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. 2026 Jun 9;17(31):14873–14886. doi: 10.1039/d6sc02904c

Recent progress on iron-based hexacyanoferrates for advanced potassium-ion batteries

Meng Zhou a, Mengna Zhang a, Qian Zhang a, Xinming Ma a, Hui Fang b, Huanhuan Dong c, Xiang Chen d,✉, Jianchao Sun e,✉, Lin Li c,✉, Xunzhu Zhou f,✉
PMCID: PMC13288142  PMID: 42344293

Abstract

Potassium-ion batteries (PIBs) are regarded as promising candidates for large-scale grid energy storage owing to the abundant reserves of potassium resources. Iron hexacyanoferrate (FeHCF), a type of Prussian blue analogue, has garnered significant attention as a cathode material for PIBs due to its robust open framework, high theoretical capacity, and cost-effectiveness. However, the practical application of FeHCF is hindered by its intrinsic limitations, including low electronic conductivity, the presence of interstitial water, and lattice vacancies, which collectively result in inadequate reversible capacity, poor cycling stability and unsatisfactory rate performance. In this review, we summarize the recent achievements of FeHCF cathode materials for PIBs, as well as the key challenges hindering their practical application. In addition, we discuss various modification strategies aimed at enhancing the potassium storage performance, categorizing them into direct approaches (e.g., structural modulation and transition metal doping) and indirect methods (e.g., morphology control, compositing with conductive materials and electrolyte modification). Finally, prospective research directions for improving the electrochemical performance of FeHCF are proposed. This review aims to offer insightful guidance for the rational design of advanced FeHCF materials for high-performance PIBs.

This review systematically summarizes the recent progress, key challenges, and modification strategies for iron-based hexacyanoferrate cathode materials in potassium-ion batteries (PIBs), offering perspectives for designing high-performance PIBs.graphic file with name d6sc02904c-ga.jpg

1. Introduction

As the adverse effects of climate change grow increasingly evident, it has become imperative for humanity to shift from traditional fossil fuels (e.g., coal, petroleum, and natural gas) to clean and renewable energy sources such as hydropower, solar, wind, geothermal, and biomass (Fig. 1a).1–3 However, these renewable energy sources still suffer from significant drawbacks, including intermittency and instability, as they remain highly susceptible to weather conditions, seasonal variations, geographical locations and other influencing factors. These constraints have also given rise to the development of large-scale energy storage technologies (pumped hydro storage, electrochemical energy storage, compressed air energy storage, etc.),4 which enable the continuous and stable output of electricity generated from renewable energy sources. Among the developed energy storage technologies, electrochemical energy storage technology stands out as a particularly promising candidate due to its advantages such as low maintenance costs and environmental friendliness.

Fig. 1. (a) Schematic diagram of the role of large-scale energy storage technology for PIBs in energy structure evolution and energy conversion/storage/utilization. (b) Schematic illustration of PIBs using aluminum foil as the current collector. (c) Comparison of Stokes radius and ionic radius of Li+, Na+, and K+ in propylene carbonate.

Fig. 1

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Lithium-ion batteries (LIBs), as a well-established electrochemical energy storage technology, are widely used in daily life. However, their application in large-scale energy storage systems is limited by the scarcity of lithium resources.5,6 These drawbacks have promoted the research and development of alternative metal ion batteries in large-scale energy storage systems, such as sodium-ion batteries (SIBs),7–11 zinc-metal batteries,12–15 magnesium-ion batteries16–18 and potassium-ion batteries (PIBs).19–23 Among them, potassium-ion batteries (Fig. 1b) are regarded as promising candidates for large-scale energy storage applications based on the following several unique advantages: (i) The K/K+ redox couple exhibits a low standard potential of −2.94 V versus the standard hydrogen electrode (SHE), which facilitates the construction of high-voltage and high-energy-density batteries.24–26 (ii) Potassium is far more abundant in the Earth's crust than lithium (1.5 wt% for K vs. 0.0017 wt% for Li), ensuring greater resource sustainability.27–29 (iii) K+ possesses a smaller Stokes radius (3.6 Å in PC) compared to Li+ (4.8 Å) and Na+ (4.6 Å), attributed to its weaker Lewis acidity, which favors faster ion transport (Fig. 1c).30–33 (iv) Potassium does not alloy with aluminium at low voltage; therefore the cheaper aluminum foil can be used as the cathode current collector to replace copper, which can significantly reduce cost in manufacturing PIBs.34,35

