Article | Open

Self-surface charge exfoliation and electrostatically coordinated 2D hetero-layered hybrids

  • Nature Communications 8, Article number: 14224 (2017)
  • doi:10.1038/ncomms14224
  • Download Citation
Published online:


At present, the technological groundwork of atomically thin two-dimensional (2D) hetero-layered structures realized by successive thin film epitaxial growth is in principle constrained by lattice matching prerequisite as well as low yield and expensive production. Here, we artificially coordinate ultrathin 2D hetero-layered metal chalcogenides via a highly scalable self-surface charge exfoliation and electrostatic coupling approach. Specifically, bulk metal chalcogenides are spontaneously exfoliated into ultrathin layers in a surfactant/intercalator-free medium, followed by unconstrained electrostatic coupling with a dissimilar transition metal dichalcogenide, MoSe2, into scalable hetero-layered hybrids. Accordingly, surface and interfacial-dominated photocatalysis reactivity is used as an ideal testbed to verify the reliability of diverse 2D ultrathin hetero-layered materials that reveal high visible-light photoreactivity, efficient charge transfer and intimate contact interface for stable cycling and storage purposes. Such a synthetic approach renders independent thickness and composition control anticipated to advance the development of ‘design-and-build’ 2D layered heterojunctions for large-scale exploration and applications.


Ultimate two-dimensional (2D) anisotropy with atomically thick layered structure is both an ideal low-dimensional system for fundamental study and an elemental building block for designed assembly1,2,3,4,5,6,7,8,9,10. Elaborate functionalities can rationally be tailored with precise molecular scale control through artificial assembly based on judicious selection and coordination of heterogeneous counterparts11,12,13,14. Intriguing surface effects and physical–chemical properties have gradually been uncovered in 2D hetero-layered materials owing to their large surface-to-volume ratio and confined thickness at an atomic scale15,16,17,18. The 2D materials, specifically metal chalcogenides, possess exquisite photo- and electrochemical capabilities that include energy storage batteries/supercapacitors and energy conversion photo/electrocatalysis systems10,19,20. Unlike electronic transistor devices, these applications generally require large quantities of 2D hetero-layered materials. Though a wide variety of 2D layered semiconductor materials have been exfoliated into individual layers, these layered materials typically undergo large extent of swelling phase induced by intercalator or solvation species21,22,23. Realization of high-volume exfoliation with ultrathin sheet-like crystallite in a facile manner and clean medium still remains scarce. Moreover, the issue of lattice mismatching hinders composition customization of heterostructures owing to the ineffective direct epitaxial growth of some mismatched metal chalcogenide materials. Collectively, all the aforementioned issues limit the scalability of 2D ultrathin hetero-layered metal chalcogenides towards fundamental exploration and advanced functional applications.

Herein, we readily exfoliate the metal chalcogenide semiconductor ZnIn2S4 into single-unit-cell layered structure (ca. 2.5 nm) via a self-surface charge exfoliation in pure water medium. Successive electrostatic coupling with another transition metal chalcogenide (for example, MoSe2) enables construction of arbitrary ultrathin hetero-layered hybrids in a large scale. Such an approach offers salient features, that is, independent thickness and composition control of individual layer assembly, and no constraint by lattice matching prerequisite into functional ultrathin heterostructures. Distinct emission lifetime reduction and photoluminescence quenching of the hetero-layered hybrid ascertain strong interlayer coupling and efficient charge transfer between the components. Surface and interfacial-dominated photocatalysis, a promising strategy for solar energy conversion24,25,26,27,28,29,30,31,32, is adopted to demonstrate the reliability of the catalytically rich 2D ultrathin ZnIn2S4/MoSe2 hetero-layered material. The as-synthesized ZnIn2S4/MoSe2 concurrently realize efficient separation and transfer of photogenerated charge carriers, acceleration of surface proton reduction with abundant active sites as well as enhanced visible light absorption that circumvent the limitations of conventional photocatalysts33. Consequently, the ZnIn2S4/MoSe2 displays high-performance visible-light-driven H2 evolution activity of 6,454 μmol g−1 h−1, 15 and 4 times as high as that of bulk and bare ZnIn2S4 nanosheets, respectively. Importantly, the 2D hetero-layered hybrid shows high stability with prolonged 80 h cycling and catalytic reactivity retention after storing over a few months that further attests to the integrity of the constructed 2D materials for prospective advanced applications. Furthermore, we test the applicability of this approach on other 2D metal sulfides, namely CdIn2S4 and In2S3 that also show scalable self-surface charge exfoliation. Similarly, the constructed hetero-layered hybrids of CdIn2S4/MoSe2 and In2S3/MoSe2 feature enhanced photocatalytic activity and stability.


Self-surface charge exfoliation of ultrathin ZnIn2S4 layers

The ultrathin single-unit-cell ZnIn2S4 layers were prepared via a facile low-temperature refluxing method, followed by a water-assisted surfactant/intercalator-free exfoliation process, as schematically illustrated in Fig. 1a (for more details, see Methods). Scanning electron microscopy (SEM) images of bulk ZnIn2S4 in Fig. 1b and Supplementary Fig. 1 reveal a uniform morphology of sheet-like structure. The energy-dispersive X-ray spectroscopy (EDX) (Supplementary Fig. 2) and X-ray diffraction (XRD) (Supplementary Fig. 3) analysis confirm the elemental composition and high purity of the as-synthesized ZnIn2S4 with hexagonal phase structure (cell parameters of a=b=3.85 Å, c=24.68 Å, JCPDS No. 65–2,023).

Figure 1: Schematic illustration of the synthesis of single-unit-cell ZnIn2S4 layers and characterization.
Figure 1

(a) A self-surface charge promoted exfoliation of clean and freestanding single-unit-cell ZnIn2S4 layers in surfactant/intercalator-free medium. (b) Scanning electron microscopy (SEM) image of bulk ZnIn2S4. Scale bar, 2 μm (c) Transmission electron microscopy (TEM) image of single-unit-cell ZnIn2S4 layers. Scale bar, 50 nm. (d) Atomic force microscopy (AFM) image and (e) corresponding height images of single-unit-cell ZnIn2S4 layers. Scale bar, 200 nm. The inset in b is photograph of Tyndall effect of the ZnIn2S4 suspension; insets in c are the corresponding selected-area electron diffraction (SAED) pattern and high-resolution TEM (HRTEM) image of single-unit-cell ZnIn2S4 layers.

