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This article presents novel, rapid, and environmentally benign synthesis method for one-step reduction and decoration of graphene oxide with gold nanoparticles (NAuNPs) by using thermostable antimicrobial nisin peptides to form a gold-nanoparticles-reduced graphene oxide (NAu-rGO) nanocomposite. The formed composite material was characterized by UV/Vis spectroscopy, X-ray diffraction, Raman spectroscopy, X-ray photoelectron spectroscopy, field emission scanning electron microscopy, and high-resolution transmission electron microscopy (HR-TEM). HR-TEM analysis revealed the formation of spherical AuNPs of 5–30nm in size on reduced graphene oxide (rGO) nanosheets. A non-volatile-memory device was prepared based on a solution-processed ZnO thin-film transistor fabricated by inserting the NAu-rGO nanocomposite in the gate dielectric stack as a charge trapping medium. The transfer characteristic of the ZnO thin-film transistor memory device showed large clockwise hysteresis behaviour because of charge carrier trapping in the NAu-rGO nanocomposite. Under positive and negative bias conditions, clear positive and negative threshold voltage shifts occurred, which were attributed to charge carrier trapping and de-trapping in the ZnO/NAu-rGO/SiO2 structure. Also, the photothermal effect of the NAu-rGO nanocomposites on MCF7 breast cancer cells caused inhibition of ~80% cells after irradiation with infrared light (0.5Wcm−2) for 5min.
In last two decades, carbon materials such as graphite and carbon nanotubes have been studied extensively. Graphene is a 2-D carbon material with a honeycomb structure of conjugated sp2 carbon1. Because of its remarkable and unique physical, chemical, electrical, optical, and biological properties, graphene has gained attention in the scientific community and industry2–4. Graphene has been used to produce biosensors, biomolecules carrier, solar cells, catalysis agent, optoelectronics, batteries, solar cells (dye sensitized or organic) and for energy storage5–8. Most studies have focused on the chemical conversion of natural graphite for large-scale production of graphene or graphene oxide (GO).
To synthesize graphene, different physical, chemical, and biological methods have been developed9. Additionally, various strategies have been employed not only to isolate graphene sheets to form single sheets with or without changing its properties, but also to synthesize reduced form of GO10–12. Chemicals such as hydrohalic acid13, hydrazine14, p-phenylenediamine15, sodium borohydride16, and hydroquinone17 have been used to reduce GO. However, because of their explosive nature and toxicity towards biological materials, rGO is not used in biochemical applications9. Sonication was shown to exfoliate and reduce GO. However, because of the high sonication frequency required, structural damage may occur, which affects the physiochemical properties of the GO18. Thus, there is demand to produce reduced graphene using eco-friendly and rapid methods. For green reduction of GO, different biomolecules such as amino acids19, proteins (bovine serum albumin)20, microorganisms21, plant extracts22, sugars23, and ascorbic acid24 have been used. In the present study, thermostable peptides were used as bio-reductants to reduce GO at very high temperature in a very short time. To improve the electrical, thermal, and optical properties of GO, metal nanoparticles such as silver, copper, platinum, and gold (AuNPs) were decorated on the honeycomb structure25. Numerous studies have examined AuNPs-GO composites because of their wide range of applications in catalysis, sensors, diagnosis, and therapy, among others26. It is known that metal nanoparticle-decorated graphene oxides are promising materials for use in various optoelectronic applications because of their unique plasmonic properties27. This is essential to enhanced light-matter interaction in graphene for their use in optoelectronic devices. The incorporation of Au NPs in graphene may produce plasmonic effects that lead to the enhancement of optical absorption, resulting in improved performance of optoelectronic devices. Furthermore, the charge confinement in Au NP incorporation in graphene can create electrical bi-stability, demonstrating memory characteristics due to charge trapping and de-trapping28.