As the core component of PIBs, electrode materials critically determine key performance metrics such as energy density, cycle life, and rate capability. On the anode side, hard carbon and modified graphite have been proven suitable anode materials for PIBs.36,37 For cathodes, various materials have been explored, including layered metal oxides,38–40 polyanionic compounds,41–43 Prussian blue analogs (PBAs),44–47 and organic cathode materials.48–50 Among these candidates, layered metal oxides deliver high theoretical specific capacities but generally suffer from structural collapse and rapid capacity fading during repeated K+ insertion/extraction. Although polyanionic materials exhibit outstanding structural stability, their relatively low specific capacity remains unsatisfactory. Organic cathode materials, despite their structural diversity and sustainability, often suffer from high solubility in electrolytes and poor cycling stability. In contrast, PBAs are regarded as competitive cathodes for PIBs for the following reasons: firstly, their open framework contains large-sized channels that enable rapid K+ intercalation/deintercalation, leading to superior kinetics. Secondly, high capacity and moderate operating voltage can be achieved by modulating the redox couples of transition metals. Moreover, PBAs can be synthesized through simple methods (e.g., coprecipitation and hydrothermal synthesis), making them cost-effective and suitable for large-scale production.

The general chemical formula of PBAs is represented as KxM[M′(CN)6]1−y□y·nH2O (0 ≤ x ≤ 2, 0 ≤ y ≤ 1), where M and M′ are transition metal ions (e.g., Fe, Mn, Ni, Co, and Cu) and □ stands for the M′(CN)6 vacancy.51–54 Among them, iron hexacyanoferrate (FeHCF, M and M′ = Fe) has garnered significant attention as a cathode material for PIBs. This attention stems from several notable advantages of iron: (i) Its high crustal abundance and low cost compared to elements like Co and Ni enhance its commercial viability for large-scale applications. (ii) The Fe2+/Fe3+ redox couple demonstrates high reversibility, contributing to superior cycling stability relative to certain non-iron-based PBAs. (iii) The non-toxic and environmentally benign characteristics of iron align well with sustainable development goals. Despite these strengths, existing review articles primarily offer broad overviews of various cathode materials for PIBs. To the best of our knowledge, a systematic review that comprehensively summarizes the research progress on FeHCF for PIBs is still absent.

This review systematically examines the recent advancements in FeHCF cathode materials for high-performance PIBs. It commences with a critical analysis of the fundamental challenges constraining the electrochemical performance and practical application of FeHCF. Subsequently, an in-depth discussion is presented on the effective modification strategies employed to enhance its potassium storage capabilities. The review concludes by proposing insightful perspectives and future research directions for the development of advanced FeHCF-based cathodes.

2. Challenges of FeHCF for PIBs

Although remarkable advancements in FeHCF cathodes have been achieved in recent years, significant challenges persist that limit its practical implementation in PIBs. These limitations primarily manifest in three aspects: firstly, the presence of interstitial water and structural vacancies from conventional synthesis methods, which adversely affect electrochemical reversibility.55 Secondly, inadequate structural stability of the framework, which leads to particle pulverization and rapid capacity fading under repeated potassium ion insertion/extraction.56 Finally, undesirable interfacial side reactions and electrolyte decomposition at high voltages further compromise the overall storage performance.57 These interconnected challenges form a multifaceted optimization problem that demands comprehensive material engineering strategies to address synergistically.

3. Modification strategies to boost potassium storage performance of FeHCF

To address the critical challenges currently hindering the practical implementation of FeHCF in PIBs, researchers have developed various modification strategies.58–62 These optimization approaches can be broadly categorized into two primary groups (Fig. 2): (i) Direct modification strategies encompassing crystal structure engineering and elemental doping; (ii) Indirect modification strategies involving morphology control, hybridization with conductive material, and electrolyte modification. In this section, we provide a comprehensive review of recent advancements in modification strategies for FeHCF materials in PIBs.

Fig. 2. The modification strategy to boost the potassium storage performance of FeHCF.

