Linia Gedi
Marazani
a,
Maureen
Gumbo
b,
Lendly
Moyo
a,
Banothile C. E.
Makhubela
c and
Gift
Mehlana
*a
aDepartment of Chemical Sciences, Faculty of Science and Technology, Midlands State University, Private Bag 9055 Senga Road, Gweru, Zimbabwe. E-mail: mehlanag@staff.msu.ac.zw
bChalmers University of Technology, Department of Chemistry and Chemical Engineering, SE-412 96, Göteborg, Sweden
cResearch Centre for Synthesis and Catalysis, Department of Chemical Sciences, Faculty of Science, University of Johannesburg, Auckland Park 2006, South Africa
First published on 31st July 2024
Two new neodymium-based metal–organic frameworks, JMS-10 and JMS-11, were synthesised using a 2,2′-bipypridine-5,5′-dicarboxylic acid (bpdc) linker. Both MOFs were solvothermally synthesised in DMF under different conditions. JMS-10 was synthesised at 120 °C while JMS-11 was synthesised at 100 °C in the presence of a modulator. Both the MOFs possessed very similar crystallographic parameters but were found to be structurally diverse. Their structures were built by secondary building units (SBUs) made up of carboxylates binding in sets of four and two to the straight rod, thus forming two types of alternating nodes that are 6- and 4-connected. Both JMS-10 and JMS-11 were functionalized using the ruthenium p-cymene complex. The functionalized MOFs were applied in the photocatalytic reduction of carbon dioxide to syngas where they produced both hydrogen and carbon monoxide (CO:H2) in the ratio of 1:2. The amount of CO to H2 produced varied depending on the additives used in the reaction medium, highlighting the importance of water, triethanolamine and acetonitrile in tuning the syngas ratio for different industrial applications.
The C4+ atom in CO2 is in its fully oxidized state, making CO2 highly thermodynamically stable; this presents a challenge in its direct conversion.3–5 To overcome this challenge, a catalyst is required to make the process easier. Chemical catalysts such as those of platinum group metals have proven to be highly active in many processes including carbon dioxide reduction. To enhance their catalytic properties, these catalysts can be supported in various materials including metal–organic frameworks (MOFs).6,7 MOFs have become an outstanding group of porous materials in reticular chemistry.8,9 These materials present unique properties, including high surface areas,10 tunable porosity, structural rigidity and diversity,11 flexible network topology and chemical functionality.12 These properties can be accredited to the periodic structures formed when the organic linkers and the inorganic metal ions are combined.13,14 The backbone of MOFs that has gained so much attention is the secondary building unit (SBU). SBUs can be simplified as geometric figures comprising metal clusters connected through non-metal bonds, typically organic components such as the oxo (M–O–M) and carboxylate (M–O–C–O–M) form recurrent 3D structures.13,15 The catalytic activity coupled with the stability of MOFs makes them superior materials, especially in photocatalysis, where they can be functionalized with other catalysts to enhance their photocatalytic properties.
Numerous studies have been conducted that focus on the artificial reduction of carbon dioxide, and these include thermocatalytic,4,16 biocatalytic,17,18 electrochemical,19,20 bioelectrocatalytic21,22 and photocatalytic methods.3,5,23–27 Electrochemical and thermocatalytic methods require extra energy to be input into the process, which becomes costly. Biocatalytic and bioelectrocatalytic methods also require ambient conditions for biological molecules not to denature, which is very difficult to maintain for good product yields. This makes photocatalytic reduction a better method due to its energy efficiency and environmental friendliness because it uses free and clean solar energy, which is also abundant.3 Photocatalytic conversion of CO2 into various industrially important products, such as methanol, methane, carbon monoxide and ethane, has been widely studied.28–30 The first photocatalytic reduction of CO2 was reported in 1979 in aqueous suspensions of semiconductors, such as ZnO, TiO2, GaP, SiC and CdS, to produce formaldehyde, formic acid and methanol.31 Since then, many studies have been reported on photocatalytic reduction of CO2 to various products and titanium dioxide, and its modified counterparts have been widely explored as photocatalysts.32–37 Photocatalytic reduction of CO2 can be done either in liquid or gas phase. In the liquid phase, the photocatalyst is usually mixed with sacrificial electron donors and other supporting reagents that are also in the liquid phase. Then, CO2 is bubbled through the solution, after which the mixture is irradiated with solar light for some time, and the products are collected and analysed usually with gas chromatography (GC). In the gas phase, however, a minimum amount or no liquid reagents are used, and the products are usually in the gas phase.