Different approaches have been used to form AuNPs-rGO composites. In the first approach, metal nanoparticles and GO are reduced separately and then mixed to form a composite, which is a time-consuming process. In another approach, metal nanoparticle precursors and GO are reduced in a single reaction. However, few studies have focused on the rapid biosynthesis of AuNPs-rGO composites in one pot. In this study, we demonstrate the rapid and simultaneous bio-reduction of GO and Au3+ to form rGO decorated with AuNPs at 121°C for 15min. Nisin is a lantibiotic that is a thermostable peptide, active at 121°C for 15min and stable at −20°C29. It consists of 34 amino acids: ITSISLCTPGCKTGA- LMGCNMKTATCHCSIHVSK. Lactococcus lactis subspecies lactis isolated from milk-based products and vegetables contains nisin peptide. Nisin is an FDA-approved antimicrobial peptide used as a food preservative30. Nisin peptide has a wide range of antimicrobial activities against gram-positive microorganisms. Here, we present one-step synthesis of a gold nanoparticle–reduced graphene oxide (NAuNP–rGO) nanocomposite using thermostable antimicrobial nisin peptides in an autoclave. In a single pot, AuNPs and rGO were formed in a very short time. The reduced GO with dispersed AuNPs was obtained in a 15-min reaction. No toxic chemicals or harsh reaction conditions were used in the synthesis of NAuNP-rGO nanocomposites that would exclude it from being used for biomedical applications. Additionally, for electrochemical application, the NAu-rGO nanocomposite was used in a thin film transistor (TFT) for use in memory devices as shown in Fig. 1 where an enhanced response in transfer characteristics was observed. These formed NAu-rGO nanocomposites were evaluated for therapeutic application for NIR photothermal therapy (PTT), where enhanced photothermal activity of AuNPs because of the presence of rGO was achieved.
The reduction of GO and formation of NAu-rGO nanocomposite was initially analyzed by UV-Vis spectrometry. Figure 2a shows the UV-Vis absorption spectra of GO, reduced GO (rGO), and NAu-rGO nanocomposite. GO showed exhibited an absorption maximum at 230nm because of the π→π* transition of the involving C=C bonds (Fig. 2a; blue). UV-Vis spectroscopy also showed absorption at ~300nm in GO because of the n→π* transition of the C=O bonds (Fig. 2a; blue). The red shifting in the absorbance towards ~270nm was observed after reduction the reducing reaction, indicating formation of rGO (Fig. 2a; red), which agrees with observations of previous reports31. Simultaneous reduction of GO and Au3+ formed the NAu-rGO nanocomposite. The appearance of an absorption peak at ~270nm for rGO and ~530nm for NAuNPs was observed by UV-Vis spectroscopy (Fig. 2a; black), clearly indicating the formation of NAuNPs on the surface of reduced graphene sheets.
The crystal structure of GO, rGO, and NAu-rGO nanocomposite was analyzed by XRD, which was also used to determine the interlayer distances of GO and rGO (Fig. 2b). The 2θ diffraction peak at 10.30° of GO showed a relative interlayer distance of 0.85nm, indicating the presence of oxidized graphite layers. After reduction by thermostable peptides, rGO showed a broad diffraction peak at 25.6°, suggesting that GO was successfully reduced32. The XRD pattern of the NAu-rGO nanocomposite showed peaks at 2θ values of approximately 38.20°, 44.48°, 64.58°, and 77.60°, which were assigned to the (111), (200), (220), and (311) crystallographic planes of cubic structure of elemental NAuNPs, respectively (Fig. 2b), confirming the formation of NAuNPs in the composite. The XRD pattern is matched with JCPDS card No 004–0784.
For more information related to structural and electrical properties, Raman spectroscopy of the rGO and NAu-rGO nanocomposite was performed. Figure 2c shows the Raman spectra of the GO powder (black) and NAu-rGO nanocomposite (red). In graphene, the G peak and 2D peak represent sp2-hybridized carbon-carbon bonds. The G peak showed a band at ~1593cm−1 and that of D was at ~1345cm−1, corresponding to the A1g mode and E2g mode of the carbon atom, respectively. A change in the electronic conjugation state is indicated by a change in the ID/IG ratio. The ID/IG ratio before reduction was 0.9 for GO, and 1.22 for the NAu-rGO nanocomposite, demonstrating that at the end of the process, the sp2 domain was reduced in size33. The graphene sheets possibly showed a break during reduction, creating greater numbers of sp2 domains, which indicated that the reduction process had occurred34. Additionally, in the NAu-rGO nanocomposite, increased intensities of the 2D peak (~2681cm−1) and S3 peak (~2931cm−1) indicated improved graphitization and the presence of few layered graphene sheets in the NAu-rGO nanocomposite. Additionally, in the NAu-rGO nanocomposite, increased intensities of the 2D peak (~2681cm−1) and S3 peak (~2931cm−1) indicated improved graphitization and the presence of few layered graphene sheets in the NAu-rGO nanocomposite35.
