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Studying the variable energy band structure for energy storage materials in charge/discharge process
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Xuancheng Chena, Yu Huan*, a, Ningqiang Suna, Yuanhui Sua, Xuesong Shenb, Guoqing Lia, Jiaqi Zhanga, Tao Wei*, a
Chinese Chemical Letters | 2024, 35(2) : 108380
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Chinese Chemical Letters | 2024, 35(2): 108380
• Communication •
Studying the variable energy band structure for energy storage materials in charge/discharge process
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Xuancheng Chena, Yu Huan*, a, Ningqiang Suna, Yuanhui Sua, Xuesong Shenb, Guoqing Lia, Jiaqi Zhanga, Tao Wei*, a
Affiliations
  • aUniversity of Jinan, Ji'nan 250022, China
  • bWeichai Power Co., Ltd., Weifang 261061, China
Published: 2024-02-15 doi: 10.1016/j.cclet.2023.108380
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So far, a clear understanding about the relationship of variable energy band structure with the corresponding charge-discharge process of energy storage materials is still lacking. Here, using optical spectroscopy (red-green-blue (RGB) value, reflectivity, transmittance, UV–vis, XPS, UPS) to study α-Co(OH)2 electrode working in KOH electrolyte as the research object, we provide direct experimental evidence that: (1) The intercalation of OH– ions will reduce the valence/conduction band (VB and CB) and band gap energy (Eg) values; (2) The deintercalation of OH– ions corresponds with the reversion of VB, CB and Eg to the initial values; (3) The color of Co(OH)2 electrode also exhibit regular variations in RGB value during the charge-discharge process.

Variable energy band structure  /  Energy storage materials  /  Charge-discharge process  /  Optical spectroscopy  /  Supercapacitors
Xuancheng Chen, Yu Huan, Ningqiang Sun, Yuanhui Su, Xuesong Shen, Guoqing Li, Jiaqi Zhang, Tao Wei. Studying the variable energy band structure for energy storage materials in charge/discharge process[J]. Chinese Chemical Letters, 2024 , 35 (2) : 108380 - . DOI: 10.1016/j.cclet.2023.108380
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Nowadays, with the rapid development of human society, the exploration of green, economic and sustainable energy storage devices has become an indispensable demand. At present, the most studied energy storage devices mainly include various batteries and capacitors, such as lithium-ion batteries, sodium-ion batteries, zinc-ion batteries, electric double-layer capacitors, and pseudocapacitors [1–9]. For energy storage devices, one of the most important components is their various energy storage materials. Such as for lithium-ion batteries, the energy storage materials include the widely studied LiCoO2- or LiFePO4-based cathode materials and the graphite or silicon-based anode materials [10–12]. For supercapacitors, the electrode materials mainly include carbon material, metal oxide, and conductive polymer [13–15]. To pursue energy storage materials with greater capacity, high power, better safety and non-pollution, it is also necessary to develop various testing techniques to systematically evaluate the energy storage materials/devices. For example, the cyclic voltammetry (CV) and galvanostatic charge-discharge (GCD) testing techniques can be used to characterize the charge-discharge voltage, capacity, rate, cycle and other properties of energy storage materials. The variations of morphology and volume of energy storage materials before, during and after charging and discharging process can be intuitively described by scanning electron microscope (SEM) and atomic force microscope (AFM). Park et al. clearly characterized the volume increase and shrinkage, and the damage of the silicon-based lithium-ion battery anode particles during the charging and discharging process by SEM technology [16]. The change of aliovalent cation valence state and the oxygen vacancy concentration in energy storage materials can be (semi-)quantitatively evaluated by XPS, EPR and chemical titration methods [17,18]. For different charge carriers charging/discharging in energy storage materials, the possible insertion site, transport route and activation energy can be calculated by theoretical computation. For example, the voltage profile for the discharge/charge curves can be described by the density-of-state diagram, which is mainly based on the corresponding positions of the bottom/top band gap and the aliovalent cation redox couples relative to the Fermi energy of lithium [19]. The possible changes in the crystal structure, bond length/angle, phase transition, etc. of energy storage materials during the charge and discharge process also can be characterized by XRD, TEM and Raman testing techniques [20–22]. Despite much progress, as mentioned above, has been made in the past decades to get a more accurate assessment for energy storage materials, however, a clear understanding of the relationship between the charge-discharge process of energy storage materials and the corresponding changes of energy band structure is still lacking.