CO2 reduction to syngas has recently gained popularity because syngas is an important feedstock in many industrial processes, such as methanol production,38 hydroformylation and the Fischer–Tropsch synthesis.39,40 The ratios of the CO to H2 gases in the syngas are important for the various productions; for example, methanol production requires a CO/H2 ratio of 1:2, whereas hydroformylation requires 1:1 and Fischer–Tropsch synthesis requires 1:2 or 2:1.40 In this work, two new rod MOFs (JMS-10 and JMS-11) were synthesised from the neodymium metal salt and 2,2′-bipyridine-5,5′-dicarboxylic acid linker in dimethylformamide under different conditions. The high coordination number associated with neodymium metal gives rise to chemical and thermal stability in MOFs, making them highly suitable as support materials for molecular catalysts.
The MOFs were functionalised with the ruthenium p-cymene complex and then used for the photocatalytic reduction of CO2 to syngas. The functionalised MOFs showed activity towards the reduction of CO2 to syngas.
A clear light, colourless block-shaped crystal of JMS-11 with dimensions 0.196 × 0.084 × 0.029 mm3 was mounted on a suitable support. Data were collected using an XtaLAB Synergy R HyPix diffractometer operating at T = 143.8(3) K. Data were measured using ω scans of 0.5° per frame for 0.5/2.1 s with Cu Kα radiation. The diffraction pattern was indexed, and the total number of runs and images was based on the strategy calculation from the program CrysAlisPro. The maximum resolution achieved was Θ = 75.7° (0.79 Å). Data reduction and scaling were achieved using the CrysAlisPro software package (CrysAlisPro 1.171.42.49).43b A numerical absorption correction using a numerical grid with Gaussian integration for the multifaceted crystal model faces was applied. Empirical absorption correction was performed using spherical harmonics, as implemented in the SCALE3 ABSPACK scaling algorithm. The absorption coefficient μ of this material is 15.901 mm−1 at this wavelength (λ = 1.542 Å). The structure was solved and the space group P21/c (# 14) was determined by the ShelXT structure solution program using Intrinsic Phasing and refined by Least Squares using version 2016/6 of ShelXL 2016.42 All non-hydrogen atoms were refined anisotropically. Hydrogen atom positions were calculated geometrically and refined using the riding model. The structures were deposited in the Cambridge Database with deposition numbers CCDC 2249596 and CCDC 2249598. Table S1 (ESI†) lists the crystallographic and refinement parameters of the two MOFs.
In JMS-11, two metal centres, three pbdc linkers, two coordinated DMF molecules and one bridging oxygen atom were modelled. A further two uncoordinated DMF molecules were also modelled. The coordination environments of the two metal centres (Nd1 and Nd2) are similar. Both metals are coordinated to six oxygen atoms from the linkers: one oxygen atom of the DMF molecule and a bridging oxygen atom to furnish a square antiprismatic geometry.
