Photoluminescent ZnO carbon nanomaterials are an emerging class of nanomaterials with unique optical properties. They each, ZnO and carbon nanomaterials, have an advantage of being nontoxic and environmentally friendly. Their cost-effective production methods along with simple synthesis routes are also of interest. Moreover, ZnO presents photoluminescence emission in the UV and visible region depending on the synthesis routes, shape, size, deep level, and surface defects. When combined with carbon nanomaterials, modification of surface defects in ZnO allows tuning of these photoluminescence properties to produce, for example, white light. Moreover, efficient energy transfer from the ZnO to carbon nanostructures makes them suitable candidates not only in energy harvesting applications but also in biosensors, photodetectors, and low temperature thermal imaging. This work reviews the synthesis and photoluminescence properties of 3 carbon allotropes: carbon quantum or nanodots, graphene, and carbon nanotubes when hybridized with ZnO nanostructures. Various synthesis routes for the hybrid materials with different morphologies of ZnO are presented. Moreover, differences in photoluminescence emission when combining ZnO with each of the three different allotropes are analysed.

1. Introduction

ZnO has been one of the most studied materials for over two decades. Being a semiconductor material with a band gap of 3.37 eV, it luminesces in the blue and ultraviolet region of the visible spectrum. ZnO is an attractive material due to easy accessibility of raw materials, low production costs, and its nontoxicity properties. On the other hand, ZnO has a superior advantage in nanotechnology as it is easy to synthesize as nanostructures [1, 2]. During the last decade, many reports have been published on the synthesis of ZnO nanoparticles [3], nanoflakes [4], hexagonal prismatic rods [5], nanoflowers [6], nanorods [7], nanopillars, or nanosheets using multiple methods of synthesis [8]. These studies have shown that the morphology of ZnO also plays a very important role in determining the physical properties of the material. Presently, the modification of the optoelectronic properties is the current area of focus and one of these methods includes doping with rare earths as well as cationic or anionic substitutions [9, 10]. However, the optical properties also vary as a function of the morphology. Furthermore, the optical properties of bulk ZnO can be modified by nanostructuring via the increase of native (intrinsic) defects in the crystalline structure or via size reduction generating in turn a substantial increase of the surface to volume ratio, thereby producing a stronger surface defect related emission. For example, rose like ZnO exhibits an enhancement in fluorescence properties [11]. Rhombus shaped ZnO nanostructures applied to dye sensitized solar cell have manifested an enhancement in the short circuit current [12]. A recent study has also shown that ZnO nanoparticles can exhibit interesting optical properties with appropriate choice of precursors [13], therefore justifying that, by engineering O and Zn vacancies, it is possible to vary the photoluminescence emission of ZnO. However, the large band gap of ZnO limits its use as a UV light photocatalyst as only 5% of sunlight is captured by ZnO. So, shifting the optical response to the visible range should increase its photocatalytic efficiencies. These methods include doping with metal, nonmetals, and the synthesis of heterostructures [14, 15]. However, ZnO nanoparticles or quantum dots on their own may not serve very well for electron transport mainly due to two reasons: firstly there may not be sufficient contact between the particles themselves and secondly even if there is contact between them, the formation of grain boundaries would hinder electron transport and deteriorate possible device fabrication. However, due to its intrinsic properties and abundance, ZnO is nevertheless widely investigated for large-scale activities such as purifying water and air [8, 16].

Another means to enhance the photoluminescent properties involves the hybridization of the material with carbon based nanomaterials such as carbon nanotubes (CNT), carbon quantum dots (CQDs), or graphene among the carbon allotropes [17, 18]. In fact, carbon based structures such as fullerenes, graphene, CNT, and CQDs have been investigated for the enhancement of performances of photodetectors and photovoltaic devices [1923]. In recent years, carbon based nanostructures have sparked tremendous research interest due to their superior chemical, physical, mechanical, and electronic properties [24]. Since they are abundant and have been successfully shown to be biocompatible, they have been integrated into bioimaging, medical diagnosis, catalysis, and optoelectronic applications [2528].