In this work, an energy storage electrode cobalt hydroxide α-Co(OH)2 with low cost, environmentally benign and high theoretical specific capacitance was chosen as research object. We studied the charge-discharge process of energy storage materials by first revealing the regular variations of colors, optical spectrum and energy band structure. Their corresponding relationships provide a new perspective to study the insertion and removal of charge carriers in energy storage materials during the charge and discharge process.
The electrochemical properties of α-Co(OH)2 electrode material are tested by forming a three-electrode configuration with Pt foil as the auxiliary electrode, Ag/AgCl as the reference electrode and 2 mol/L KOH solution as the electrolyte. Here, the initial Co(OH)2 electrode is fabricated with 90 wt% pristine Co(OH)2 powders + 10 wt% poly(vinylidene fluoride) (PVDF) coating on nickel foam. In charge-discharge process, the Co(OH)2 electrode is discharged and charged to 0 V and 0.45 V respectively in a 2 mol/L KOH solution. In order to study the changes of Co(OH)2 during discharging and discharging process, the pristine, discharged and charged Co(OH)2 powders are collected and analyzed, respectively. As shown in Figs. 1a–c, the crystal structure and morphology of the three samples are characterized clearly. X-ray diffraction (XRD) evaluation results prove that all of the pristine, discharged and charged Co(OH)2 samples appear in pure phase with characteristic peaks of Co(OH)2. And the morphologies of the three Co(OH)2 samples, as observed by field-emission scanning electron microscopy (FE-SEM), all show in hexagonal sheet structure, which is consistent with other reports [23]. No apparent XRD and SEM variations were observed from pristine to discharged and charged Co(OH)2. All the GCD profiles are nonlinear and show obvious potential plateau (Fig. 1d), indicating that the charge storage of α-Co(OH)2 electrode with (de)intercalating OH− ions originated predominantly from Faradaic reaction [24]. The device exhibits a specific capacitance of 475 F/g at 1 A/g in accordance with Eq. 1 [25].
Furtherly, the shapes of GCD curves remain unchanged and keep symmetric with current densities increasing from 1 A/g to 5 A/g, which proves the good reversibility and rate capability of Co(OH)2 electrode. The CV curve of α-Co(OH)2 electrode with scan voltage from –0.3 V to +0.5 V and scan rate at 10 mV/s also shows obvious redox peaks (Fig. 1e), which corresponds to the potential of charge-discharge behavior in GCD curves. By comparing the cycled capacity for more than 2000 cycles, the excellent long-term stability means the good redox reversibility while Co(OH)2 using as energy storage electrode (Fig. S2 in Supporting information). In addition, adding 10 wt% super P carbon black (SP) as conductor, the composite electrode demonstrates superior electrochemical performance (Figs. S3–S6 in Supporting information). As shown in Fig. 1f, the Co(OH)2 coated on nickel foam is tested by electrochemical Mott–Schottky plots in 2 mol/L KOH solution. The result shows that the Efb values of the pristine, discharged and charged samples are 0.2, 0.05 and 0.1 V, respectively. The measured flat-band voltage reflects the change of valence state of the three samples, which also proves that Co(OH)2 undergoes the redox reactions during the charging and discharging process.
