Kai Fang’s research while affiliated with Xiamen University and other places

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Publications (9)


Figure 2. Charge compensation from the perspective of transition metals revealed by TM K-edge XANES. (a) Normalized Mn, Co, and Ni Kedge XANES spectra of pristine and charged NCM333 and NCM811 cathodes charged to 4.2, 4.5, and 4.8 V (vs. Li/Li + ). (b, c) Edge positions of the Ni, Co, and Mn K-edges for NCM333 (b) and NCM811 (c) cathodes at the pristine state and various states of charge.
Figure 3. Charge compensation of transition metals revealed through local structure evolution. (a) Ni K-edge EXAFS fitting results of NCM333 and NCM811. (b) XAFS-derived bond lengths for TM-O (Ni-O, Co-O, Mn-O) and TM-TM (Ni-TM, Co-TM, Mn-TM) in NCM333 and NCM811 at pristine state and various delithiation states. (c) Schematic illustration of the nearest coordination local structural changes and their effects on the layered structure during delithiation.
Figure 4. Oxidation-state changes of transition metals upon delithiation revealed by TM L-edge NEXAFS. (a) Ni L 2,3 -edge NEXAFS spectra of pristine and charged NCM333 and NCM811 cathodes charged to 4.2, 4.5, and 4.8 V (vs. Li/Li + ). (b) Co L 2,3 -edge NEXAFS spectra of pristine and charged NCM333 and NCM811 cathodes at various states. Reference spectra: Ni 2+ O, Ni 2 3+ O 3 , Co 2+ O, and Co 2 3+ O 3 . NEXAFS data were collected at total electron yield (TEY) mode. (c) Differential Ni L 2,3 -edge spectra of NCM333 and NCM811 cathodes at various states. (d) Differential Co L 2,3 -edge spectra of NCM333 and NCM811 cathodes at various states. (e) Quantification of the oxidation states from Ni and Co L 2,3 -edge NEXAFS of the NCM333 at various states. (f) Quantification of the oxidation states from Ni and Co L 2,3 -edge NEXAFS of the NCM811 at various states.
Figure 5. Illustrations of different electronic structure models. (a) Schematic representation of the ionic-bonding model, where TM cations and O anions are considered to possess discrete electronic bands. (b) Schematic illustrations represent the Mott-Hubbard Model with charge transfer, depicting the d Coulomb interactions U and charge transfer Δ. These diagrams also demonstrate how delithiation affects the electronic structure as interpreted by each model.
Figure 7. Relationship between covalent electron structure and extra capacity. (a) Schematic illustration of the covalent Model and its influence on the charging process. Oxygen contributes to capacity through hybridization with metal but does not provide extra capacity. (b) Schematic illustration of the non-bonding O 2p states formed by TM migrations or Li/TM mixing and their effect on the charge compensation.

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Reassessing Anionic Redox in Conventional Layered Oxide Cathodes for Li-Ion Batteries: Ionic and Covalent Mechanisms
  • Article
  • Full-text available

January 2025

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12 Reads

Jianhua Yin

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Zixin Wu

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Kai Fang

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[...]

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Shi-Gang Sun

Efforts to improve the specific capacity and energy density of lithium nickel-cobalt-manganese oxide (NCM) cathodes focus on operating at high voltages or increasing nickel content. However, both approaches necessitate a...

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Precisely Tunable Instantaneous Carbon Rearrangement Enables Low‐Working‐Potential Hard Carbon Toward Sodium‐Ion Batteries with Enhanced Energy Density

September 2024

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107 Reads

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16 Citations

As the preferred anode material for sodium‐ion batteries, hard carbon (HC) confronts significant obstacles in providing a long and dominant low‐voltage plateau to boost the output energy density of full batteries. The critical challenge lies in precisely enhancing the local graphitization degree to minimize Na⁺ ad‐/chemisorption, while effectively controlling the growth of internal closed nanopores to maximize Na⁺ filling. Unfortunately, traditional high‐temperature preparation methods struggle to achieve both objectives simultaneously. Herein, a transient sintering‐involved kinetically‐controlled synthesis strategy is proposed that enables the creation of metastable HCs with precisely tunable carbon phases and low discharge/charge voltage plateaus. By optimizing the temperature and width of thermal pulses, the high‐throughput screened HCs are characterized by short‐range ordered graphitic micro‐domains that possess accurate crystallite width and height, as well as appropriately‐sized closed nanopores. This advancement realizes HC anodes with significantly prolonged low‐voltage plateaus below 0.1 V, with the best sample exhibiting a high plateau capacity of up to 325 mAh g⁻¹. The energy density of the HC||Na3V2(PO4)3 full battery can therefore be increased by 20.7%. Machine learning study explicitly unveils the “carbon phase evolution−electrochemistry” relationship. This work promises disruptive changes to the synthesis, optimization, and commercialization of HC anodes for high‐energy‐density sodium‐ion batteries.




