Graphite oxide was dispersed in deionized water, followed by the addition of equimolar amounts of Fe(NO₃)₃·9H₂O, NaH₂PO₄, and citric acid. The mixture was continuously stirred at 80 °C until a homogeneous sol formed, which was then dried to obtain the precursor. This precursor was freeze-dried, ground, and subsequently calcined at 350 °C for 4 h, followed by calcination at 600 °C for 8 h under an Ar/H₂ atmosphere. The resulting product was designated NFP/C.

The NFP/C material was stirred in a 0.3 M HCl solution for 1 h and then washed until neutral, yielding the acid-treated product labeled NFP/C H. In a separate procedure, the precursor was mixed with nano CaCO₃ at a mass ratio of 1:0.01, ground, and uniformly dispersed in deionized water. After freeze-drying and calcination under the same conditions described above, the resulting product was washed and designated NFP/C T_0.01.

Furthermore, the precursor was mixed with nano-CaCO₃ at mass ratios of 1:0.01, 1:0.02, and 1:0.03, respectively. Each mixture was homogenized in deionized water, freeze-dried, ground, and calcined under identical conditions. The calcined products were then ground again, stirred in diluted HCl for 1 h, and washed until neutral. The final products were labeled NFP/C-HT_0.01, NFP/C-HT_0.02, and NFP/C-HT_0.03, respectively.

The elemental composition of the samples was determined by inductively inductively coupled plasma optical emission spectrometry (ICP-OES) using an Optima 8000 instrument. The crystal structure was analyzed with an X-ray diffractometer (XRD, SmartLab SE) employing Cu Kα radiation. The carbon content of the materials was measured by thermogravimetric analysis (TGA) using a HITACHI STA7300. The chemical states of surface elements were investigated via X-ray photoelectron spectroscopy (XPS) with a Thermo Scientific K-Alpha system. X-ray absorption fine structure (XAFS) spectroscopy was performed in transmission mode on a Rapid XAFS 2M instrument (Anhui Absorption Spectroscopy Instrument Co., Ltd.) at 20 kV and 20 mA. For iron analysis, a Ge (620) spherical bent crystal analyzer with a curvature radius of 500 mm was employed. The morphology and structural characteristics of the materials were examined by scanning electron microscopy (SEM, Hitachi S-4800), transmission electron microscopy (TEM, FEI Tecnai F20), high-resolution TEM (HRTEM), selected-area electron diffraction (SAED), and energy-dispersive X-ray spectroscopy (EDS) elemental mapping. Dispersion stability was evaluated using a zeta potential analyzer (Zetasizer Pro 46500). Nitrogen adsorption-desorption isotherms were obtained with an Autosorb-iQ physisorption analyzer (Micromeritics APSP 2460). The specific surface area was calculated using the Brunauer-Emmett-Teller (BET) method, and the pore size distribution was determined by the Barrett-Joyner-Halenda model.

The electrochemical performance of the samples was evaluated using a LAND battery test system (CT2001A, Wuhan, China) and a CHI760D electrochemical workstation. The active material, Ketjen black, and polyvinylidene fluoride were mixed in a mass ratio of 7:2:1 and dispersed in N-methyl-2-pyrrolidone (NMP) to form a homogeneous slurry. This slurry was cast onto carbon-coated aluminum foil and dried to form the cathode. The electrode films were vacuum-dried at 110 °C for 12 h. The mass of active material on each electrode sheet was approximately 0.8 mg. Coin-type half-cells were assembled in an argon-filled glove box. The cathode electrolyte (TC-E201) was purchased from Tianjin Tianchi Materials Technology Co., Ltd. Metallic sodium was used as both the counter and reference electrode. Electrochemical measurements of the cathodes were conducted within a voltage range of 1.5 to 4.3 V. Electrochemical impedance spectroscopy (EIS) was recorded over a frequency range of 0.01 Hz to 100 kHz. The electrolyte consisted of 1 M NaClO₄ in a mixture of ethylene carbonate and propylene carbonate (v/v, 1:1), with 5% fluoroethylene carbonate added as a high-voltage additive. A glass fiber GF/F membrane was used as the separator.