Figure 3a shows the XPS survey spectra of the GO and NAu-rGO nanocomposite, which shows characteristic peaks for C1s and O1s. The survey spectra also revealed the presence of Au 4f and N 1s elements in the NAu-rGO nanocomposite. From the survey spectra, O1s peak was clearly weakened in the NAu-rGO nanocomposite as compared to GO and the peak associated with C1s was predominant in NAu-rGO nanocomposite compared to in GO. An Au 4f peak was observed by XPS of the NAu-rGO nanocomposite after reduction of Au3+ to Au°. Additionally, the presence of N 1s in the NAu-rGO nanocomposite indicate peptides on the surface of the rGO. Figure 3b shows characteristic XPS spectra of metallic Au°, which is centred at 83.6 and 86.9eV, suggesting the formation of AuNPs on the surface of NAu-rGO nanocomposite36. The contribution of carbon-oxygen binding arrangement in GO and NAu-rGO nanocomposite was demonstrated by high-resolution XPS spectra of region C 1s (Fig. 3c and d). Two main components were present from C=C/C–C at ~284.56eV and C–O at ~286.61eV, and one minor component from C=O at 288.1eV in high-resolution spectra from C1s of GO (Fig. 3c)37. After reduction by thermostable nisin peptide, the intensities of the oxygen-dominated groups (hydroxyl and epoxy groups) were remarkably decreased and the C–C bond remained dominant as a single peak at higher energy (Fig. 3d). These results confirm that the structure of the thermostable peptide significantly changed the structure of GO during the reduction process19.
Figure 4a and b shows FE-SEM micrograph of the rGO and NAu-rGO nanocomposite. The clear surface of the rGO is shown in Fig. 4a, whereas the NAu-rGO nanocomposite showed a rough surface in Fig. 4b because of the presence of AuNPs. The presence of NAuNPs on the surface of rGO was evident in magnified FE-SEM micrograph (Fig. 4b; Inset). Figure 4c,d show HR-TEM micrographs of the as-prepared NAu-rGO nanocomposite. The AuNPs were dispersed on the surface of rGO and nearly unaggregated, but in a polydispersed form (Fig. 4d; Inset). All AuNPs were present on the surface of the rGO and did not protrude from the surface, indicating very strong interactions between rGO and NAuNPs through nisin peptides. The average diameter of the AuNPs was 25nm, which agrees with the size obtained by XRD analysis. The Energy-dispersive X-ray spectroscopy (EDS) study confirmed that the formed nanoparticles on the rGO surface are of Au NPs (Supplementary Fig. 1) showing the characteristics signals of elemental gold metal36.
Different synthetic and biological chemicals were used to reduce GO (Table 1), such as L-cysteine, bovine serum albumin, and hormone, under very high alkaline conditions. Microorganisms, plant extracts, and some amino acids reduce GO at room temperature or high temperature under alkaline conditions, but the process is very time consuming. Thus, we used thermostable antimicrobial nisin peptides to reduce GO under neutral condition. Various chemicals could simultaneously reduce the AuNPs and GO to form AuNPs-rGO nanocomposites. Table 2 shows the different chemicals and reaction conditions used to synthesise AuNPs-rGO nanocomposites. Some reducing components required high alkaline and high temperature conditions for the reaction. For tyrosine-, bovine serum albumin-, ascorbic acid-, and tannic acid-mediated synthesis of AuNPs-rGO nanocomposites, rGO was first synthesized and then used as a template for AuNPs synthesis. In this study, the thermostable nisin peptide was used for one-step reduction, which is an efficient and rapid reduction process for forming AuNPs-rGO nanocomposites.
The mechanism of the reduction process is not still clear. Due to the thiol groups of peptides, high temperature, and high pressure, the formation of AuNPs-rGO nanocomposites may have occurred. The thermostable nisin peptide consists of thiol group containing amino acids like methionine and cysteine, which may act as hydrogen donor to the oxygen moieties of graphene oxide37. The carbonyl, hydroxyl, and epoxide groups contribute for the oxygen moiety in graphene oxide38. Under mild basic condition, the oxygen containing carbonyl and epoxide groups are converted to hydroxyl group and thiol group containing amino acids reacts with hydroxyl group with removal of water molecule. Diez et al. demonstrated reduction of graphene oxide under high pressure of 80bar at 180°C, whereas in this present work, 1.034bar (15 lbs) at 120°C was used for the reduction process39. Thus, there was very negligible role of pressure and temperature for the reduction reaction. In our previous work, we have demonstrated the synthesis of gold nanoparticles using thermostable antimicrobial nisin peptides at autoclave reaction condition40. The antimicrobial peptide remained active even after formation of AuNPs at 121°C. Au3+ ions have affinity towards thiol groups forming Au – S bonds, which converts Au3+ to Au° under high temperature. Therefore, the thiol group contributed for the simultaneous and rapid reduction reaction to form reduced graphene oxide and NAuNPs under mild pressure and high temperature. These nisin peptides also contribute to stabilization of the AuNPs as well as rGO.
