The synthesis mechanism of g-C3N4/Nb2C MXene/CsPbBr3 ternary heterojunction is presented in Fig. 1. The complete synthesis control details are given in the experimental section.
The XRD patterns of g-C3N4, CsPbBr3, Nb2C MXene, CC43 sample, and CCM30 sample are shown in Fig 2a. The characteristic peak patterns indicate the synthesis of pure phase g-C3N4, CsPbBr3, and Nb2C MXene, which are consistent with the corresponding standard references (Fig S1). The crystal structure of the ternary heterojunction CCM series (Fig. S1d) composites still maintain the original perovskite structure. Detailed characterization results in Fig. S1a further support the structural integrity of three parent materials. The XRD peaks of the CC(Fig. S1c) and CCM composites(Fig. S1d, Fig. S2) show similar diffraction peaks to those of g-C3N4, CsPbBr3 and Nb2C MXene, indicating that the phase structure of g-C3N4, CsPbBr3 and Nb2C MXene remain unchanged during the composite formation process. It should be noted that the peaks corresponding to g-C3N4 and Nb2C MXene are relatively weak in the CCM series composites due to the amorphous nature of the g-C3N4 and the few layers structure of the Nb2C MXene.
The morphologies of the prepared samples were characterized using SEM, TEM, and High-resolution TEM (HRTEM) techniques, as shown in Fig. 2c and Fig. S3-5. The SEM image (Fig. 2b, S5a) reveals a sheet structure decorated with numerous particles. TEM and HRTEM were performed to confirm the three-phase composition of the CCM30 compound (Fig. 2d). Amorphous g-C3N4 is dispersed in the surface layer of the sample (Fig. 2c). In Fig. 2e and 2g, lattice fringes with a d-spacing of 0.291 nm correspond to (220) panes of CsPbBr3 QDs, while the lattice fringes with d-spacing of 0.296 nm and 0.431 nm correspond to (220) and (200) planes of Nb2C MXene, respectively. HRTEM image with corresponding live Fast Fourier transformation (FFT) patterns (Fig. 2e and 2g) clearly displaylattice signals of CsPbBr3 and Nb2C MXene. The angle between them measures 28° and 30°, indicating a near-parallel relationship between CsPbBr3 and Nb2C MXene. EDS results (Fig. S5b) demonstrate that the mass fraction of each element in CCM30 composites aligns with the proportion of the synthetic materials used. Additionally, energy-dispersive X-ray spectrometer mapping data (Fig. 2i-l, S2) reveals a uniform distribution of elements (C, N, Br, Pb, Cs, Nb, and F) throughout the nanocomposite structure. Based on the above characterizations, it is evident that the g-C3N4/Nb2C MXene/CsPbBr3 heterostructure has been successfully formed (Fig. 2c).
We carried out a series of optical properties to deeply understand the interaction among ternary compounds and their influence. The FTIR spectra of g-C3N4, CsPbBr3 QDs, and Nb2C MXene photocatalysts are shown in Fig. 3a and Fig. S6a-d. In the case of g-C3N4[51, 52], the peak at 1639 cm−1, 1241 cm−1correspond to C‒N and C=N stretching vibration modes, respectively. The absorption peaks at 1325 and 1245 cm−1 are associated with the out-of-plane bending vibration of triazine ring. The peak at 808 cm−1 is attributed to the molecule breathing modes of tris-triazine units. The peaks at 2924 cm−1, 2853 cm−1, and 1458 cm−1 can be assigned to the asymmetric and symmetric Pb–Br stretching vibrations[53] as well as the bending vibrations of Cs-Pb of CsPbBr3 QDs. Nb2C MXene shows typical peaks at 621 cm-1and 1086 cm-1, attributing to the interlayer vibrations of C-Nb [54]. In the FTIR spectrum of the ternary compounds, in addition to the typical peaks of g-C3N4, CsPbBr3 QDs, and Nb2C MXene, a clear red shift in peak position of in C–N stretching mode and the vibrational modes of tris-s-triazine units in g-C3N4 is observed. The red shift indicates a strong interaction among the g-C3N4, CsPbBr3 QDs, and Nb2C MXene interface. Moreover, the typical stretching mode of aromatic C–N and C=N heterocycles in g-C3N4 at 1241 cm-1 are shifted to higher values with an increasing content of Nb2C MXene (Fig. 3d). This shift can be ascribed to a chemical interaction between the g-C3N4 and Nb2C MXene surfaces, leading to an increase in the electron density of ternary heterocycles in g-C3N4. It is noteworthy that even with a single molar ratio of 1:1:1, all CsPbBr3 QDs can be effectively incorporated onto the surface of two two-dimensional materials, forming a ternary heterojunction structure.