JMS-11 had a smaller unit cell volume compared to JMS-10 (Table S1, ESI†). The smaller unit cell volume originates from the bending nature of the pbdc linkers, which buckle inside the channels. This effectively reduces the distance between the rod SBUs. The structure of JMS-10 is made up of Nd2C4O8 and Nd2C2O5 secondary building unit (SBU) rods that grow along the c-axis (Fig. 1b). Interestingly, these two SBUs are found in the rod alternates in an ABAB fashion. The structure of JMS-11 is also built by a rod similar to JMS-10, which consists of two alternating SBU units of Nd2C4O8 and Nd2C2O5 (Fig. 2b). The bpdc linkers connect the rods to give 3D structures with large rhombic channels of 26.386 Å by 15.228 Å (Fig. 1c) in JMS-10. However, JMS-11 exhibits small pores in the absence of solvated DMF molecules (Fig. 2c). The solvent accessible surface was modelled using the Mercury program using a probe radius of 1.2 Å and grid spacing of 0.7 Å.45 JMS-10 has a solvent-accessible void volume of 27%. However, JMS-11 had a lower solvent accessible void volume of 3% attributed to the presence of coordinated DMF molecules. The 2,2′-bipyridine-5,5′-dicarboxylate linker used in the synthesis of the two MOFs showed a great deal of flexibility, as evidenced by the torsional angles formed within the linkers of the frameworks, especially in JMS-10 (Fig. 3a). These torsional angles aided in creating larger and more open channels in the MOF. Three of the linkers in JMS-10 had torsional angles of 166.33(7)° to approximately 168.9(11)°, and the other had a torsional angle of 180.00(4)°. However, JMS-11 had linkers with torsional angles close to 180°, with one linker having a torsional angle of 172.7(7)° (Fig. 3b). In JMS-10, the flexibility observed between the phenyl rings of the linker gave rise to open channels. On the contrary, the buckling in and out of the linkers in JMS-11 may have restricted the rotation between the phenyl rings, reducing the distance between adjacent SBU and giving rise to smaller channels.
Fig. 3 Linker flexibility in (a) JMS-10 channel and (b) JMS-11 channel. Diagrams showing the torsional (dihedral) angles within the linkers. |
The unit cell parameters of JMS-10 and JMS-11 were too close. Their calculated PXRD patterns were compared to rule out the possibility of these structures being isostructural. As illustrated in Fig. S1 (ESI†), it can be confirmed that the two MOFs are not isostructural because their PXRD patterns are different. JMS-10 and JMS-11 are highly crystalline, showing good agreement between the calculated PXRD and the as-synthesised MOFs, as shown in Fig. 4a and b for JMS-10 and JMS-11, respectively. The major peaks on the experimental and calculated PXRD patterns correlated well for both MOFs, showing the phase purity of the synthesised MOFs.
Fig. 4 Simulated and experimental PXRD patterns (a) JMS-10 and (b) JMS-11; TGA of (c) JMS-10 and (d) JMS-11. |
The thermal stability of JMS-10 and JMS-11 was studied using thermogravimetric analysis. Both MOFs were thermally stable, as shown by their TGA results. Both MOFs decompose above 425 °C (Fig. 4c and d). Thermal analysis of JMS-10 showed a 23.4% weight loss in the temperature range ranging from 50 °C to around 200 °C, as shown in Fig. 4c. This weight loss corresponds to the loss of three DMF molecules and two water molecules (calculated at 23.9%). The TGA thermogram of both the activated and native JMS-10 shows no significant weight loss between 340 °C and 425 °C, indicating high thermal stability after solvent loss until decomposition. JMS-11 showed a total weight loss of 25.3% within the same temperature range as JMS-10, as shown in Fig. 4d. Of special note was the 3% weight loss in JMS-11 in the temperature region of around 350 °C. This weight loss is also present in the activated material of the same MOF, which could be the onset of the decomposition of JMS-11 due to the loss of the carboxylate group. The literature has also proven that some MOFs with carboxylate linkers, such as MOF-5, tend to undergo decarboxylation, which releases CO2 at 350 °C. MOF-5 was heated to 380 °C for 24 hours, and the TG-MS and VT-PXRD results showed a 60% loss of CO2 units.46 Variable temperature PXRD studies of the two MOFs are shown in Fig. S2 (ESI†). The two MOFs were thermally stable up to 400 °C. This result correlates well with the TGA results showing thermal degradation at around 425 °C for both MOFs. However, some peaks are lost as the temperature increases, especially at 100 °C for JMS-11, which could be attributed to the loss of coordinated and solvated water molecules. Interestingly, at 100 °C, the PXRD pattern for JMS-11 is the same as that of JMS-10. However, at 200 °C, JMS-11 loses the small peak at around 8.7 2θ degrees, which remains on JMS-10 until 500 °C, as shown in Figure S2 (ESI†). This means that JMS-11 changes its phase initially to JMS-10 at 100 °C and then again to another phase at higher temperatures. The PXRD of the sample collected at 500 °C exhibits the same diffraction pattern after cooling the sample to room temperature (25 °C). This suggests an irreversible structural transformation above 500 °C.