The samples were prepared using a conventional sol-gel method. A schematic illustration of the synthesis process is presented in Figure 1A. To elucidate the individual and combined effects of the nano-CaCO₃ template and HCl washing, control samples NFP/C-T_0.01 and NFP/C-H were also synthesized. The XRD patterns of NFP/C, NFP/C-T_0.01, NFP/C-H, and NFP/C-HT_0.01 are shown in Figure 1B. All diffraction peaks correspond well with the reference pattern of maricite NFP (JCPDS no. 29-1216)^[23], and no impurity peaks were detected, confirming the phase purity of the as-prepared samples. Notably, NFP/C exhibits the sharpest diffraction peaks, indicating the highest crystallinity^[24]. In contrast, NFP/C-T_0.01, which includes the template agent, shows weakened peak intensities. The acid-washed sample NFP/C-H displays a significant reduction in peak intensity, while the NFP/C-HT_0.01 sample, treated with both templating and acid washing, demonstrates the lowest crystallinity^[25], indicating that the combined treatment effectively reduces the material's crystallinity and likely introduces a considerable number of random crystal defects, thereby disrupting its long-range ordered structure.

The morphology of the samples was characterized by SEM [Supplementary Figure 1]. As shown in [Supplementary Figure 1A, the NFP/C sample exhibits large, block-like structures with significant aggregation. After introducing the templating agent, the NFP/C-T_0.01 sample [Supplementary Figure 1B] displays a markedly reduced particle size, forming uniform spherical particles with less agglomeration. Further acid washing of the NFP/C-H sample [Supplementary Figure 1C] results in even finer particles and increased surface roughness, indicating that the acid treatment effectively disrupts the surface structure and promotes particle refinement of maricite NFP. The reduction in particle size increases the specific surface area, providing more active sites for sodium-ion insertion and extraction, thereby enhancing electrode reaction kinetics^[26,27]. Additionally, both templating and acid washing contribute to a more developed porous structure, further optimizing the material architecture^[28-30]. Zeta potential measurements [Supplementary Figure 2] indicate a higher surface charge density for both NFP/C-T_0.01 and NFP/C-H. This enhanced electrostatic repulsion, combined with their reduced particle size, effectively suppresses agglomeration and promotes dispersion stability^[31,32].

The morphology of NFP/C-T_0.01 and NFP/C-H was further examined using TEM. As shown in Supplementary Figure 1D and E, the NFP/C-T_0.01 sample consists of relatively large particles uniformly coated with graphene sheets. The HRTEM image [Supplementary Figure 1F] reveals clear lattice fringes with spacings of 0.36 and 0.26 nm, corresponding to the (111) and (301) planes of maricite NFP, respectively^[18]. The SAED pattern (inset of Supplementary Figure 1F) exhibits distinct diffraction rings indexed to the (111) and (301) planes, further confirming the maricite-type structure^[21]. In contrast, the NFP/C-H [Supplementary Figure 1G and H] displays smaller particle sizes and improved dispersion, consistent with the SEM observations. The HRTEM image [Supplementary Figure 1I] shows lattice fringes of 0.26 nm, assigned to the (301) plane of maricite NFP, indicating that the material retains a certain degree of crystallinity at the microscopic scale. The presence of only a few discrete diffraction spots in the SAED pattern (inset of Supplementary Figure 1I) suggests lower crystallinity compared with NFP/C-T_0.01, which can be attributed to the loss of sodium ions during acid washing, resulting in the formation of sodium-deficient defects. EDS elemental mapping of NFP/C-T_0.01 [Supplementary Figure 1J] confirms a homogeneous distribution of Na and Fe throughout the material. Additionally, a thin carbon coating is observed on the material’s surface.

Figure 1C illustrates the crystal structure of maricite NFP, with additional orientations shown in Supplementary Figure 3. TEM analysis confirms that the (111) plane is the primary exposed facet, and a cross-sectional view of this plane is presented in Figure 1D. In the pristine maricite structure, sodium ions are confined between [FeO₆] octahedra and [PO₄] tetrahedra within a closed framework, which impedes efficient Na⁺ diffusion and results in electrochemical inactivity. In contrast, after our processing method, the (111) facet in maricite NFP effectively exposes sodium ions, facilitating their release from the lattice and enabling rapid Na⁺ transport.