Furtherly, during the charging-discharging process, the color variation of Co(OH)2 samples was recorded by Spectrophotometric colorimeter. As shown in Fig. 2a, its red-green-blue (RGB) value varies regularly with the corresponding GCD curves (presented by the black dots linked with broken black lines). For the pristine Co(OH)2 powders, its RGB value is in (147, 186, 139). The initial Co(OH)2 electrode (90 wt% Co(OH)2 + 10 wt% PVDF coating on nickel foam) was infiltrated into 2 mol/L KOH solution electrolyte for 2 h, and its RGB value is in (75, 70, 62). Furtherly, the discharged Co(OH)2 electrode (with voltage at 0 V) with saturated KOH solution shows the color in RGB value (79, 79, 76). For Co(OH)2 electrode charged to 0.45 V, OH− as charge carriers were inserted into the interlayer structure of α-Co(OH)2. The redox reaction is as follows (Eq. 2) [26].
With the introduction of OH− ions, Co(OH)2 was oxidized to CoOOH, which leads the color of charged Co(OH)2 electrode varying to the RGB value (78, 78, 76). For Co(OH)2 electrode discharging to 0 V, the OH− ions were taken off from the interlayer. The corresponding RGB value of the discharged Co(OH)2 electrode was recovered to (79, 79, 76) again. And the corresponding RGB values of Co(OH)2 electrode also were recorded for 20 cycles. As shown in Fig. 2a, the changes of the obtained color vary regularly during the charge-discharge process, which is consistent with the excellent capacitance stability.
In addition, the optical images for pristine Co(OH)2 powders, discharged and charged Co(OH)2 electrode powders (Fig. S1 in Supporting information) are inserted into Fig. 2a to compare the color variation. The color of pristine Co(OH)2 powders is green, corresponding with its RGB value. In the macroscopic view, the color of discharged/charged Co(OH)2 electrode powders is obviously different from pristine powder, both showing in black gray, which is consistent with their RGB values. For Co(OH)2 + PVDF + SP electrode, its RGB values and optical images also vary regularly with the GCD curves (Fig. S7 in Supporting information).
The varied colors of Co(OH)2 samples under the charge-discharge process can be reflected by detecting their varied optical properties, such as reflection, refraction and transmission [27]. For pristine Co(OH)2, the powder is pressed into circular flakes with a certain diameter and thickness to test its reflectance, and the reflectance is obtained by the Spectrophotometer colorimeter. As shown in Fig. 2b, the reflectance of pristine green Co(OH)2 powder varies from 20% to 70% with the test wavelength switching from 400 nm to 780 nm. For Co(OH)2 electrodes, with the electrode sheet (Co(OH)2 powder coated on nickel foam) discharging/charging to 0/0.45 V, the corresponding reflectance can be recorded. The Co(OH)2 electrode in black gray absorbed most of the exciting light, herein, its reflectivity is significantly lower than pristine Co(OH)2, less than 10%. Moreover, for semiconductors, the wider band gap corresponds with less absorbance for white exciting light [28,29]. Herein, the higher reflection coefficient for discharged Co(OH)2 electrode (than charged electrode) means bigger band gap.
For polycrystalline semiconductor materials, their optical properties are mainly affected by scattering and reflection, and are almost opaque to exciting light. However, evaluating the variation of transmittance is still an effective way to reveal the changed band gap from pristine to discharged and charged Co(OH)2. To measure the light transmittance, 90 wt% Co(OH)2 and 10 wt% PVDF are coated on FTO conductive glass to form a thin and uniform film as working electrode, which ensures the transmission of light. The electrode is charged and discharged to 0.45 and 0 V, and then the transmittance is measured after drying. As shown in Figs. 2c and d, the transmittance of pristine Co(OH)2 varies between 1 and 10%, while discharged Co(OH)2 and charged Co(OH)2 transmissivity is less than 0.1%. The significantly higher transmittance for pristine Co(OH)2 means larger band gap (for exciting light passing through) than discharged and charged Co(OH)2. Furtherly, the comparison of transmittance in Fig. 2d represents that discharged Co(OH)2 has the larger band gap than charged Co(OH)2, which can be explained by the higher transmittance.
