In Situ Fabrication of Mn-Doped NiMoO4 Rod-like Arrays as High Performance OER Electrocatalyst

The slow kinetics of the oxygen evolution reaction (OER) is one of the significant reasons limiting the development of electrochemical hydrolysis. Doping metallic elements and building layered structures have been considered effective strategies for improving the electrocatalytic performance of the materials. Herein, we report flower-like nanosheet arrays of Mn-doped-NiMoO4/NF (where NF is nickel foam) on nickel foam by a two-step hydrothermal method and a one-step calcination method. The doping manganese metal ion not only modulated the morphologies of the nickel nanosheet but also altered the electronic structure of the nickel center, which could be the result of superior electrocatalytic performance. The Mn-doped-NiMoO4/NF electrocatalysts obtained at the optimum reaction time and the optimum Mn doping showed excellent OER activity, requiring overpotentials of 236 mV and 309 mV to drive 10 mA cm−2 (62 mV lower than the pure NiMoO4/NF) and 50 mA cm−2 current densities, respectively. Furthermore, the high catalytic activity was maintained after continuous operation at a current density of 10 mA cm−2 of 76 h in 1 M KOH. This work provides a new method to construct a high-efficiency, low-cost, stable transition metal electrocatalyst for OER electrocatalysts by using a heteroatom doping strategy.


Introduction
The increasingly serious environmental pollution and the excessive consumption of fossil fuels have prompted people to start looking for efficient and green energy [1]. Hydrogen, due to its high combustion value, non-polluting, and abundant source, is seen as a highly efficient and clean energy alternative to traditional fossil energy sources and has attracted increasing scientific attention [2]. Electrochemical hydrolysis is an up-and-coming technology for sustainable hydrogen production with zero carbon emissions [3]. Two half-reactions are involved in electrochemical hydrolysis: the hydrogen evolution reaction (HER) and the oxygen evolution reaction (OER). The slow kinetics of the four-electron transfer for OER requires a larger overpotential to drive the reaction [4,5]. Electrocatalysts can effectively reduce the reaction energy barrier and accelerate the charge transfer rate. Thus far [6], RuO 2 and IrO 2 are known as efficient catalysts for HER and OER, respectively, however, the low stability, high cost, and scarcity of resources of these noble metal catalysts remain and limit their widespread application [7]. Therefore, designing a highly stable, low-cost, and widely available OER catalyst is imperative.

Preparation of Precursors NiMoO 4 /NF
Prior to the synthesis, nickel foam was sonicated in 3 M HCl, ethanol, acetone, and deionized water for 15 min to remove the oxide layer and then vacuum dried. The NiMoO 4 micro-rod array structure precursors were prepared by the conventional hydrothermal method [39]. Samples of 2.4 mmol of Ni(NO 3 ) 2 ·6H 2 O and 0.6 mmol of (NH 4 ) 6 Mo 7 O 24 ·4H 2 O were dissolved in 35 mL of deionized water and magnetically stirred for 30 min until the solution turned light green, after which the above resolution was transferred to a reaction vessel with a 50 mL polytetrafluoroethylene (PTFE) liner, then the pretreated nickel foam was added and held at 150 • C for 6 h. When left to cool naturally, the precursor was rinsed from the nickel foam with deionized and ethanolic solutions. Then, the NiMoO 4 ·xH 2 O/NF precursor was placed in a high-temperature tube furnace and heated to 350 • C for 2 h under an argon atmosphere at a heating rate of 5 • C/min. The sample obtained was recorded as NiMoO 4 /NF.

Preparation of Mn-Doped-NiMoO 4 /NF
We precisely weighed 2.5 mmol of urea, 1 mmol of ammonium fluoride, and x mmol (x = 0.2, 0.25, 0.33) MnCl 2 ·4H 2 O, keeping the molar ratio of Ni to Mn at (1:15, 1:12, 1:9), and 35 mL of deionized water, which was stirred magnetically for 20 min, and subsequently transferred to a reaction vessel with 50 mL with a PTFE liner, then the NiMoO 4 /NF precursor prepared in Section 2.2 above was added and reacted at 120 • C for 5 h. After being left to naturally cool, the sample was removed and then placed into a vacuum drying oven and dried at 60 • C for 12 h. These samples were recorded as Mn-doped-NiMoO 4 /NF(x) (x = 20, 25, 33 for 1:15, 1:12, 1:9, respectively). To better compare the effect of Mn ion doping on the electrocatalytic performance of the samples, Mn-doped-NiMoO 4 /NF (0) was prepared by the same process, except for the addition of manganese chloride.