The use of rGO is widely focused on optoelectronic applications because of its superior electrical and optical properties. The Fermi levels and work function of graphene and rGO can be tailored via chemical doping. This property has been utilized recently in device applications such as high-efficiency chemically doped solar cells. Therefore, rGO is expected to provide a multi-band structure to effectively manipulate charge carrier trapping behaviour in TFT memory devices. Several research groups have tested GO and rGO as charge-trapping media for organic TFT non-volatile memory devices and obtained satisfactory results53, 54. A simple approach for modulating the trapping behaviour of solution-processed ZnO TFT non-volatile memory devices involves placing NAu-rGO nanocomposites in dielectric layers.
A schematic of the NAu-rGO nanocomposite-based ZnO TFT memory device is presented in Fig. 5a, on which a layer of NAu-rGO nanocomposite was introduced in-between the SiO2 and ZnO layers. Transfer characteristic [Drain current (IDS) vs. gate voltage (VGS)] of ZnO TFT memory device embedded with rGO at ZnO and SiO2 interface is shown in Fig. 5b. The transfer curve exhibits small hysteresis window during the double sweep mode. Figure 5c shows the transfer characteristics of the ZnO TFT embedded with NAu-rGO nanocomposite in-between ZnO semiconductor and SiO2 dielectric layers with various drain voltage (VDS). A clear clockwise wider hysteresis IDS-VGS curve was obtained by sweeping VGS in the forward (−40 V to 120V) to reverse (120V to −40 V) voltage direction. It is seen from the figure that the obtained hysteresis became wider with varying drain voltage from 10 to 30V, indicating more charge carriers are trapped at the charge trapping media in-between ZnO semiconductor and SiO2 dielectric layer. This suggests that the large hysteresis is attributed to electron/hole trapping in the NAu-rGO nanocomposite during the forward and reverse voltage sweep. Comparison of the reference device with the no NAu-rGO nanocomposite (Fig. 5d) revealed a low hysteresis characteristic, confirming that the presented memory TFT operated through electrostatic charging and discharging of the NAu-rGO nanocomposite rather than the interface between ZnO and SiO2 dielectric layers. Large numbers of structural defects were formed in the chemically synthesised NAu-rGO nanocomposite, which were the main cause of charge trapping of the NAu-rGO nanocomposite ZnO TFT memory device. However, the ratio of sp2 and sp3 fractions can be tuned by additionally reducing GO. Therefore, its band gap can be easily altered and then controllability transforms GO from an insulator to a semiconductor and to a graphene-like semi-metal. It is thought that the semi-metallic nature of rGO, having a covalently bonded honeycomb lattice structure, overcomes various defects including holes, which play an important role as charge trapping sites in charge trap memory devices. Transfer characteristics of ZnO TFT embedded with NAu-rGO nanocomposite exhibited a wider hysteresis window than that observed for various Au NP- and r-GO-based nano-floating gate dielectrics55, 56. Figure 5e shows the output characteristics of the ZnO semiconductor layer with SiO2/NAu-rGO nanocomposite dielectric stack memory TFT as the gate voltage was varied from 0 to 40V. The drain current increased with increasing gate voltage and reached saturation because of pinching-off of the active channel of the transistor, exhibiting typical n-type transistor behaviour. The electrical parameters of a ZnO TFT non-volatile memory device embedded with NAu-rGO nanocomposites at the interface of ZnO and SiO2 were calculated by applying standard MOSFET equations to its transfer characteristic. The saturated mobility was extracted to be 0.52cm2/V.s. Forward and reverse threshold voltage was observed to be 14.52 and 45.52V, respectively. The on/off current ratio was found to be in the range of 103.