To investigate the light-harvesting property, UV-vis spectra were recorded, as shown in Fig. 3c. The absorption edge of g-C3N4, CsPbBr3 QDs, CC30, and CCM30 groups are observed around 450 nm, 570 nm, 560 nm, and 550nm, respectively, corresponding to the band gap energy of approximately 2.95 eV, 2.31 eV, 2.29 eV, and 2.23 eV [33, 55] (Fig. S7). It is evident that all the binary (Fig. S6g) and ternary (Fig. S6h) samples can be excited under visible-light irradiation. Upon the addition of Nb2C MXene, both the absorption intensity in the visible region and at the absorption edges increase, which might be correlate with the black color of Nb2C MXene.
To further investigate the interactions among g-C3N4/Nb2C MXene/CsPbBr3 binary catalysts, photoluminescence (PL) emission spectra were recorded. The PL intensity is typically indicative of the recombination rate of photoinduced electron-hole pairs, where a lower PL emission intensity suggests a strongly suppressed recombination. As shown in Fig. 3d, it can be observed that pure g-C3N4 and CsPbBr3 exhibit strong and broad PL emission at approximately 498 nm and 524 nm, respectively, which is consistent with the literature. However, the PL peak intensity of the ternary heterojunction is significantly quenched compared to the other composite samples. In particular, PL emissions of CC43 and CCM30 exhibit the lowest intensity within their respective group (Fig. S6e and S6f). It is important to note that Nb2C MXene does no exhibit any emission peak due to its metallic characteristics. These PL results indicate that the addition of Nb2C MXene can effectively inhibit the recombination of charge carriers within the system, leading to improved photocatalytic performance.
The charge transfer and separation behavior of the photocatalyst was investigated using time-resolved fluorescence decay technique. As shown in Fig. 3e, all samples exhibit a rapid decay within the nanosecond timescale. The average emission lifetime (Fig. 3f) of g-C3N4 CsPbBr3 QDs, CC43, and CCM30 are 11.20 ns, 9.80 ns, 9.24ns, and 8.70ns, respectively. These results indicate that both binary (Fig. S6i) and ternary heterostructures (Fig. S6j) provide efficient pathways for rapid charge transfer of the photogenerated carriers. The shortened emission lifetimes suggest enhanced charge separation and reduced recombination, which are favorable for efficient photocatalytic performance
The bonding information of g-C3N4, Nb2C MXene, CsPbBr3, and their composites was investigated using X-ray photoelectron spectroscopy (XPS) (Fig. 4a,c-f and Fig. S8-9). In Fig. 4, CCM30 shows distinct binding energies ascribed to C, N, Br, Pb, Cs, and Nb, indicating the successful synthesis of the ternary composites of g-C3N4 / Nb2C MXene / CsPbBr3. After fitting the spectra, small binding energy shifts are observed in the ternary structures compared to their individual components such as C1s, N1s, Br3d, and Nd3d. These shifts suggest the presence of intimate interactions within the structure, resulting in charge redistribution. This binding energy shift indicates chemical reactions between the other parent components and g-C3N4. Consequently, Nb2C MXene becomes electron-rich, while the other two components become electron-deficient. This is supported by the negative shift in the binding energy of Nb 3d in CCM30. The binding energy of Br 3d (Fig. 4f) in the CsPbBr3 QDs is 68.4 eV and 69.5 eV, corresponding to Br 3d5/2 and Br 3d3/2 respectively. The shift is -0.2 eV (68.2eV) and -0.3 eV (69.5eV). The binding energy of Nb 3d (Fig. 4e) in the Nb2C MXene shows six peaks at 203.1 eV, 205.8 eV, 206.8 eV, and 209.6eV. The shift is 0.4 eV (203.5eV), 0.5 eV (206.3eV), 0.2 eV (207.0eV), and 0.2 eV (209.8eV), indicating a strong electron deficient in Nb2C MXene. Fig 4b shows the differential charge density of the three parent materials. According to whether there is a broken band gap at 0eV, it is obvious that g- C3N4 and CsPbBr3 have obvious semiconductor properties, while Nb2C MXene has obvious gold properties.
