{'fraction_non_alphanumeric': 0.037929908576404006, 'fraction_numerical': 0.01714192424902046, 'mean_word_length': 4.541917973462002, 'pattern_counts': {'":': 0, '<': 1, '<?xml version=': 0, '>': 6, 'https://': 0, 'lorem ipsum': 0, 'www.': 0, 'xml': 0}, 'pii_count': 0, 'substrings_counts': 0, 'word_list_counts': {'cursed_substrings.json': 1, 'profanity_word_list.json': 0, 'sexual_word_list.json': 0, 'zh_pornsignals.json': 0}}
An efficient factor for fast screening of high-performance two-dimensional metal–organic frameworks towards catalyzing the oxygen evolution reaction

Two-dimensional (2D) metal–organic frameworks (MOFs) are promising materials for catalyzing the oxygen evolution reaction (OER) due to their abundant exposed active sites and high specific surface area. However, how to rapidly screen out highly-active 2D MOFs from numerous candidates is still a great challenge. Herein, based on the high-throughput density functional theory (DFT) calculations for 20 kinds of different transition metal-based MOFs, we propose a factor for fast screening of 2D MOFs for the OER under alkaline conditions (pH = 14.0), that is, when the Gibbs free energy change of the O–O bond formation (defined as ΔG1) is located at ∼1.15 eV, the peak OER performance would be achieved. Based on the high-throughput calculation results, the prediction factor can be further simplified by replacing the Gibbs free energy with the sum of the associated single point energy (SPE) and a binding energy-dependent term. Guided by this factor, we successfully predicted and then obtained the high-performance Ni-based 2D MOFs. This factor would be a practical approach for fast screening of 2D MOF candidates for the OER, and also provide a meaningful reference for the study of other materials.


Introduction
Developing clean energy materials is of great importance since the environmental issues caused by fossil fuels have been increasingly emerging. [1][2][3][4][5] Hydrogen, which is a kind of environmentally-friendly energy carrier with a high energy density, 6 has drawn increasing attention. 7,8 Water splitting has been widely considered to be a promising strategy to generate hydrogen. 9,10 However, the electrocatalyzed oxygen evolution reaction (OER) is the efficiency-determining step of water splitting because the OER is a multistep, four-electron transfer process, which is a Gibbs free energy uphill process and then suffers from slow kinetics and requires a high overpotential to drive the reaction. [11][12][13] Hence, designing highly efficient OER materials is a key subject to further improving the application of hydrogen energy technology. [14][15][16][17] Metal-organic frameworks (MOFs) are a kind of porous material formed by the coordination bonds between inorganic metal atoms and organic ligands. 18,19 Due to their unique structural features, MOFs could deliver a series of inherent advantages in heterogeneous catalysis, such as a well-dened chemical structure, large specic surface area and high porosity. [20][21][22] Unfortunately, MOFs are usually assembled in the form of a three-dimensional (3D) network structure, which hinders the metal atoms in the body phase from being accessed by the reactants, and thus limits the enhancement of catalytic activity. 23 To address this issue, ultra-thinning MOFs into twodimensional (2D) nanosheets is an efficient strategy to obtain MOF-based high-performance catalysts due to the ultrathin thickness for rapid mass and electron transfer, and high percentages of exposed active metal sites. 24 Thus, 2D MOFs have been widely studied and have become one of the hottest subjects in the catalysis eld. 25,26 However, a noteworthy fact is that more than 80 000 kinds of MOFs have been reported so far, and this value is still growing rapidly. 27 Screening out desired high-performance 2D MOFs from numerous candidates efficiently remains a challenge. Therefore, a convenient screening factor is urgently needed to improve screening efficiency. However, there has been no correlative report for a MOF screening factor in the OER catalysis system so far. Exploring a general factor that can be used to accelerate the screening process would be greatly signicant. [28][29][30] Since the formation of the O-O bond and the deprotonation step in the OER process have a great inuence on the reaction thermodynamics, the binding strength of the related intermediates may be highly correlated with the overpotential. This view was veried by our high-throughput calculations and experimental results. Based on these, we propose a factor for constructing high-performance 2D MOFs for the OER in this work, and it points out that when the Gibbs free energy change of the O-O bond formation step (dened as DG 1 ) is around 1.15 eV, the peak OER performance would be obtained. With the DG 1 further deviating from this value, a higher overpotential for the OER would be needed to drive the reaction. We further predicted that Ni-based MOFs would offer better activity than other counterparts based on this factor, which was validated by the experimental results and so as to the predictive power of the factor. This successful practice indicates that the factor would offer credible guidance for constructing highly active MOFs for the OER, and would signicantly reduce the research cost and shorten the development period thanks to its lower amount of computation compared with direct high-throughput calculation screening.