XRD patterns of a) LFP, b) LF0.5M0.5P, c) LF0.3M0.7P, d) NFP, e) NF0.7M0.3P, f) NF0.5M0.5P. Inset: the corresponding SEM images.
a) Galvanostatic charge–discharge profiles of LFP, LF0.5M0.5P, and LF0.3M0.7P cathodes at a current rate of 0.1 C (1 C = 170 mA g⁻¹). b) Rate performances of LFP, LF0.5M0.5P, and LF0.3M0.7P cathodes. c) Cycling performances of LFP, LF0.5M0.5P, and LF0.3M0.7P cathodes at 1 C. d) The initial cycle galvanostatic charge–discharge profiles of NFP, NF0.7M0.3P, and NF0.5M0.5P cathodes at a current rate of 0.1 C (charging under constant current‐constant voltage (CC–CV) chagre mode and 5 h holding at 4.5 V 1 C = 155 mA g⁻¹). e) Rate performances of NFP, NF0.7M0.3P, and NF0.5M0.5P cathodes. f) Cycling performances of NFP, NF0.7M0.3P, and NF0.5M0.5P cathodes at 1 C.
a) GITT potential curves and chemical diffusion coefficient [log(DLi⁺)] of LFP, and LF0.5M0.5P cathodes at the first cycle. b) GITT potential curves and chemical diffusion coefficient [log(DNa⁺)] of NFP, and NF0.7M0.3P cathodes at the first cycle. c) In situ XRD patterns of LFP and LF0.5M0.5P. The diffraction peaks of (002), (131), and (112) marked by blue or red dashed lines are attributed to LiFePO4 (LFP) and FePO4 (FP), respectively. d) Ex situ XRD patterns of NFP and NF0.7M0.3P in different voltages. The diffraction peaks marked by blue dashed lines (220), (121), and (131) are attributed to the NaFePO4.
a) Average output voltage, real specific capacity, and energy density for the LFP, LFMP, NFP, and NFMP cathodes. Herein, real capacity indicates that the specific capacity is normalized by the entire cathode mass, including inactive components (binder, carbon, and so on). Structural sketching diagrams of b) olivine‐type LiFe(Mn)PO4 and c) maricite‐type NaFe(Mn)PO4. The radar map covers five aspects for evaluating materials performance.
From Li to Na: Exploratory Analysis of Fe‐Based Phosphates Polyanion‐Type Cathode Materials by Mn Substitution

August 2023

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49 Reads

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10 Citations

Both LiFePO4 (LFP) and NaFePO4 (NFP) are phosphate polyanion‐type cathode materials, which have received much attention due to their low cost and high theoretical capacity. Substitution of manganese (Mn) elements for LFP/NFP materials can improve the electrochemical properties, but the connection between local structural changes and electrochemical behaviors after Mn substitution is still not clear. This study not only achieves improvements in energy density of LFP and cyclic stability of NFP through Mn substitution, but also provides an in‐depth analysis of the structural evolutions induced by the substitution. Among them, the substitution of Mn enables LiFe0.5Mn0.5PO4 to achieve a high energy density of 535.3 Wh kg⁻¹, while NaFe0.7Mn0.3PO4 exhibits outstanding cyclability with 89.6% capacity retention after 250 cycles. Specifically, Mn substitution broadens the ion‐transport channels, improving the ion diffusion coefficient. Moreover, LiFe0.5Mn0.5PO4 maintains a more stable single‐phase transition during the charge/discharge process. The transition of NaFe0.7Mn0.3PO4 to the amorphous phase is avoided, which can maintain structural stability and achieve better electrochemical performance. With systematic analysis, this research provides valuable guidance for the subsequent design of high‐performance polyanion‐type cathodes.



Injecting Excess Na into a P2-Type Layered Oxide Cathode to Achieve Presodiation in a Na-Ion Full Cell

July 2023

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67 Reads

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19 Citations

Nano Letters

The initial Na loss limits the theoretical specific capacity of cathodes in Na-ion full cell applications, especially for Na-deficient P2-type cathodes. In this study, we propose a presodiation strategy for cathodes to compensate for the initial Na loss in Na-ion full cells, resulting in a higher specific capacity and a higher energy density. By employing an electrochemical presodiation approach, we inject 0.32 excess active Na into P2-type Na0.67Li0.1Fe0.37Mn0.53O2 (NLFMO), aiming to compensate for the initial Na loss in hard carbon (HC) and the inherent Na deficiency of NLFMO. The structure of the NLFMO cathode converts from P2 to P'2 upon active Na injection, without affecting subsequent cycles. As a result, the HC||NLFMOpreNa full cell exhibits a specific capacity of 125 mAh/g, surpassing the value of 61 mAh/g of the HC||NLFMO full cell without presodiation due to the injected active Na. Moreover, the presodiation effect can be achieved through other engineering approaches (e.g., Na-metal contact), suggesting the scalability of this methodology.