Preparation of RuO 2 /NF
To better compare the activity of the catalysts, 16 mg of RuO 2 powder, 2 mg of carbon black, 2 mg of PVDF, and 5 µL of NMP were added to an agate mortar and ground for about 15 min, during which ethanol was added as a dispersant as required. The prepared-ink was evenly applied to the ready Ni foam and subsequently dried under vacuum at 60 • C for 12 h to obtain RuO 2 /NF. After weighing, the RuO 2 loading mass was approximately 5 mg cm −2 .

Characterization
The XRD characterization in this work was carried out using a Smartlab model X-ray diffractometer manufactured by Rigaku, Japan. The experimental parameters used in the experiments were as follows: radiation type Cu Kα (λ = 0.15406 nm), voltage 40 kV, Nanomaterials 2023, 13, 827 4 of 14 current 100 mA, scanning speed 8 • /min, scanning range 5-70 • . Raman characterization was through a Renishaw inVia Reflex laser Raman spectrometer. The laser power was 6 mW and the laser excitation wavelength was 532 nm. The scanning electron microscope (SEM) was a Sigma 300 field emission scanning electron microscope from Zeiss, Germany. In addition, the SEM was equipped with an X-ray energy spectrometer (EDS) to obtain the elemental surface distribution and the elemental content of the sample surface under the accelerating voltage of 20 kV. The microstructure of the material and the lattice stripes were obtained through a transmission electron microscope (TEM) Tecanai G2 F30 from FEI, USA, and the X-ray photoelectron spectroscopy (XPS) characterization was carried out using an ESCALAB 250XI from Thermo Fisher, USA. The ray type was Al Kα rays with a step size of 1 eV and a spot size of 650 µm, and the sample-making process was similar to SEM.

Electrochemical Measurement
All electrochemical tests in this work were carried out on an electrochemical workstation (CHI 660E Shanghai Chenhua). A standard three-electrode system was used: a Hg/HgO electrode as the reference electrode, graphite carbon rods as the counter electrode, and the experimentally prepared self-supporting material as the working electrode, using an electrolyte with a concentration of 1 M KOH. All tests were carried out in a constant temperature laboratory under 25 • C and the electrolyte needed to be saturated with O 2 for 30 min before the OER tests were carried out. As a result, the potential in all tests will be converted to a reversible hydrogen electrode potential (RHE) E(RHE) = E(Hg/HgO) + 0.059 × pH + 0.098 (pH = 14). In addition, the scan rate of the linear scanning voltammetry (LSV) was set to a uniform 5 mV s −1 and the voltage range of the tests was 0 to 1 V. To accurately evaluate the overpotential in the OER tests, it was further corrected for iR compensation according to the formula E(RHE) compensation = E(RHE) − iR. The cyclic voltammetry (CV) curves were recorded at sweep rates of 20-160 mV s −1 to calculate the double layer capacitance (CDL) of the electrode material and hence estimate the active electrochemical area (ECSA) of the electrocatalyst material. The electrochemical impedance spectroscopy (EIS) technique was used to test the frequency range of 0.1 to 100,000 Hz. The Nyquist diagram was fitted by Zview software (version: Zview2). The stability of the electrocatalyst materials was assessed by chrono-potentiometry (CP). Figure 1 shows the preparation of a Mn-doped-NiMoO 4 /NF self-supporting electrode. First, NiMoO 4 /NF micron-rod arrays were grown on nickel foam by the hydrothermal reaction and annealing calcination. Next, secondary hydrothermal doping of Mn elements and etching of the original micrometer rods into nanosheets to form a hierarchical structure were carried out. After a two-step hydrothermal reaction and one-step calcination, the color of the Ni foam changed from the original silver-grey into light green. The physical phase composition and crystal structure of NiMoO4/NF precursors and Mn-doped-NiMoO4/NF were studied by XRD, as shown in Figure 2a,b. Except for the diffraction peaks at 44.5°, 51.8°, and 76.4°, which perfectly matched the standard PDF card of metallic nickel foam (JCPDS 04-0850), the other diffraction peaks perfectly matched the standard PDF cards of NiMoO4·xH2O (JCPDS 13-0128) and NiMoO4 (JCPDS 86-0361 and JCPDS 45-0142) (as shown in Figure 2a) [40]. There was a significant decrease in the lattice  Figure 2a) [40]. There was a significant decrease in the lattice parameters of the NiMoO 4 /NF precursors with the doping of Mn as the reaction time increased from 3 h to 8 h, as shown in Figure 2b. The diffraction peak was slightly shifted to the right, which can be attributed to the fact that the radius of the Mn 2+ ion is smaller than that of the Ni 2+ ion. In addition, a diffraction peak attributed to MnO (JCPDS 04-0326) could be observed around 26.6 • , corresponding to a crystal plane of (1 2 0). The physical phase composition and crystal structure of NiMoO4/NF precursors and Mn-doped-NiMoO4/NF were studied by XRD, as shown in Figure 2a,b. Except for the dif fraction peaks at 44.5°, 51.8°, and 76.4°, which perfectly matched the standard PDF card of metallic nickel foam (JCPDS 04-0850), the other diffraction peaks perfectly matched the standard PDF cards of NiMoO4·xH2O (JCPDS 13-0128) and NiMoO4 (JCPDS 86-0361 and JCPDS 45-0142) (as shown in Figure 2a) [40]. There was a significant decrease in the lattice parameters of the NiMoO4/NF precursors with the doping of Mn as the reaction time in creased from 3 h to 8 h, as shown in Figure 2b. The diffraction peak was slightly shifted to the right, which can be attributed to the fact that the radius of the Mn 2+ ion is smaller than that of the Ni 2+ ion. In addition, a diffraction peak attributed to MnO (JCPDS 04-0326 could be observed around 26.6°, corresponding to a crystal plane of (1 2 0).