Fig. 2

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3.1. Direct modification strategies

3.1.1. Crystal structure engineering

In general, the crystal structure of the FeHCF cathode plays an important role in potassium storage performance. For instance, Li et al. synthesized a series of FeHCF materials to investigate the effect of crystal structure on potassium storage performance, including irregular Prussian white (PW, K1.64Fe[Fe(CN)6]0.89·0.895H2O), spindle-like PB (K0.993Fe[Fe(CN)6]0.997·0.67H2O), and spindle-like PW (K1.72Fe[Fe(CN)6]0.96·0.342H2O).63 The K-rich spindle-like PW exhibited an obviously improved electrochemical performance, with an initial discharge capacity of 124.2 mAh g−1 at a current density of 20 mA g−1 as well as satisfactory rate performance. In situ XRD manifested that the spindle-like PW undergoes no obvious structural evolution and maintains its monoclinic phase during the charge/discharge process (Fig. 3a and b). In addition, density functional theory (DFT) calculations illustrated that the defective PW provides higher energy barriers than the low-defect PW, implying the fast electrochemical reaction kinetics of the spindle-like PW (Fig. 3c and d). They proposed that the high K+ content, low vacancy concentration, and low water content of the spindle-like PW cathode are responsible for the elevated electrochemical performance. To demonstrate the potential of the spindle-like PW for practical application, a spindle-like PW‖graphite full cell was assembled (Fig. 3e). As shown in Fig. 3f and g, the spindle-like PW‖graphite full cells delivered superior cycling stability (a high capacity retention of 97.4% after 100 cycles) and a high discharge capacity (122.5 mAh g−1). Similarly, Kang's group prepared two kinds of Prussian blue cathodes with different contents of vacancies and lattice water at temperatures of 0 °C (K1.36Fe[Fe(CN)6]0.74·0.48H2O, PB0) and 25 °C (K1.43Fe[Fe(CN)6]0.94·0.42H2O, PB25).64 The low-defect PB25 exhibited lower polarization than PB0 during the charge/discharge process. In addition, the elimination of interstitial water provided more space to facilitate K+ migration and storage, resulting in a significant improvement in the electrochemical performance. As a result, PB25 exhibited an excellent cycling performance in both half cells and full cells.

Fig. 3. (a) In situ XRD patterns and (b) the relevant 2D and 3D contour maps of spindle-like PW. (c) Schematic illustration of possible K+ migration paths for the defective and low-defect PWs. (d) Corresponding migration energies of the two paths in the defective and low-defect PWs. (e) Schematic plots of spindle-like PW‖graphite full cells and (f) cycling performance of the spindle-like PW‖graphite full cell at 100 mA g−1. (g) Typical charge/discharge curves of the spindle-like PW‖graphite full cell. Reproduced with permission.63 Copyright 2023, American Chemical Society.