For semiconductors, the color variation corresponds to the variation of band gap energy (Eg) value. Herein, the changed color (or RGB value) of Co(OH)2 samples can be evaluated by the ultraviolet-visible spectroscopy, which can give the variation of Eg value. Fig. 3 is the UV–vis spectra of Co(OH)2 samples with the absorption wavelength ranging from 300 nm to 800 nm. For pristine Co(OH)2 powders (Fig. 3a), the strong absorption wavelength ranges from 560 nm to 680 nm, and the absorption peak at around 550 nm results in the dominant green color [30]. Then, the E value can be calculated by Tauc's plot and expressed using the following Eq. 3 [31].
The calculated Eg value for pristine Co(OH)2 is 2.85 eV, shown in the insert chart of Fig. 3a. For PVDF binder, the calculated Eg value is 3.54 eV (Fig. 3b). For Co(OH)2 + PVDF electrode, the calculated UV–vis spectra shows two individual Eg values at 3.54 and 2.85 eV, which means the Eg values of Co(OH)2 samples are unaffected by the introduction of PVDF binder (Figs. 3c and d). For Co(OH)2 + PVDF + SP electrode, the absorption peaks of Co(OH)2 and PVDF are covered by the introduced SP carbon black (Fig. S8 in Supporting information). Herein, the optical spectroscopy was conducted with Co(OH)2 + PVDF as the working electrode.
To obtain the Eg value of discharged and charged Co(OH)2 powders, the initial Co(OH)2 sample was coated on FTO conductive glass as a working electrode and then the electrode was charged/discharged in 2 mol/L KOH solution electrolyte. After the electrode was charged and discharged to 0.45 and 0 V individually, the corresponding Co(OH)2 electrode sheet is rinsed gently with deionized water, subsequently dried in an oven at 75 ℃. The dried charged/discharged Co(OH)2 powders are scraped from conductive glass to test the Eg value. Figs. 3e and f show the absorption peaks and the corresponding Tauc plot of discharged and charged Co(OH)2 powders. It is observed that the range of strong absorption peaks of the two samples is much different with pristine Co(OH)2 powders. We think the main reason is the adsorption (or chemical reaction) of OH− ions with Co(OH)2 particles. The strong absorption peaks of the two samples both appear around 680 nm, corresponding with the gray-black color. Furtherly, the calculated Eg for discharged Co(OH)2 electrode powders is 1.94 eV. For charged Co(OH)2 electrode powders, the calculated Eg was reduced furtherly to 1.75 eV. This means the intercalation/deintercalation of OH– ions during the charge and discharge process causes further change of Eg of Co(OH)2 electrode. From discharged to charged Co(OH)2, the smaller Eg was explained: for p-type Co(OH)2 semiconductor, we think the intercalation of OH– ions will produce impurity level near the VB, which causes the further reduction of Eg.
In order to construct the schematic diagram of energy band structure, the valence band potential (EVB, XPS) of pristine, discharged and charged Co(OH)2 samples were measured via X-ray photoelectron spectroscopy (XPS) analysis. And the XPS absorption spectra of the three samples as a function of binding energy were shown in Figs. 4a–c. The VB positions of the Co(OH)2 samples are calculated by linear extrapolation of the valence band leading edge with the corresponding baseline of the background signal [32].
According to the test results, the corresponding EVB, XPS of pristine, discharged and charged Co(OH)2 samples is measured to be 0.97, 0.09 and 0.23 eV. Then, the EVB values of the corresponding standard hydrogen electrode (EVB, NHE) can be obtained by to the following Eq. 4.