The valence band (VB) potential can be determined by analyzing the VB XPS spectra. As shown in Fig. S10, the energy level of the valence band maximum (VBM) for g-C3N4 and CsPbBr3 QDs is 2.25 eV and 1.12 eV, respectively. Based on these results, the band structures of g-C3N4 and CsPbBr3 QDs can be derived, with VBM energies of 2.36 eV and 1.23 eV, respectively. Consequently, the corresponding conduction band energies are -0.59 eV and -1.08 eV respectively. Evidently, the conduction band minimum of g-C3N4 is 0.49 eV lower than that of CsPbBr3 QDs. These dataprovide insights into the band structure of g-C3N4 and CsPbBr3.
To further demonstrate the improved efficiency of photocarrier transfer and separation efficiency, we conducted transient photocurrent measurements for g-C3N4, CsPbBr3, CC43, and CCM30 samples (Fig.5a). Among all the samples, CCM30 exhibited the highest photocurrent indicating enhanced photocarrier separation and transfer. The presence of Nb2C Mxene is believed to facilitates the efficient separation of photoexcited electrons and holes[15, 56]. Furthermore, electrochemical impedance spectroscopy (EIS) was performed to investigate the catalytic activity of the prepared samples (g-C3N4, CsPbBr3 CC43, and CCM30 samples) (Fig.5b). The arc radius of g-C3N4 and CsPbBr3 samples was larger than that of CC43 and CCM30 composite samples. In contrast, CCM30 exhibited a smaller arc radius, suggesting reduced resistance and enhanced charge transfer. The presence of Nb2C Mxene is attributed to the improved conductivity and facilitated charge transfer within the composite structure.
The photocatalytic CO2 reduction activity (Fig. S11) of the samples was evaluated in a photocatalytic system filled with carbon dioxide-saturated water vapor under simulated sunlight[57, 58]. A controlled trial without light irradiation, CO2 or any photocatalyst did not show any detectable production of CO, CH4, H2, or other hydrocarbons (Fig. S12), confirming the necessity of the photocatalyst for the CO2 reduction process. As expected, the bare Nb2C MXene showed no photocatalytic activity (Fig. 5c, d) because it is not a photocatalyst[59]. In our system, CO was the main product, accompanied by a small amount of CH4. The yields of CO and CH4 were 6.27 μmol g-1 h-1 and 0.15 μmol g-1 h-1 for pure g-C3N4, and 5.31 μmol g-1 h-1 and 0.02 μmol g-1 h-1 for CsPbBr3 QDs, respectively (Fig. S13). The production of CO, significantly improved in the g-C3N4/CsPbBr3 binary composite photocatalysts compared to the individual components (Fig. 5d). Furthermore, the introduction of 2D Nb2C MXene in ternary heterojunction nanocomposites resulted in even higher performance. Among the samples, CCM30 exhibited the highest CO production rate of 53.07 μmol g-1 h-1 which was about 8.4, 10, and 2 times higher than that of pure g-C3N4, CsPbBr3 QDs, and the binary composite g‑C3N4/CsPbBr3, respectively. This significant enhancement in CO production highlights the synergistic effect of the ternary heterojunction nanocomposites.
