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Unveiling the Direct Correlation between the CVD-Grown Graphene and the Growth Template.

1. Introduction

Graphene is one-atomic-layer-thick carbon atoms with honeycomb lattice structures, which is the first kind of 2-dimensional materials that have been experimentally discovered since 2004 [1]. With its outstanding physical and chemical properties, graphene has been proposed as an emerging nanomaterial for the next-generation electronic devices, such as flexible electronics, high-frequency transistors, or photonic devices, exceeding the performance of conventional devices [2-9]. Ever since its experimental demonstrations, various synthesis routes have been introduced for the production of graphene [10-16]. To list a few, mechanical exfoliation can yield high-quality of pristine graphene, but it lacks the large-scale production capability, an essential feature required for industrial applications [1]. Liquid-phase exfoliation technique, commonly used in the synthesis of graphene oxide (GO) or graphene intercalation compound (GIC), is promising for large-scale production. However, this approach suffers from the relatively low-quality of graphene as well as the difficulty in layer control, thereby limiting its applications in high-performance electronic devices [12-14]. Chemical vapor deposition (CVD) method, which utilizes catalytic metal substrates as the growth template, is well-known to produce large-area, high-quality graphene films suitable for electronic applications [17,18]. In CVD process, several factors can affect the properties of the grown graphene film. In particular, the electrical properties of graphene are highly dependent on the grain boundaries, which induce charge carrier scatterings and thus deteriorate the carrier mobility [19]. Since the grain boundaries mostly originate from the lattice mismatch during the growth process that is primarily influenced by the orientation of catalytic metal substrates, single-crystal metals like Ge (110), Cu (111), or Ni (111) have been investigated as the alternative growth template to avoid such grain boundaries, and high-quality single-crystalline graphene has been demonstrated which epitaxially grew onto those substrates [20-22]. However, the process involved with the production of single-crystalline materials is generally cost-intensive, which is not suitable for widespread industrial applications. Another strategy to improve the electrical properties of graphene is to increase the domain size, which can be achieved by suppressing the nucleation densities during the synthesis [23-25]. Such approaches include introducing oxygen gas, using enclosed metal catalysts, or resolidifying metallic substrates to create smooth surfaces during the growth stage. Among these various approaches in the CVD process, modifying the surface morphologies of catalytic growth substrates is considered one of the most viable approaches for obtaining high-quality graphene. Mechanical or chemical treatments are typically used in such approach which significantly reduces the impurities present in the metal catalysts, the major source of the nucleation center, leading to the improved carrier mobility [26-32]. In this work, we revisit the role of surface morphology of metal catalyst to the quality of CVD graphene using commercially available copper foil via simple chemical treatments and analyze the resulting physical properties. Chemical treatments on the growth substrates typically involve etching process, and we show that proper control of the metal catalyst pretreatment can be a simple yet facile approach to enhance the overall quality of CVD-grown graphene.

2. Experimental

2.1. Synthesis and Transfer of Graphene. Copper foil (99.8%, 25 [micro]m thickness, 13,382, Alfa Aesar) was pretreated with 5.8% nitric acid (HN[O.sub.3]) under varying exposure time from 0 s (reference sample) to 60 s and washed with D.I. water, followed by acetone and isopropyl alcohol (IPA). We note that the synthesis result of reference sample exhibited relatively low reproducibility compared with those samples synthesized from the pretreated metal catalysts, likely due to the impurities present on the metal catalyst surface. After the chemical treatment, the copper foil turned to slightly dark brown due to the oxidation. The copper foil was then loaded into the CVD chamber which was purged with Ar (100 sccm) for 10 min. After annealing the copper under [H.sub.2] (10 sccm) environment for 30 min at 1000[degrees]C, graphene synthesis was carried out with C[H.sub.4] (20sccm) and [H.sub.2] (10sccm) for 30 min (~30mTorr). After the growth, the samples were rapidly cooled down to room temperature.