Results and discussion
According to a previous report, 31 the potential determining step (PDS) of the OER under alkaline conditions (pH ¼ 14.0) is the formation of O-O bonding (eqn (1)) or the deprotonation process (eqn (2)).

M-O + OH
Here, M is the active metal site of catalysts, e À is the electron and OH À is hydroxyl, and the Gibbs free energy change of eqn (1) (that is the DG 1 ), and the Gibbs free energy change of the second deprotonation step (the reaction in eqn (2), dened as DG 2 ) could be derived as follows: Here, G is the Gibbs free energy of the corresponding species, and similarly hereinaer. The overall equation is as follows: The high-throughput DFT calculations (see computational details in the ESI †) of the MOFs based on the rst twenty kinds of transition metals, which cover a wide range of the commonly used transition metals to prepare MOFs, indicate that DG 1 + As shown in Fig. 1a, twenty kinds of different transition metal-based MOFs possess an almost constant value of DG O (the uctuation is about 0.01 eV per cell, 10 À3 eV per atom), which agrees with the tendency on oxide surfaces that was reported in the previous literature, 32 indicating that OER processes on MOF surfaces follow the same scaling relationship as that on metal oxide surfaces. This could be explained as follows: in this equation, the G(OH À ) and G(H 2 O) are constants no matter what the metal is. Besides, the DG O was also observed to be a constant due to their similar structure derived nearly equal zero point energy (ZPE) and entropy correction TS term ( Taking the OH À and H 2 O molecules into consideration, the value of DG 1 + DG 2 would be obtained. In this work, the G(OH À ) was derived from the denition of the standard hydrogen electrode (SHE) because the periodic DFT calculations can't predict the thermodynamic properties of OH À since it would cause the articial electrostatic interaction between the periodic images of the charged ions. 33 Hence, the G(OH À ) is derived as follows: Here, the pH is the pH value of the system. Hence, eqn (5) could be transformed to be the following equation: When the calculated Gibbs free energies of H 2 O (G(H 2 O) ¼ À466.98 eV) and H 2 (G(H 2 ) ¼ À30.89 eV) were substituted in eqn (8) with pH ¼ 14.0, we can conclude the following equation: Combined with the result of DG O shown in Fig. 1a, we can obtain the value of DG 1 + DG 2 . As shown in Fig. 1b, the value of DG 1 + DG 2 is also a constant value of $2.3 eV for different metalbased MOFs since the DG O is almost constant as mentioned above. Based on this, it is reasonable to conclude that when DG 1 ¼ DG 2 ¼ 1.15 eV, the lowest overpotential, namely, the peak OER performance would be achieved since the overall overpotential is dependent on the max[DG 1 , . This implies that the following condition must be met to achieve the peak OER performance: (10) Here, we dened the difference between G(M-O-OH) À G(M-O) and G(OH À ) as DG OH : Considering that DG 1 is the difference between DG OH and G(OH À ), we can replace the G(OH À ) with eqn (7) and obtain the below factor to achieve the peak OER performance: As shown in Fig. 2a, our results indicate that the DG OH of different metal-based MOFs is not a constant like DG O . This should be attributed to the more complex potential surface (PES) induced by the more structural freedom of M-OOH, especially for the H atom, which would signicantly contribute to ZPE due to the light mass. The different DG OH values lead to the different performances of the OER. A too high DG OH value will lead to a high overpotential for the formation of O-O bonding, while a too small DG OH value will cause a high overpotential for the deprotonation process. From the DG OH , we could obtain the DG 1 and DG 2 respectively. As shown in Fig. 2b, different metal-based MOFs have different DG 1 and DG 2 , implying that the PDS and overall overpotential are different as the metal ions change. Meanwhile, from the DG 1 and DG 2 , we could also rank the OER performance for different MOFs theoretically according to eqn (10), that is, the closer to 1.15 eV of DG 1 , the lower the overpotential would be delivered.
Considering the requirement of the frequency, the calculation of Gibbs free energy is usually computationally intensive, leading to a high calculation cost. 34 Hence, an ideal way to obtain the Gibbs free energy is by deriving from a specic quantity that is easy to obtain and strongly correlated with the Gibbs free energy. Based on this purpose, we seek to explore the desired specic quantity. Quite sensibly, the SPE, which is easily acquired, may be a promising candidate. Note that the difference between SPE and the Gibbs free energy is the contribution from the vibration at the limited temperature, and the vibration frequency is strongly dependent on the bond strength. 35 Since the bond strength is usually described by the bond order, the difference between SPE and Gibbs free energy should have a certain correlation with the associated bond order, that is, the O-O bond and O-H bond. However, the O-O bond orders and O-H bond orders in different metal-based MOFs should not vary signicantly, which is not enough to accurately distinguish different metal-based MOFs. Hence, the binding energy, derived from the formula below, is employed. 36 Fig. 3