Notably, the dispersion of ZnIn2S4 in deionized (DI) water reveals a strong negatively charged surface with a zeta potential value of −36.5 mV (Supplementary Fig. 4). This can be ascribed to the presence of excess amount of S2− that has been adsorbed onto the ZnIn2S4 surface during the synthesis process34,35,36. Other supporting evidences are appended in Supplementary Figs 5 and 6. The self-surface charge within the layered nanostructure significantly weakens the interaction between ZnIn2S4 interlayers. Owing to Coulombic repulsion, these layers repel each other and are readily exfoliated with the assistance of shear forces triggered by mild sonication in the absence of any intercalator and surfactant species (Supplementary Fig. 7).

Transmission electron microscopy (TEM) images (Fig. 1c and Supplementary Fig. 8) of the as-exfoliated ZnIn2S4 layers display 2D sheet structure with a nearly transparent feature, implying the ultrathin nature of the exfoliated product. This self-surface charge promoted exfoliation can be corroborated by the controlled experiment of ultrasonic exfoliation of ZnIn2S4 synthesized from the addition of a stoichiometric amount of S2− (denoted as ZnIn2S4-S, see Methods for more details), as illustrated in Supplementary Fig. 9. The as-obtained ZnIn2S4-S displays a weak zeta potential of −5.2 mV (Supplementary Fig. 10). Accordingly, the dispersion of ZnIn2S4-S can be easily centrifuged after ultrasonication. The TEM image in Supplementary Fig. 11 demonstrates that the ZnIn2S4-S is composed of aggregated layers. In addition, negatively charged ZnIn2S4 surface can also be validated by a layer electrostatic self-assembly demonstration of the ZnIn2S4 nanosheets on positively charged 3-aminopropyl-triethoxysilane (APTES)-modified glass substrate (Supplementary Figs 12 and 13). Correspondingly, a pale yellow thin film can be observed only for the strong negatively charged ZnIn2S4 (−36.5 mV) coating on the glass surface. SEM image reveals uniform coverage/assembly of strong negatively charged ZnIn2S4 nanosheets on the positive APTES-glass substrate. Conversely, no obvious adsorption of the weak negatively charged ZnIn2S4-S (−5.2 mV) has been observed on the glass substrate. Altogether, these findings confirm the existence of strong negatively self-charged ZnIn2S4 surface that facilitates facile interlayer exfoliation of ultrathin ZnIn2S4 nanosheets without the assistance of surfactant/intercalator additives.

Moreover, the corresponding selected-area electron diffraction pattern in Fig. 1c inset shows clear bright spots that correspond to the hexagonal structure and single-crystalline characteristic of the ultrathin ZnIn2S4 nanosheets. In addition, the high-resolution TEM (HRTEM) image in Fig. 1c inset displays distinct lattice fringes of ca. 0.32 nm, corresponding to the (102) crystallographic plane of ZnIn2S4. The typical Tyndall effect observed for the as-exfoliated ZnIn2S4 suspension using a red laser (Fig. 1b, inset) indicates the formation of freestanding and highly dispersed ultrathin ZnIn2S4 layers. More importantly, the colloid ultrathin ZnIn2S4 nanosheets can be easily exfoliated into large scale (Supplementary Fig. 14) that is essential for further utilization.

TEM characterization cannot unambiguously determine the ultimate thickness of the layers. In this context, atomic force microscopy (AFM) is used to provide an estimated quantitative layer thickness. As shown in Fig. 1d, the topography of the as-prepared ZnIn2S4 presents 2D structure with smooth surface. The corresponding height profiles in Fig. 1e show that the typical thickness of the as-exfoliated layers is 2.5 nm, validating the ultrathin nature of the ZnIn2S4. Considering that the c parameter of ZnIn2S4 is 24.68 Å (Supplementary Fig. 15), the thickness of ZnIn2S4 is well in agreement with the thickness of a unit cell along the [001] axis37. Thus, it is reasonable to deduce that each ultrathin ZnIn2S4 nanosheet with a thickness of ca. 2.5 nm is a single-unit-cell ZnIn2S4 atomic layer. According to the diffusion formula of t=d2/k2D (d is the particle size, k is a constant, D is the diffusion coefficient of electron–hole pairs)5,7, the ultrathin single-unit-cell ZnIn2S4 atomic layer will significantly shorten the diffusion length and time of charge carriers taken to reach the surface, enable the photoexcited electron–hole pairs to transport from the interior to the surface fast, and thus lead to higher charge separation efficiency of the ultrathin ZnIn2S4 than its counterpart of bulk ZnIn2S4, as verified by the photocurrent and photoluminescence (PL) analysis in Supplementary Figs 16 and 17.

Generalized synthesis of ultrathin CdIn2S4 and In2S3 layers

The suitability of self-surface charge exfoliation as a general approach for large-scale preparation of other 2D metal sulfides, that is, CdIn2S4 and In2S3, has also been demonstrated. As shown in Supplementary Fig. 18, the CdIn2S4 dispersion in DI water shows a strong negative charge with a zeta potential value of −39.7 mV. TEM images in Supplementary Fig. 19 demonstrate the 2D sheet structure of the exfoliated CdIn2S4 nanosheets without using any surfactant or intercalator under moderate ultrasonication. The inset in Supplementary Fig. 19 shows HRTEM image where the distinct lattice fringes of 0.33 nm correspond to the (311) crystallographic plane of CdIn2S4. AFM topography reveals the ultrathin structure of the exfoliated CdIn2S4 with the thickness of 2.3 nm (Supplementary Fig. 20). Typical Tyndall effect is observed for the as-exfoliated CdIn2S4 suspension (Supplementary Fig. 21), indicating the formation of large-scale freestanding and highly dispersed CdIn2S4 layers. Moreover, the respective EDX and XRD analyses in Supplementary Figs 22 and 23 confirm the as-synthesized CdIn2S4 nanosheets with cubic phase structure (JCPDS No. 27-0060).

Likewise, this self-surface charge strategy is also exploited to exfoliate In2S3 into a large-scale colloidal dispersion of ultrathin nanosheets (Supplementary Fig. 24). Zeta potential measurement displays a strong negatively charged surface (zeta potential of −41.9 mV) of In2S3 (Supplementary Fig. 25). TEM images in Supplementary Fig. 26 show 2D sheet structure with distinct lattice fringes (ca. 0.32 nm) of In2S3 (311) crystallographic plane. The thickness of the obtained In2S3 is 4.5 nm (Supplementary Fig. 27). Moreover, EDX result confirms the elemental composition of In2S3 and XRD pattern reveals the pure cubic phase of the synthesized In2S3 (JCPDS No. 65-0459) (Supplementary Figs 28 and 29).