The morphology of JMS-10 and JMS-11 was evaluated using SEM. As illustrated in Fig. 6 and 7, both MOFs had rod morphology; however, JMS-11 had rods aligned in the form of shrubs (forming multiple branches) (Fig. 7). JMS-10 had different particle sizes, which may be attributed to the different rates of crystallisation. JMS-11 had more uniform particle sizes that were well shaped, as shown in Fig. 7, a sign that the crystallisation rate in the synthesis of the crystals was also uniform. Another interesting observation was that JMS-10 had the most cracked crystals compared to JMS-11 (Fig. 6), with smooth, well-defined rod surfaces. This could be due to the higher synthesis temperature used in JMS-10. The SEM elementary mapping confirmed the presence and uniform distribution of the expected elements in the crystals, as shown in Fig. S3 and S4 (ESI†), for JMS-10 and JMS-11, respectively.
PXRD studies in Fig. 8 show similarities between the activated material and the ruthenium functionalised MOF. TEM studies on Ru(II)@JMS-10 and Ru(II)@JMS-11 indicated that the ruthenium particles were either dispersed on or close to the surface of the MOF crystals. Two areas were chosen on the TEM image, and EDX was performed on these specific areas to identify the ruthenium particles in the framework. Fig. 9a shows the TEM image of Ru(II)@JMS-10, and area marked 1 exhibits a significantly higher amount of ruthenium compared to area 2, as indicated by the peak intensity (Fig. 9b and c). Fig. 9d shows a section of the Ru(II)@JMS-11 rod composite. The image revealed whitish particles on the surface of the MOF (area marked 1) that contained more ruthenium than in area marked 2, as proven by EDX studies (Fig. 9e and f).
ICP-OES analysis of the functionalised MOFs showed an uptake of 2% and 1.8% of ruthenium by JMS-10 and JMS-11, respectively. Proton NMR was selectively done on JMS-10 and Ru(II)@JMS-10 MOF composites to check for the presence of the ruthenium p-cymene complex that was used for the functionalisation of the MOFs. As shown in Fig. S5 (ESI†), 1H NMR proton signals at 6 ppm and 6.3 ppm, as well as between 1 ppm and 3 ppm, are attributed to the ruthenium p-cymene complex that was used in the functionalisation process. These peaks were unavailable on the JMS-10 1H NMR spectrum (Fig. S6, ESI†).
Further evidence of the presence of the functionalizing complex in the MOFs was provided by FTIR studies (Fig. 10). The band at 1642 cm−1 in JMS-10 and its functionalized form can be attributed to the C–C vibrations of the pyridyl ring. The asymmetric and symmetric stretches of the carboxylate appear at 1564 cm−1 and 1388 cm−1, respectively, in both JMS-10 and Ru(II)@JMS-10. In JMS-11, the vibrations of the pyridyl ring are observed at 1671 and 1639 cm−1 for the activated and functionalized forms, respectively. The positions of the asymmetric and symmetric carboxylate stretches moved to lower wave numbers after functionalisation. Of interest is the stretch at 2950 cm−1 and 2968 cm−1 in Ru(II)@JMS-10 and Ru(II)@JMS-11, respectively. This is due to the presence of the methyl group in the ruthenium p-cymene complex.
