Source: https://pubs.rsc.org/en/content/articlehtml/2019/sc/c8sc04083d
Timestamp: 2019-04-19 14:27:25+00:00

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Graphene is the simplest stable atomically flat material that is being intensively investigated due to its unique physical and chemical properties.1–3 The chemistry of the interface between graphene and its environment (gas or liquid) plays a crucial role in the characteristic properties.4–7 Hence, it is important to devise methods to modify this chemistry precisely as well as to understand the effect of the modification on the ensuing properties, to engineer graphene for an application of interest.8,9 Many methods for modification of graphene in its various forms are currently pursued.10–14 As the surface dictates many properties of bulk materials, the edge of graphene is known to influence its electronic and chemical properties. The role played by the edges becomes dominant when narrowing down graphene sheets to nanoribbons, e.g. by lithographic patterning.15,16 The honeycomb lattice consists of different configurations of edges referred to as zigzag and armchair. Practically, however, combinations of both configurations are expected. The type of the edge determines the stability and the electronic structure.17–20 Graphene edges have been characterized using electrochemistry,21 Raman spectroscopy,22,23 and at atomic resolution using scanning probe microscopy24 and electron microscopy.25,26 Theoretically, the modification of the graphene edge is expected to modify the observed properties, such as oxygen groups modulating the electronic and magnetic properties of nanoribbons.20,27 Until now, most of the edge functionalization methods have been used on graphene flakes dispersed in solution, where a single object control and observation is not possible.28–32 There are two examples of chemical modification of the graphene edge carried out in the gas phase in ultrahigh vacuum at low temperatures. Using surface assisted coupling, tetrapyrroles were fused covalently to a graphene edge,33 while in another report individual tetrafluoro-tetracyanoquinodimethane molecules were fixed on the graphene edge by using an electronically inert molecular anchor.34 For both cases, the graphene edge was partially modified by using an elaborate and indirect methodology. The selective homogeneous modification of the edge of a single graphene sheet under ambient conditions has not been explored yet. Here we present a strategy to achieve this and at the same time gather spectroscopic information using the same construct, enabling us to corroborate the chemistry of the functional groups present or formed at the edge.
The deposition of AuNPs serves a twofold purpose. First, the exclusive deposition of particles at the edge can be confirmed by surface characterization as detailed above. Secondly, the presence of AuNPs at the edge allows us to perform selective spectroscopic characterization of the chemistry exclusively of the edge by virtue of surface enhanced Raman scattering (SERS).38,41 Raman spectroscopy is widely used to investigate the electronic and chemical properties of graphene.42–44 It is sensitive to the nature of graphene defects and edges, and has been used to monitor doping effects.45 In our case, the presence of particles at the GrEdge results in a surface enhancement exclusively at the edge and in this manner, the observed SERS signals can be associated as coming predominantly from the edge. Another important advantage of using AuNPs is that it allows for local vibrational mapping by SERS, which has enabled us in the past to obtain information about functional groups on the graphene surface.46 Hence, the construct can be directly used to investigate the presence or absence of functional groups at the patterned GrEdge.
Fig. 2(a) presents background-subtracted38 Raman spectra obtained at the basal plane, at the GrEdge without AuNPs and with AuNPs. Fig. 2(b) presents an AFM image of the GrEdge–AuNPs sample and the corresponding Raman maps (Fig. 2c, see Fig. S6 in ESI† for further analysis). For a better characterization of the edge, incident polarization was kept parallel to the edge, because the D-peak intensity strongly depends on the angle between incident polarization and edge.22 The Raman 2D map shows clearly that the intensity is relatively higher along the edge (indicative of SERS enhancement38,47), while the other Raman maps show that the disorder is exclusively observable at the edge.
Fig. 2 (a) Comparison of Raman spectra from the graphene basal plane (black curve), the graphene edge (red curve) and the graphene edge with AuNPs (blue curve). (b) AFM image of a GrEdge with AuNPs and (c) the corresponding Raman map of D′ (1620 cm−1), D (1330 cm−1, relative to G 1587 cm−1), and 2D (2653 cm−1) intensities (λex: 633 nm, 4.5 mW, 1 s).