Among the various carbon allotropes, CQD or carbon nanodots have emerged as a rising candidate for many applications. Due to their high quantum yield [29], low cytotoxicity [30], high photostability [31], and nonblinking character [32] they are seen as potential candidates for applications in photovoltaics, photocatalysis [33], and light emitting diodes [34]. The significantly large amount of π electrons moreover makes them viable for hot carrier solar cells [35]. Yu et al. have recently demonstrated that graphene-CQDs have this potential contrary to CNT-CQD or TiO2-CQDs where charge transfer in the latter two was absent [36].

Graphene on the other hand has shown enormous potential in the fabrication of solar cells. In one instance, graphene is used as a charge conducting layer in a solar cell device [37]. Some other studies have reported that graphene can be used as an electrode for dye-sensitized and organic solar cells [3841]. Similarly, carbon nanotubes (CNT) or cylindrical fullerenes have interesting optical properties because their excitation gives rise to strongly bound excitons [42]. CNT are classified into single-wall carbon nanotube (SWCNT) and multiwall carbon nanotube (MWCNT). SWCNT finds applications in the electronic industry considering their high electron mobility and also in biomolecule sensors [43]. SWCNT have also been studied as a possible solar cell material [44]. Additionally, MWCNT find applications as counterelectrodes in dye sensitized solar cells [45, 46].

This review article aims at bringing together various ZnO-nanocarbon hybrid materials. Three major allotropes of carbon nanomaterials, namely, CNT, graphene, and CQD hybridizing with nano-ZnO, are analysed. This work also evaluates and compares the photoluminescence properties of these hybrid materials in terms of their defects and morphologies determined by various growth techniques which are also reviewed and assessed.

2. Synthesis and Morphological Characterization of ZnO Carbon Based Nanostructures

2.1. ZnO-CQD Synthesis

ZnO-CQD nanohybrids have been prepared by various groups. Yu et al. have used hydrothermal synthesis by introducing Zn(Acetate)2, 2H2O (0.25 M) in an alcoholic solution containing CQD for 8 H at 100°C [47]. The resulting nanohybrids shown in Figure 1 are indeed ZnO-CQD nanocomposite with the CQD encapsulating the ZnO nanoparticle. Different morphologies of ZnO nanoparticles have been combined with CQD. Zhang et al. have used electrospinning hydrothermal synthesis and have obtained ZnO nanoflowers. They subsequently dispersed these ZnO nanoflowers in a solution containing CQD. The nanohybrid material was then dried at 80°C [48]. In their study, the CQDs were themselves prepared via a green synthesis route using sucrose. On the other hand, the ZnO nanoflowers were prepared via electrospinning of zinc acetate dehydrated at 470°C followed by hydrothermal synthesis of the Zn nanospheres using a solution of zinc nitrate hexahydrate and hexamethylenetetramine at 95°C. The nanocomposite was subsequently synthesized by dispersing CQD dots in water along with different concentrations of ZnO nanoflowers.

Another green synthesis approach consists of using D-fructose and NaOH. The nanocomposite was then prepared by hydrothermal synthesis of Zn(CH3COO)2·2H2O in the presence of CQD at 80°C [49]. Other approaches of combining ZnO and CQD using sol-gel methods also exist. ZnO mesoporous films have been studied by Suzuki et al. but contrary to the above-mentioned studies the CQDs were synthesized by less environmentally friendly methods such as Arginine·HCl and 1,2-ethylendiamine. The solution for ZnO was produced using Zn(CH3COO)2·2H2O/EtOH/H2O/Zonyl and then mixed with various concentrations of CQD [50]. The morphology of the hybrid nanocomposite consisted of agglomerated nanocrystals of ZnO blended with CQDs.