ICP-OES analysis was performed to examine the chemical composition [Figure 1E]. A trace amount of Ca was detected in NFP/C-T_0.01, accompanied by partial Fe loss, suggesting possible lattice doping by the templating agent. It should be noted that the samples were thoroughly washed, eliminating the possibility of Ca residue. In the acid-treated sample NFP/C-H, the Na content decreased to 0.71, indicating the formation of sodium vacancies while the maricite structure remained intact, as confirmed by XRD [Figure 1B]. These results demonstrate that the template mildly tunes the composition and microstructure of maricite NFP, whereas acid washing introduces sodium defects and disrupts the long-range order. This structural change breaks the closed framework and creates efficient pathways for Na⁺ migration. The surface chemical states of NFP/C-T_0.01, NFP/C-H, and NFP/C-HT_0.01 were analyzed by XPS. As shown in Figure 1F-H, all samples contain Na, Fe, P, O, and C as the primary elements. The acid-washed samples NFP/C-H and NFP/C-HT_0.01 exhibit a clear reduction in Na XPS intensity, further confirming sodium loss due to acid treatment. Trace Ca is detected in the templated samples NFP/C-T_0.01 and NFP/C-HT_0.01, consistent with ICP-OES results. The Fe 2p XPS spectra are presented in Figure 1I-K. A higher binding energy is observed for the Fe 2p peaks in NFP/C-H and NFP/C-HT_0.01, indicating an elevated Fe oxidation state^[33,34]. This shift results from charge compensation following Na⁺ removal, which promotes the oxidation of Fe²⁺ to Fe³⁺. Peak fitting analysis [Supplementary Figure 4] further reveals a progressive increase in the Fe³⁺/Fe²⁺ ratio with sodium deficiency, confirming that acid treatment induces redox reactions and modifies the Fe valence distribution.

Raman spectroscopy was performed on NFP/C-T_0.01, NFP/C-H, and NFP/C-HT_0.01 to investigate the defect structure of the amorphous carbon in the composites. As shown in Supplementary Figure 5, all samples exhibit distinct characteristic peaks at 1,586.5 cm^-1 (G band, representing graphitic carbon) and 1,343.2 cm^-1 (D band, associated with structural defects)^[35,36]. The I_D/I_G ratios for NFP/C-T_0.01, NFP/C-H, and NFP/C-HT_0.01 are 0.78, 0.91, and 0.92, respectively. The higher I_D/I_G values of NFP/C-H and NFP/C-HT_0.01 indicate a lower degree of structural order in the carbon, suggesting that acid treatment effectively disrupts the surface regularity and introduces more defects and disordered structures^[37]. Among them, NFP/C-HT_0.01 shows the highest I_D/I_G ratio, reflecting the greatest defect concentration and structural disorder in its carbon layers. These structural defects can serve as active sites during electrochemical processes, thereby enhancing reaction activity. The specific surface area and pore structure of the samples were characterized by BET measurements. As shown in Supplementary Figure 6A, all samples display type IV isotherms with clear hysteresis loops in the P/P₀ range of 0.4-1.0, confirming their mesoporous nature. The specific surface areas of NFP/C-T_0.01, NFP/C-H, and NFP/C-HT_0.01 are 52.0, 109.7, and 123.7 m²·g^-1, respectively. The markedly higher surface area of the acid-treated samples suggests that acid treatment induces surface restructuring and increases the accessible area, consistent with SEM and zeta potential analyses. Pore size distribution profiles [Supplementary Figure 6B] show that NFP/C-HT_0.01 exhibits the most developed porosity with abundant mesopores. Its hierarchical pore structure enhances electrolyte infiltration and ionic diffusion, supporting fast ion transport and improved electrode reaction kinetics.