Reactive plasma treatment is considered a possible source of generation of oxygenated chemical groups.56 In order to verify if we are sensitive to oxygen-related functional groups, we have deliberately oxidized a GrEdge electrochemically57 and subsequently attached the nanoparticles. In this case, we can observe additional oxygen-related peaks in the SERS spectra (ESI, Fig. S7†). Such oxygen-related peaks are however absent in the SERS spectra of the pristine GrEdge (Fig. 2(a)) suggesting that we have a rather low density of oxygen-related functional groups here. This is most likely due to the very mild plasma conditions used. Stronger plasma conditions are not suited since this would affect the photoresist adversely. The absence of oxygen-related groups at the edge has also been reported in other occasions, e.g. at the graphene edge under inert high vacuum conditions.25 SERS is known to be sensitive down to the single molecule level.47 It is worth mentioning that in the many 100 spectra (Fig. S8, ESI†) that were measured on the pristine GrEdge with varying particle sizes, we could only observe the edge related graphene modes. Hence, we conclude that the patterned edge is most likely predominantly hydrogen terminated, with a rather low density of other functionalities.
Fig. 3 (a) AFM image of a typical GrEdge functionalized with poly(aminobenzylamine) (pABA) and AuNPs, referred to as GrEdge–pABA–AuNPs. (b) Comparison of the Raman spectra at GrEdge–pABA (red curve) and GrEdge–pABA–AuNPs (blue curve). (c) Raman map along the line shown in (a). (d) Map of the C–N stretching mode (1358 cm−1) of the same region as in (a) (λex: 633 nm, 3.4 mW, 2 × 1 s).
Table 1 presents a summary of the assigned Raman modes for the peaks observed commonly in the spectra recorded at many positions on several samples (Fig. S10, ESI†). The Raman modes of pABA have some similarity with that of polyaniline due to their chemical structure.46,62,63 The mode at 1632 cm−1 is assigned to NH2 deformation characteristic of primary amine group,64 while the other modes at 1593 and 1566 cm−1 are due to C–C/C C ring stretching of the benzenoid form.65 The occurrence of two bands at 1358 and 1399 cm−1 is attributed to C–N stretch.66 The mode at 1175 cm−1 is attributed to C–H bending. The band at around 1504 cm−1, arises from aromatic C–C stretching and a mode in low frequency region at 409 cm−1 is assigned to C–N–C bending of amines. The remaining modes at 1137 and 1214 cm−1, which are assigned to C–N stretch and C–C–N bending, may arise due to the free NH2 group, which is not participating in polymerization reaction.64 These characteristics of the Raman spectra of pABA confirm its formation at the GrEdge. A Raman map along a cross-section across the edge is shown in Fig. 3(c), where it is apparent that the pABA modes are found exclusively at the edge. This is further confirmed by the Raman map of the C–N stretching mode, as shown in Fig. 3(d). The spots corresponding to the vibrational modes of the pABA layer are elongated since the signals are convoluted by the diffraction-limited spot and the size of the nanoparticles.
In conclusion, we have demonstrated a versatile strategy for the realization of single functionalized graphene edges by selective and homogeneous non-covalent modification with Au nanoparticles or aromatic amino groups under ambient conditions on an insulating substrate. The presence of aromatic amino groups at the modified GrEdge could be corroborated by local vibrational fingerprinting. By varying the type of functional groups attached at the graphene edge, we can now tune this nanoscale interface in a versatile manner and systematically study its effect on the ensuing physical and chemical properties.