The as-grown graphene was transferred to Si[O.sub.2] (300nm)/Si substrate via PMMA--(poly(methyl methacrylate)-) assisted transfer method. In brief, PMMA (9% in anisole) was spin-coated onto the graphene, which was dried in oven to remove the solvent. Copper foil was then etched away by ferric chloride solution, and the PMMA/ graphene stack was thoroughly rinsed with mild hydrochloric acid and D.I. water. After transferring to the target substrate, PMMA was finally removed by acetone.

2.2. Characterization. Graphene channel was formed by standard photolithography and [O.sub.2] plasma etching process. Source and drain contacts (Ti/Au, 10/50 nm) were deposited by e-beam evaporation system. Heavily p-doped Si substrate was used for the gate electrode, and the Si[O.sub.2] layer was working as the gate insulator. Source-drain voltage was fixed to 0.05 V, and gate voltage ([V.sub.G]) sweep was from -100 V to 100 V to measure the source-drain currents ([I.sub.DS]). The obtained [I.sub.DS]--[V.sub.G] curve is shown in Figure 1(b). Sheet resistance of graphene was measured by 4-point probe (CMT-SR2000N, Advanced Instrument Technology). Surface morphology of graphene was analyzed by optical microscopy (OM, Eclipse LV150, Nikon) and scanning electron microscopy (SEM, S-4800, Hitachi). Raman spectra were obtained from Alpha300R, WITec, with excitation wavelength at 532 nm. Transmittance was measured by UV-vis NIR spectroscopy (Carry 5000, Agilent).

3. Results and Discussion

In this work, low-pressure CVD with copper substrate was used for the graphene synthesis and nitric acid was applied to modify the surface morphology of the as-received copper foil (see Experimental). In general, HN[O.sub.3] reacts with copper and forms Cu[(N[O.sub.3]).sub.2] which is soluble in water as described in the following chemical reaction [26].

Cu(s) + 4HN[O.sub.3](aq) [right arrow] Cu[(N[O.sub.3]).sub.2](aq) + 2N[O.sub.2](g) + 2[H.sub.2]O (1)

The overall reaction is dependent on the nitric acid treatment time, where the amount of Cu[(N[O.sub.3]).sub.2] increases with prolonged treatments which renders the copper surface morphology more rough and nonuniform as illustrated in Figure 2(a), leading to potential defect sites during the CVD process. The as-received pristine copper, with only conventional solvent rinsing such as acetone or isopropanol, typically exhibits bright regions due to the impurities naturally present in the copper (Figure 2(b)), which can be eliminated with such acid treatment. As shown in Figure 2(c), these bright spots are substantially reduced, and the surface becomes relatively smoother only after 30 s of acid treatment. However, extended chemical treatments typically result in highly nonuniform surface morphology due to the continued etching of the copper (Figure 2(d)). After 60 s of such reaction, the resulting morphology of copper becomes significantly rough compared to the pristine one despite the removal of impurities as shown in Figure 2(e).

To verify the effect of copper morphology to the growth of CVD graphene, surface morphologies of the as-transferred graphene grown on copper substrates with various pretreatment conditions were analyzed. Figure 3 shows the OM and SEM images of graphene sheets prepared under the same synthesis conditions and transferred onto the Si[O.sub.2] substrates. Several multilayer graphene domains are observed from the pristine copper substrate due to the large number of impurities which act as the nucleation center during the growth stage (red arrow, Figure 3(a)) [33]. The presence of typical wrinkle formation is also observed which originates from the difference in thermal expansion coefficients between the graphene and metal substrate as well as during the transfer process (blue arrow, Figure 3(b)) [34]. The bright spot is the polymer residue resulting from the transfer process (white arrow, Figure 3(b)) [35]. Such formation of multilayer graphene was significantly suppressed with copper substrate treated by 30 s of nitric acid as shown in Figures 3(b) and 3(f). However, multilayer graphene started to reappear with increasing acid treatment to 45 s due to the corresponding increase in roughness of the copper substrate (Figures 3(c) and 3(g)). Activated carbon atoms tend to aggregate more at the rough surface, which consequently increases the probability of multilayer formation [11, 25]. After 60 s treatment time, the presence of multilayer graphene even became comparable to that of the pristine copper case as shown in Figures 3(d) and 3(h). Figure 3(i) illustrates the distribution of monolayer graphene formation over the multilayer of the above, showing that monolayer graphene is mostly synthesized for the 30 s treatment case.