To identify the switching behaviour of the NAu-rGO nanocomposite-based ZnO memory TFT, a gate bias of±50V was applied for the writing and erasing processes. Under the positive voltage bias condition (writing process), a positive voltage threshold voltage shift (Vth) was observed in the transfer characteristics. Figure 6a shows the increased positive shift of transfer curves with increasing programming time. After programming at+50V for 0.1s, Vth increased from 22.25V for a programming time of 0.1s to 61.30V for a programming time of 0.01 ms. Figure 6b shows the transfer curves of erasing characteristics. After programming at −50 V for 1s, a negative erasing gate pulse was applied for an erasing time of 1s as the source, drain, and channel regions were grounded. Upon applying a −50 V gate bias (erasing process), the transfer curve shifted down by approximately 40–50V. These reversible threshold voltage shift behaviours of NAu-rGO nanocomposite-based ZnO memory TFT may be related to carrier trapping and de-trapping in the NAu-rGO nanocomposite, suggesting that the NAu-rGO nanocomposite can be used as a charge trap layers for memory device application.
Figure 6c shows a simple description of charge trap and de-trap processes in the form of schematic band diagram of a ZnO-TFT-based non-volatile memory device embedded with NAu-rGO nanocomposite at the interface of ZnO semiconductor and SiO2 dielectric layers. After applying positive voltage during the programming stage, electrons accumulated in the channel were transferred into the NAu-rGO nanocomposites. It is expected that most electrons were trapped at the NAu-rGO nanocomposites (Fig. 6d). These trapped electrons occupied through shallow level states to deep level states. Charge trapping energy levels in chemically synthesized NAu-rGO nanocomposites may be attributed to structural defects and the work functions of NAu- rGO, the channel layer, and the gate dielectric. Large numbers of structural defects form in the chemically synthesized NAu-rGO nanocomposites and are a primary cause of charge trapping in related devices. Additionally, there were several oxygen groups between the rGO and NAu-rGO nanocomposites. These oxygen groups trapped charge carriers efficiently. Therefore, additional trapping levels were present with the NAu-rGO nanocomposites. During the erasing process, electrons occupied at a shallow level can be firstly de-trapped and transported to the channel, and then deep level state-trapped electrons were de-trapped (Fig. 6e). This study is particularly innovative because it uses a nanocomposite with a core–shell structure that functions a charge storage node.
Minimally invasive treatment methods such as near infrared PTT have gained attention over the past few decades. Various biomolecule-functionalized rGOs and Au-functionalized rGOs have been used as photothermal active nano-formulations against cancerous cells using NIR-wavelength laser illumination, and photothermal conversion efficacy and biocompatibility have been examined57–59. Here, to demonstrate the biomedical application of the peptide-synthesized NAu-rGO nanocomposite in vitro, PTT was performed on breast cancer cells (MCF7 cells), where cells were irradiated with NIR radiation using an 800-nm diode laser (power=0.5W/cm2) for varied times with GO, NAuNPs, and NAu-rGO nanocomposites. Here, to demonstrate the biochemical application of the biological synthesized NAu-rGO nanocomposite, in vitro PTT was performed on breast cancer cells (MCF7 cells), where cells were irradiated with near infra-red radiation using an 800-nm diode laser (power=0.5W/cm2) for varied times with GO, NAuNPs, and NAu-rGO nanocomposite. Cell viability was tested for 2 and 24h after each exposure time. For biomedical application of the NAu-rGO nanocomposite, cytotoxicity analysis was performed on cervical cancer cells (HeLa cell line) and fibroblast cells (L929 cell line) using the MTT assay, where cells were grown in presence of NAu-rGO nanocomposite for 24 and 48h (Fig. 7). In both cells, dose-dependent cytotoxicity was observed. Up to 40μg/mL concentration, both cells showed ~90% viability for 24 and 48h incubation. A further increase in the concentration showed increased toxicity towards both cell lines. Therefore, 10μg/mL of NAu-rGO nanocomposite was used and compared with the same concentration of GO and NAuNPs as controls. UV-Vis-NIR spectroscopy analysis was performed for GO, rGO, and NAu-rGO nanocomposite to examine their absorbance in the NIR region before application of the as-prepared nanocomposite for photothermal activity (Supplementary Fig. 2). The NAu-rGO nanocomposite showed absorbance at ~540nm, which is the characteristic absorbance of Au NPs, but showed no absorbance at 800nm. From TEM micrographs (Fig. 4c and d), it is evident that the formed NAu NPs on rGO are varied in size, which may be the reason for the absorbance in visible and NIR regions. A similar phenomenon was observed by Komarala et al. and Sharma et al. where gold nanospheres decorated with layered double hydroxides (LDHs) and silica nanoparticles showed no absorbance in the NIR region, but demonstrated photothermal activity at 808nm60, 61.
