Pearson’s Principle-Inspired Robust 2D Amorphous Ni-Fe-Co Ternary Hydroxides on Carbon Textile for High-Performance Electrocatalytic Water Splitting

Layered double hydroxide (LDH) is widely used in electrocatalytic water splitting due to its good structural tunability, high intrinsic activity, and mild synthesis conditions, especially for flexible fiber-based catalysts. However, the poor stability of the interface between LDH and flexible carbon textile prepared by hydrothermal and electrodeposition methods greatly affects its active area and cyclic stability during deformation. Here, we report a salt-template-assisted method for the growth of two-dimensional (2D) amorphous ternary LDH based on dip-rolling technology. The robust and high-dimensional structure constructed by salt-template and fiber could achieve a carbon textile-based water splitting catalyst with high loading, strong catalytic activity, and good stability. The prepared 2D NiFeCo-LDH/CF electrode showed overpotentials of 220 mV and 151 mV in oxygen evolution and hydrogen evolution reactions, respectively, and simultaneously had no significant performance decrease after 100 consecutive bendings. This work provides a new strategy for efficiently designing robust, high-performance LDH on flexible fibers, which may have great potential in commercial applications.


Introduction
Electrocatalytic water splitting is an economical and clean method for obtaining new energy, which consists of a hydrogen evolution reaction (HER) and oxygen evolution reaction (OER) [1]. Low-cost non-metal and non-noble metal catalysts have become the alternatives to catalysts, especially for layered double hydroxide (LDH) [2]. Although LDH has excellent intrinsic catalytic activity, its low conductivity will seriously affect electron transfer and reduce catalytic activity and stability [3][4][5], even in the widely used binary catalytic systems (such as NiFe-, NiCo-, CoFe-, CoMn-LDHs, etc.) [6][7][8][9]. It is reported that the electronic structure of a ternary solid solution can be further improved by introducing Co, V, or Mo elements on the basis of a binary catalyst [10][11][12]. By enhancing the synergistic effect between the newly added metal ions and the main metal in the lamellar network, ternary LDH with high electrocatalytic activity and good electrical conductivity can be formed [13,14]. For example, Duan et al. verified the influence of Co-doping on the performance of NiFe-LDHs through theoretical calculations and experiments [15]. The initial overpotentials of Co 3+ -doped NiFe-LDHs and Co 2+ -doped NiFe-LDHs were 33 mV and

Preparation of Cu 2 O Nanocrystal
To begin, 0.85 g CuCl 2 ·2H 2 O was dissolved in 500 mL water until the solution was blue and clear in hue. Then, 50 mL 2.0 M NaOH aqueous solution was added to the aforementioned solution. The hue of the solution progressively changed from blue-green to dark brown over time. Following that, a turbid red suspension was formed by adding 50 mL 0.6 M ascorbic acid solution to the mixture drop by drop under agitation. After treatment in an oil bath at 55 • C, the products were cleaned with deionized water and anhydrous ethanol 3 times, and then placed in a 60 • C vacuum oven to dry overnight.

Preparation of NiFeCo-LDH
A 300 mg Cu 2 O template was added to a 500 mL ethanol and aqueous solution. Then, 1.5 g PVP (MW = 30,000) was added and stirred for 10 min. A 10 cm × 10 cm carbon cloth was placed into soaking for 1 min and dip-padded once with a rolling car (repeated dip-padding twice). A carbon cloth loaded with Cu 2 O was obtained after vacuum drying at 70 • C. Then, a 2 cm × 2 cm carbon cloth was taken from it and added to 20 mL of an ethanol/water mixed solvent containing 1 mg CoCl 2 , 1 mg FeCl 2 , and 1 mg NiCl 2 . After soaking for 10 min, a certain amount of Na 2 S 2 O 3 aqueous solution was added. Ternary NiFeCo hydroxide was prepared after a period of reaction at room temperature.