Other methods to grow CQD comprise reacting graphite with HSO4 for a longer period of 6 days and subsequently combining them with ZnO prepared by sol-gel methods using Zn(NO3)2·6H2O [51]. Muthulingam et al. have used N doped ZnO via low temperature hydrothermal synthesis at 60°C. The CQDs were isolated by combining carbon black ink H2SO4 and HNO3 at 240°C for 2 hours [52]. Pyrolysis has also been used by Ma et al. for the synthesis of these nanocomposites which consisted of hydrothermal synthesis of ZnO and pyrolysis of a metal organic framework as precursor. Here, oxybisbenzoic acid, zinc nitrate hexahydrate, 4,4′-bipyridine, and N,N-dimethylformamide were combined [53]. Currently, porous materials are regarded as attractive materials for photocatalytic activity due to their large surface areas. Very recently, Ding et al. have combined ZnO foam with CQD [54]. In their work, they synthesized the ZnO foam with a one-step combustion method where Zn(NO3)2·6H2O was dissolved into ethylene glycol monomethyl ether and burnt at 120°C. They also obtained CQD via a green hydrothermal synthesis route using sucrose. The nanocomposite was then formed by dispersing the ZnO foam into the CQD solution.

2.2. ZnO-Graphene Synthesis

For the synthesis of reduced graphene oxide (rGO) ZnO nanocomposites, the first step involves the reduction of the graphene oxide (GO) with hydrazine also known as one-step reduction process. When followed by thermal annealing on a quartz substrate, it is known as a two-step reduction process [55]. The difference in the morphology of the reduced graphene oxide (rGO) via a one-step or two-step process is mostly depicted in the roughness of the films where a two-step reduction process produces a smoother surface with a few cracks and folds [56, 57]. Other than reducing graphene oxide, graphene can be produced by other methods described in this section. The synthesis of ZnO-graphene composites is very well studied in the literature. Synthesis techniques as simple as ultrasonication of ZnO with rGO are available [58]. Liu et al. have used microwave assisted synthesis [59] where commercial graphite was first oxidized via Hummers’ method [60]. GO suspension was added to ZnSO4 and sonicated to homogenise the solution. NaOH was further added to increase the pH to 9 and was subject to microwaves. The pH of 9 was found to be optimal for the precipitation of ZnO.

Additionally, different morphologies of ZnO have been used to fabricate ZnO-graphene nanocomposites. Yin et al. have used electrochemical deposition of ZnO nanorods on the rGO where the conductivity of the rGO determined the growth rate of ZnO nanorods. In effect, the conductivity of graphene is instrumental in producing hydroxyl ions which promote the growth of ZnO rods [57]. CVD growth of graphene on Ni and Cu substrates is also commonly practised. Dong et al. have obtained ZnO nanorod-graphene nanocomposite via hydrothermal synthesis of ZnCl2 at 120°C [61]. Yi et al. have used hydrophilic plasma-etched ZnO nanorods that were subsequently dispersed in a solution containing distilled water and CVD grown graphene [62]. Other ZnO-graphene nanocomposites have also been synthesized where ZnO either was deposited by CVD [63] or was hydrothermally grown as nanorods [64, 65] onto GO obtained via Hummers method. Sol-gel methods have been used to grow ZnO nanoparticles that were subsequently spin coated onto graphene and thermally annealed [66]. The spin coating and annealing were performed twice before the substrate with ZnO seeds on the surface was dipped into zinc nitrate hexahydrate and hexamethylenetetramine at 90°C for 90 min thereby producing nanorods.

Flower shaped ZnO-graphene nanocomposites have also been prepared by various groups. Xu et al. have reduced GO with hydrazine and hydrothermally synthesized ZnO nanoflowers in the presence of graphene [67]. Hummers’ method to prepare graphene followed by hydrothermal synthesis of ZnO nanoflowers has also been conducted by various groups [68]. CVD growth of graphene followed by electrochemical deposition of ZnO nanoflowers has also been carried out [69].