φ is the work function of the instrument (4.72 eV) [33]. As a result, the EVB, NHE of the three samples is calculated to be 1.25, 0.37 and 0.51 eV, respectively. For the sake of unity with band gap, the EVB, NHE is converted into solid physical energy level scales (vacuum level) for comparison. Finally, the valence band value of the pristine, discharged and charged Co(OH)2 is calculated to be –5.69, –4.81 and –4.95 eV, respectively, according to the conversion Eq. 5 [34].
First, the valence band value of discharged/charged Co(OH)2 electrodes is more positive than pristine Co(OH)2, which was also attributed to the adsorption (or chemical reaction) of OH− ions with Co(OH)2 particles. Second, the intercalation/deintercalation of OH– ions in Co(OH)2 electrode will introduce new filled/empty electronic states at or around the VB maximum, which sheds light on the change of valence band values. Here, from the discharged to charged electrode, the intercalation of OH− ions will oxidize Co2+(OH)2 to Co3+OOH. So the further spillover of electrons from Co3+ ions of Co3+OOH needs higher energy (work function, WF), which explains the more negative Evac of charged Co(OH)2 than discharged Co(OH)2 (Figs. 4b and c).
To further verify the accuracy of changed EVB, XPS as evaluated by XPS technology, we also use the ultraviolet photon electron spectroscopy (UPS) and electrochemical Mott–Schottky equation to further determine the band edges of Co(OH)2 electrode under charging and discharging process. UPS is a widely used way which probes the electronic VB [35]. It measures the kinetic energy of photoelectrons emitted by solid surfaces under the irradiation of ultraviolet light, which provides the distribution of electron density in the VB as well as on the WF. The UPS test was prepared by coating Co(OH)2 on FTO conductive glass to form a thin and uniform film electrode [36]. The charge-discharge process of the thin film electrode is carried out in a 2 mol/L KOH solution by a three-electrode test device. Figs. 4d–f show the low binding energy slopes of pristine, discharged and charged Co(OH)2 samples. The intersection of the slope curve is the VB maximum below Femi level. It is calculated that the VB of the three samples is 0.49, 0.1 and 0.26 eV, respectively. The WF is defined as the energy difference from the Fermi level to the vacuum energy level. In the UPS spectrum, it can be calculated from the difference between the energy of the UV photons and the secondary electron cutoff (high-binding energy (BE) cutoff) [37]. The cut-off energy of the three samples is 16.01, 15.96 and 15.98 eV (Fig. S9 in Supporting information). Furthermore, the WF can be calculated by the following Eq. 6.
hν is the energy of the He Ι ultraviolet photon source (21.22 eV), BEmax = Ecutoff. It can be assumed that EF = 0 by calibrating the energy spectrum scale of the spectrum. Therefore, the W of the three materials can be calculated as 5.21, 5.26 and 5.24 eV. Herein, the energy band structure relative to the energy level of the solid physical scale can be obtained according to the WF and EVB, UPS. The valence band positions relative to the vacuum level can be obtained as –5.70, –5.36 and –5.50 eV, respectively.
For semiconductor-like materials, the Mott–Schottky equation can be used to measure the flat band potential (Efb) at the electrode-electrolyte interface, which then was used to reflect the valence/conduction band values. Herein, the testing system for Efb was prepared with Co(OH)2 coating on nickel foam as working electrode with Ag/AgCl as reference electrode and with 2 mol/L KOH solution as electrolyte. In the Mott–Schottky test, the voltage range is –0.45 V to 0.5 V and the frequency is 1000 Hz. As shown in Fig. 1f, the Efb is determined by the x-intercept (potential axis) of the tangent line of the Mott–Schottky plot. The result shows that the Efb values of the pristine, discharged and charged samples are 0.2, 0.05 and 0.1 V, respectively. It is evident that the slope of the tangent line is negative, suggesting α-Co(OH)2 a p-type semiconductor [38–40]. There is a certain relationship between the valence band value and the varied flat band voltage (Eq. 7).