The electrochemical performance of the prepared cathodes was evaluated in coin-type half-cells over a voltage range of 1.5 to 4.3 V. At a current density of 100 mA g^-1 [Supplementary Figure 7A], the initial discharge capacities of NFP/C, NFP/C-T_0.01, NFP/C-H, and NFP/C-HT_0.01 were 55.8, 67.2, 79.8, and 96.0 mAh g^-1, respectively. Among these, NFP/C-HT_0.01 exhibited the highest reversible capacity and retained 93.3% of its initial capacity after 100 cycles, demonstrating excellent cycling stability. This enhancement is attributed to the tailored microstructure and increased lattice disorder. Smaller particles mitigate volume strain during Na⁺ insertion and extraction, thereby improving structural integrity. Additionally, the larger specific surface area provides more Na⁺ storage sites and accelerates electrode kinetics. Furthermore, the disordered framework induced by sodium vacancies, combined with Ca²⁺ incorporation, creates additional ion transport pathways, thereby activating the electrochemical activity of maricite NFP.

Rate performance data are presented in Supplementary Figure 7B. NFP/C-HT_0.01 delivers capacities of 112.1, 94.8, 84.9, 79.5, 75.9, and 69.4 mAh g^-1 at current densities of 0.05, 0.1, 0.2, 0.3, 0.5, and 1 A g^-1, respectively. When the current density is returned to 0.05 A g^-1, the capacity recovers to 110.4 mAh g^-1, demonstrating excellent reversibility and rate capability. These results confirm that the combination of templating and acid treatment effectively optimizes the microstructure and lattice disorder of NFP/C-HT_0.01. The resulting porous network and sodium defects synergistically facilitate Na⁺ diffusion, underpinning the remarkable cycling stability and rate performance.

To investigate the influence of the template ratio on electrochemical behavior, NFP/C HT_0.02 and NFP/C HT_0.03 were synthesized with precursor-to-template mass ratios of 1:0.02 and 1:0.03, respectively. XRD patterns [Figure 2A] show that both samples retain the maricite-type NFP crystal structure. As the template ratio increases, the intensity of the diffraction peaks gradually decreases, indicating reduced crystallinity and increased structural disorder. Rietveld full-pattern refinements yield lattice parameters for pristine NFP (a = 8.986 Å, b = 6.869 Å, c = 5.045 Å) [Supplementary Figure 8A] and NFP/C HT_0.02 (a = 8.895 Å, b = 6.870 Å, c = 5.046 Å) [Supplementary Figure 8B]. Upon Ca²⁺ substitution, a slight contraction of the a-axis occurs, while the b- and c-axes remain nearly unchanged. This anisotropic lattice change induces lattice strain and local structural rearrangement, which modulates the geometric configuration of Na⁺-migration tunnels. Such lattice-distorted local environments are beneficial for Na-ion transport and enhance electrochemical performance.

Raman spectroscopy was employed to investigate the effect of the template ratio on the carbon structural order of NFP/C-HT_0.02 and NFP/C-HT_0.03 [Figure 2B]. Both samples exhibit characteristic G band (1,586.5 cm^-1) and D band (1,343.2 cm^-1) peaks. The I_D/I_G ratio of NFP/C-HT_0.02 is 0.94, higher than that of NFP/C-HT_0.03 (0.88), indicating greater structural disorder and defect density in its carbon matrix. TGA analysis [Supplementary Figure 9] reveals a carbon content of 7.1 wt% for NFP/C-HT_0.02. Notably, the slight weight gain observed between 280 and 350 °C is attributed to the oxidation of surface Fe²⁺ species to Fe³⁺ in air.

To investigate the surface and porous structural characteristics, N₂ adsorption-desorption tests were performed [Supplementary Figure 10A]. NFP/C-HT_0.02 exhibits a specific surface area of 192.1 m² g^-1 and a pore volume of 0.42 cm³ g^-1, both significantly higher than those of NFP/C-HT_0.03 (162.8 m² g^-1 and 0.35 cm³ g^-1, respectively). The larger specific surface area provides abundant electroactive sites, while the increased pore volume accommodates sufficient electrolyte and continuous transport channels, reducing sodium ion diffusion resistance and collectively facilitating rapid ion transport. The pore size distribution [Supplementary Figure 10B] further confirms that NFP/C-HT_0.02 possesses well-developed hierarchical pores. Macropores enable rapid electrolyte infiltration and accommodate lattice volume changes during cycling, whereas mesopores shorten the solid-state diffusion pathway of Na⁺ ions and expose numerous redox-active sites. The synergistic effect of this dual pore architecture significantly accelerates ion transport and optimizes the interfacial reaction kinetics of the electrode. ICP-OES data reveal a continuous decline in sodium content as the template ratio increases [Figure 2C]. The molar ratios of Na:Fe:Ca in NFP/C-HT_0.01, NFP/C-HT_0.02, and NFP/C-HT_0.03 are 0.52:0.95:0.03, 0.33:0.95:0.06, and 0.19:1.04:0.09, respectively. Although NFP/C-HT_0.03 exhibits the lowest sodium content, excessive sodium loss may lead to the collapse of the NFP crystal structure.