Here, the E binding(A-B) is the binding energy of A and B. E(A-B) is the total energy of the binding conguration of A and B. E(A) and E(B) is the total energy of component A and component B, respectively. This inference was conrmed by the phonon calculations of M-OOH and M-O. As shown in
Hence, the DG OH could be replaced by the DE OH plus an additional binding energy-dependent term. As a result, this substitution would signicantly reduce the amount of computation, lowering the calculation cost and shortening the calculation time as the computationally intensive frequency calculation was rationally substituted. Collectively, eqn (10) could be transformed as follows: Based on the factor proposed by eqn (15), we could predict the OER performance for different metal-based 2D MOFs rapidly, which is signicant for catalyst design and screening.
Based on the prediction from the factor, the Ni, Co, Mn and Fe based 2D MOFs should deliver incremental performance in the order of Ni > Co > Mn > Fe. For validation purpose, we seek to verify the factor experimentally since the electrochemical measurements would offer a validation of the predictive power   of the factor. Hence, four kinds of different metal-based 2D MOFs were prepared for further validation. The morphology of these four kinds of 2D MOF nanosheets is shown in Fig. 4 and S2, † in which the 2D ultrathin feature of the as-prepared MOFs could be identied clearly from the scanning electron microscope (SEM) and transmission electron microscopy (TEM) images, and this agrees with the simulated morphology (Fig. S3 †) by means of the Bravais-Friedel-Donnay-Harker (BFDH) method. 38 The high education ring dark eld scanning transmission electron microscope (HAADF-STEM) images and the corresponding energy disperse spectroscopy (EDS) mapping images are shown in Fig. S4-S7, † indicating that the metal elements and N and O are uniformly distributed on the entire surface of these 2D MOFs, and the carbon element that dominates the eld of view arises from the carbon membrane that was used to prepare the TEM sample. The size of the nanosheets was estimated at hundreds of nanometers and the thickness was measured at $10 nm through the side view SEM images of Ni-MOFs (Fig. S8 †), which agree well with the atomic force microscopy (AFM) measurement shown in Fig. 4e-h. Besides, the powder X-ray diffraction (PXRD) results (Fig. S9 †) showed that all these as-prepared MOFs are isostructural, and no obvious peak shi was detected, indicating that the interplanar spacing and lattice parameters almost remained unchanged, and this should be attributed to the similar atomic radius for Ni, Co, Fe and Mn. Moreover, the PXRD patterns are in accordance with the simulated pattern of the optimized model structure, which further conrmed the successful preparation of the 2D-MOFs. The high-resolution X-ray photoelectron spectroscopy (XPS) spectra of the metal elements are shown in Fig. S10. † According to previous reports, 23,24 the location of these main peaks indicates that the metal nodes are coordinated octahedrally by six oxygen atoms. Based on the above results, the atomic arrangements in 2D MOFs could be well dened as shown in Fig. 4i and j. In addition, the N 2 isotherm (Fig. S11 †) of these four kinds of 2D MOFs at 77 K was supposed to be type IV with a H4-type hysteresis loop, which should be attributed to the formation of narrow slits. Note that these 2D MOFs have nearly the same Brunauer-Emmett-Teller (BET) specic surface area (25.91 m 2 g À1 , 26.32 m 2 g À1 , 25.47 m 2 g À1 , and 23.92 m 2 g À1 for Ni-MOFs, Co-MOFs, Fe-MOFs and Mn-MOFs, respectively), which should be assigned to their similar lattice structure. Collectively, these results conrmed the successful preparation of 2D MOF nanosheets and were able to be used for subsequent evaluation of the OER performance experimentally.