Raman Analysis
To gain insights into the structural composition of the material, the electrocatalys was further characterized by Raman spectroscopy. As shown in Figure 3a, the Mn-doped NiMoO4/NF possessed characteristic peaks attributed to NiMoO4 at positions 356 cm −2 827 cm −2 , 872 cm −2 , and 948 cm −2 [41]. The band at 923 cm −1 and 872 cm −1 indicates the symmetric stretching and asymmetric stretching bonds of the Mo-O bonds, respectively Another band at 356 cm −1 was assigned to the bending vibration of the O-Mo-O unit [42,43]. In contrast to NiMoO4/NF, the broad Raman band located in the range of 440 cm − to 600 cm −2 may be attributed to the Mn-O bonding vibrational mode of the oxides o amorphous Mn (Figure 3b). The above conclusions are consistent with the XRD results.

Raman Analysis
To gain insights into the structural composition of the material, the electrocatalyst was further characterized by Raman spectroscopy. As shown in Figure 3a, the Mn-doped-NiMoO 4 /NF possessed characteristic peaks attributed to NiMoO 4 at positions 356 cm −2 , 827 cm −2 , 872 cm −2 , and 948 cm −2 [41]. The band at 923 cm −1 and 872 cm −1 indicates the symmetric stretching and asymmetric stretching bonds of the Mo-O bonds, respectively. Another band at 356 cm −1 was assigned to the bending vibration of the O-Mo-O units [42,43]. In contrast to NiMoO 4 /NF, the broad Raman band located in the range of 440 cm −2 to 600 cm −2 may be attributed to the Mn-O bonding vibrational mode of the oxides of amorphous Mn (Figure 3b). The above conclusions are consistent with the XRD results.

SEM and TEM Analysis
The microscopic morphology and elemental distribution of the material were characterized by SEM and an accompanying EDS spectrometer. Chemical etching formed many self-assembled nanosheets, which showed a uniform thickness of about 120 nm and