The Fe K-edge X-ray absorption near-edge structure (XANES) spectra [Figure 2D] exhibit a distinct shift to higher energy for NFP/C-HT_0.02 compared to low-valent references (FeO, Fe foil), indicating an iron oxidation state approaching +3. This shift is attributed to the loss of sodium ions, which triggers the oxidation of some Fe²⁺ to Fe³⁺ to maintain charge balance, resulting in a mixed Fe²⁺/Fe³⁺ valence state. The presence of mixed Fe²⁺/Fe³⁺ valence is crucial for inducing structural disorder. In pristine NFP, the absence of Fe³⁺ ensures high structural stability without Jahn-Teller distortion. However, the introduction of low-spin Fe³⁺(t_2g⁵e_g⁰) promotes Jahn-Teller distortion around high-spin Fe²⁺(t_2g⁴e_g²) centers, leading to local lattice distortion and further structural disorder. This disordered configuration broadens sodium migration pathways and enhances Na⁺ diffusion kinetics^[38,39].

The Fourier transform-extended X-ray absorption fine structure (FT-EXAFS) spectrum of NFP/C-HT_0.02 [Figure 2E] reveals a significant increase in the Fe-O bond length. This change can be attributed to local lattice distortion induced by the Jahn-Teller effect, which optimizes the electronic structure and enhances electron transport within the electrode material, thereby facilitating faster electron transfer during charge and discharge processes^[40]. In the Fe 2p XPS spectra [Figure 2F], the Fe 2p peaks shift further toward higher binding energies, indicating a gradual increase in the iron oxidation state. This shift results from the oxidation of Fe²⁺ to Fe³⁺ to maintain charge balance during desodiation, leading to an elevated average Fe oxidation state. This conclusion is consistent with the absorption edge shift observed in the XANES spectra.

The SEM characterization [Figure 2G] reveals that NFP/C-HT_0.02 consists of small nanospheres with an average particle size of approximately 22 nm and significantly improved dispersion. This refined microstructure increases the specific surface area, facilitating rapid Na⁺ insertion and extraction while reducing volume strain during cycling, thereby enhancing structural stability and cycle life^[41]. In contrast, although NFP/C-HT_0.03 also exhibits a nano-spherical morphology [Supplementary Figure 11A andB], the excess template causes pore collapse and severe particle agglomeration, resulting in poor dispersion. This observation is further supported by zeta potential measurements shown in Supplementary Figure 12.

TEM images [Figure 2H] reveal a uniform graphene coating on the nanospheres in NFP/C-HT_0.02, which enhances electrical conductivity and provides additional pathways for Na⁺ migration. HRTEM [Figure 2I] shows no distinct lattice fringes, and the corresponding SAED pattern lacks clear diffraction rings, confirming a highly disordered structure. This disorder, induced by Jahn-Teller lattice distortion, facilitates Na⁺ migration by lowering the diffusion energy barrier and creating more ion transport channels. Furthermore, the NFP/C-HT_0.02 particles are uniformly coated with an amorphous carbon layer approximately 2.1 nm thick. This thin, continuous carbon shell accelerates electron conduction, shortens Na⁺ diffusion distances, and buffers lattice volume changes during sodiation and desodiation, synergistically enhancing the electrode’s electrochemical kinetics and cycling stability. EDS mapping [Figure 2J] demonstrates a homogeneous distribution of Na, Fe, and C, with Na content notably lower than Fe, consistent with ICP-OES results. Trace Ca, derived from the template agent, is also detected.