Citations (6)


... Reproduced with permission. [13] Copyright 2024, American Chemical Society. f) Operating and average (red dot) voltage comparison of different cathode materials with LSV results of electrolytes in LIBs and SIBs. ...

Reference:

A Perspective on Pathways Toward Commercial Sodium‐Ion Batteries
Elucidating the Structural Evolution of O3-type NaNi 1/3 Fe 1/3 Mn 1/3 O 2 : A Prototype Cathode for Na-Ion Battery
  • Citing Article
  • November 2024

Journal of the American Chemical Society

... At the end stage of delithiation, a rapid drop of D Li + for all the cathodes can be inspected, for which the contraction of lattice along c-axis should be responsible. [37,38] However, NM91 displays significantly dropped voltage decay compared to EL-N9-3 after the 200 th cycles ( Figure S15), accompanied by the pronouncedly reduced D Li + values, which is almost one orders of magnitude smaller than that of EL-N9-3 during the H2-H3 phase transition process. These findings powerfully demonstrate that NM91 undergoes more severe structural degradation to form surface Li-insulative rock-salt phase and thicker detrimental by-products layers, whereas EL-N9-3 maintains a more stable layered structure that enables better conduction of Li + while reducing detrimental side reactions. ...

Revealing Gliding-Induced Structural Distortion in High-Nickel Layered Oxide Cathodes for Lithium-Ion Batteries
  • Citing Article
  • September 2024

ACS Nano

... Additionally (Fig. 5c), the C 1s spectrum clearly demonstrates the presence of four peaks for C at the binding energies corresponding to C = C (284.8 eV), C-N (289.31 eV), C = N (292.91 eV), and N-C = N (295.67 eV) [28,29]. The low intensity of the C-N peak at 289.31 eV may be attributed to factors such as limitations in spectral resolution, overlap with other C species, baseline drift, or the relatively low nitrogen content in the composite. ...

Precisely Tunable Instantaneous Carbon Rearrangement Enables Low‐Working‐Potential Hard Carbon Toward Sodium‐Ion Batteries with Enhanced Energy Density

... All of the microstructure, phase components, particle shape, particle size, and specific surface of NaFePO 4 /C cathode materials were resources constrains their application in energy storage systems. Sodium (Na) and lithium (Li) are in the same main group of the periodic table and share similar chemical properties, which suggests that NaFePO 4 can theoretically offer performance comparable to LiFePO 4 [7][8][9][10][11][12][13]. However, sodium resources are more abundant, NaFePO 4 cathode material attracts much attention. ...

From Li to Na: Exploratory Analysis of Fe‐Based Phosphates Polyanion‐Type Cathode Materials by Mn Substitution
  • Citing Article
  • August 2023

... Subsequently, in 1991, Sony commercialized the first lithium-ion batteries (LIBs) product [9][10][11][12][13] . With the continued strong demand in the new energy market and the release of production capacity in the industry, new batteries such as zinc ions [14] , sodium ions [15] , and lithium-sulfur [16] have appeared dramatically. During this period, scientific researchers conducted continuous research on the battery efficiency and found that it largely depended on the characteristics of the cathode materials [17] . ...

Recognition and Application of Catalysis in Secondary Rechargeable Batteries
  • Citing Article
  • July 2023

ACS Catalysis

... [21] Besides, the lower Debye-Waller factor (σ 2 ) for NFM-CZF also demonstrates lower degree of structural disorder level for Fe in relation to its neighboring atoms. [22] Lastly, TMÀ O and TM-TM coordination strengths of NFM-CZF are perfectly coincident to their original values after the charge/discharge process, underscoring high reversibility and structural flexibility under high voltage. Combining insights from in situ XRD and ex situ XANES, it is unquestionable that the function of CZFmodification is majorly focused on safety control the lattice evolution, improving reversibility of the TM redox and phase transition, restraining irreversible migration of Fe 4 + , and thus contributing to maintain highly electrochemical capacity and avoid the interphase structure degradation during long-term cycling. ...

Injecting Excess Na into a P2-Type Layered Oxide Cathode to Achieve Presodiation in a Na-Ion Full Cell
  • Citing Article
  • July 2023

Nano Letters