SEM and TEM Analysis
The microscopic morphology and elemental distribution of the material were characterized by SEM and an accompanying EDS spectrometer. Chemical etching formed many self-assembled nanosheets, which showed a uniform thickness of about 120 nm and a uniform distribution. Even with the high density of the nanosheets, the original rod-like array structure grown on nickel foam could still be vaguely distinguished, as shown in Figure 4h. By comparing (Figure 4a-c) Mn-doped-NiMoO 4 /NF (0) and (Figure 4d-f) Mn-doped-NiMoO 4 /NF (25), it can be seen that the size and the density of the nanosheets increased significantly after doping with Mn elements, and the gap in the nanosheets increased, which was conducive to further penetration of the electrolyte solution into the catalyst and accelerated the diffusion of bubbles. This suggests that the Mn element can modulate the morphology of the electrocatalyst material, providing more nanosheets and thus exposing more active sites and increasing the electrochemically active area, which may facilitate enhanced electrochemical activity. As shown in Supplementary Figure S1c,f,i, it was also observed that as the reaction time changed from 3 h to 8 h, the size of the nanosheets gradually became more significant. The different sized pores in the nanosheets accelerate the rate of electron transport and provide more channels for the release of oxygen [44]. As shown in Figure 4i  The structure of the Mn-doped-NiMoO4 was further investigated by TEM. To avoid the influence of the nickel foam substrate on the test, a small sample was chosen for sonication in an ethanol solution, after which a pipette was used to measure and disperse a uniform drop onto the copper grid. As shown in Figure 5a, the rod-like structure of the electrocatalyst material could be observed, which is consistent with the characterization results of SEM. Therefore, a rod-like structure with a high aspect ratio can effectively increase the contact area between the catalyst and the electrolyte. Figure 5b-d further reveals that the Mn-doped-NiMoO4/NF (25) lattice stripe characteristics, as shown in Figure  5b, showed two different widths in the lattice stripe. The lattice stripe spacing was equal to 0.321 nm, corresponding to NiMoO4·H2O. In comparison, a small amount of Mn ions took the place of Mo ions to form NiMnO3 (JCPDS 48-1330), with a lattice stripe spacing The structure of the Mn-doped-NiMoO 4 was further investigated by TEM. To avoid the influence of the nickel foam substrate on the test, a small sample was chosen for sonication in an ethanol solution, after which a pipette was used to measure and disperse a uniform drop onto the copper grid. As shown in Figure 5a, the rod-like structure of the electrocatalyst material could be observed, which is consistent with the characterization results of SEM. Therefore, a rod-like structure with a high aspect ratio can effectively increase the contact area between the catalyst and the electrolyte. reveals that the Mn-doped-NiMoO 4 /NF (25) lattice stripe characteristics, as shown in Figure 5b, showed two different widths in the lattice stripe. The lattice stripe spacing was equal to 0.321 nm, corresponding to NiMoO 4 ·H 2 O. In comparison, a small amount of Mn ions took the place of Mo ions to form NiMnO 3 (JCPDS 48-1330), with a lattice stripe spacing of 0.358 nm corresponding to the crystal plane (0 1 2), as analyzed by the software Digital micrograph. As shown in Figure 5c,d, lattice stripes with a lattice spacing equal to 0.306 nm and 0.331 nm were observed that corresponded to the (3 1 0) and (2 2 0) crystal planes of NiMoO 4 (JCPDS 86-0361 and JCPDS 45-0142), respectively. It could also be seen that there was a large amount of amorphous manganese oxide present on the surface of the material, with defects at the interface between the lattice stripe and the lattice stripe, favoring the exposure of more active sites [45].

XPS Analysis
The elemental composition and chemical states in the Mn-doped-NiMoO4/NF and NiMoO4/NF samples were investigated by XPS. The binding energy of the standard C 1s (284.80 eV) was used to correct the binding energy of all XPS spectra. The XPS spectra (Supplementary Figure S3a) show that Ni, Mo, Mn, O, and C co-existed in the Mn-doped-NiMoO4/NF (25), and the binding energies of the standard in Figure 6a shows that all of the spin-orbit splits of Ni 2p could be fitted to Ni 2p3/2 and Ni 2p1/2, accompanied by a satellite peak. Compared with Mn-doped-NiMoO4/NF (0) and NiMoO4/NF, the binding energy of Ni 2p3/2 (855.95 eV) in the Mn-doped-NiMoO4 /NF (25) shifted toward a higher binding energy with 0.23 eV and 0.32 eV; the binding energy of Ni 2p1/2 (873.51 eV) was