Construction of hetero-layered hybrids

Recent advances in creating heterostructures based on 2D atomic crystals by artificial combination of various 2D materials have shown to strongly modulate electronic and optical properties17. By virtue of the 2D configuration with large surface area, along with its complementary high interfacial contact with other components, the single-unit-cell ZnIn2S4 layers provide a favourable platform for the fabrication of hybrid composite17,38. In this context, MoSe2 nanosheets are integrated with the ultrathin ZnIn2S4 via a surface charge promoted self-assembly method that is driven by strong electrostatic attraction between the negatively charged ZnIn2S4 layers and positively charged MoSe2 (see Methods for more details). The electrostatic self-assembly method efficiently circumvents the requirement of lattice matching of two individual layers for assembling hetero-layer structure39,40. Consequently, a large quantity of hetero-layered ZnIn2S4/MoSe2 can be facilely obtained (Supplementary Fig. 30). Moreover, this method also imparts strong hetero-interlayer coupling that effectively promotes interfacial charge carriers transfer41,42,43 that will be discussed later.

Figure 2a,b shows the TEM images of MoSe2, indicating that the sheets are typically composed of 2–4 layers with an interlayer spacing of 0.65 nm that corresponds to the (002) plane of hexagonal MoSe2 (refs 44, 45). The HRTEM image in Fig. 2c shows a d spacing of 0.28 nm that matches with the interspacing of (100) MoSe2 (refs 46, 47). After the integration of MoSe2 with the single-unit-cell ZnIn2S4 layers, the as-prepared ZnIn2S4/MoSe2 yields a hetero-layered structure (Fig. 2d,e). Figure 2f and Supplementary Fig. 31 show HRTEM images of ZnIn2S4/MoSe2 that display interlayer spacing of MoSe2 (0.65 nm) and distinct lattice fringes of ZnIn2S4 (0.32 nm), confirming the co-existence and interfacial contact of the two components. In addition, Supplementary Fig. 32 shows overlapping TEM mapping of various elements, also indicating the lamellar structure formation of vertically coordinated ZnIn2S4 and MoSe2 heterostructure. The corresponding EDX spectrum (Fig. 3a) shows the coexistence of Zn, In, S, Mo and Se elements, whereas the EDX mapping (Fig. 3b) demonstrates the homogeneous distribution of these elements throughout the ZnIn2S4/MoSe2 composite. Therefore, based on the above analyses, it is reasonable to infer that the ultrathin single-unit-cell ZnIn2S4 layers are intimately coupled with the layered MoSe2 featuring a sheet-on-sheet hetero-layer structure, as schematically reflected in Fig. 3c.

Figure 2: Morphology and structure of few-layered MoSe2 and hetero-layered ZnIn2S4/MoSe2.
Figure 2

(a,b,d,e) Transmission electron microscopy (TEM) images of few-layered MoSe2 (a,b) and hetero-layered ZnIn2S4/MoSe2 (d,e). Scale bar, 10 nm. (c,f) High-resolution TEM (HRTEM) images of MoSe2 (c) and ZnIn2S4/MoSe2 (f). Scale bar, 2 nm. The inset in e is the magnification of the image shown in the black box of Fig. 2e. Scale bar, 2 nm.

Figure 3: Characterization of hetero-layered ZnIn2S4/MoSe2.
Figure 3

(a) Energy-dispersive X-ray (EDX) spectrum and (b) mapping images of the as-prepared ZnIn2S4/MoSe2. Scale bar, 200 nm. (c) Schematic illustration of the sheet-on-sheet ZnIn2S4/MoSe2 hetero-layer structure. (d) Raman spectra of ZnIn2S4 and ZnIn2S4/MoSe2. (e) High-resolution X-ray photoelectron spectroscopy (XPS) spectra of Mo 3d and Se 3d.

Moreover, the XRD patterns of ZnIn2S4 and ZnIn2S4/MoSe2 composite (Supplementary Fig. 33) present analogous diffraction peaks of hexagonal phase ZnIn2S4. The absence of typical MoSe2 peaks (Supplementary Fig. 34) could be ascribed to the relatively low diffraction intensity of MoSe2 peaks shielded by the strong and broad peaks of ZnIn2S4. Notably, Fig. 3d shows the Raman spectra of ZnIn2S4 and ZnIn2S4/MoSe2 where a characteristic peak at 240 cm−1 corresponding to the ‘A1g’ band of MoSe2 (refs 44, 48, 49) (Supplementary Fig. 35) is observed for ZnIn2S4/MoSe2 sample, confirming the formation of a composite with MoSe2 in the matrix of ZnIn2S4. In addition, the shift of the ‘A1g’ band of ZnIn2S4/MoSe2 as compared with that of bare MoSe2 (241.1 cm−1) also implies the reduced layer aggregation of MoSe2 nanosheets in the hybrid composite48,49. The ultraviolet–visible (UV–vis) absorption spectra in Supplementary Fig. 36 show that the ZnIn2S4/MoSe2 displays enhancement in visible-light absorption as compared with ZnIn2S4. This can be attributed to the intrinsic background absorption of black-coloured MoSe2 (Supplementary Fig. 37). To further determine the composition and chemical states of the composite, the ZnIn2S4/MoSe2 has been characterized by X-ray photoelectron spectroscopy (XPS). The doublet peaks for Mo 3d at 228.7 and 231.9 eV (top panel of Fig. 3e) can be assigned to the Mo+4 valence state, whereas the peak at 226.4 eV should be assigned to S 2s (ref. 15). In the Se 3d XPS spectrum (bottom panel of Fig. 3e), the peaks at 54.4 and 55.3 eV are ascribed to Se2− (ref. 47). Meanwhile, the high-resolution XPS spectra of Zn 2p peaks at 1021.8 and 1044.8 eV, In 3d peaks at 445.0 and 452.6 eV and S 2p at 161.9 and 163.0 eV (Supplementary Fig. 38) can be assigned to Zn2+, In3+ and S2− of ZnIn2S4, respectively50,51,52. The XPS analysis corroborates the presence of MoSe2 in the ZnIn2S4/MoSe2 composite.