The electrochemical performance of the as-prepared cathodes was evaluated using coin-type half-cells within a voltage range of 1.5-4.3 V. As shown in the cyclic voltammetry (CV) curves [Figure 3A], NFP/C-HT_0.01, NFP/C-HT_0.02, and NFP/C-HT_0.03 all exhibit a pair of redox peaks at approximately 2.1 and 2.9 V, corresponding to the Fe²⁺/Fe³⁺ redox reaction associated with Na⁺ extraction and insertion. Notably, NFP/C-HT_0.02 displays sharper and more symmetric redox peaks, indicating enhanced electrochemical reversibility and improved charge transfer kinetics. This improved performance is attributed to the highly disordered structure induced by the Jahn-Teller effect, combined with Ca²⁺ incorporation, which synergistically promotes rapid Na⁺ diffusion. EIS measurements [Figure 3B] further reveal that NFP/C-HT_0.02 possesses the smallest charge transfer resistance (Rct), significantly lower than those of NFP/C-HT_0.01 and NFP/C-HT_0.03, confirming its superior ion electrochemical kinetic characteristics. At a current density of 100 mA g^-1, NFP/C-HT_0.02 delivers an initial charge capacity of 65.1 mAh g^-1 [Figure 3C]. The theoretical specific capacity of NFP/C-HT_0.02 is 55.9 mAh g^-1, calculated from the ICP-OES-derived formula of Na_0.33Fe_0.95Ca_0.06PO₄ (molar mass 158.02 g mol^-1). The slightly higher initial charge capacity relative to the theoretical value is mainly attributed to the additional extraction of Ca²⁺ and partial oxidation of Fe³⁺ to Fe⁴⁺ during the first charge.

The slightly higher charging capacity may be attributed to the extraction of Ca²⁺ from the crystal structure. During the discharging process, a high reversible capacity of 148.7 mAh g^-1 is achieved. Even after 100 cycles, a reversible capacity of 128.3 mAh g^-1 is maintained [Figure 3D]. The rate performance evaluated at different current densities is shown in Figure 3E. NFP/C-HT_0.02 exhibits outstanding rate capability, delivering reversible capacities of 178.6, 149.4, 128.6, 112.6, 108.7, and 93.8 mAh g^-1 at current densities ranging from 0.05 to 1 A g^-1. This high reversible capacity of 178.6 mAh g^-1 corresponds to the reversible insertion and extraction of one electron per formula unit of the Na_0.33Fe_0.95Ca_0.06PO₄ cathode. In contrast, NFP/C-HT_0.03 shows poor rate performance due to excessive template use, which causes structural collapse and hinders Na⁺ transport and storage. In the Ragone plot [Figure 3F], NFP/C-HT_0.02 demonstrates higher energy and power densities than other recently reported NFP cathodes, highlighting its practical potential. Moreover, after 500 cycles at 1 A g^-1 [Figure 3G], NFP/C-HT_0.02 retains a reversible capacity of 75.8 mAh g^-1 with 77.8% capacity retention, confirming the advantages of its durable porous framework and optimized Na⁺ insertion/extraction kinetics for long-term cycling.

Galvanostatic intermittent titration technique (GITT) measurements were performed to evaluate the Na⁺ diffusion coefficients (D_Na+) of various samples [Supplementary Figure 13]. The NFP/C-HT_0.02 electrode exhibits a D_Na+ of 5.3 × 10^-12 cm² s^-1, which is notably higher than that of bulk NFP (3.3 × 10^-12 cm² s^-1). This enhancement can be attributed to the reduced particle size, which shortens the solid-state diffusion length, as well as the moderate lattice disorder induced by Jahn-Teller distortion, facilitating Na⁺ migration within the crystal structure. To further assess the interfacial charge-transfer kinetics, temperature-dependent EIS was conducted from 293.15 to 313.15 K in 5 K intervals [Supplementary Figure 14A]. The Nyquist plots show a high-frequency semicircle whose diameter decreases markedly upon heating, indicating that Rct is strongly temperature-dependent. Arrhenius fitting of R_ct^-1 yields an apparent activation energy of 0.417 eV [Supplementary Figure 14B], which is significantly lower than values reported for iron-based polyanion cathodes in the literature^[44,45]. This quantitative agreement between the low E_a and the high D_Na+ from GITT demonstrates that both interfacial charge transfer and bulk ionic diffusion are synergistically optimized in NFP/C-HT_0.02.