Optical transmittance of the respective graphene films was measured to evaluate the appearance of multilayer graphene (Supporting Information, Figure S1). Transmittance of 30 s sample was ~97.5% at 550 nm, similar to the theoretical value of monolayer graphene film (97.7%) [7]. This value was decreased to ~97.2 and ~96.5% with increasing acid treatments of 45 and 60 s, respectively, whereas the pristine copper sample showed ~96.9% transmittance likely due to the presence of multilayer graphene and light scattering induced from the rough graphene surface lowering the transmittance. These optical microscopy and transmittance results confirm that the formation of multilayer graphene is highly affected by the morphology of underlying catalytic growth substrate, which can be modulated and remedied via appropriate pretreatment conditions.

Next, Raman spectroscopy analysis was performed to investigate the overall quality of graphene sheets prepared from different types of copper substrates. All graphene films under study exhibit primarily monolayer characteristics with G and 2D peaks at ~1580 and 2680 [cm.sup.-1], respectively, and intensity ratio I(2D)/I(G) of nearly 2 as shown in Figure 4(a) [20]. We note that the intensity of D peak at ~1350 [cm.sup.-1], representing the degree of defects in [sp.sup.2] carbon domains, increases with acid treatment time, that is, the roughness of metal substrates (Figure 4(b)). We speculate that the increase of defect is related to multilayer graphene patches, which is formed by surface impurities or rough surfaces [36]. The value of full width at half maximum (FWHM) of 2D peak is another indicator commonly used to evaluate the quality of graphene, where the sharp peak is associated with the high-quality [37]. FWHM of 2D peak from 30 s sample is ~35[cm.sup.-1] which is comparable to that of the mechanically exfoliated graphene, and gradually increases to ~43 and ~52 [cm.sup.-1] for 45 and 60 s cases, respectively, while the pristine sample being ~44 [cm.sup.-1] (Supporting Information, Figure S2) [38]. Arial defect analysis was also performed using Raman mapping. Figure S3 (Supporting Information) presents the I(D)/I(2D) intensity ratio mapping, which indicates the overall defects in the assynthesized graphene increase with acid treatment time from 30 to 60 s. These results elucidate that the quality of CVD graphene is closely related to the starting morphology of the growth substrate.

The effect of defect sites in graphene on electrical properties was investigated via conductivity and field-effect mobility measurements. The sheet resistance of graphene film prepared from the aforementioned conditions was measured by the 4-point probe as shown in Figure 1(a). Consistent with previous results, the 30 s sample again showed the lowest sheet resistance of 290 [+ or -] 24 [OMEGA] x [sq.sup.-1], lower than that of the pristine graphene (420 [+ or -] 30 [OMEGA] x [sq.sup.-1]), potentially due to the low defects present on the graphene which act as the charge carrier scattering sites lowering the overall electrical properties in the graphene film [19]. The sheet resistance was also increased to 427 [+ or -] 33 and 643 [+ or -] 45 [OMEGA] x [sq.sup.-1] with increasing acid treatment time (45 and 60 s, resp.) and the associated increase in the degree of defect sites. We also note that large deviations of sheet resistance values also occur with increasing chemical treatments to the metal substrate. We suspect this phenomenon is closely related to the nonuniformity of copper surface morphology originating from the prolonged etching process.