Photoelectrochemical properties

It has been well accepted that layered transition metal chalcogenides with exposed edge sites can effectively decrease activation energy/overpotential of redox reaction17 that are desirable for photo-/electrocatalytic processes. According to the energy band structures of ZnIn2S4 and MoSe2, the photogenerated electrons from the excitation of ZnIn2S4 are thermodynamically available for transferring to MoSe2. Therefore, it is anticipated that the ZnIn2S4/MoSe2 hetero-layered structure not only promotes charge separation and transport driven by junction/interface between the MoSe2 and the light harvester ZnIn2S4, but also facilitates the proton reduction on the surface of MoSe2. To gain more insight into its optoelectronic properties, a series of complementary photo- and electrochemical characterizations were carried out. Figure 4a displays the linear sweep voltammetry curves of ZnIn2S4/MoSe2 composite and bulk ZnIn2S4, revealing a higher cathodic current density that is attributed to the reduction of water to H2 (ref. 53) over hetero-layered ZnIn2S4/MoSe2 than bulk ZnIn2S4. Simultaneously, the controlled experiment over bare fluoride tin oxide (FTO) shows no obvious cathodic current under the same potential range (Supplementary Fig. 39). The result indicates that the integration of MoSe2 with ZnIn2S4 accelerates the protonation and subsequent H2 formation rate of ZnIn2S4/MoSe2 as compared with that of bulk ZnIn2S4.

Figure 4: Photoelectrochemical properties.
Figure 4

(a) Linear sweep voltammetry (LSV) curves, (b) time-resolved transient photoluminescence (PL) decay (excitation at 400 nm and emission at 495 nm), (c) schematic illustration of the interfacial charge carrier transfer, (d) steady-state PL spectra, (e) electrochemical impedance spectroscopy Nyquist plots and (f) transient photocurrent responses of bulk ZnIn2S4 and hetero-layered ZnIn2S4/MoSe2 composite. CB, conduction band; VB, valence band.

In addition, Fig. 4b displays the time-resolved photoluminescence spectra of bulk ZnIn2S4 and hetero-layer structured ZnIn2S4/MoSe2, which probe the specific charge carrier dynamics of nanosystems54,55. The emission decay curves of the samples are fitted by biexponential kinetics function (Supplementary Note 1, Supplementary Equation 1) in which two decay components are derived (insets in Fig. 4b) (τ1 is originated from the nonradiative recombination of charge carriers in the defect states of ZnIn2S4, whereas the longer lifetime component of τ2 is caused by the recombination of free excitons in the ZnIn2S4). For ZnIn2S4/MoSe2, the emission lifetimes of both components (τ1=0.31 ns, τ2=0.38 ns) are shorter than that of the corresponding bulk ZnIn2S4 counterpart (τ1=0.73 ns, τ2=3.77 ns). The average emission lifetime (calculated from Supplementary Note 1, Supplementary Equation 2), which reflects the overall emission decay behaviour of sample, has also displayed an obvious decrease for ZnIn2S4/MoSe2 (2.43 ns) as compared with that of bulk ZnIn2S4 (3.78 ns). Meanwhile, the steady-state PL spectra in Fig. 4d show obvious PL quenching of hetero-layered ZnIn2S4/MoSe2 hybrid. The corresponding observations of PL quenching and lifetime reduction suggest the establishment of an electron transfer channel from ZnIn2S4 to MoSe2 in a nonradiative quenching pathway (Fig. 4c)54,55. Accordingly, this leads to efficient interfacial charge transfer and suppression of photoexcited charge recombination in the hetero-layered ZnIn2S4/MoSe2 structure.

Furthermore, the electrochemical impedance spectrum of ZnIn2S4/MoSe2 (Fig. 4e) shows a smaller semicircular in the Nyquist plot than that of bare ZnIn2S4 nanosheets, indicating a lower charge-transfer resistance in the hybrid composite that warrants efficient transportation and separation of charge carriers56,57,58,59. As shown in Fig. 4f, the ZnIn2S4/MoSe2 displays obvious transient photocurrent response under visible light irradiation. The current density is comparable to recently reported 2D-based photocatalyst systems (Supplementary Table 1). In addition, it is notable that the ZnIn2S4/MoSe2 displays ca. 22-fold photocurrent enhancement as compared with bulk ZnIn2S4 under the same experimental condition, and this is a marked improvement that suggests the structure and composition advantage of the hetero-layered ZnIn2S4/MoSe2 composite in promoting the separation and transportation of photogenerated charge carriers. Collectively, these commendable photo- and electrochemical properties support efficient electron–hole pair separation and high surface reaction rate of the ZnIn2S4/MoSe2 hetero-layered structure.

Photocatalytic H2 production performance

Recent experimental results and theoretical predictions suggest that metal chalcogenides are a class of promising inexpensive, earth-abundant and visible responsive catalyst alternatives. However, nonoptimal interfacial contact and bulk metal chalcogenides structure limit catalytic activity owing to poor electronic coupling effect and low active sites exposure. Correspondingly, the constructed metal chalcogenide heterostructure that is thinned down to a few layers with incorporated electrostatic coupling is evaluated by photocatalytic H2 production. The photocatalytic performance provides a useful and explicit evaluation to assert the structural integrity and stability of the 2D hetero-layered structure.

The photocatalytic activity, H2 generation of the ultrathin ZnIn2S4 layers and ZnIn2S4/MoSe2 hetero-layered nanohybrids was performed under visible light irradiation (λ>400 nm) using lactic acid as the hole scavenger. As shown in Fig. 5a, the single-unit-cell ZnIn2S4 layers show a H2 evolution rate of 1,748 μmol g−1 h−1 that is fourfold of the pristine bulk ZnIn2S4 (446 μmol g−1 h−1), indicating enhanced activity of the ultrathin layers. In addition, the photoactivity of the ultrathin ZnIn2S4 is also demonstrated to be much higher than the H2 generation rate of the hydrothermal synthesized ZnIn2S4 nanoflowers (Supplementary Fig. 40) of ca. 260 μmol g h−1. The augmented photoactivity of ZnIn2S4 nanosheets can be attributed to its unique 2D ultrathin structure that lowers charge-transfer resistance and shortens the diffusion pathway of charge carriers, thus favouring the fast and efficient separation of photogenerated charge carriers (Supplementary Figs 16 and 17).

Figure 5: Photocatalytic H2 production performance.
Figure 5

(a,b) Photocatalytic H2 evolution over ZnIn2S4 nanoflowers, bulk ZnIn2S4 and single-unit-cell ZnIn2S4 layers (a), and ZnIn2S4/MoSe2 composites with different weight ratios of MoSe2 (b). (c,d) Comparison of photocatalytic H2 evolution activities over ZnIn2S4/1%Pt, ZnIn2S4/1%MoS2 and ZnIn2S4/1%MoSe2. (e) Recycling photoactivity test of ZnIn2S4/1%MoSe2. Note that the error bars represent the photoactivity s.d. values calculated from triplicate experiments.