Ex situ XRD and in situ EIS analyses of NFP/C-HT_0.02 were performed to elucidate the relationship between structural evolution and electrochemical performance. During the discharge process, the diffraction peaks at 33° and 35°, corresponding to the (121) and (301) crystal planes, respectively, showed no significant shift, indicating excellent structural stability of the sample. Notably, when discharged below 2.5 V, these two peaks gradually broadened, primarily due to the reduction of Fe³⁺ to Fe²⁺. The strong Jahn-Teller distortion associated with Fe²⁺ causes the structure to deviate from ideal octahedral coordination, resulting in decreased crystallinity and increased amorphous characteristics of the material [Figure 4A]. The corresponding evolution of the unit cell volume is shown in Figure 4B, displaying an initial contraction followed by expansion, which correlates with the in situ EIS results during the discharge process [Figure 4C]. The in situ EIS spectra of NFP/C-HT_0.02 during discharge [Figure 4C] reveal a clear decrease in Rct below 2.5 V. This decline is attributed to the stronger Jahn-Teller effect of Fe²⁺ compared to Fe³⁺, which induces greater structural disorder and unit cell expansion, thereby accelerating the electrode’s charge transfer rate.

It should be noted that in a well-ordered structure, whether composed entirely of symmetric units (e.g., Fe³⁺O₆, PO₄) or entirely of asymmetric units (e.g., Fe²⁺O₆), the stability of the structure is determined by these fundamental building blocks. If unstable factors arise, specifically a mixed phase containing both symmetric and asymmetric units (e.g., Fe²⁺O₆, Fe³⁺O₆, or even Fe⁴⁺O₆), the overall structural stability is compromised. This results in dynamic Jahn-Teller disorder, which prevents the structure from maintaining a stable phase consistent with thermodynamic equilibrium. Instead, the system undergoes continuous transformations between dynamically unstable phases, resembling a metastable equilibrium state.

The in situ EIS results during the charging process are presented in Figure 4D. As the charging voltage increases, the Rct gradually rises, primarily due to the oxidation of Fe²⁺ to Fe³⁺ and the relatively weak Jahn-Teller effect associated with Fe³⁺. When the voltage exceeds 4.0 V, Rct decreases significantly. This decrease can be attributed to the formation of Fe⁴⁺ (t_2g³e_g¹), which exhibits an extremely strong Jahn-Teller effect, causing distortion and deformation of the sample structure and thereby creating more Na⁺ transport channels. The fitted results of the in situ EIS spectra at various charging voltages are shown in Supplementary Figure 15. To verify the oxidation of Fe³⁺ to Fe⁴⁺ during charging, high-resolution Fe 2p XPS spectra were collected after the process. The presence of distinct Fe⁴⁺ peaks in Figure 4E provides direct evidence of this reaction. The valence change of iron induces a structural transition toward an amorphous state, which enhances Na⁺ migration and interface reactivity, thereby significantly improving the electrochemical kinetics of the electrode material^[46,47].

The dynamic Jahn-Teller effect maintains the material in a distorted state, facilitating rapid Na⁺ migration. Schematic structures with different iron valences are shown in Supplementary Figure 16. Although dynamic Jahn-Teller lattice distortion occurs continuously during cycling, NFP/C-HT_0.02 retains a uniform and intact nanospherical morphology without particle cracking or pulverization after charging and extended cycling [Figure 4F and G]. This remarkable structural stability results from the high surface charge density of the particles, which inhibits the agglomeration of ultrafine nanoparticles through electrostatic repulsion. The hierarchical pores accommodate lattice volume variations caused by Na⁺ deintercalation and intercalation, while the continuous outer carbon coating preserves the integrity of the conductive network. The synergy of these three factors mitigates internal stress accumulation during cycling.