Further, the photothermal transduction efficacy of GO, NAuNPs, and NAu-rGO nanocomposite in cell medium was measured by irradiating the solution with a near infrared laser (laser power density of 0.5W/cm2) containing GO, NAuNPs, and NAu-rGO nanocomposite (10μg/mL) (Fig. 8a). The rapid rise in the temperature of the medium to 49°C was observed within 2min of laser exposure, while GO and NAuNPs were only at 25°C and 38°C, respectively, under the same irradiation conditions. Thus, GO showed much lower energy conversion efficiency after laser irradiation. After decoration of the NAuNPs on the GO sheets, spherical NAuNPs functioned as catalysts to improve the photothermal properties of GO. The photothermal conversion efficacy of NAuNPs, which showed a lower temperature increase compared to NAu-rGO nanocomposites, was also improved. The cumulative effect of the absorbance of NAu NPs and rGO in the NIR region (Supplementary Fig. 2) may be responsible for the photothermal activity of NAu-rGO nanocomposites. The Au NPs have a tendency to attach at defects and vacancies of rGO in NAu-rGO nanocomposites, which seizes the mobility of NAu NPs upon laser irradiation in the nanocomposite and consequently, there is no shape transformation of the spherical NAu NPs. Moreover, laser irradiation caused deoxygenation of rGO, which in turn increased the thermal conductivity and heat transfer capability of the rGO, which indeed improved the photothermal convergence properties of the NAu-rGO nanocomposites at 808nm62.
Next, the photothermal conversion efficiency of NAu-rGO the nanocomposite was analyzed by MTT assay, where irradiation experiments were performed in presence of breast cancer cells (MCF7 cell line) and compared with GO and NAuNPs. Here, MCF7 cells were incubated with 10μg/mL GO, NAuNPs, and NAu-rGO nanocomposite for effective interaction of the particles with the cells and then the medium was irradiated for different times (1–5min). After exposure followed by incubation for 2h, cells survival was analyzed by MTT assay (Fig. 8b). MCF7 cells showed only 50% survival after 2h of incubation when irradiated for 5min with 10μg/mL NAu-rGO nanocomposite. In contrast, more than 90% survival of MCF7 cells was observed in the presence GO under the same reaction conditions. Further, these cells were incubated for 24h and the percent survival of the cells was calculated. Less than 20% survival was observed after 24h incubation in NAu-rGO nanocomposite-treated cells (Fig. 8c). In contrast, more than 80% and 45% survival rates of MCF7 cells were observed in the GO and NAuNPs, respectively, under the same reaction conditions as used for the NAu-rGO nanocomposite. Therefore, compared to GO and NAuNPs, the NAu-rGO nanocomposite showed improved and effective photothermal conversion efficacy and can be used for biomedical applications.
To demonstrate the therapeutic efficiency of the NAu-rGO nanocomposite, a qualitative live/dead cell assay was performed using PI, DAPI, and FDA dyes following irradiation of MCF7 cells with an 800-nm diode laser for 5min (Fig. 9). Cells were observed by CLSM. The living cells cannot uptake the PI dye (nucleus penetrating) because of its intact cell membranes. In contrast, necrotic or early apoptotic cells can take up the PI. Therefore, for this study we used FDA dye to stain live cell nucleus, PI for dead cells and DAPI for nucleus of live and dead cells. MCF7 cells in absence of GO, NAuNPs, and NAu-rGO nanocomposite showed intact morphology as demonstrated by the blue and bright green fluorescence and absence of red fluorescence (Fig. 9a–d) after 24h of incubation. Very few cells were affected by the photothermal activity of GO, as very few cells showed red fluorescence and a large number of cells showed green fluorescence (Fig. 9e–h). From the MTT assay results, NAuNPs clearly caused the death of more than 50% of MCF7 cells. This effect is shown in Fig. 9i–l, which shows an increase in the number of red fluorescent cells and lower number of green fluorescent cells. Although NAuNPs showed good photothermal activity against MCF7, the NAu-rGO nanocomposite exhibited remarkable photothermal transduction efficacy, as there was nearly no green fluorescence in CLSM analysis for MCF7 cells (Fig. 9m–p). Both the MTT assay and CLSM analysis showed that the as-prepared NAu-rGO nanocomposite have high potential as near infrared PTT agents and low cytotoxicity towards mammalian cells, and thus can be used for various biomedical applications such as antimicrobial agents and drug delivery vehicles.