2.3. CNT-ZnO Synthesis

Carbon nanotubes and ZnO nanocomposites have been prepared by various techniques. In the literature, reports of CNT-ZnO hybrids prepared by ball milling are available [70]. Zhang et al. deposited ZnO nanodots onto the CNT films by ultrasonic spray for applications as electrodes [71]. 3D structures of ZnO CNT have also been grown by many groups [72]. Chemical precipitation of ZnO on SWCNT was carried out by Paul et al. [73]. Pulsed laser deposited (PLD) ZnO on MWCNT was synthesized via a hydrothermal method by Saleh et al. [74, 75]. A large majority of the synthesis techniques use a functionalizing agent to prepare the CNT for decoration. The acid treatment debundles the nanotubes and disposes functional groups on their sidewalls which serve as anchorage points for the ZnO nanoparticles. Aziz et al. have dispersed CNT in sodium dodecyl sulphate followed by ball milling the ZnO that was previously obtained by hydrothermal synthesis [76]. CNT have also been grown by spray pyrolysis methods and purified thereafter to get rid of the iron impurities; they were then sintered at 700°C with ZnO prepared by oxidizing Zn dust at very high temperatures under oxygen rich conditions [77]. Another type of ZnO-CNT hybrid structure has been synthesized via Atomic Layer Deposition (ALD). Here coating of ZnO is applied to the outer wall and also to the inner walls of the CNT. Depending upon the inert or functional groups present on the CNT, the morphology of the ZnO coating can be varied. Li et al. have obtained a smooth conformal coating of ZnO on vertically aligned CNT using diethyl zinc and water as Zn and O sources, respectively [78]. Kim et al. have obtained nanoparticle like ZnO coating on the CNT giving a rough appearance to the nanohybrid material [79].

3. Photoluminescence of ZnO Carbon Based Structures

3.1. Photoluminescence of ZnO Nanoparticles

ZnO on its own luminesces in the visible and UV regions. In the visible region the emission is attributed to intrinsic defects induced during the synthesis itself. The UV emission is due to excitonic recombination [80, 81]. Various luminescence emissions in the visible region are possible depending upon the synthesis procedure, morphology, vacancies, and surface defects [82]. Rauwel et al. have studied the influence of hydrate precursor in nonaqueous sol-gel methods and have shown that the PL emission can be tuned by using the appropriate precursor (Figure 2) [13]. Moreover, they have also shown that the embedment of ZnO nanoparticles in a metal oxide matrix produces differences in the PL response due to the passivation of the surface defects [83]. Various colored emissions have been obtained for ZnO: orange [84], blue [85], green, and red [86].

3.2. Photoluminescence of ZnO and Nanocarbon Hybrid Materials
3.2.1. ZnO-Graphene Nanohybrids

Combining ZnO with graphene has produced various photoluminescence emissions. Blue and red emissions have been observed in graphene alone [87, 88]. Khenfouch et al. [89] have succeeded in obtaining white light emission from ZnO nanorod hybridized with few layers of graphene as shown in Figure 3. At room temperature (RT) excitation of 280 nm in the deep UV, they have observed several PL emission wavelengths and have been able to attribute them to various defects. For example, the green luminescence at 524 nm has been attributed to radiative recombination of simple ionized oxygen vacancies. This is very commonly observed in oxygen deficient ZnO [13]. The yellow-orange luminescence is typical of sol-gel or hydrothermal methods [90]. They have attributed the emissions at 482 nm and 498 nm to isolated sp2 clusters within the carbon-oxygen sp3 matrix. Moreover, poor dispersion or aggregation of graphene flakes gives rise to emissions at 684 nm and 686 nm. Kwon et al. have illustrated an increase in the PL intensity corresponding to the free exciton transition (FEE) at 375 nm with increase in GO concentration in their sample. Biroju et al. have grown vertically aligned ZnO on graphene and have compared the PL emission before and after annealing the hybrid material [91]. They noticed a significant improvement in the UV and visible PL on annealing. The reduction in the green and yellow emissions was attributed to the reduction in deep level defects or neutral . The yellow emission was attributed to a reduction in ionized .