Elemental mapping of the metallic sodium surface on the counter electrode after charging NFP/C-HT_0.02 is shown in Figure 4H. Notably, calcium was detected alongside sodium. Since physical adsorption on the anode has been accounted for, the calcium signal must originate from the extraction of Ca²⁺ ions from the cathode during charging. This finding corresponds with the observed higher initial charging capacity, which exceeds the theoretical value, confirming the successful Ca²⁺ doping of the NFP/C-HT_0.02 lattice. Although the standard electrode potential of Ca²⁺/Ca (-2.87 V vs. SHE) is more negative than that of Na⁺/Na (-2.71 V vs. SHE), kinetic factors, including interfacial polarization and local potential changes during Na⁺ extraction, enable partial co-migration of Ca²⁺ during charging. The resulting calcium deposition (1.55 on the Mohs hardness scale) on the sodium metal surface (0.4 on the Mohs hardness scale) can also suppress dendrite growth. Furthermore, the stable incorporation of larger Ca²⁺ ions expands Na⁺ migration pathways within the lattice structure, enhancing the ionic transport kinetics of maricite NFP^[48,49].

Throughout the entire text, a multiscale and universal strategy to activate these potentially electrochemically inert materials is proposed as follows.

(1) Configuring intrinsic structural disorder. The dynamic Jahn-Teller effect in transition metal ions (e.g., Fe²⁺, Mn³⁺) induces persistent lattice distortions during cycling^[50,51]. This disrupts long-range order and promotes an amorphous-like structure, creating widened three-dimensional ion migration channels that lower diffusion barriers and enhance intrinsic electrochemical activity^[52,53]. Other chemical methods can also increase the intrinsic disorder of crystal structures. For example, high-entropy design, where multiple principal elements cause significant lattice distortion, leading to chemical structural disorder; doping, which introduces vacancies and point defects that cause lattice relaxation; and non-equilibrium preparation, which limits atomic migration to form metastable disorder.

(2) Reconstructing external material disorder (i.e., altering particle size and morphology). Manual nanosizing of the material not only creates more active sites but also introduces cation and oxygen vacancies. These defects generate preferential migration pathways and additional active centers, while synergistically shortening ion and electron transport distances to enhance external disorder^[54,55]. This paper introduces nanostructures through chemical methods such as templating agents and acid etching. In practical production, a series of high-entropy oxides or ceramics can be prepared using methods like co-precipitation, sol-gel, and mechanochemical synthesis. Additionally, alloy-type materials can be obtained through techniques such as arc melting, mechanical alloying, and magnetron sputtering. Rapid quenching or melt spinning is also a classic and commonly used method for preparing amorphous alloys (metallic glasses). Through the mechanical impact and shear forces provided by high-energy ball milling, powder particles of different materials continuously undergo plastic deformation, cold welding, and fracture, eventually diffusing and mixing at the atomic scale. This is our most fundamental method for inducing external structural disorder.

(3) Achieving interface and process stabilization. First, interactions between particles must be minimized to enhance overall flowability. For example, a high surface charge (zeta potential) prevents particle aggregation through electrostatic repulsion. Dispersants firmly adsorb onto particle surfaces via “anchor groups,” while their long chains extend into the solvent, forming a protective layer. The physical overlap of these long chains and the resulting entropic repulsion generate a strong repulsive force. Surface coatings (e.g., carbon, polymers), elemental doping, and heterostructure construction create conductive networks that improve electron transfer and cycling stability^[56,57]. Through process optimization, such as refining powder characteristics, ensuring thorough mechanical dispersion, using an appropriate feeding sequence, and judiciously applying other additives, strong repulsive forces can be introduced between particles, surpassing van der Waals attractions. This enables particles to remain stable and uniformly dispersed in the solvent, effectively achieving “de-agglomeration.” Such slurries exhibit low viscosity, good flowability, and desirable rheological properties, including shear thinning.

In summary, the coordinated implementation of internal structural disorder and external material disorder, combined with interface stabilization, constitutes an effective "internal-external" synergistic strategy. This multiscale approach systematically optimizes charge and ion transport pathways, providing a general principle for developing high-performance electrochemical energy materials.