Electrochemical Measurements
A typical three-electrode setup with a CHI Electrochemical Station was used to evaluate electrochemical measurements (model CHI660E, Shanghai Chenhua Technology Co., Ltd., Shanghai, China). The reference electrode was a saturated calomel electrode (SCE) (0.5 M H 2 SO 4 ) and Hg/HgO (1 M KOH), whereas the counter electrode was a carbon rod. To acquire the polarization curves, linear sweep voltammetry was performed at room temperature at a scan rate of 5 mV s −1 , with an Ar flow maintained throughout the scanning procedure. The double layer capacitance (C dl ) of the samples was used to calculate the electrochemical surface area (ESCA). The C dl was calculated using a straightforward cyclic voltammetry (CV) approach. The CV was performed in a potential window at scan speeds ranging from 20 to 200 mV s −1 . The twelve capacitive current (j anodic -j cthodic ) at 0.575 V vs. RHE was plotted against various scan rates, while the slope obtained was divided by two to obtain the C dl value. EIS was performed at the overpotentials with frequencies from 0.1 to 10 5 Hz and an amplitude of 10 mV. Long durability tests were performed at their overpotentials.

Mechanism for the Pearson's Principle-Inspired Amorphous NiFeCo-LDH/CF
The growth process of amorphous NiFeCo-LDH/CF is mainly divided into two stages: Stage I, the stable anchoring of the Cu 2 O salt-template on the CF surface, and Stage II, the growth of amorphous LDH on the Cu 2 O template sacrifice. Figure 1 is a schematic diagram of the growth mechanism. In Stage I, it is difficult for the active material to directly grow stably on the interface of CF due to its inherent inertia. However, the Cu 2 O template can be stably anchored on the surface of CF by roller-pressing and vacuum-heating in the process of textile dip-padding, and the oxidation of Cu 2 O can be avoided. This stable template/CF interface architecture provides a guarantee for subsequent templates to sacrifice the growth of stable amorphous NiFeCo-LDH, and the cubic Cu 2 O templates also lay a foundation for the high-load construction of continuous growth. In Stage II, according to Pearson's HSAB Principle [25][26][27]  is deposited at the interface first, which causes the generated hydroxides to imitate the geometry of the Cu 2 O template. It should be noted that the size of M(OH) 2 will continue to grow as the reaction progresses until the metal ion concentration is reduced to a value that is not sufficient for precipitation. conducive to the formation of hydroxides. S2O3 2-is the best choice for a Cu2O etching agent. Its main functions are as follows: Because of the highest concentration of OH at the etching interface, M(OH)2 is deposited at the interface first, which causes the generated hydroxides to imitate the geometry of the Cu2O template. It should be noted that the size of M(OH)2 will continue to grow as the reaction progresses until the metal ion concentration is reduced to a value that is not sufficient for precipitation.

Characterizations of Amorphous NiFeCo-LDH/CF
Based on the above mechanism, we designed the experimental process as shown in Figure 2a. Firstly, the cubic Cu2O was evenly dispersed in the mixed solvent of ethanol and water, while using the process of double dip-padding to fix it on CF. Then, PVP and metal chloride (nickel chloride, cobalt chloride, ferrous chloride) were added. These metal ions exist in the free state of the reaction system, and PVP can slow down the synergistic etching-precipitation rate and improve the quality of M(OH)2. Finally, Na2S2O3 was added to make Cu2O co-etch, accompanied by the formation of amorphous M(OH)2 and the load of M(OH)2 was realized on the fiber surface. Subsequently, the morphology and structure of the product were characterized. As shown in Figure 2b, the sample presents an obvious cubic shape with uniform particle distribution and a side length of about 400 nm. Figure 2c shows that the 2D lamellar structure grew uniformly on the surface of the cubic particle, which is similar to the core-shell