In summary, we developed a novel, rapid synthesis method for eco-friendly NAuNPs decorated with rGO nanocomposite using thermostable antimicrobial nisin peptide under autoclave conditions. Various analytical methods were used to confirm the reduction of Au3+ ions and GO. The as-prepared NAu-rGO nanocomposite showed charge transfer characteristics and photothermal energy conversion. Solution process sol-gel derive ZnO TFT memory devices with SiO2/NAu-rGO nanocomposite dielectric stack were developed. The transfer characteristics of the memory device showed a hysteresis window in dual sweep mode. The charge trapping and de-trapping on SiO2/NAu-rGO nanocomposite dielectric stack was verified by the shifts in threshold voltage by applying positive and negative bias voltage. In vitro cytotoxicity effects (MTT assay) of the NAu-rGO nanocomposite on the L929 and HeLa cell lines showed very low dose-dependent cytotoxic effects towards mammalian cell lines. The as-prepared nanocomposite showed very effective near infrared PTT activity compared to NAuNPs and rGO following 5-min exposure against MCF7 breast cancer cells, in which more than 80% cell growth was inhibited. The large-scale green production of the rGO and NAu-rGO nanocomposite using nisin thermostable peptides is more effective than existing chemical reduction methods and avoids the use of hazardous chemicals and harsh preparation methods.
All reagents were purchased from Sigma Aldrich Co. Ltd. (St. Louis, MO, USA) and were of analytical grade. HiMedia Laboratories Ltd. (Mumbai, Maharashtra, India) provided media components. The solubility of all chemicals in water was 100% and no further purification was required for experiments.
The method described by Hummers and Offeman was used to prepare GO by oxidizing natural graphite63. The aqueous brown solution of GO (4mg/mL) was used for further experiments. For each experiment, GO sonication was performed to obtain homogeneous graphene sheets.
The NAu-rGO nanocomposite was synthesized by using thermostable nisin peptides (2.5% [w/w], approximately 1×106 IU/g). In phosphate buffer (pH 6.8), 5mg/mL of nisin peptides were added to an aqueous solution of 0.5mM HAuCl44H2O and incubated for 2h at 25°C room temperature. GO (0.8mg/mL) was then dispersed in the above mixture under sonication for 1h. The same method without HAuCl4 was employed to synthesize rGO. Both solutions were autoclaved at 121°C under 15 lbs pressure for 15min. The synthesis of rGO and NAu-rGO was monitored by UV-Vis spectroscopy.
Zinc acetylacetonate hydrate (Sigma Aldrich) was dissolved in 2-methoxyethanol to produce a 0.1M solution. The as-prepared precursors were stirred for 2h to ensure that they were completely dissolved. For device fabrication, a B-doped p-type Si wafer (resistivity between 0.001 and 0.003 Ω-cm) served as the gate electrode, and 300nm of thermally grown SiO2 was used as the dielectric layer. Prior to spin-coating, SiO2/Si substrates were cleaned ultrasonically in acetone and methanol for 10min each. They were then rinsed with deionized water for 5min. The previously prepared AuNPs-rGO nanocomposite solution was spin-coated onto the SiO2/Si substrates at 2000 rpm for 20s. Next, ZnO solution was spin coated at 4000rpm for 40s to produce layers that were ~25nm thick. The films were dried on a hot plate at 200°C for 10min to evaporate the solvents. Finally, the films were annealed for 1h in a tube furnace at 400°C to decompose and oxidize the precursors.
Finally, Al electrodes were thermally grown on the active layer using a shadow mask, with the channel width and length maintained at 1000 and 100µm, respectively. The resulting source and drain electrodes were approximately 100nm thick. Current–voltage (I–V) measurements were performed using a semiconductor analyser.