Fig. 3

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Using an electrostatic spray-assisted coprecipitation strategy, Zi and colleagues prepared a K2Fe[Fe(CN)6] material, with the chemical formula K1.56Fe[Fe(CN)6]0.89·□0.11·1.86H2O (denoted as PBFe@ES).65 This synthesis method was carried out under an inert atmosphere to effectively inhibit the oxidation of Fe2+ into Fe3+ and get a highly crystalline sample. Therefore, PBFe@ES exhibited higher potassium content, fewer vacancies and a larger specific surface area. As a result, the electrochemical performances of PBFe@ES were significantly improved, with elevated initial discharge specific capacity, better cycling stability and enhanced rate performance. Subsequently, Wang et al. employed ethylenediaminetetraacetic acid dipotassium (EDTA-2K) as a strong chelating agent to remove Fe atoms from the crystal lattice of PBAs during the synthesis process, constructing the FeIII vacancies in Fe-based PBAs.66 They found that the existence of FeIII vacancies can effectively restrain the lattice distortion and prevent the structural deformation. Therefore, the PBAs with FeIII vacancies show an improvement in the electrochemical stability. To obtain FeHCF with a superior crystal structure, Ma et al. proposed a dual-salt (potassium citrate (K-CA) and potassium chloride (KCl)) assisted co-precipitation method for fabricating cubic-like monoclinic high-quality K1.64FeFe(CN)6 (denoted as PW-HQ) with less crystalline water (6.21%).67 The chelator K-CA could slow down the nucleation process and the subsequent crystal growth by chelating coordination with iron ions, while KCl can increase the K+ content, adjust the morphology and eliminate the interstitial water of the material. Noticeably, K ions were not completely extracted from the monoclinic structure and the remaining K ions were estimated to support the crystal structure during the charge/discharge process, ensuring superior structural stability. Therefore, PW-HQ delivers a high capacity retention of 93% after 1000 cycles at 200 mA g−1. Shu et al. also realized better control of the crystallization process to prepare K1.61Fe[Fe(CN)6]0.88·0.43H2O (denoted as KFeHCF-E) with high crystallinity by using EDTA-2K as the chelating agent.68 Compared with the material synthesized without the addition of EDTA-2K, KFeHCF-E exhibited elevated specific capacity, high rate performance and outstanding cycling stability. Recently, Zhang and colleagues developed a novel reaction environment-tailored strategy for the synthesis of high-quality PB.69 During the synthesis process, a mother liquor, containing concentrated potassium bis(fluorosulfonyl)imide (KFSI)/water was employed to provide a high K+ concentration and low activity of free water. Thus, the prepared PB material K1.69Fe[Fe(CN)6]0.95□0.05·0.74H2O (PB-ML) exhibited highly crystallinity with remarkably low [Fe(CN)6]4− vacancy (denoted as VFeCN) content (5%) and minimized crystal water content (3.98%), while the VFeCN content and crystal water content of K1.08Fe[Fe(CN)6]0.74□0.26·1.24H2O (PB-W) prepared via a water-based coprecipitation method is much higher. Especially, the cycling performance of PB-ML was greatly improved, showing outstanding cyclic stability with a capacity retention of 71.3% after 2500 cycles at 50 mA g−1 and 67.5% after more than 20 000 cycles at 500 mA g−1, much better than that of PB-W.

3.1.2. Transition metal element doping

Element doping can effectively enhance the structural stability of FeHCF and significantly improve its potassium storage performance.70–72 Huang et al. proposed that doping with an appropriate amount of Ni may activate the C-coordinated Fe2+C6/Fe3+C6 redox couple, inducing an increase in high-voltage plateau capacity.73 Among the prepared samples, K1.63Ni0.05Fe0.95[Fe(CN)6]0.92·0.42H2O showed the best electrochemical performance, with an initial discharge capacity of 135 mAh g−1. Subsequently, Qiao et al. utilized a medium entropy concept to synthesize potassium manganese iron copper hexacyanoferrate (K1.90Fe0.67Mn0.16Cu0.09□0.09[Fe(CN)6]·1.78H2O).36 The incorporation of the inert Cu-ion with high electronegativity endowed a robust Cu–N bond and superior structural stability, enabling the cathode material to undergo a zero-stress solid-solution reaction during the charge/discharge process. Therefore, the as-prepared material delivered a high initial discharge capacity of 127.5 mAh g−1, significantly enhanced rate performance and excellent cycling stability with a high-capacity retention of 90.7% after 100 cycles. Recently, Zhou's group reported Mn-substituted KFHCF (K1.81Fe0.90Mn0.10[Fe(CN)6]0.95·0.92H2O, KMFHCF-0.1) for PIBs.74 As shown in Fig. 4a–c, a small amount of high-spin Mn (MnHS-N) substitution can effectively reduce the band gap and energy barrier for K+ migration. Meanwhile, the low-spin Fe coordinated with carbon atoms (FeLS-C) is activated after Mn substitution, resulting in an increased reversible capacity (Fig. 4d and e). Compared with unsubstituted KFHCF (K1.78Fe[Fe(CN)6]0.94·1.01H2O), KMFHCF-0.1 exhibited a high discharge capacity of 135 mAh g−1, with a capacity retention of 85% after 50 cycles (Fig. 4f and g). More importantly, the KMFHCF-0.1‖hard carbon full cell demonstrated excellent rate performance (Fig. 4h), high reversible capacity of 110 mAh g−1 and considerable energy density of 275 Wh kg−1 (Fig. 4i).