Characterizations of Amorphous NiFeCo-LDH/CF
Based on the above mechanism, we designed the experimental process as shown in Figure 2a. Firstly, the cubic Cu 2 O was evenly dispersed in the mixed solvent of ethanol and water, while using the process of double dip-padding to fix it on CF. Then, PVP and metal chloride (nickel chloride, cobalt chloride, ferrous chloride) were added. These metal ions exist in the free state of the reaction system, and PVP can slow down the synergistic etching-precipitation rate and improve the quality of M(OH) 2 . Finally, Na 2 S 2 O 3 was added to make Cu 2 O co-etch, accompanied by the formation of amorphous M(OH) 2 and the load of M(OH) 2 was realized on the fiber surface. Subsequently, the morphology and structure of the product were characterized. As shown in Figure 2b, the sample presents an obvious cubic shape with uniform particle distribution and a side length of about 400 nm. Figure 2c shows that the 2D lamellar structure grew uniformly on the surface of the cubic particle, which is similar to the core-shell structure formed on the surface of the cube. This structure corresponds to the above-mentioned co-etch deposition theory. Furthermore, scanning electron microscopy (SEM) images show that the cubic structure is completely etched and forms a network structure firmly wrapped on the fiber surface ( Figure 2d). The SEM magnifying selection shows that the network structure is composed of interlacing connections of ordered two-position sheet structures ( Figure 2e). This 2D structure can expose more active centers. Meanwhile, the long-range ordered structure increases the charge transfer and promotes the improvement in electrocatalytic performance. The spatial distribution of elements in the NiFeCo-LDH/CF structure is represented by energy-dispersive X-ray spectroscopy (EDS) mapping. Figure 2f shows the component elements of Ni, Fe, Co, C, and O, clearly showing the uniform composition profile of Ni, Fe, and Co in NiFeCo-LDH/CF. Nanomaterials 2022, 12, 2416 5 of 12 structure formed on the surface of the cube. This structure corresponds to the above-mentioned co-etch deposition theory. Furthermore, scanning electron microscopy (SEM) images show that the cubic structure is completely etched and forms a network structure firmly wrapped on the fiber surface ( Figure 2d). The SEM magnifying selection shows that the network structure is composed of interlacing connections of ordered two-position sheet structures ( Figure 2e). This 2D structure can expose more active centers. Meanwhile, the long-range ordered structure increases the charge transfer and promotes the improvement in electrocatalytic performance. The spatial distribution of elements in the NiFeCo-LDH/CF structure is represented by energy-dispersive X-ray spectroscopy (EDS) mapping. Figure 2f shows the component elements of Ni, Fe, Co, C, and O, clearly showing the uniform composition profile of Ni, Fe, and Co in NiFeCo-LDH/CF. X-ray diffraction (XRD) patterns are used to analyze the crystal structure changes of samples during the reaction process. As shown in Figure 3a, the diffraction characteristic peaks located at 29.9°, 37.0°, 42.5°, 62.4°, and 74.4° in the XRD diffraction pattern well correspond to the cubic phase Cu2O (PDF: 00-005-0667) [28], which proves that the cubic particles with uniform morphology are successfully synthesized cuprous oxides. The XRD pattern of NiFeCo-LDH/CF is similar to that of pure CF. There is no obvious diffraction peak, indicating that the prepared sample presents an amorphous nature [29]. This disordered structure and irregular surface provide a high degree of activity and exposure to abundant active sites. The amorphous state can also promote good mass transfer and provide more stable performance [30]. The X-ray photoelectron spectrometer (XPS) test was used to verify the chemical composition of NiFeCo-LDH/CF. The presence of Ni, Fe, Co, O, and C in NiFeCo-LDH/CF is further confirmed by the wide-sweep measurement spectrum shown in Figure 3b. The Ni 2p spectra show two peak binding energies of 873.1 eV and 855.9 eV, corresponding to Ni 2p1/2 and Ni 2p3/2, respectively, which are attributed to the Ni 2+ oxidation state (Figure 3c). Additionally, two peaks were observed at 875.2 eV and 857.6 eV, respectively, indicating the presence of Ni 3+ [31]. The spectra of Fe 2p show two peaks at 711.7 eV and 724.3 eV, respectively, belonging to Fe 2p3/2 and Fe 2p1/2 ( Figure  3d). The peak value of Fe 2p3/2 can be divided into 710.6 eV and 713.3 eV and are assigned to Fe 2+ -OH and Fe 3+ -OH bonds, respectively [32]. Figure 3e shows two peaks at 781.2 eV (Co 2p3/2) and 796.9 eV (Co 2p1/2) in the Co 2p spectra, consistent with the Co 2+ [33]. Furthermore, the Fourier-transform infrared (FT-IR) spectra of NiFeCo-LDH/CF are shown X-ray diffraction (XRD) patterns are used to analyze the crystal structure changes of samples during the reaction process. As shown in Figure 3a, the diffraction characteristic peaks located at 29.9 • , 37.0 • , 42.5 • , 62.4 • , and 74.4 • in the XRD diffraction pattern well correspond to the cubic phase Cu 2 O (PDF: 00-005-0667) [28], which proves that the cubic particles with uniform morphology are successfully synthesized cuprous oxides. The XRD pattern of NiFeCo-LDH/CF is similar to that of pure CF. There is no obvious diffraction peak, indicating that the prepared sample presents an amorphous nature [29]. This disordered structure and irregular surface provide a high degree of activity and exposure to abundant active sites. The amorphous state can also promote good mass transfer and provide more stable performance [30]. The X-ray photoelectron spectrometer (XPS) test was used to verify the chemical composition of NiFeCo-LDH/CF. The presence of Ni, Fe, Co, O, and C in NiFeCo-LDH/CF is further confirmed by the wide-sweep measurement spectrum shown in Figure 3b. The Ni 2p spectra show two peak binding energies of 873.1 eV and 855.9 eV, corresponding to Ni 2p 1/2 and Ni 2p 3/2 , respectively, which are attributed to the Ni 2+ oxidation state (Figure 3c). Additionally, two peaks were observed at 875.2 eV and 857.6 eV, respectively, indicating the presence of Ni 3+ [31]. The spectra of Fe 2p show two peaks at 711.7 eV and 724.3 eV, respectively, belonging to Fe 2p 3/2 and Fe 2p 1/2 (Figure 3d). The peak value of Fe 2p 3/2 can be divided into 710.6 eV and 713.3 eV and are assigned to Fe 2+ -OH and Fe 3+ -OH bonds, respectively [32]. Figure 3e shows two peaks at 781.2 eV (Co 2p 3/2 ) and 796.9 eV (Co 2p 1/2 ) in the Co 2p spectra, consistent with the Co 2+ [33]. Furthermore, the Fourier-transform infrared (FT-IR) spectra of NiFeCo-LDH/CF are shown in Figure 3f. The wide peaks centered at 3445 cm −1 and 1634 cm −1 are assigned to the O-H stretching vibration of interlayer water molecules [34], and the skeleton vibration peak of the carbon ring in the NiFeCo-LDH/CF sample is located at 1546 cm −1 . This is further evidence that graphene exists. The absorption peaks at 680 cm −1 and 510 cm −1 are derived from the vibration of the metal-O bond and the metal-O-metal bond, respectively [35]. in Figure 3f. The wide peaks centered at 3445 cm −1 and 1634 cm −1 are assigned to the O-H stretching vibration of interlayer water molecules [34], and the skeleton vibration peak of the carbon ring in the NiFeCo-LDH/CF sample is located at 1546 cm −1 . This is further evidence that graphene exists. The absorption peaks at 680 cm −1 and 510 cm −1 are derived from the vibration of the metal-O bond and the metal-O-metal bond, respectively [35].