Furthermore, significant improvement in H2 generation was established after coupling of MoSe2 layers to the ultrathin ZnIn2S4 nanosheets forming hetero-layered composites. The amount of H2 evolved increases with MoSe2 content up to 1% (Fig. 5b). The as-obtained ZnIn2S4/1%MoSe2 displays the highest H2 evolution rate of 6,454 μmol g−1 h−1, that is 15 and 4 times as high as that of bulk ZnIn2S4 and ZnIn2S4 nanosheets, respectively. Notably, the photoactivity is considerable higher than that of the reference photocatalysts, that is, ZnIn2S4/1%Pt (4,353 μmol g−1 h−1) and ZnIn2S4/1%MoS2 (3,860 μmol g−1 h−1), as shown in Fig. 5c,d. Pt and MoS2 are two exemplary co-catalysts that have been used in reported literature for photocatalytic H2 evolution. The result highlights the effectiveness of MoSe2 that surpasses the classic Pt and MoS2, as a co-catalyst in promoting photocatalytic H2 evolution44,60. Importantly, the hetero-layered ZnIn2S4/MoSe2 displays good stability. The cycling test over the optimal ZnIn2S4/1%MoSe2 (Fig. 5e) shows negligible photoactivity loss after 20 consecutive cycles with accumulatively 80 h under visible light irradiation. Moreover, after storing in ambient conditions for 3 months, the ZnIn2S4/1%MoSe2 retains a high photoactivity as that of the fresh sample (Supplementary Fig. 41). The high photoreactivity and stability of the 2D hetero-layer ZnIn2S4/1%MoSe2 hybrid provide direct evidence of the large exposed active surface and strong electronic coupling between the interlayers.

Besides, photocatalytic H2 activities of ultrathin CdIn2S4 and In2S3 layers also exceed that of their bulk counterparts (Supplementary Fig. 42). Self-assembly construction of 2D hetero-layer hybrids, that is, CdIn2S4/MoSe2 and In2S3/MoSe2, also verifies the enhanced photoactivity and stability. Essentially, the coupling of ultrathin CdIn2S4 and In2S3 with a few layers of MoSe2 co-catalyst has enhanced the H2 evolution activity (Supplementary Fig. 43). The rates of H2 evolved over the optimal CdIn2S4/1%MoSe2 and In2S3/1%MoSe2 are 9- and 10-fold of bare CdIn2S4 and In2S3 nanosheets, respectively. In addition, the photoactivities of the resulted metal sulfide/MoSe2 (CdIn2S4/1%MoSe2 and In2S3/1%MoSe2) are also much higher than those of the reference photocatalysts, that is, metal sulfide/Pt and metal sulfide/MoS2 (Supplementary Fig. 44). Furthermore, the cycling tests of the optimal CdIn2S4/1%MoSe2 and In2S3/1%MoSe2 show negligible photoactivity degradation after 20 consecutive cycles with accumulatively 80 h under visible light irradiation (Supplementary Fig. 45).


Although prior literature has already reported exfoliated 2D layered metal chalcogenides commonly induced by intercalator osmotic swelling, self-surface charge exfoliation into single-unit-cell thick layer structure in pure water is unprecedented. Successive artificially coupled hetero-layered structure with ultrathin and intimate interface characteristics, guided by unconstraint electrostatic coordination of a dissimilar metal chalcogenide, is demonstrated in this work. In contrast, thin-film epitaxial growth is strongly influenced by the surface of the substrate and degree of lattice matching. This limits the production yield and imposes a high cost of 2D hetero-layer metal chalcogenide for practical implementation. To test the hypothesis of the satisfactorily high quality of the as-prepared 2D hetero-layer, surface and interfacial-dominated photocatalysis is used as an ideal testbed for reliability verification. Diverse 2D ultrathin metal sulfide/MoSe2 hetero-layered materials reveal outstanding visible-light photoreactivity and efficient charge transfer exceeding that of metal sulfide/Pt and metal sulfide/MoS2 reference photocatalysts. More remarkably, the ultrathin hetero-layer structures demonstrate highly stable contact interface promising for long-term cycling and storage purposes.

In summary, we have developed a scalable method to artificially coordinate ultrathin metal chalcogenide hetero-layer structure via a combination of pristine self-surface charge exfoliation and electrostatic coupling of dissimilar layers. This generic approach to the preparation of 2D hetero-layered hybrids is attractive as it allows selection of individual constituent materials and thickness control, opening up the possibility of ‘design-and-build’ 2D layered heterojunction for large-scale theoretical exploration and practical applications.



Zinc acetate dehydrate (Zn(CH3COO)2·2H2O, ≥98%), sodium molybdate dehydrate (Na2MoO4·2H2O, ≥99%) and hydrazine hydrate (N2H4·H2O, 99.99%) solution were obtained from Sigma-Aldrich. Indium chloride (InCl3, 99.995%), L(+) lactic acid (90%) and selenium (99.5+%) were obtained from ACROS Organics. Thioacetamide (C2H5NS, >98%) was obtained from TCI. All of the reagents were used as received without further purification. The DI water used in the catalyst preparation was from local sources.

Synthesis of single-unit-cell ZnIn2S4 layers

Single-unit-cell ZnIn2S4 layers were fabricated by a facile low-temperature refluxing method followed by a moderate exfoliation. In detail, 1.5 mmol of Zn(CH3COO)2·2H2O and 3 mmol of InCl3 were added into 250 ml DI water and stirred for 30 min. Subsequently, an excess amount of thioacetamide (TAA, 8 mmol) was added into the above solution and stirred for another 30 min. The solution was then heated to 95 °C and maintained at that temperature for 5 h under vigorous stirring. The resulted precipitation was collected by centrifugation, rinsed with water for 2 times and re-dispersed into 200 ml DI water. The dispersion was sonicated continuously for 30 min and then centrifuged at 6,000 r.p.m. for 5 min to remove aggregates. After that, the colloidal single-unit-cell ZnIn2S4 layers were obtained. For each set of experimental synthesis, 0.6 g of ZnIn2S4 can be obtained. The comparative sample of ZnIn2S4-S was synthesized via the same procedure except that a stoichiometric amount of TAA (6 mmol) was added during the synthesis process.