Band gap tuning of graphene-ZnO hybrid structures was studied by Singh et al. [92]. They observed not only a blue shift in their photoluminescence emission but also a quenching effect on increasing the rGO concentration. They attribute both phenomena to a depletion region being formed at the interface of the nanocomposite arising due to the p-type conductivity of ZnO and n-type conductivity of graphene. In fact, a green light emitting diode has been fabricated by Wu et al. [93], where they combine ZnO nanowires and graphene. Under forward bias conditions at 6 V they observe a green emission and a reduced UV emission. Here, the injected holes from graphene combine with electrons located in defects in ZnO. Since a nanowire has a large surface to volume ratio, implying that the majority of defects are on the surface, this suggests that the interface between graphene and ZnO plays an important role in the emission properties of the material. Quenching of emission from surface states of ZnO by passivating it with a layer of rGO has also been studied by Han et al. [9496]. Nevertheless, the contrary was observed for the UV emission which was enhanced owing to the increase in sp2 carbon. This phenomenon is further reinforced by Lee et al. who used nonoxidized graphene with ZnO and studied their photoluminescent properties [97]. Their study provides fundamental understanding of the effect of oxygen filling effect of graphene when hybridized with ZnO. The FEE was decreased for ZnO nonoxidized graphene samples on increasing the nonoxidized graphene proportion. They also observed a deep level emission at 530 eV which was attributed to interband transitions from Zn interstitials to O vacancies. Another possible effect was also the excitonic recombination from the conduction band to oxygen defect band gap state. However, for the GO-ZnO, the effect on FEE emission was the opposite. Moreover, other than the formation of a p-n junction another possible explanation to the blue shift was a reduction in oxygen defects when combined with GO which was also translated by a reduction of the green visible luminescence. Furthermore indirect excitation of zinc, commonly termed as sensitization or “antenna” effect [98], has also been observed when combining ZnO with graphene. In fact, Han et al. have observed an increase in the PL luminescence coming from the hybrid material due to an antenna effect, compared to ZnO alone. They attribute it to the resonant excitation of graphene plasmon and their conversion into photons that propagate to the conjugated ZnO surface [94, 99].

3.2.2. ZnO-CQD Nanohybrids

Carbon quantum dots or graphene quantum dots emanate a wide range of luminescence in the visible region depending upon their size and surface defects. Moreover, their photoluminescence emission varies as a function of the excitation wavelength [100102]. In the PL spectra presented in Figure 4(a), a blue shift is observed when excited with higher wavelengths [103]. This also indicates that the CQD can be excited with visible wavelengths. As presented above, nanosized ZnO presents a defect related emission in the blue-green part of the visible spectrum. Such a hybrid structure therefore becomes a good candidate for white light emission [104]. Overlapping of energy bands of the two materials has been successful in producing a charge transfer between them when the hybrid material is excited in the visible or UV regions [47, 104].

In Figure 4(b) a significant peak at 550 nm corresponding to deep level defects in ZnO is visible along with its band edge emission at 375 nm. However, the emission intensities of ZnO-CQD hybrid show a heightened intensity implying energetic interactions in such systems. It also shows quenching in the defect related emission when the ratio of ZnO : C is at 4 : 1. Suzuki et al. [105] have explained that the quenching of the FEE as a function of CQD increase in the sample could be attributed to the internal absorption with higher CQD concentration. In their samples, they also present orange luminescence at 1.85 eV emanating from deep level defects or neutral and it is a result of their synthesis route. They also observe a blue shift in the defect level emission from 1.8 eV to 2.2 eV with increase in CQD concentration. This implies that the oxygen interstitial related defects no longer emit the orange luminescence and the contributions were mostly from surface defects of ZnO and CQD as indicated by the green luminescence. This also implies that the addition of CQD increases the oxygen vacancies in ZnO by the reduction reaction. In a previous work, He et al. have explained the quenching of luminescence with increase in CQD by the lack of dispersion and formation of CQD aggregates which reduces contact between ZnO and CQD thereby quenching the PL spectrum [104]. The mechanisms for the various colored emissions in the visible region are provided in Figure 5. Moreover, they also observed white light emission for intermediate concentrations of CQD along with a nonlinear increase in CQD/ZnO PL ratio with the incorporation of CQD. Such a nonlinear interaction is indicative of excitation transfer through dipole interactions. Using the energy level structure of N doped CQD of Tang et al. [106], they have compared the band gap of ZnO to the HOMO-LUMO states in CQD and have suggested a charge transfer from conduction band of ZnO to the O LUMO of CQD via dipole resonance mechanisms.