Evaluation of HER and OER Performance
Water splitting separation consists of two half-cell reactions: HER at the cathode and OER at the anode (Figure 4a). In order to evaluate the electrocatalytic performance of Ni-FeCo-LDH, a Hg/HgO electrode and graphite rod were used as the reference electrode and counter electrode, respectively. The catalytic performance of NiFeCo-LDH/CF was investigated in a 1 M KOH aqueous solution saturated with Ar using a typical three-electrode system. As shown in Figure 4b, when the current density of OER was 10 mA cm −2 , the overpotential of NiFeCo-LDH/CF was 220 mV, which is better than that of commercial RuO2 (270 mV) and far better than that of original carbon cloth. It indicates that the 2D NiFeCo-LDH is the main source of electrocatalytic activity. Meanwhile, the illustrated contact angles of 133° on CF and 0° on NiFeCo-LDH/CF indicate that the morphology of the nanostructure improves the solvent wettability and leads to a superhydrophilic surface. Superhydrophilicity greatly improves the kinetics by increasing the contact area between the catalyst and H2O and promotes the performance of electrocatalytic water splitting [36]. The Tafel slope obtained by the LSV curve in Figure 4c is calculated according to the Tafel equation: η = b log j +a (where η represents overpotential, b represents the Tafel slope, and j represents the current density) [37]. NiFeCo-LDH/CF has a lower Tafel slope (58 mV dec −1 ) than those of the commercial RuO2 (96 mV dec −1 ) and pure carbon cloth (245 mV dec −1 ). The high conductivity and hydrophilicity of NiFeCo-LDH/CF promote the reaction kinetics. Subsequently, HER activity of NiFeCo-LDHs/CF was investigated in a 1 M KOH aqueous solution saturated with Ar. As shown in Figure 4d, NiFeCo-LDH/CF shows excellent HER activity with an overpotential of 151 mV at a current density of 10 mA cm −2 . The low Tafel slope (67 mV dec −1 ) indicates that the ternary synergistic effect of Ni-Fe-Co in NiFeCo-LDH/CF, and the high electrical conductivity of carbon fiber,