XPS Analysis
The elemental composition and chemical states in the Mn-doped-NiMoO 4 /NF and NiMoO 4 /NF samples were investigated by XPS. The binding energy of the standard C 1s (284.80 eV) was used to correct the binding energy of all XPS spectra. The XPS spectra (Supplementary Figure S3a) show that Ni, Mo, Mn, O, and C co-existed in the Mn-doped-NiMoO 4 /NF (25), and the binding energies of the standard in Figure 6a shows that all of the spin-orbit splits of Ni 2p could be fitted to Ni 2p 3/2 and Ni 2p 1/2 , accompanied by a satellite peak. Compared with Mn-doped-NiMoO 4 /NF (0) and NiMoO 4 /NF, the binding energy of Ni 2p 3/2 (855.95 eV) in the Mn-doped-NiMoO 4 /NF (25) shifted toward a higher binding energy with 0.23 eV and 0.32 eV; the binding energy of Ni 2p 1/2 (873.51 eV) was also positively shifted with 0.12 eV and 0.21 eV; and the binding energy difference between Ni 2p 3/2 and Ni 2p 1/2 was 17.56 eV. The electron transfer in the nickel center may be attributed to the doping of the Mn elements and their interactions, suggesting that Ni 2+ converted to a higher valance state [46]. As shown in Figure 6b, the binding energies at Mo 3d 5/2 (231.86 eV) and Mo 3d 3/2 (235.06 eV) shifted toward a lower binding energy with 0.37 eV and 0.39 eV compared to NiMoO 4 /NF. The peak separation of 3.2 eV indicates a high valence of Mo 6+ species [47]. As shown in Figure 6c, the O 1s orbitals for Mn-doped-NiMoO 4 /NF (25) could be fitted to two peaks: lattice oxygen (O 1 : 530.53 eV), and absorbed oxygen may be attributed to surface oxygen defects/vacancy species (O 2 : 531.70 eV) [48]. The calculated S O2 /(S O2 + S O1 ) for Mn-doped-NiMoO 4 /NF (25) was 30.2%, which was 10.1% higher than Mn-doped-NiMoO 4 /NF (0) and 13.4% higher than NiMoO 4 /NF, respectively, demonstrating that more oxygen defects are generated, which is beneficial to the overall electrocatalytic process [49]. The Mn 2p orbital for Mn-doped-NiMoO 4 /NF (25) could be fitted to three subpeaks at binding energies of 637.86 eV, 639.94 eV, and 642.56 eV, corresponding to Mn 2+ , Mn 3+ , and Mn 4+ , respectively (Figure 6d), while the other peaks were attributed to the oxidation state of the Mn formed on the surface. All of these results could help to confirm that Mn has been successfully doped into NiMoO 4 . The calculated SO2/(SO2 + SO1) for Mn-doped-NiMoO4/NF (25) was 30.2%, which was 10.1% higher than Mn-doped-NiMoO4/NF (0) and 13.4% higher than NiMoO4/NF, respectively, demonstrating that more oxygen defects are generated, which is beneficial to the overall electrocatalytic process [49]. The Mn 2p orbital for Mn-doped-NiMoO4/NF (25) could be fitted to three subpeaks at binding energies of 637.86 eV, 639.94 eV, and 642.56 eV, corresponding to Mn 2+ , Mn 3+ , and Mn 4+ , respectively (Figure 6d), while the other peaks were attributed to the oxidation state of the Mn formed on the surface. All of these results could help to confirm that Mn has been successfully doped into NiMoO4.

OER Performance Testing
In order to avoid the influence of the oxidation peak of Ni on the test, a reverse scan in the potential range 1-0 V was chosen to obtain a LSV polarization curve. To find the optimum reaction time, the electrocatalysts prepared at different reaction times (3 h, 5 h, and 8 h) were tested for LSV (Supplementary Figure S4), and the optimum reaction time

