphene sheet, we demonstrate modulation of the guided

159 s and nanotubes tunneling multiple layers of graphene sheets were also observed.

160 m fluorescence property from nanohybrid, the graphene sheets were chemically doped with cadmium sulph

161 The graphene sheets were deposited on 1.00mm thick copper sh

162 With the aid of sonication, multilayer graphene sheets were exfoliated by NaC, leading to bette

163 Graphene sheets were found in the TEM images of the carb

164 Herein, single-layered and few-layered graphene sheets were produced by dispersion and exfoliat

165 inate from periodic nanoscale ripples in the graphene sheet, which enhance puckering around a sliding

166 Thus, separated graphene sheets, which are referred to as microwave-enab

167 n be obtained by fragmentation/truncation of graphene sheets, which creates surface areas exceeding o

168 f polymer nanocomposites with functionalized graphene sheets, which overcome these obstacles and prov

169 er of confined solvent molecules between the graphene sheets, which results from the strong affinity

170 t to directly measure the adhesion energy of graphene sheets with a silicon oxide substrate.

171 we find that, counter to standard reasoning, graphene sheets with large-angle tilt boundaries that ha

172 y attaching chemical moieties at the edge of graphene sheets with minimal damage of the carbon basal

173 t an interconnected macroporous framework of graphene sheets with uniform dispersion of Fe(3)O(4) nan

174 Ni(OH)(2) nanocrystals grown on graphene sheets with various degrees of oxidation are in

175 ispersion of individual, chemically modified graphene sheets within polymer hosts.

176 nitrogen atoms can be incorporated into the graphene sheet without destroying it.

177 oscopic flattening and in-plane shrinkage of graphene sheets without a complete loss of crystallinity