The effect of surface morphology of graphene on the electrical property was further analyzed from the field-effect mobility measurement. Graphene-based field-effect transistor (FET) was fabricated by standard photolithography with Ti (10 nm)/Au (50 nm) contacts formed by thermal evaporation as illustrated in Figure 1(b). Consistent with the sheet resistance measurement, electron mobility was highest with 30 s sample (1280[cm.sup.2] x [V.sup.-1] x [s.sup.-1]) and decreased to 957 and 613[cm.sup.2] x [V.sup.-1] x [s.sup.-1] for 45 and 60 s cases, respectively, with the pristine sample being 1156 [cm.sup.2] x [V.sup.-1] x [s.sup.-1] (Figure 1(b)). The charge neutral point of graphene is slightly p-doped which is well-matched with Raman data shown in Figure S2.

4. Conclusions

In this work, we showed that the quality of CVD-grown graphene is closely related to the underlying surface morphology of the metal catalyst growth template. Via simple and facile modification of the metal catalyst with commonly used acid, high-quality graphene film could be readily obtained, an important factor to consider for the widespread industrial applications of graphene-based electronic devices. The acid reacts with the metal catalyst by etching the metal surface, thus removing the impurities present which tend to deteriorate the overall quality of graphene. We believe that the simple yet effective approach proposed in this study, which enables the synthesis of high-quality graphene films with low defects, will benefit a variety of graphene-based functional devices such as thin-film transistors, optoelectronic devices, and flexible electronics.

https://doi.org/10.1155/2018/7610409

Data Availability

The SEM data used to support the findings of this study are included within the article. The Raman spectrum data used to support the findings of this study are included within the article. The OM image data used to support the findings of this study are included within the article. The FET mobility data used to support the findings of this study are included within the article. The transmittance data used to support the findings of this study are included within the supplementary information file(s). The Raman mapping data used to support the findings of this study are included within the supplementary information file(s).

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This work was supported by Basic Science Research Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Education (2015R1D1A1A0105791) and the Ministry of Science and ICT (2016R1A2B4014762).

Supplementary Materials

Figure S1: transmittance data shows the reduction of optical transmission by multilayer graphene under each condition. Figure S2: the FWHM value of the Raman 2D peak supports that the graphene quality depends on the nitric acid treatment time. Figure S3: Raman mapping results support that as-synthesized graphene shows high uniformity. (Supplementary Materials)

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Junghyun Lee [ID], (1) Jihyung Seo [ID], (1) Sungchul Jung, (2) Kibog Park [ID], (2) and Hyesung Park [ID] (1)

(1) Department of Energy Engineering, School of Energy and Chemical Engineering, Low Dimensional Carbon Materials Center, Ulsan National Institute of Science and Technology (UNIST), Ulsan 44919, Republic of Korea

(2) Department of Physics, Ulsan National Institute of Science and Technology (UNIST), Ulsan 44919, Republic of Korea

Correspondence should be addressed to Hyesung Park; hspark@unist.ac.kr

Received 29 April 2018; Accepted 24 June 2018; Published 19 August 2018

Academic Editor: Mohamed Bououdina

Caption: Figure 1: Electrical properties of the graphene film showing the (a) sheet resistance and (b) FET mobility characteristics (inset image indicates the FET device structure).

Caption: Figure 2: (a) Schematic of copper pretreatment process via nitric acid. The surface roughness of copper increases with longer acid treatment time. SEM images of surface morphologies of (b) pristine copper and (c-e) after various acid treatment conditions.

Caption: Figure 3: Optical (a-d) and SEM (e-h) images of graphene synthesized from various types of copper substrates and transferred onto the Si[O.sub.2] substrates and (i) the corresponding distribution on the ratio of monolayer to bilayer graphene formation. Red, blue, and white arrows indicate few layer graphene, wrinkles, and PMMA residues on the graphene, respectively.

Caption: Figure 4: (a) Raman spectra of graphene films synthesized from different types of copper substrates. (b) Zoom-in regions of D peak from the whole Raman spectra. As shown in (b), the D peak intensity increases with prolonged acid treatment time.
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Title Annotation:Research Article
Author:Lee, Junghyun; Seo, Jihyung; Jung, Sungchul; Park, Kibog; Park, Hyesung
Publication:Journal of Nanomaterials
Date:Jan 1, 2018
Words:3887
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