The comparison of g-C3N4 and CsPbBr3 QDs revealed that the CO yield rate in binary photocatalysts increased by more than 2 times, suggesting the formation of heterojunction structure between g-C3N4 and CsPbBr3, which facilitates the transfer of photo-excited charges. This finding is consistent with the results obtained from EIS and photocurrent measurements, as well as with previous reports[32, 33]. By adjusting the ratio of components, slightly changes in the photocatalytic performance were observed. Among the binary photocatalysts, CC43 demonstrateed the best performance. Upon the addition of Nb2C MXene, the CO yield rate of ternary photocatalysts initially reached a comparable level to that of the binary ones when the percentage of Nb2C MXene was low (CCM10 and CCM20). Subsequently, the maximum performance was achieved in CCM30. However, with further increase in Nb2C MXene (CCM40), a slight decrease in the photocatalytic ability was observed, although it still outperformed all the binary photocatalysts. This suggests that the good conductivity of Nb2C MXene facilitates charge transfer between g-C3N4 and CsPbBr3, as supported by PL and PL delay lifetime characterizations. As a result, the maximum photocatalytic performance in terms of CO production was achieved with a yield rate of 53.07 μmol g-1 h-1, surpassing the majority of previously the reported studies[60]. The relevant literature on previous reports is listed in Table 1. Obviously,
The CO evolution rate on CCM30 has obvious advantages.
Table 1 Comparison CO evolution rates of the prepared photocatalyst with other literature.
Table 1 Comparison CO evolution rates of the prepared photocatalyst with other literature.
Photocatalyst
|
Light source
|
Solvents
|
CO evolution (μmol/g/h)
|
Ref.
|
PCN
CsPbBr3
CsPbX3/g-C3N4.
|
300 W Xe-lamp
(>420 nm)
|
CO2 and water vapor
|
5.5
5.0
28.5
|
[32]
|
PCN
CsPbBr3
CPB-PCN
|
300 W Xe-lamp
|
acetonitrile/water
Ethyl acetate/water
|
52
9.8
149
|
[33]
|
CsPbBr3
CsPbBr3/MXene
|
300 W Xe-lamp
(>420 nm)
|
Ethyl acetate
|
4.13
26.3
|
[61]
|
CsPbBr3 NCs
CsPbBr3 NCs/GO
|
100 W Xe lamp
|
Ethyl acetate
|
4.12
4.89
|
[62]
|
CPB-CN
|
300 W Xe-lamp
(>420 nm)
|
CO2 and water vapor
|
11.5
|
[63]
|
g‑C3N4
CsPbBr3
g‑C3N4/Nb2C MXene/CsPbBr3
|
300 W Xe-lamp
(>420 nm)
|
CO2 and water vapor
|
6.27
5.30
53.07
|
this work
|
From a thermodynamic perspective, the reduction potential for converting CO2 to CO and CH4 (-0.53V and -0.24V) [64]. We have provided a diagram illustrating all possible pathways for CO2 reduction to C1 products (Fig S12) The formation of CO is believed to proceed through a single elementary step, in which our ternary heterojunction provides the necessary photocatalytic energy for CO generation. On the other hand, the formation of CH4 is thought to occur through a series of elementary steps involving the transfer of one or two electrons, with CO serving as an intermediate. It is important to note that when the reduction potential of the electrons system is low, the kinetic reaction rate of elementary elements decreases. Consequently, the subsequent catalytic reaction steps after CO formation may not proceed rapidly enough before CO desorbs from the surface of the photocatalyst. This leass to CO being the main product, with CH4 being the secondary product.