Synthesis of hetero-layered ZnIn2S4/MoSe2 structure

MoSe2 was synthesized via a one-step hydrothermal method44. The surface modification of MoSe2 was carried out as follows: 50 mg MoSe2 was dispersed in 100 ml ethanol and sonicated continuously for 1 h. Then, 0.25 ml of APTES was added into the above MoSe2 dispersion. The mixture was heated at 60 °C for 4 h under mild stirring. The resulted product was rinsed with ethanol for 3 times and redispersed in 100 ml DI water with the aid of ultrasonication for 1 h. After that, the dispersion was centrifuged at 6,000 r.p.m. for 5 min to remove aggregates. Then, the colloid APTES-modified MoSe2 with positive surface charge was obtained. The 2D hetero-layer composite can be built up by dipping of MoSe2 nanosheet suspension into colloidal ZnIn2S4 of constraint supply or controlled amount of dilute solution. In brief, the APTES-modified MoSe2 was added dropwise into the negatively charged ZnIn2S4 colloid slowly. Driving by the strong electrostatic attractive interaction, the ultrathin ZnIn2S4 nanosheets can self-assemble with the MoSe2 layers, forming intimately integrated ZnIn2S4/MoSe2 hetero-layer structure.

Synthesis of ultrathin CdIn2S4 and In2S3 layers

Ultrathin CdIn2S4 layers were fabricated via the similar facile low-temperature refluxing method followed by moderate exfoliation. In detail, 1.5 mmol of Cd(CH3COO)2·2H2O and 3 mmol of InCl3 were added into 250 ml DI water and stirred for 30 min. Subsequently, an excess amount of thioacetamide (TAA, 8 mmol) was added into the above solution and stirred for another 30 min. The solution was then heated to 100 °C and maintained at that temperature for 12 h under vigorous stirring. The resulted precipitation was collected by centrifugation, rinsed with water for 2 times and redispersed into 200 ml DI water. The dispersion was sonicated continuously for 30 min and then centrifuged at 6,000 r.p.m. for 5 min to remove aggregates. After that, the colloidal ultrathin ZnIn2S4 layers were obtained. Ultrathin In2S3 layers were synthesized via the same method as that of synthesizing ZnIn2S4 layers without the addition of Zn(CH3COO)2·2H2O precursor.

Synthesis of hetero-layered CdIn2S4/MoSe2 and In2S3/MoSe2

The hetero-layered CdIn2S4/MoSe2 and In2S3/MoSe2 were synthesized following the same procedure as that of preparing of ZnIn2S4/MoSe2.


The XRD patterns of the samples were collected on a Philips X-ray diffractometer with Cu Kα radiation (λ=1.541 Å). UV–vis absorption spectra were recorded on a Shimadzu UV-3600 UV–vis spectrophotometer. XPS measurement was performed on a Thermo Scientific ESCA Lab 250 spectrometer that consists of a monochromatic Al Kα as the X-ray source, a hemispherical analyser and sample stage with multiaxial adjustability to obtain the surface composition of the samples. All of the binding energies were calibrated by the C 1 s peak at 284.6 eV. Zeta-potential (ξ) measurements of the samples were determined by dynamic light scattering analysis (Zeta sizer 3000HSA) at a room temperature of 25 °C. SEM images were taken on a JEOL JSM-7001F field emission scanning electron microscope. HRTEM images, EDX and elemental mapping images were obtained on a JEOL JEM-2100 electron microscope. The steady-state PL spectra were recorded on a Shimazu RF-5301PC under the excitation of 400 nm. Tapping-mode AFM measurement was performed on a commercial SPM instrument (MPF-3D, Asylum Research, CA, USA).

Time-resolved photoluminescence measurement was performed under excitation of 400 nm fs pulses. The excitation source is a mode-locked Ti:sapphire laser (Chameleon Ultra II, Coherent) working with repetition rate of 80 MHz and pulse duration of 140 fs. The second harmonic generation of 700 nm output from the laser was employed to excite the samples. The photoluminescence of the samples was collected and detected by a photon-counting photomultiplier (PMA, Picoquant). The emission centred at 495 nm was selected by a monochrometer (SpectroPro 2300i, Princeton Instrument). The PL decay dynamics were achieved by a time-correlated single photon counting module (TCSPC Picoharp 300, Picoquant).

Photoelectrochemical measurements were performed in a conventional three-electrode quartz cell. A Pt plate was used as counter electrode, and Ag/AgCl electrode/saturated calomel electrode were used as reference electrode, whereas the working electrode was prepared on FTO conductor glass. The sample powder (3 mg) was ultrasonicated in 0.5 ml of N,N-dimethylformamide (supplied by Sigma-Aldrich) to disperse it evenly to get a slurry. The slurry was spread onto FTO glass with the area of 1 cm2. After air drying, the working electrode was further dried at 90 °C for 2 h to improve adhesion. The electrolyte was 0.2 M aqueous Na2SO4 solution (pH=6.8). Linear sweep voltammetry curves were performed in a mixed solution of 10% (v/v) lactic acid and 0.2 M aqueous Na2SO4 solution.

Photocatalytic H2 evolution measurements

With the aid of ultrasonication, 5 mg of photocatalyst, 9 ml DI water and 1 ml lactic acid were mixed in a 25 ml quartz cylindrical reaction cell to form a homogeneous suspension. Then, the reactor was purged with argon gas for 10 min before illumination with a 300 W xenon arc lamp (λ>400 nm). The evolved H2 was analysed using an online gas chromatograph (GC-2014AT, Shimadzu Co., Japan) equipped with a thermal conductivity detector.

The recycling test of catalytic H2 evolution over the as-prepared photocatalyst was performed as follows. After the reaction of the first run under visible light irradiation, the suspension was purged with argon gas for 10 min. The process was carried out for four more cycles. After every five cycles, the photocatalyst was centrifuged and mixed with fresh 9 ml DI water and 1 ml lactic acid for continuous test.

Data availability

The data that support the findings of this study are available from the corresponding author on request.

Additional information

How to cite this article: Yang, M.-Q. et al. Self-surface charge exfoliation and electrostatically coordinated 2D hetero-layered hybrids. Nat. Commun. 8, 14224 doi: 10.1038/ncomms14224 (2017).

Publisher’s note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.


  1. 1.

    et al. A general method for the large-scale synthesis of uniform ultrathin metal sulphide nanocrystals. Nat. Commun. 3, 1177 (2012).

  2. 2.

    & The rise of graphene. Nat. Mater. 6, 183–191 (2007).

  3. 3.

    et al. Progress, challenges, and opportunities in two-dimensional materials beyond graphene. ACS Nano 7, 2898–2926 (2013).

  4. 4.

    et al. Oxyhydroxide nanosheets with highly efficient electron–hole pair separation for hydrogen evolution. Angew. Chem. Int. Ed. 55, 2137–2141 (2016).