Evaluation of HER and OER Performance
Water splitting separation consists of two half-cell reactions: HER at the cathode and OER at the anode (Figure 4a). In order to evaluate the electrocatalytic performance of NiFeCo-LDH, a Hg/HgO electrode and graphite rod were used as the reference electrode and counter electrode, respectively. The catalytic performance of NiFeCo-LDH/CF was investigated in a 1 M KOH aqueous solution saturated with Ar using a typical threeelectrode system. As shown in Figure 4b, when the current density of OER was 10 mA cm −2 , the overpotential of NiFeCo-LDH/CF was 220 mV, which is better than that of commercial RuO 2 (270 mV) and far better than that of original carbon cloth. It indicates that the 2D NiFeCo-LDH is the main source of electrocatalytic activity. Meanwhile, the illustrated contact angles of 133 • on CF and 0 • on NiFeCo-LDH/CF indicate that the morphology of the nanostructure improves the solvent wettability and leads to a superhydrophilic surface. Superhydrophilicity greatly improves the kinetics by increasing the contact area between the catalyst and H 2 O and promotes the performance of electrocatalytic water splitting [36]. The Tafel slope obtained by the LSV curve in Figure 4c is calculated according to the Tafel equation: η = b log j +a (where η represents overpotential, b represents the Tafel slope, and j represents the current density) [37]. NiFeCo-LDH/CF has a lower Tafel slope (58 mV dec −1 ) than those of the commercial RuO 2 (96 mV dec −1 ) and pure carbon cloth (245 mV dec −1 ). The high conductivity and hydrophilicity of NiFeCo-LDH/CF promote the reaction kinetics. Subsequently, HER activity of NiFeCo-LDHs/CF was investigated in a 1 M KOH aqueous solution saturated with Ar. As shown in Figure 4d, NiFeCo-LDH/CF shows excellent HER activity with an overpotential of 151 mV at a current density of 10 mA cm −2 . The low Tafel slope (67 mV dec −1 ) indicates that the ternary synergistic effect of Ni-Fe-Co in NiFeCo-LDH/CF, and the high electrical conductivity of carbon fiber, greatly promote the dynamic performance [14,35]. It is worth noting that the electrocatalytic water splitting performance of NiFeCo-LDH/CF is superior to many LDH catalysts at present (Figure 4f) [22,33,[38][39][40][41][42][43][44][45][46][47][48][49][50].
greatly promote the dynamic performance [14,35]. It is worth noting that the electrocatalytic water splitting performance of NiFeCo-LDH/CF is superior to many LDH catalysts at present (Figure 4f) [22,33,[38][39][40][41][42][43][44][45][46][47][48][49][50]. The activity of the catalytic reaction is closely related to the exposed active area. Larger electrochemical active areas (ECSAs) can provide more reaction sites for catalytic reactions. ECSA can be calculated using the following formula: ESCA = Cdl/Cs, where Cdl is an electrochemical double-layer capacitor [51]. Cdl was measured by cyclic voltammetry in the 0.55-0.6 V vs RHE range of scanning rates from 20 mV s −1 to 200 mV s −1 , without a Faraday current ( Figure 4g). As shown in Figure 4h, Cdl of NiFeCo-LDH/CF was 1.4 mF cm −2 , much higher than 0.6 mF cm −2 of bare CF. It indicates that the NiFeCo-LDH/CF structure exposed more active sites, which contributed to enhancing the electrocatalytic activity. Meanwhile, the performance of catalysts is also closely related to the conductivity. To explore the electron transport capability, EIS was measured in an Ar-saturated aqueous solution of 1 M KOH [52]. Figure 4i shows that NiFeCo-LDH/CF has the smallest charge transfer resistance compared with the original carbon cloth, which means good reaction kinetics. Its good catalytic activity is attributed to the higher active sites exposed by this long-range interwoven 2D The activity of the catalytic reaction is closely related to the exposed active area. Larger electrochemical active areas (ECSAs) can provide more reaction sites for catalytic reactions. ECSA can be calculated using the following formula: ESCA = C dl /Cs, where C dl is an electrochemical double-layer capacitor [51]. C dl was measured by cyclic voltammetry in the 0.55-0.6 V vs RHE range of scanning rates from 20 mV s −1 to 200 mV s −1 , without a Faraday current (Figure 4g). As shown in Figure 4h, C dl of NiFeCo-LDH/CF was 1.4 mF cm −2 , much higher than 0.6 mF cm −2 of bare CF. It indicates that the NiFeCo-LDH/CF structure exposed more active sites, which contributed to enhancing the electrocatalytic activity. Meanwhile, the performance of catalysts is also closely related to the conductivity. To explore the electron transport capability, EIS was measured in an Ar-saturated aqueous solution of 1 M KOH [52]. Figure 4i shows that NiFeCo-LDH/CF has the smallest charge transfer resistance compared with the original carbon cloth, which means good reaction kinetics. Its good catalytic activity is attributed to the higher active sites exposed by this long-range interwoven 2D structure, as well as the good electrical conductivity and the synergistic effect of Ni-Fe-Co [18,53]. In addition, we further tested the electrocatalytic hydrogen evolution reaction (HER) performance of monadic and binary metal hydroxides, and their performance is shown in Figures S1 and S2. It can be seen that 3D transition metal base hydroxides, such as Ni, Co, and Fe, have quite high activity, since Fe 3+ can broaden the interlaminar space of 2D materials and enhance their mass transfer behavior [54]. Meanwhile, the synergistic effect between Fe and the LDH lamellar structure can shorten the ion transport distance at the nanometer scale, so that Fe-doping can further improve its catalytic performance. Moreover, Co-doping can accelerate the *OOH formation step of NiFe-LDH and reduce the overpotential of the deprotic step of NiFe-LDH [15], which further indicates that ternary NiFeCo-LDH has excellent catalytic performance in the HER process.
Generally, the interface between the active material and flexible substrate is unstable for flexible catalysts. It is speculated that this tight and stable NiFeCo-LDH/CF interface may be beneficial for improving its service life during deformation. We tested the cyclic stability of NiFeCo-LDH/CF under different bending deformations. Figure 5a shows the current stability of NiFeCo-LDH/CF in motion [55], which is continuously bent and recovered from 0 • to 180 • at a fixed potential of 1 V, with each cycle time being 50 s. It can be seen that the current hardly changes in the process of bending and recovering 10 times, showing good bending stability. We then tested its electrocatalytic properties in different bending states. As shown in Figure 5b, the OER performance was almost the same under different deformation states, and it also showed excellent long-term stability at a current density of 20 mA cm −2 (Figure 5c). Similarly, the stability of HER performance was also excellent (Figure 5d-e). Furthermore, we explored its bending resistance. After 100 bending recovery repeats, we tested its long-term stability, and its current density hardly changed after 100 bending repeats (Figure 5f-g). The illustration in Figure 5g shows the current change caused by bubble detachment. It shows that the superhydrophilic structure can increase the contact area between the catalyst and H 2 O and promote the electrocatalytic cracking water process from kinetics. Finally, the stabilities of the structure and morphology were characterized by XRD and SEM (Figure 5h). After the long-term stability test of NiFeCo-LDH/CF, both morphology and structure were also maintained, which further indicates that the NiFeCo-LDH/CF prepared by this method has excellent stability.