The OER performance was measured with a typical threeelectrode conguration. For comparison purpose, OER performance was evaluated via the onset potential (dened as the potential to achieve a current density of 1 mA cm À2 for the OER) of these four kinds of MOFs. Note that the peak of Ni-MOFs around 1.37 V should be attributed to the oxidation of Ni. 24 As shown in Fig. 5a-d, the OER performance was ranked in the order of Ni-MOFs > Co-MOFs > Mn-MOFs > Fe-MOFs with an onset potential of 1.45 V, 1.48 V, 1.56 V and 1.60 V versus the reversible hydrogen electrode (RHE) respectively, which agrees well with the calculated results and the factor proposed by eqn (10), that is, the DG 1 of Ni-MOFs is the closest to 1.15 eV and thus delivered the best OER performance. As DG 1 goes away from 1.15 eV, more positive potential was needed to drive the reaction (Fig. 5e). Note that the value of jDG 1 À 1.15j in Fig. 5e is derived from eqn (15), rather than from the Gibbs free energy calculations, and it obviously indicates that the factor also has the predictive power aer the DG OH in eqn (10) is substituted by the DE OH , and no signicant loss of accuracy was detected. As a result, a good compromise is achieved between accuracy and computational cost. Besides, the factor in eqn (10) indicated that the onset potential should be linearly correlated to the jDG 1 À 1.15j, and this was also observed in Fig. 5f, which further conrmed the credibility of the proposed factor.
Apart from the onset potential, the Tafel slope, which reects the kinetics of the reaction, was also calculated based on the corresponding linear sweep voltammetry (LSV) curves. As shown in Fig. 5a, the Ni-MOFs could deliver the lowest Tafel slope of 34 mV dec À1 compared with other samples (43 mV dec À1 for Co-MOFs, 45 mV dec À1 for Mn-MOFs and 48 mV dec À1 for Fe-MOFs) in this work, conrming the outstanding reaction kinetics for the OER. Compared to state-of-the-art RuO 2 , IrO 2 and Pt/C (Fig. S12 †), the as prepared Ni-MOFs could deliver much better OER performance, which opened up ne prospects for practical applications. Moreover, the correlation between OER performance and the d-band center was also investigated. As shown in Fig. S13, † when the d-band center increased, the adsorption energy of *OH also increased, which agrees well with the d-band center proposed by Hammer and Nørskov. [39][40][41] Meanwhile, a too high d-band center would lead to decreased OER activity, which could be explained by Sabatier's principle, which means that the best catalytic activity can be achieved with moderate binding strength, and too strong or too weak binding is not conducive to the catalytic process. Besides, the long-term stability of the catalysts is another key parameter in evaluating the OER performance. As shown in Fig. 5g, the chronoamperometry measurements at 1.65 V vs. RHE were also conducted and only <5% current density decay was observed aer the 24 h test for all the samples, indicating the excellent stability of these prepared 2D MOFs, which possess the potential for production run.

Conclusions
In conclusion, this work proposes a factor for fast screening of 2D-MOFs for catalysis of the OER under alkaline conditions aided by the high-throughput DFT calculations. This factor is straightforward and feasible for practical application. When the DG 1 is located at 1.15 eV, the peak OER performance will be delivered. Further deviation from this value would lead to a higher overpotential. Further simplication was achieved by replacing the Gibbs free energy with the sum of the associated SPE and a binding energy-dependent term. The predictive power of this factor was validated by our successful prediction and preparation of the high-performance Ni-based 2D MOFs. This factor would be a practical approach for fast screening of 2D MOF candidates for the OER, and also provides a meaningful reference for the study of other materials.

Data availability
All the calculation data and experimental data reported in this paper could be accessed from the authors.