Ti/Pt (50 nm/10 nm) electrode lines were pre-patterned on Si with SiO2 (thickness of 500 nm) with 4-micron gaps using photolithography. The chips were cleaned in a piranha solution (H2SO4 : H2O2) (3 : 1) for 1 minute, and then in an oxygen plasma cleaner for 2 minutes before transfer of graphene. CVD grown-graphene-on-copper was cut into rectangular pieces (typically 2 cm × 2 cm) and a solution of poly(styrene) (PS) (50 mg mL−1 in toluene) was spotted over the CVD graphene foil as a polymer support and dried at 75 °C for 10 minutes. Then, the underlying copper was removed by etching in a solution of hydrochloric acid with added hydrogen peroxide (1.4 mol L−1 HCl + 0.5 mol L−1 H2O2) for 10 minutes. The PS/graphene slab was transferred to the Si/SiO2 chips with the pre-patterned Ti/Pt electrode lines and baked in an oven at 95 °C for 10 minutes before removal of PS in toluene (5 minutes with mechanical stirring). Finally, Si/SiO2/graphene chips were annealed at 600 °C under nitrogen atmosphere for 1 minute to improve the adhesion of graphene onto the silicon chips and remove possible residual organic contamination from the surface of the electrode. Prior to patterning of GrEdge electrodes, the removal of reminiscent copper particles was carried out by electrochemical etching (e-etching) in HCl 0.1 mol L−1, 15 scans in the potential range from −1 V to +0.1 V (vs. Ag/AgCl) at 50 mV s−1. The patterning of GrEdge was also done by photolithography (using a Maskless Aligner MLA-100, Heidelberg Instruments) followed by oxygen plasma etching. Specifically, a polymer layer of the commercial positive photoresist S1805 (Microposit) was spin-coated on top of the sample (∼500 nm thickness), pre-baked for 2:20 minutes at 90 °C and the negative of the desired area was exposed to light (λ = 365 nm). The photoresist from the exposed areas was removed by development using mf-319 developer (Microposit). The electrodes including contacted graphene are hence protected, with graphene being half protected and half exposed, separated by a sharp edge of the resist. The GrEdge was then obtained by exposure of non-protected graphene to oxygen plasma etching. For Raman spectroscopy and AFM imaging, the remaining photoresist was removed in acetone for 15 seconds.
Electrochemical modification was carried out using a three-electrode system comprising of GrEdge as working electrode, platinum wire (Φ = 0.5 mm) as the auxiliary electrode and Ag/AgCl as the reference electrode. The experiments were performed in an electrochemical cell with 20 mL of solution using an Ivium Compacstat potentiostat.
The electrochemical modification was performed in the same electrochemical setup described above. GrEdge–AuNPs were obtained potentiostatically in four deposition steps as following: 0.4 V for 20 s, −0.5 V for 5 s, 0.4 V for 20 s and −0.5 V for 5 s (Fig. S3†). For GrEdge, the concentration of aqueous solution of gold metal salt and the background electrolyte for all the depositions were 10 μmol L−1 KAuCl4 and LiClO4 0.1 mol L−1.
For the functionalization of GrEdge with pABA, 4-aminobenzylamine (4-ABA) aqueous solution at a concentration of 5 mmol L−1 with 0.1 mol L−1 LiClO4 was polymerized using cyclic voltammetry at a potential range of −0.2 V to 0.8 V vs. Ag/AgCl for two cycles. Then, AuNPs arrays were deposited by chronoamperometry as described above by the use of 30 μmol L−1 KAuCl4 in 0.1 mol L−1 LiClO4. The gold salt solution was always prepared right before the electrochemical deposition experiments.
Raman spectra for GrEdge–AuNP electrodes were obtained on LabRam HR 800 equipped with a 1024 × 256 CCD detector (symphony; liquid N2 cooled), a 300 L mm−1 grating, a HeNe laser with an excitation wavelength of 632.8 nm, a 100 × (NA 0.90) objective, and a detection pinhole of 100 μm. The power was maintained at 4.5 mW for acquisitions on all the graphene samples. Raman spectra for GrEdge–pABA–AuNPs were obtained on a JASCO NRS-4100 Raman spectrometer equipped with a 1650 × 256 CCD detector (Andor; air/Peltier-cooled, operating temperature: −60 °C), a 400 L mm−1 grating, a diode laser with an excitation of 632.8 nm, and a 100× (NA 0.90) objective and a power of 3.4 mW. The Raman spectra and maps were recorded using LabSpec 6 for GrEdge–AuNPs electrodes and spectra manager for GrEdge–pABA–AuNPs. The spectrometer for both instruments was calibrated by determining the wavenumber position of Raman line of a silicon substrate at 520.7 cm−1 before data acquisition. Raman spectra and map images were processed using Origin 9.1. The Raman data was fitted with Lorentzian profile in Origin 9.1 or Mathematica to determine the peak position and FWHM. Raman maps were obtained by integrating the intensity in the range of ±10 cm−1 around the main peak. AFM images were obtained using a commercial Dimension IV working in tapping mode in the ambient. AFM images were processed using Gwyddion.
AY thanks the funding from the German Science Foundation (DFG) via the Graduate School of Analytical Sciences Adlershof (SALSA GSC1013). RMI acknowledges CAPES/AvH-Foundation (Iost-CAPES-2017-18) for financial support.
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