Efb is the flat band potential, NA is the volume carrier density, NV is the valence band effective state density, k is the Boltzmann constant and T is the temperature in absolute scale. The second term depends on the doping concentration, which for semiconductors is usually 0.1–0.2 eV and is negligible. Herein, we ignore the second term to compare the change of valence band values.
Then, we convert the valence bands into the solid physical level scale (vacuum level) according to Eqs. 5 and 8 [34,41].
pH value is 14.3 for 2 mol/L KOH electrolyte. The calculated final valence band value of the three samples is –5.68, –5.53 and –5.58 eV, respectively. Herein, in the process of the Mott–Schottky test, Co(OH)2 may react with KOH solution with the increase of testing voltage, which would affect the flat band potential (valance band) in a certain state. For example, although the trend of the obtained valence band position by the Mott–Schottky equation is still upward from pristine to charged/discharged Co(OH)2 samples, the concrete data does not change much as compared with XPS and UPS results.
Fig. 5 draws a comparison of the band diagrams for pristine, discharged and charged Co(OH)2 samples based on the results of UV–vis spectrum, XPS, UPS and Mott–Schottky plot. And the calculating formula is as follows (Eq. 9) [28].
Fig. 5a is a schematic diagram of the energy bands obtained by XPS and UV–vis tests. The calculated VB, CB and E of pristine Co(OH)2 are –5.69, –2.84 and 2.85 eV, which are in line with the existing research results [42,43]. For discharged Co(OH)2 electrode, with the adsorption (or chemical reaction) of OH− ions with Co(OH)2 particles, the calculated VB increased to –4.81 eV. At the same time, the CB and Eg values were reduced to –2.87 and 1.94 eV.
For charged Co(OH)2 electrode, the present study has demonstrated that the charging process of α-Co(OH)2 is processed by OH− intercalation [44]. The intercalation of OH− ions further reduces the VB, CB and Eg values of charged Co(OH)2 electrode to –4.95, –3.20 and 1.75 eV (compared with –4.81, –2.87 and 1.94 eV of discharged Co(OH)2). Figs. 5b and c are the schematic band diagrams of VB, CB and Eg values obtained by UPS/UV–vis and Mott–Schottky/UV–vis tests. The calculated results for pristine, discharged and charged Co(OH)2 samples are basically same with the XPS/UV–vis results. As discussed above, the apparent variation of Co(OH)2 energy band structure from pristine powders to charged/discharged electrodes was attributed to the adsorption (or chemical reaction) of OH− ions with Co(OH)2 particles. The varied energy band structure from discharged to charged Co(OH)2 can be explained by the reversible Faradaic reaction. As shown in Table S1 (Supporting information), the XPS results reveal the coexistence of Co2+ and Co3+ ions in discharged and charged Co(OH)2. The calculated Co2+/Co3+ ratios are 2.07 and 0.53 in discharged and charged samples. During the charging and discharging process, the intercalation/deintercalation of OH– ions from the interlayers of Co(OH)2 electrode will oxidize/reduce more Co2/3+ to Co3/2+, which causes changes in the energy band structure. Recently, Gabrelian et al. have studied the valence-band electronic structure and main optical properties of Cu2HgGeTe4 materials by theoretical simulation within a DFT framework and experimental XPS [45], and the obtained trend is consistent with the varied VB and CB of Co ion as studied in this work.
In this work, by combining optical spectroscopy characterization with electrochemical studies, we have demonstrated that the charge-carrier intercalation/deintercalation in energy storage materials not only governs the variations of color RGB values but also the energy band structure. Specifically, with Co(OH)2 electrode working in KOH electrolyte as an example, the VB, CB and Eg values show apparent reduction/increment with OH− ions intercalating or taking off from its interlayer structure. In addition, the intercalation/deintercalation of OH− ions also triggered the redox reaction of Co2+ and Co3+ ions, resulting in the regular variation of RGB values. This work provides a feasible way to characterize the changes of energy band structure during the charge-discharge process by optical spectroscopy, which is helpful for the design of high-performance energy storage materials.