  5. 5.

    et al. Fabrication of flexible and freestanding zinc chalcogenide single layers. Nat. Commun. 3, 1057 (2012).

  6. 6.

    & Wet-chemical synthesis and applications of non-layer structured two-dimensional nanomaterials. Nat. Commun. 6, 7873 (2015).

  7. 7.

    et al. Single unit cell bismuth tungstate layers realizing robust solar CO2 reduction to methanol. Angew. Chem. 127, 14177–14180 (2015).

  8. 8.

    et al. The chemistry of two-dimensional layered transition metal dichalcogenide nanosheets. Nat. Chem. 5, 263–275 (2013).

  9. 9.

    , , , & Waltzing with the versatile platform of graphene to synthesize composite photocatalysts. Chem. Rev. 115, 10307–10377 (2015).

  10. 10.

    , , , & Two-dimensional transition metal dichalcogenides as atomically thin semiconductors: opportunities and challenges. Chem. Soc. Rev. 44, 8859–8876 (2015).

  11. 11.

    & Two-dimensional oxide and hydroxide nanosheets: controllable high-quality exfoliation, molecular assembly and exploration of functionality. Acc. Chem. Res. 48, 136–143 (2015).

  12. 12.

    et al. Engineered interfaces of artificial perovskite oxide superlattices via nanosheet deposition process. ACS Nano 4, 6673–6680 (2010).

  13. 13.

    et al. A superlattice of alternately stacked Ni–Fe hydroxide nanosheets and graphene for efficient splitting of water. ACS Nano 9, 1977–1984 (2015).

  14. 14.

    , , , & X-ray diffraction study on restacked flocculates from binary colloidal nanosheet systems Ti0.91O2−MnO2, Ca2Nb3O10−Ti0.91O2 and Ca2Nb3O10−MnO2. J. Phys. Chem. C 115, 8555–8566 (2011).

  15. 15.

    et al. One-pot synthesis of CdS nanocrystals hybridized with single-layer transition-metal dichalcogenide nanosheets for efficient photocatalytic hydrogen evolution. Angew. Chem. Int. Ed. 54, 1210–1214 (2015).

  16. 16.

    , & Exciton radiative lifetimes in two-dimensional transition metal dichalcogenides. Nano Lett. 15, 2794–2800 (2015).

  17. 17.

    et al. Catalysis with two-dimensional materials and their heterostructures. Nat. Nanotech. 11, 218–230 (2016).

  18. 18.

    et al. Liquid-phase epitaxial growth of two-dimensional semiconductor hetero-nanostructures. Angew. Chem. Int. Ed. 54, 1841–1845 (2015).

  19. 19.

    et al. Enhanced superconductivity in atomically thin TaS2. Nat. Commun. 7, 11043 (2016).

  20. 20.

    , , , & Physical and chemical tuning of two-dimensional transition metal dichalcogenides. Chem. Soc. Rev. 44, 2664–2680 (2015).

  21. 21.

    et al. High yield exfoliation of two-dimensional chalcogenides using sodium naphthalenide. Nat. Commun. 5, 2995 (2014).

  22. 22.

    et al. Liquid exfoliation of solvent-stabilized few-layer black phosphorus for applications beyond electronics. Nat. Commun. 6, 8563 (2015).

  23. 23.

    et al. Large-scale exfoliation of inorganic layered compounds in aqueous surfactant solutions. Adv. Mater. 23, 3944–3948 (2011).

  24. 24.

    , , , & Inorganic-modified semiconductor TiO2 nanotube arrays for photocatalysis. Energy Environ. Sci. 7, 2182–2202 (2014).

  25. 25.

    et al. A versatile strategy for shish-kebab-like multi-heterostructured chalcogenides and enhanced photocatalytic hydrogen evolution. J. Am. Chem. Soc. 137, 11004–11010 (2015).

  26. 26.

    et al. One-dimensional densely aligned perovskite-decorated semiconductor heterojunctions with enhanced photocatalytic activity. Small 11, 1436–1442 (2015).

  27. 27.

    , , , & Plasmon-mediated solar energy conversion via photocatalysis in noble metal/semiconductor composites. Adv. Sci. 3, 1600024 (2016).

  28. 28.

    , , & Design of a metal oxide–organic framework (MoOF) foam microreactor: solar-induced direct pollutant degradation and hydrogen generation. Adv. Mater. 27, 7713–7719 (2015).

  29. 29.

    & Corrosion-mediated self-assembly (CMSA): direct writing towards sculpturing of 3D tunable functional nanostructures. Angew. Chem. Int. Ed. 54, 15804–15808 (2015).

  30. 30.

    , & Plasmonic photothermic directed broadband sunlight harnessing for seawater catalysis and desalination. Energy Environ. Sci. 9, 3151–3160 (2016).

  31. 31.

    & Photocatalytic conversion of CO2 over graphene-based composites: current status and future perspective. Nanoscale Horiz. 1, 185–200 (2016).

  32. 32.

    , & Insight into the effect of highly dispersed MoS2 versus layer-structured MoS2 on the photocorrosion and photoactivity of CdS in graphene–CdS–MoS2 composites. J. Phys. Chem. C 119, 27234–27246 (2015).

  33. 33.

    , , & Roles of cocatalysts in photocatalysis and photoelectrocatalysis. Acc. Chem. Res. 46, 1900–1909 (2013).

  34. 34.

    , & Ligand-free, colloidal, and luminescent metal sulfide nanocrystals. J. Phys. Chem. Lett. 4, 1676–1681 (2013).

  35. 35.

    , , & Cu doping in ligand free CdS nanocrystals: conductivity and electronic structure study. J. Phys. Chem. Lett. 5, 2382–2389 (2014).

  36. 36.

    , & Surface effects on regularities of electron transfer in CdS and CdS/CuxS colloids as studied by photoluminescence quenching. Langmuir 15, 4722–4727 (1999).

  37. 37.

    et al. A 1D/2D helical CdS/ZnIn2S4 nano-heterostructure. Angew. Chem. Int. Ed. 53, 2339–2343 (2014).

  38. 38.

    , , & Artificial photosynthesis over graphene-semiconductor composites. Are we getting better? Chem. Soc. Rev. 43, 8240–8254 (2014).

  39. 39.

    et al. Layer-by-layer assembly and spontaneous flocculation of oppositely charged oxide and hydroxide nanosheets into inorganic sandwich layered materials. J. Am. Chem. Soc. 129, 8000–8007 (2007).

  40. 40.

    et al. Tuning the surface charge of 2D oxide nanosheets and the bulk-scale production of superlatticelike composites. J. Am. Chem. Soc. 137, 2844–2847 (2015).