The electronic states of the elements were also determined using XPS analysis. The XPS results for the ruthenium functionalised JMS-10 and JMS-11 MOF are presented in Fig. S7 and S8 (ESI†), respectively. The XPS survey spectra for the MOFs before and after functionalisation were compared to verify the presence of the catalysts. Fig. S7a and b (ESI†) show the XPS survey spectra for JMS-10 and Ru(II)@JMS-10, respectively. The functionalised MOFs show the presence of the ruthenium element, as evidenced by the doublet peaks centred at 464.7 eV and 494.8 eV for Ru 3p3/2 and Ru 3p1/2, respectively.47 This proves that the oxidation state of the Ru in this case is +2, which again concurs with the oxidation state of ruthenium in the ruthenium p-cymene complex. XPS results of JMS-11 and its ruthenium functionalised derivative (Fig. S8, ESI†) are similar to those of JMS-10 with Ru(II)@JMS-11 showing the presence of the ruthenium.
The effect of the additives on the production of syngas was evaluated using JMS-10 functionalised MOF (Table 1). Entry 1 shows that 6.33 × 10−1 and 0.11 × 101 micromoles of H2 and CO, respectively, were produced in the presence of TEOA/MeCN/H2O using the Ru(II)@JMS-10 MOF. In the presence of the unfunctionalized JMS-10 MOF, insignificant amounts of the syngas were produced (entry 2). In the absence of water (entry 3), the amount of syngas produced by Ru(II)JMS-10 was reduced by approximately 800 times for H2 and 373 times for CO. Furthermore, the ratio of CO to H2 produced in the absence of water was approximately 1:1. With only water as an additive (entry 4), insignificant amounts of hydrogen were produced, highlighting the importance of TEOA/MeCN in the production of syngas. In the absence of TEOA (entry 5), the amount of syngas produced by Ru(II)@JMS-10 is also reduced with the ratio of CO to H2 changing from 1:2 in entry 1 to approximately 2:1. The catalysis was successful with all three reagents (TEOA, acetonitrile, and H2O) available, producing CO:H2 gas in a ratio of 1:2. However, in the absence of TEOA (entry 5) and water (entry 3), the ratio of CO:H2 changed to 2:1 and 1:1, respectively, with a significant decrease in the amount of syngas produced. This observation suggests that these additives are important for tuning the ratio of CO:H2 for various industrial applications.
Entry | Catalyst | Additives | H2 produced (micromoles) | CO produced (micromoles) | Approximate syngas ratio (CO/H2) |
---|---|---|---|---|---|
1 | Ru(II)@JMS-10 | TEOA/MeCN/H2O | 5.5 × 10−1 | 2.5 × 10−1 | 1:2 |
2 | JMS-10 | TEOA/MeCN/H2O | 2.00 × 10−3 | 1.90 × 10−4 | |
3 | Ru(II)@JMS-10 | TEOA/MeCN | 6.80 × 10−3 | 6.70 × 10−3 | 1:1 |
4 | Ru(II)@JMS-10 | H2O | 8.00 × 10−3 | — | |
5 | Ru(II)@JMS-10 | MeCN/H2O | 1.95 × 10−3 | 3.50 × 10−3 | 2:1 |
The importance of light was demonstrated by placing the samples in the dark for 24 hours. In this instance, no syngas was produced in both MOF composites. The kinetics of the syngas production was studied within the first 2 hours of production; then, the experiment was left to run for 21 hours. It was observed that in the first 2 hours, the syngas production was low but gradually increased to 10 μmol g−1 h−1 for H2 and 16 μmol g−1 h−1 for the CO gas (Fig. 11b). This means that syngas production was not instant, and the process took time. Compared to other MOFs and polymeric compounds, functionalised JMS-10 and JMS-11 had commensurate activities, as shown in Table 2. This shows that these MOFs are potential catalysts for the reduction of CO2 to syngas.