UV-Vis spectra were measured with a UV 1800 spectrophotometer (Shimadzu, Kyoto, Japan). X-ray diffraction (XRD) studies of the nanocomposites were performed with an X-ray diffractometer (Bruker, Billerica, MA, USA) with Cu Kα radiation (λ-0.15418nm). Raman spectra were collected from a Renishaw confocal microscope Raman system with laser 532nm (Gloucestershire, UK). Field-emission scanning electron microscope images were obtained with a Carl Zeiss 200 FEG FESEM (Jena, Germany). Transmission electron microscopy (TEM) and high-resolution TEM (HRTEM) analyses were performed using a JEM-3010 (JEOL, Tokyo, Japan) operated at an accelerating voltage of 300kV. X-ray photoelectron spectroscopy (XPS) analysis was performed on a PHI 5000 Versa Probe (ULVAC PHI, Chigasaki, Japan) spectrometer using Al Kα as the irradiation source. Current–voltage (I–V) measurements were performed using a semiconductor analyzer (Keithley 4200, Tektronix, Beaverton, OR, USA) with a probe station.
Human cervical cancer cells (HeLa) and human breast adenocarcinoma cells (MCF7) were purchased from ATCC (Manassas, VA, USA), and sub-cultured in McCoy’s 5A medium containing fetal bovine serum (10%) and antibiotics (100g/mL penicillin and 100μg/mL streptomycin) from Sigma (St. Louis, MO, USA). In 25-cm2 tissue culture flasks, the cells were enriched and kept in an incubator at 37°C with CO2 (5%) humidified atmosphere. After 90% confluence of the cells, Dulbecco’s phosphate-buffered saline (DPBS) was used to wash these cells. To detach the cells, 2mL of trypsin−EDTA solution (0.25%) was applied and finally these cells were dispersed in complete medium (10mL).
The percent viability of the cells was quantified by MTT assay where the cells (2×105 cells/mL) were incubated with 3-(4,5-dimethylthiazol-2-yl)-2,5-diphenyltetrazolium bromide (MTT) solution and colorimetrically observed for the mitochondrial oxidation of MTT using EZ-CYTOX-Enhanced Cell Viability Assay Kit. The cells were incubated in DMEM (Dulbecco’s modified Eagle Medium) with different concentrations of NAu-rGO nanocomposite (10, 20, 40, 60, 80 and 100μg/mL). After incubation for 24 and 48h, NAu-rGO nanocomposite with medium was removed and freshly prepared 10μL MTT solution was added. The cells were further incubated for 4h and then treated with dimethyl sulfoxide (100μL). Finally, the absorbance at 405nm was measured for each well using an ELISA plate reader (BIORAD, USA).
In-vitro photothermal conversion efficacy was analysed with an 800-nm infrared diode laser with a power density of 0.5W/cm2 (Changchun New Industries Optoelectronics Technology Co., Ltd., Changchun, China) and a thermometer (UNI-T 1310, UNI-T Electronic Corp., Dongguan, China). MCF7 breast cancer cells incubated with rGO, NAuNP, and NAu-rGO nanocomposites for 24h were exposed to an 800-nm diode laser (power=0.5W/cm2) for 1–5min and allowed to grow for 24h. Following laser illumination, the cells were incubated with the fluorescent labels 4′,6-diamidino-2-phenylindole (DAPI), propidium iodide (PI), and fluorescein diacetate (FDA) dyes to produce blue, red, and green fluorescence from live and dead cells, respectively, for visualization under a confocal laser scanning microscope (CLSM). Cell viability was quantified using the MTT assay at 2 and 24h post-treatment with the laser.
This research was supported by the Ministry of Science, ICT and Future Planning, Republic of Korea (2013M3A6A8073184, NRF-2017R1A2B3011676, NRF-2017R1A4A1014806). This work also was supported by the Energy Efficiency & Resources Core Technology Program of the KETEP, granted financial resource from the Ministry of Trade, Industry & Energy, Republic of Korea (20153030091450, 20153010092130). This work was supported by the 2015 KU Brain Pool Fellowship of Konkuk University. This research was supported by the KU Research Professor program of Konkuk University.
J.L., Y.C.K., and L.Z. supervised the project. S.V.O. designed experiments. S.V.O., M.K., M.Z.A., N.D.T., S.K.S.P., L.Z., and D.L. performed experiments. S.V.O., J.H.L., L.Z., Y.C.K., and J.L. wrote and revised the manuscript. All authors analyzed the results and reviewed the manuscript.
The authors declare that they have no competing interests.
Electronic supplementary material
Supplementary information accompanies this paper at doi:10.1038/s41598-017-10777-1
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Jung-Kul Lee, Email: rk.ca.kuknok@eehrkj.
Yun Chan Kang, Email: rk.ca.aerok@gnakcy.
Liaoyuan Zhang, Email: moc.621@nauyoailz.