Conclusions
In summary, we successfully prepared 2D amorphous ternary NiFeCo-LDH/CF by using the salt-template-assisted method. The Cu2O template can be stably anchored on a CF surface by textile dip-padding technology. Subsequently, based on the Pearson's HSAB Principle, the amorphous NiFeCo-LDH grew on the template surface through a synergistic corrosion-precipitation process. Compared with traditional methods, this unique growth mode was more conducive to obtaining amorphous LDH flexible catalysts with high loading, strong catalytic activity, and good stability. The prepared NiFeCo-

Conclusions
In summary, we successfully prepared 2D amorphous ternary NiFeCo-LDH/CF by using the salt-template-assisted method. The Cu 2 O template can be stably anchored on a CF surface by textile dip-padding technology. Subsequently, based on the Pearson's HSAB Principle, the amorphous NiFeCo-LDH grew on the template surface through a synergistic corrosion-precipitation process. Compared with traditional methods, this unique growth mode was more conducive to obtaining amorphous LDH flexible catalysts with high loading, strong catalytic activity, and good stability. The prepared NiFeCo-LDH/CF electrode could not only show the overpotential of 220 mV and Tafel slope of 58 mV dec −1 in OER, but also show the overpotential of 151 mV and Tafel slope of 67 mV dec −1 in HER. Additionally, there was no significant reduction in catalytic performance, even after 100 repeats of continuous bending. This Pearson's HSAB Principle-inspired strategy is expected to provide a new idea for the commercial preparation of high-performance LDH and the highly stable construction of 2D materials at fiber interfaces.

Data Availability Statement:
The data presented in this study are available upon request from the corresponding authors.