After stability testing for eight hours, the loss in activity is only 7.1% (Fig 5d), indicating the good stability of our ternary heterojunction photocatalyst. The XRD patterns and FTIR spectra of CsPbBr3 and CCM30 before and after the stability test were shown in Fig S17. It is evident that CsPbBr3 undergoes noticeable crystal changes[65], transitioning from the all-orthorhombic structure to an elongated polyhedron[66, 67]. However, even after nearly 24 hours of catalytic activity, the CO production yield relatively stable. Similar structural changes can also be observed in CCM30 after the stability test, indicating that the transformation is primarily due to the change of CsPbBr3. These results suggest that the photocatalyst exhibits goodstability under the reaction conditions.
To investigate the electronic and transport properties of the ternary heterojunction, we performed DFT calculations[68, 69]. The (110) surface orientation of three parent materials was chosen as the model to simulate the density of states (DOS) and charge density difference[70]. Since catalysis primarily occurs on the surface rather than in the inner layers, two different slabs of Nb2C MXene were used to construct the ternary heterojunction photocatalyst (Fig 6a). In the ternary heterojunction, the conduction band is mainly occupied by Nb and Cs, consisting empty d orbitals (Fig. S14), On the other hand, the valence band is composed of orbitals from N and Br elements. This confirms that Nb2C MXene can modify the energy band structure of ternary heterojunction. To maximizethe influence of the ternary composites on the electronic structure, Nb2C MXene is positioned in the middle layer. The total and partial DOS of the ternary heterostructures for (110) crystal faces is shown in Fig. S13a-f. Upon formation of the heterostructure, a shift in the band gap is observed near the Fermi level, indicating improved conductivity compared to the three individual parent components. This suggests that the ternary heterojunction exhibits enhanced electronic and transport properties, which can contribute to its improved photocatalytic performance.
To gain further insights into the electronic properties at the interface between the CsPbBr3/Nb2C MXene and Nb2C MXene/g‑C3N4, we performed calculations of the 3D charge density difference and the plane-averaged electrostatic potential drop across the interfaces of the three parent materials. As shown in Fig. 6b and c, the calculated results indicate a charge transfer from CsPbBr3 to Nb2C MXene and subsequently from Nb2C MXene to g‑C3N4, confirming an unbalanced charge distribution at the interfaces. For the ternary heterojunction interface, CsPbBr3/Nb2C MXene and Nb2C MXene/g‑C3N4, higher electrostatic potential and potential difference of approximately 15.83 eV and 11.93 eV, and 16.21 eV and 11.88 eV, respectively, were observed. This potential drop corresponds to the internal electric field pointing from g‑C3N4 and CsPbBr3 towards Nb2C MXene. Consequently, the internal electric field generated by the potential difference aligns with the direction of the ternary heterostructures. Due to this internal electric field, photogenerated electrons tend to drift from the surfaces of g-C3N4, or CsPbBr3 QDs towards the surface of Nb2C MXene, while photogenerated holes tend to drift in the opposite direction. This phenomenon facilitates the separation and transfer of photogenerated carrier, thereby promoting enhanced photocatalytic performance. We also compared the charge transfer and distribution ofthe binary interface g-C3N4/CsPbBr3, g-C3N4/ Nb2C MXene, and CsPbBr3/ Nb2C MXene shown in Fig. S14. The charge transfer from CsPbBr3 to g‑C3N4, g‑C3N4 to Nb2C MXene, and CsPbBr3 to Nb2C MXene reveals some unbalanced charge distribution, although less pronounced compared to the ternary heterojunction. The 3D charge density difference and plane-averaged electrostatic potential exhibit lower values, namely 7.18 eV and 2.92 eV, 12.64 eV, and 14.69 eV, respectively. These values indicate a less significant change compared to the ternary heterojunction. The total DOS of the g-C3N4/CsPbBr3 binary heterojunction (Fig. S16) shows a relatively large band gap, reflecting the energy difference between the valence band and conduction band. This further supports the improved electronic properties and potential for efficient charge transfer and separation in the ternary heterojunction structure.