OER Performance Testing
In order to avoid the influence of the oxidation peak of Ni on the test, a reverse scan in the potential range 1-0 V was chosen to obtain a LSV polarization curve. To find the optimum reaction time, the electrocatalysts prepared at different reaction times (3 h, 5 h, and 8 h) were tested for LSV (Supplementary Figure S4), and the optimum reaction time was set at 5 h. The LSV curves of the different catalyst samples are shown in Figure 7a. The overpotential of the commercial RuO 2 /NF at 10 mA cm −2 was 242 mV. It is worth noting that Mn-doped-NiMoO4/NF (25) had the optimum overpotential (230 mV) when the current density was 10 mA cm −2 , which was 62 mV lower than the pure NiMoO 4 /NF (299 mV). As shown in Figure 7b, Mn-doped-NiMoO 4 /NF (25) achieved the highest current density (225 mA cm −2 ) and exhibited a lower overpotential compared to other samples at both the 10 mA cm −2 and 50 mA cm −2 current densities of all samples in the potential range tested. These results indicate that the Mn-doped-NiMoO 4 /NF (25) catalyst had the optimum OER catalytic activity. The reason why the Mn-doped-NiMoO 4 /NF (25) sample showed excellent OER activity is that the content of Mn ions during the chemical etching process affects the surface reconstruction and enrichment of the high oxidation state hydroxide, and only the optimum amount of doping can further improve the OER catalytic activity of NiMoO 4 [50,51].
The Tafel slope is an essential indicator of the kinetics of the catalytic reaction, with a smaller Tafel slope indicating a faster OER reaction as the potential increases [52]. As shown in Figure 7c, the Tafel slope of the control RuO 2 /NF was 177.07 mV dec −1 , the Tafel slope of Mn-doped-NiMoO 4 /NF (25)  To better explain the Mn-doped-NiMoO 4 /NF (25) OER performance, the electrochemical active surface area (ECSA) of different samples was evaluated by performing CV tests to calculate the C dl of the material, and larger ECSA indicates more active sites exposed by the electrocatalyst. As shown in Figure 7d optimum OER catalytic activity. The reason why the Mn-doped-NiMoO4/NF (25) sample showed excellent OER activity is that the content of Mn ions during the chemical etching process affects the surface reconstruction and enrichment of the high oxidation state hydroxide, and only the optimum amount of doping can further improve the OER catalytic activity of NiMoO4 [50,51]. The Tafel slope is an essential indicator of the kinetics of the catalytic reaction, with a smaller Tafel slope indicating a faster OER reaction as the potential increases [52]. As shown in Figure 7c, the Tafel slope of the control RuO2/NF was 177.07 mV dec −1 , the Tafel The stability of the catalyst is an important criterion to assess whether the catalyst can be used in the long-term. As shown in Figure 7f, the stability of Mn-doped-NiMoO 4 /NF (25) was tested for 76 h at a constant current density of 10 mA cm −2 using the chronopotential (CP), which showed an increase in overpotential of only 18 mV. The LSV polarization curves were compared before and after the CP test, and the difference between the two curves was not significant, demonstrating the excellent stability of the catalyst under alka-line conditions. After 76 h of chronopotential testing, the morphology of the nanosheets did not change significantly, but the gap between the rod arrays became slightly larger and the thickness of each nanosheet increased by nearly 20 nm (details can be found in Supplementary Figure S2). The main reasons for its long-term stability are mainly the rougher surface of the nanosheets and the wider gap in the rod array structure, which increases the direct contact area between the electrolyte and the electrocatalyst, thus exposing more active sites. As a side note, the appropriate density of electrocatalytic material optimizes the entire OER reaction process. According to the EDS energy spectrum analysis, the elements Ni, O, and Mn were still present on the surface of the electrocatalyst, but the amount of Mo was barely detectable. Raman testing of the sample after the chronopotentiometric method was carried out and revealed distinct Raman peaks at 477 cm −1 and 548 cm −1 , attributed to the E g (Ni 3+ -O) bending vibration mode and A 1g (Ni 3+ -O) stretching vibration mode of γ-NiOOH, respectively [53] (details can be found in Supplementary Figure S6).

Conclusions
In summary, we successfully prepared self-supported electrodes (Mn-doped-NiMoO 4 /NF (25)) on 3D conductive nickel foam with a rod-like nanosheet array structure by a twostep hydrothermal and low-temperature calcination method. The electrocatalytic performance tests demonstrates that the doping of Mn elements could effectively modulate the NiMoO 4 /NF morphology, and the electronic valence state of its surface improved the electrical conductivity as well as provided more active sites. In addition, the tight connection between NiMoO 4 and Ni foam effectively prevented agglomeration between the electrocatalysts, giving the catalyst excellent stability. In particular, the Mn-doped-NiMoO 4 /NF (25) only required 230 mV to drive a current density of 10 mA cm −2 , and stable tests were completed for at least 76 h under alkaline conditions. During this process, the oxidation state of Ni increased and there was more Ni 3+ as well as the rapid dissolution of MoO 4 2− , thus showing excellent OER activity. The designed electrocatalyst has the advantages of high activity and stability, and show the potential to be applied to the OER on a large scale. This work provides a new idea for the design and development of non-precious metal catalysts with a transition metal element doping strategy.  Table S1: Comparisons of OER activity for the Mn-doped electrocatalysts and NiMoO 4 -based electrocatalysts in alkaline conditions (η: overpotential at the current density of 10 mA cm −2 ). References [16,32,[54][55][56][57][58][59][60]

Conflicts of Interest:
The authors declare no conflict of interest.