Declaration of competing interest
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The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
Acknowledgment
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This work was supported by the National Natural Science Foundation of China (Nos. 51972146, 52072150).
Supplementary materials
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Supplementary material associated with this article can be found, in the online version, at doi:10.1016/j.cclet.2023.108380.
References
Less
[1]
A. Manthiram, ACS Cent. Sci. 3 (2017) 1063–1069.
[2]
G.Q. Li, M.Y. Ma, X.C. Chen, et al., Energy Fuels 37 (2023) 702–710.
[3]
J.Y. Hwang, S.T. Myung, Y.K. Sun, Chem. Soc. Rev. 46 (2017) 3529–3614.
[4]
L.Q. Mai, A. Minhas-Khan, X. Tian, K.M. Hercule, et al., Nat. Commun. 4 (2013) 2923.
[5]
C.G. Wang, P.X. Sun, G.M. Qu, et al., Chin. Chem. Lett. 29 (2018) 1731–1740.
[6]
M.R. Guo, J. Zhan, Z.K. Wang, et al., Chin. Chem. Lett. 34 (2023) 107709.
[7]
N.N. Yang, L. Ji, H.C. Fu, et al., Chin. Chem. Lett. 34 (2022) 3961–3967.
[8]
X.W. Wang, Y.C. Sun, W.C. Zhang, et al., Chin. Chem. Lett. 34 (2023) 107593.
[9]
Q. Xia, T. Xia, X. Wu, et al., Rare Met. 41 (2022) 1195–1201.
[10]
N. Balke, S. Jesse, A.N. Morozovska, et al., Nat. Nanotechnol. 5 (2010) 749–754.
[11]
W. Kim, W. Ryu, D. Han, et al., ACS Appl. Mater. Interfaces 6 (2014) 4731–4736.
[12]
Y. Son, N. Kim, T. Lee, et al., Adv. Mater. 32 (2020) e2003286.
[13]
S.M.Y. Zhu, M.D. Stoller, K.J. Ganesh, et al., Science 24 (2011) 1537–1541.
[14]
H. Gao, F. Xiao, C.B. Ching, et al., ACS Appl. Mater. Interfaces 4 (2012) 2801–2810.
[15]
D. Sheberla, J.C. Bachman, J.S. Elias, et al., Nat. Mater. 16 (2017) 220–224.
[16]
H. Park, S. Choi, S. Lee, et al., J. Mater. Chem. A 3 (2015) 1325–1332.
[17]
G. Li, K. He, F. Zhang, et al., Appl. Catal. B: Environ. 309 (2022) 121231.
[18]
W.C. Huo, X.A. Dong, J.Y. Li, et al., Chem. Eng. J. 361 (2019) 129–138.
[19]
J.B. Goodenough, Y. Kim, Chem. Mater. 22 (2009) 587–603.
[20]
W. Yao, A.R. Armstrong, X. Zhou, et al., Nat. Commun. 10 (2019) 3483.
[21]
L. Feng, Y. Liu, L. Wu, et al., J. Alloy. Compd. 881 (2021) 160626.
[22]
Q.F. Xiao, M. Gu, H. Yang, et al., Nat. Commun. 6 (2015) 8844.
[23]
K. Ding, X. Zhang, J. Li, et al., CrystEngComm 19 (2017) 5780–5786.
[24]
U.M. Patil, M.S. Nam, J.S. Sohn, et al., J. Mater. Chem. A 2 (2014) 19075–19083.
[25]
X. Wu, L. Meng, Q. Wang, et al., Sol. Energy Mater. Sol. Cells 174 (2018) 325–332.
[26]
A.D. Jagadale, V.S. Kumbhar, D.S. Dhawale, et al., Electrochim. Acta 98 (2013) 32–38.