3.2.3. ZnO-CNT Nanohybrids

There have been several theoretical and experimental studies related to the defect related luminescent properties enhancement of CNT-ZnO structure [107, 108]. Depending on the method of the ZnO grown with regard to the defects present [109], determined also by its morphology, namely, flower, rod, and dots, the characteristic green emission of ZnO is either intensified or quenched. For example, Gupta et al. noticed enhancement of the photoluminescence emission in their hybrid structure at 510 nm compared to ZnO alone [77]. This enhancement was explained by enhancement of oxygen vacancy related defects at the interface of ZnO-CNT. Considering the large surface to volume ratio, the green emission becomes dominant. On the other hand, in lily-like-ZnO, a broad yellow-green emission (ionized oxygen vacancy, oxygen vacancy, or Zn interstitial) band along with a strong near band edge emission is indicative of a high quality ZnO sample [110]. When combined with ZnO, the red shift of the FEE band was attributed to excitonic recombination in shallow traps or surface states created on hybridizing. Moreover, quenching of the visible luminescence or filling of defects when combined with CNT along with a transfer of photoexcited charges from ZnO to CNT empty states has also been reported. Stability of these hybrid structures is also of importance as studied by Zhu et al. [111]. They studied ZnO nanoparticles with a high density of stacking faults hybridized to CNT on growth and after 24 days. In both cases their PL spectra were identical indicating the stability of these structures. They both consisted of emissions at 376 nm and 490 nm. After annealing, the peak at 490 nm became more intense and blue shifted to 485 nm indicating that new defects such as O and Zn (peak at 632 nm) vacancies were formed through a probable conversion of stacking faults into oxygen vacancies. All of the above were studied under band gap excitation. In general, each peak has its significance and a band edge emission intensity helps identify the crystalline quality of ZnO used. Yellow-green emission corresponds to a recombination of a photogenerated hole and an ionized oxygen vacancy [112]. The FEE emission enhancement not only is a function of crystallinity but is also enhanced by the surface plasmon emission effects of CNT [113]. Moreover ZnO-CNT systems exhibit charge transfer from ZnO to CNT manifested by enhanced quenching of the luminescence and very short lifetime as compared to bulk ZnO alone [114] as determined by time resolved PL. In order to better understand all the phenomena that occur at the interface between ZnO NPs and CNT, theoretical calculations have been performed by Chai et al. to model the charge transfer from ZnO to metallic CNT [115]. More recently, ZnO carbon based nanohybrids have been synthesized by nonaqueous sol-gel method. One observes that ZnO nanoparticles with sharp edges are directly connected to the CNT network (Figure 6(a)). The direct synthesis of ZnO nanoparticles in the presence of CNT and their bonding to CNT promote the green emission usually exhibited by oxygen vacancies (Figure 6(b)). The complete result of these investigations will be published in a forthcoming paper and cannot be discussed in this review.