Catalyst | Photosensitizer | Sacrificial agent | H2 Produced | CO produced | Ref. |
---|---|---|---|---|---|
Ru(II)@JMS-10 | RuPCy | TEOA | 16.9 μmol g−1 h−1 (TON = 9) | 14 μmol g−1 h−1 (TON = 3.8) | This work |
Ru(II)@JMS-11 | RuPCy | TEOA | 12.5 μmol g−1 h−1 (TON = 6) | 26.2 μmol g−1 h−1 (TON = 10) | This work |
SnS2/Au/g-C3N4 | Au NP | TEOA | — | 93.81 μmol g−1 h−1 | 48 |
Fe MOF | Ru(bpy)32+ | TEOA | 11.4 μmol h−1 | 2.3 μmol h−1 | 49 |
Ni MOF | Ru(bpy)32+ | TEOA | 0.2 μmol h−1 | 13.6 μmol h−1 | 49 |
(Co/Ru)n-UiO-67(bpydc) | Ru(bpy)2Cl2 | TEOA | 9121.5 μmol g−1 | 4520 μmol g−1 | 50 |
Fe-TCPP@NU-1000 | — | TEOA | 21 (TON) | 22(TON) | 51 |
CoFeOX | Ru(bpy)32+ | TEOA | 8.7 μmol | 45.7 μmol | 52 |
Ag-LaFeO3 | Ag nanoparticles | — | 8 μmol g−1 h−1 | 2.41 μmol g−1 h−1 | 39 |
CoAl-LDH | Ru(bpy)32+ | TEOA | 2.25 μmol h−1 | 1.75 μmol h−1 | 53 |
AMTC | — | TEOA | 0.179 mmol | 0.502 mmol | 54 |
Polymeric carbon nitride (PCN) | Co(bpy)32+ | TEOA | 0.89 μmol h−1 | 0.13 μmol h−1 | 55 |
PCN-T-23 | Co(bpy)32+ | TEOA | 7.06 μmol h−1 | 24.85 μmol h−1 | 55 |
The stability of the functionalised MOFs during catalysis was probed using FTIR to check for the changes in the binding mode of the carboxylate moiety of the linker. Fig. 12a and b show that the characteristic bands of the functionalised MOFs were maintained before and after catalysis. The asymmetric and symmetric carboxylate stretches, which appear at 1587 cm−1 and 1377 cm−1, respectively, in Ru(II)@JMS-10, do not change their positions after catalysis. This indicates that the binding mode of the carboxylate moiety was not affected. The same effect was also noted for Ru(II)@JMS-11. In Ru(II)@JMS-10, the C–H stretch observed at 2970 cm−1 is enhanced after catalysis and appears from 2948 to 2814 cm−1 due to the presence of residual acetonitrile used during catalysis. A similar feature was also noted for Ru(II)@JMS-11 in which the C–H stretch at 2969 cm−1 became prominent after catalysis and appeared from 2946 to 2824 cm−1 after catalysis. A broad band centred at 3310 cm−1 in both Ru(II)@JMS-10 and Ru(II)@JMS-11 was observed after catalysis, which is attributed to the presence of water from the reaction medium. These FTIR results correlate well with the PXRD results (Fig. S9, ESI†) of the composites after catalysis, showing that the major diffraction peaks were maintained. The new peaks observed in the diffraction patterns of the used catalysts could be attributed to the solvent used during photocatalysis.
Fig. 12 A comparison of the FTIR spectra of @JMS-10, @JMS-11, Ru@JMS-10 and Ru@JMS-11 before and after catalysis. |
To gain a better understanding of the mechanism of photocatalysis of syngas production, photoluminescence studies were conducted on the functionalised MOFs (Fig. S10 and S11, ESI†). Interestingly, the ruthenium functionalised MOFs, which produced higher amounts of syngas, had the lowest emissions in photoluminescence in comparison to the pristine MOFs. This could be due to quenching that could have occurred in the ruthenium functionalised MOFs. This means that electron transfer could have occurred from the photo-excited MOF to the ruthenium metal. The same electron transfer could not occur in the bare MOFs, which could explain why insignificant amounts of syngas were produced. This observation is similar to what was recently observed by Kun Zhang and co-workers51 when they functionalized Nu-1000 with Fe-TCCP and used the catalyst for the reduction of CO2 to syngas. Additionally, it was discovered that a lower photoluminescence emission could mean a lower rate of recombination between holes and electrons due to loss of energy, and this leads to better photocatalytic performance,39 as observed in the ruthenium complexes.
Footnote |
† Electronic supplementary information (ESI) available. CCDC 2249596 and 2249598. For ESI and crystallographic data in CIF or other electronic format see DOI: https://doi.org/10.1039/d4nj01420k |
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