  41. 41.

    et al. Near-field dielectric scattering promotes optical absorption by platinum nanoparticles. Nat. Photonics 10, 473–482 (2016).

  42. 42.

    , & Highly photoactive, low bandgap TiO2 nanoparticles wrapped by graphene. Adv. Mater. 24, 1084–1088 (2012).

  43. 43.

    , , , & Surface charge modification via protonation of graphitic carbon nitride (g-C3N4) for electrostatic self-assembly construction of 2D/2D reduced graphene oxide (rGO)/g-C3N4 nanostructures toward enhanced photocatalytic reduction of carbon dioxide to methane. Nano Energy 13, 757–770 (2015).

  44. 44.

    , , , & MoSe2 nanosheets and their graphene hybrids: synthesis, characterization and hydrogen evolution reaction studies. J. Mater. Chem. A 2, 360–364 (2014).

  45. 45.

    et al. Ultrathin S-doped MoSe2 nanosheets for efficient hydrogen evolution. J. Mater. Chem. A 2, 5597–5601 (2014).

  46. 46.

    et al. Perpendicularly oriented MoSe2/graphene nanosheets as advanced electrocatalysts for hydrogen evolution. Small 11, 414–419 (2015).

  47. 47.

    , , , & Atomically thin MoSe2/graphene and WSe2/graphene nanosheets for the highly efficient oxygen reduction reaction. J. Mater. Chem. A 3, 24397–24404 (2015).

  48. 48.

    et al. Chemical vapor deposition growth of monolayer MoSe2 nanosheets. Nano Res. 7, 511–517 (2014).

  49. 49.

    et al. Rapid and nondestructive identification of polytypism and stacking sequences in few-layer molybdenum diselenide by Raman spectroscopy. Adv. Mater. 27, 4502–4508 (2015).

  50. 50.

    , , , & Novel mesoporous P-doped graphitic carbon nitride nanosheets coupled with ZnIn2S4 nanosheets as efficient visible light driven heterostructures with remarkably enhanced photo-reduction activity. Nanoscale 8, 3711–3719 (2016).

  51. 51.

    , , , & Hierarchical sheet-on-sheet ZnIn2S4/g-C3N4 heterostructure with highly efficient photocatalytic H2 production based on photoinduced interfacial charge transfer. Sci. Rep. 6, 19221 (2016).

  52. 52.

    , & A low-temperature and one-step method for fabricating ZnIn2S4-GR nanocomposites with enhanced visible light photoactivity. J. Mater. Chem. A 2, 14401–14412 (2014).

  53. 53.

    , & Edge-terminated molybdenum disulfide with a 9.4-A interlayer spacing for electrochemical hydrogen production. Nat. Commun. 6, 7493 (2015).

  54. 54.

    et al. Multichannel-improved charge-carrier dynamics in well-designed hetero-nanostructural plasmonic photocatalysts toward highly efficient solar-to-fuels conversion. Adv. Mater. 27, 5906–5914 (2015).

  55. 55.

    et al. Insight into electrocatalysts as co-catalysts in efficient photocatalytic hydrogen evolution. ACS Cata. 6, 4253–4257 (2016).

  56. 56.

    , , & Toward improving the graphene–semiconductor composite photoactivity via the addition of metal ions as generic interfacial mediator. ACS Nano 8, 623–633 (2014).

  57. 57.

    , , , & Hierarchically CdS decorated 1D ZnO nanorods-2D graphene hybrids: low temperature synthesis and enhanced photocatalytic performance. Adv. Funct. Mater. 25, 221–229 (2015).

  58. 58.

    , & Layer-by-layer self-assembly of CdS quantum dots/graphene nanosheets hybrid Films for photoelectrochemical and photocatalytic applications. J. Am. Chem. Soc. 136, 1559–1569 (2014).

  59. 59.

    et al. Unconventional route to hairy plasmonic/semiconductor core/shell nanoparticles with precisely controlled dimensions and their use in solar energy conversion. Chem. Mater. 27, 5271–5278 (2015).

  60. 60.

    et al. Enhanced visible-light photocatalytic hydrogen evolution activity of Er3+:Y3Al5O12/PdS–ZnS by conduction band co-catalysts (MoO2, MoS2 and MoSe2). Int. J. Hydrogen Energy 41, 12826–12835 (2016).

Download references


This work is supported by Ministry of Education (MOE) R-263-000-B38-112 and R-263-000-B63-112.

Author information


  1. Department of Electrical and Computer Engineering, National University of Singapore, 4 Engineering Drive 3, 117583 Singapore, Singapore

    • Min-Quan Yang
    •  & Ghim Wei Ho
  2. State Key Laboratory of Photocatalysis on Energy and Environment, College of Chemistry, Fuzhou University, Fuzhou 350002, China

    • Yi-Jun Xu
  3. College of Chemistry, New Campus, Fuzhou University, Fuzhou 350108, China

    • Yi-Jun Xu
  4. Department of Mechanical Engineering, National University of Singapore, 9 Engineering Drive 1, 117576 Singapore, Singapore

    • Wanheng Lu
    •  & Kaiyang Zeng
  5. Department of Chemistry, National University of Singapore, 3 Science Drive 3, 117543 Singapore, Singapore

    • Hai Zhu
    •  & Qing-Hua Xu


  1. Search for Min-Quan Yang in:

  2. Search for Yi-Jun Xu in:

  3. Search for Wanheng Lu in:

  4. Search for Kaiyang Zeng in:

  5. Search for Hai Zhu in:

  6. Search for Qing-Hua Xu in:

  7. Search for Ghim Wei Ho in:


G.W.H. proposed the research direction and supervised the project. M.-Q.Y. designed and preformed the experiments. Y.-J.X. performed XPS measurement and provided helpful suggestions in conducting the study. W.H.L. and K.Y.Z. carried out AFM characterization and analysis. H.Z. and Q.-H.X. performed the PL lifetime measurement and analysis. G.W.H. and M.-Q.Y. wrote and revised the manuscript. All authors participated in discussion and reviewed the manuscript before submission.

Competing interests

The authors declare no competing financial interests.

Corresponding author

Correspondence to Ghim Wei Ho.

Supplementary information

PDF files

  1. 1.

    Supplementary Information

    Supplementary Figures, Supplementary Table, Supplementary Note and Supplementary References.


By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.

Creative Commons BYThis work is licensed under a Creative Commons Attribution 4.0 International License. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in the credit line; if the material is not included under the Creative Commons license, users will need to obtain permission from the license holder to reproduce the material. To view a copy of this license, visit