4. Conclusions

The technological advancement in the synthesis and characterization of metal oxide nanomaterials is a rapidly growing field. Zinc oxide is a very versatile optical material having a relatively wide range of UV absorption and demonstrating photostability. Moreover, being nontoxic therefore makes it biocompatible. ZnO nanomaterials can be synthesized via a broad range of chemical of physical methods that enable obtaining different morphologies. Defect engineering or surface modification by choosing appropriate synthesis techniques is a way of tailoring the photoluminescence properties of the material that has been demonstrated in numerous reports. ZnO has already been exploited by industry, with applications in photocatalysis or in sunscreens which are solar filters that block all ultraviolet radiations.

The interest in ZnO has not only grown but, with the advent of the abundant and ecofriendly carbon based nanomaterials, hybrid ZnO carbon based materials have aroused the curiosity of several researchers. This work has focused on the three widely used carbon based materials that combine with ZnO nanoparticle: graphene, CNT, and carbon quantum dots. However the synthesis of ZnO hybrid for each carbon based material is different. The synthesis is a minimum 2- or 3-step procedure with synthesizing the carbon nanomaterial as a first step. The second step consists usually of growing the ZnO nanomaterial and the third step involves combining them. Sometimes a fourth step such as postsynthesis annealing is necessary when passivating defects. A two-step method reduces the number of steps by growing the ZnO directly on the carbon based material as a second step.

CNT are usually grown by CVD methods on metal catalyst nanoparticles such as Ni. Furthermore, as-grown CNT contain a large number of impurities. Treating the CNT with acid or heat has a twofold advantage: firstly, it gets rid of the residual impurities in the as-grown sample and secondly it creates functional groups on the side wall of the CNT which facilitate their decoration with various nanoparticles. A more environmentally friendly technique to purify the CNT is sonication. ZnO can also be directly grown via, for example, an Atomic Layer Deposition (ALD) coating on CNT, among other techniques. CQD used in ZnO-CQD hybrid materials, on the other hand, can be synthesized by green synthesis routes, for instance, by reacting D-fructose with NaOH or via sucrose. Green synthesis routes have been developed as a more economical and valuable alternative for the large-scale production of metal nanoparticles to avoid the use of the generation of hazardous substances and can be based on the utilization of plant extracts or molecules produced by plants that may act as both reducing and capping agents, for example. Less ecofriendly techniques by acid treating graphite are also used in the production of CQD. In graphene-ZnO hybrid material, rGO is obtained from graphene oxide in one or two steps. GO is usually reduced via hydrazine and could be followed by a thermal treatment. GO is usually obtained from Hummers’ method. CVD grown graphene on Ni and Cu is also used in the hybrid mix. Other techniques combine the carbon nanomaterial with ZnO with the latter having been prepared by spray pyrolysis, ball milling, hydrothermal synthesis, or spin coating.

These hybrid materials present photoluminescence properties which vary as a function of the carbon based materials used. In fact, the emission from ZnO, either UV or visible, can be engineered by passivating or generating defects at the interface of the hybrid materials, considering their large surface to volume ratios. Characteristic emissions from these materials such as red, blue, green, yellow, and orange can therefore be enhanced or quenched. In some cases white light emission has also been obtained. Moreover, charge transfer in these materials due to overlapping bands in the excited state makes them highly suitable for photocurrent generation and next generation of solar cells, including flexible, transparent photovoltaics. Carbon and ZnO are ecofriendly, biodegradable, and omnipresent. Even though more ecofriendly synthesis routes exist for the carbon based materials, nonetheless, very few reports where the former are applied to the synthesis of hybrid ZnO-carbon based nanomaterials, are available. For example, presently, acid treatments of CNT and graphite and the use of hydrazine which are all very toxic are of common usage. Nevertheless, being of very high potential in various optoelectronic applications, new and green routes for their synthesis are the need of the hour.

Competing Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


The authors wish to acknowledge the Estonian Research Council (Grant PUT431), the European Regional Development Fund Project TK134 (TAR16019), MENESR, MAEDI French Ministries (Parrot Program no. 33787YJ), and the Norwegian Research Council. The NAMUR Project of the European Regional Development Funds is acknowledged for access to the FEI Titan G2 80-200.