[27]
M.G. Berhe, H.G. Oh, S.K. Park, et al., J. Mater. Res. Technol. 16 (2022) 322–334.
[28]
F.P. Hagen, D. Kretzler, T. Häber, et al., Carbon 182 (2021) 634–654.
[29]
J.F. Luo, C.Q. Xie, S.L. Pan, et al., J. Quant. Spectrosc. Radiat. Transf. 287 (2022) 108228.
[30]
Z.L.R. Ma, K. Takada, K. Fukuda, et al., Inorg. Chem. 61 (2006) 3964–3969.
[31]
I. Thaheem, K.J. Kim, J.J. Lee, et al., J. Mater. Chem. A 7 (2019) 19696–19703.
[32]
H. Li, X. Liu, L. Sang, et al., Phys. Status Solidi 251 (2014) 788–791.
[33]
X. Li, B. Kang, F. Dong, et al., Nano Energy 81 (2021) 105671.
[34]
S. Trasatti, Pure Appl. Chem. 58 (1986) 955–966.
[35]
G. Xiong, R. Shao, T.C. Droubay, et al., Adv. Funct. Mater. 17 (2007) 2133–2138.
[36]
C. Maheu, L. Cardenas, E. Puzenat, et al., Phys. Chem. Chem. Phys. 20 (2018) 25629–25637.
[37]
P. Ramaswamy, S. Devkota, R. Pokharel, et al., Sci. Rep. 11 (2021) 8329–8342.
[38]
M. Forghani, J. McCarthy, A.P. Cameron, et al., J. Electrochem. Soc. 168 (2021) 020508.
[39]
M.A. Hughes, J.A. Allen, S.W. Donne, Electrochim. Acta 338 (2020) 135847.
[40]
D.P. Sahoo, S. Nayak, K.H. Reddy, et al., Inorg. Chem. 57 (2018) 3840–3854.
[41]
Z. Dong, D. Ding, T. Li, et al., Appl. Surf. Sci. 443 (2018) 321–328.
[42]
M. Suksomboon, K. Kongsawatvoragul, S. Duangdangchote, et al., ACS Omega 6 (2021) 20804–20811.
[43]
S. Kalasina, P. Pattanasattayavong, M. Suksomboon, et al., Chem. Commun. 53 (2017) 709–712.
[44]
X. Li, L. Lu, J. Shen, et al., J. Power Sources 477 (2020) 228974.
[45]
B.V. Gabrelian, A.A. Lavrentyev, Tuan. V. Vu, et al., Mater. Today Commun. 23 (2020) 100828.
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Year 2024 volume 35 Issue 2
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doi: 10.1016/j.cclet.2023.108380
  • Receive Date：2023-02-14
  • Online Date：2025-11-20
  • Published：2024-02-15
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  • Received：2023-02-14
  • Revised：2023-03-10
  • Accepted：2023-03-24
Affiliations
    aUniversity of Jinan, Ji'nan 250022, China
    bWeichai Power Co., Ltd., Weifang 261061, China
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表12种不同金属材料的力学参数
科
Family		 属数
Number of
genus		 种数
Number of
species		 占总种数比例
Percentage of
total species (%)		 属
Genus		 种数
Number of
species		 占总种数比例
Percentage of total
species (%)
鹅膏菌科Amanitaceae 2 11 5.26 鹅膏菌属 Amanita 10 4.78
小菇科 Mycenaceae 2 12 5.74 丝盖伞属 Inocybe 5 2.39
多孔菌科 Polyporaceae 8 14 6.70 蜡蘑属 Laccaria 5 2.39
红菇科 Russulaceae 3 23 11.00 小皮伞属 Marasmius 6 2.87
小菇属 Mycena 11 5.26
光柄菇属 Pluteus 5 2.39
红菇属 Russula 17 8.13
栓菌属 Trametes 5 2.39
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