Fig. 4. (a) The energy barriers of K+ diffusion in KFHCF and KMFHCF-0.1, respectively. The density of (DOS) states for (b) the KFHCF and (c) KMFHCF-0.1 model structures. The Fermi energy is set as zero. (d) Discharge curves at different cycles and (e) the corresponding capacity contribution of the FeLS-C voltage platform after various cycles at a current density of 100 mA g−1. (f) First charge/discharge patterns of KFHCF and KMFHCF-0.1 at 100 mA g−1, respectively. (g) Cycling performance of KFHCF and KMFHCF-0.1 at a current density of 100 mA g−1. (h) Rate capability of KMFHCF-0.1. (i) Cycling performance at 100 mA g−1. Reproduced with permission.74 Copyright 2023, Elsevier.

Fig. 4

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Similarly, Zhou et al. constructed a defect-free potassium iron manganese hexacyanoferrate (K1.47Fe0.5Mn0.5[Fe(CN)6]·1.26H2O, KFMHCF-1/2) as a cathode material for PIBs.75 The Fe and Mn binary synergy can increase the entropy in the cation positions coordinated with N atoms, which can effectively suppress [Fe(CN)6]4− anionic defects based on charge balance, thus generating a vacancy-free PBA cathode material and improving the electrochemical performances. Via DFT calculations and dynamics analysis, they evidenced that the band gap and K-ion diffusion barrier can be obviously reduced, thus, achieving excellent electronic and K+ transport kinetics. Importantly, Mn and Fe as dual active centers enabled an ultrahigh specific capacity of 155.3 mAh g−1 at 10 mA g−1 with an energy density of 599.5 Wh kg−1 and superior cyclic stability of over 450 cycles at 50 mA g−1. The full cell using K deposited on graphite (K@G) as the anode and KFMHCF-1/2 as the cathode also delivered a long lifespan of over 1000 cycles at 50 mA g−1 with the lowest capacity decay rate of 0.044% per cycle. In addition, Huang et al. synthesized three different samples with the chemical compositions K1.08Fe[Fe(CN)6]0.62·1.64H2O (KFHCF), K1.68Mn[Fe(CN)6]0.88·1.90H2O (KMHCF) and K1.30Fe0.42Mn0.45Sn0.13[Fe(CN)6]0.94·1.35H2O (KFMSHCF). Among these three samples, KFMSHCF constructed via entropy engineering and d10 cation incorporation performed best as a cathode material for PIBs.76 The construction of high configurational entropy increases cation disorder at N-coordinated sites, thereby effectively suppressing the [Fe(CN)6]4− vacancies. And the entropy-induced cation disorder also enables KFMSHCF to exhibit a reduced band gap and low K-ion diffusion barrier (Fig. 5a and b), thereby ensuring excellent electrochemical kinetics (Fig. 5c and d). And the entropy stabilization effect as well as strong Sn–N coordination induced by the completely occupied d10 configuration of Sn2+ can restrain serious lattice distortion with a structural evolution from monoclinic to cubic which can be verified by in situ XRD (Fig. 5e and f), enabling reversible K+ storage, with a high reversible energy density of 364.2 Wh kg−1 and long-term cycling stability of more than 300 cycles at 100 mA g−1 with a capacity retention of 82.1%. This tailored structure also enabled the full cell to exhibit excellent durability over 2500 cycles with an ultralow capacity fading rate of only 0.017% per cycle and a superior initial energy density compared with other reported cathodes (Fig. 5g and h).

Fig. 5. (a) DOS plots and (b) calculated K-ion diffusion barrier of the three electrodes. (c) Linear fitting relationship of Ipvs. v1/2 and (d) galvanostatic intermittent titration technique (GITT) profiles and corresponding K+ diffusion coefficients. The initial charge/discharge curves and intensity contour maps of XRD for (e) KMHCF and (f) KFMSHCF. (g) The long-term cycling performance of the KFMSHCF‖graphite full cell at 100 mA g−1. (h) Comparison of the cycle life and initial energy density of published work. Reproduced with permission.76 Copyright 2025, American Chemical Society.

Fig. 5

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3.2. Indirect regulation

3.2.1. Morphology design

Morphology design can effectively shorten the K+ diffusion path and facilitate electrolyte permeation, resulting in an improved potassium storage performance of electrode materials. Chong and co-workers reported KFe[Fe(CN)6]0.82·2.87H2O nanoparticles with a 3D open framework for PIBs.77Ex situ XRD confirmed the great structural stability of the material during the charge/discharge process. Therefore, superior cycling stability (a high capacity retention of 80.49% after 1000 cycles) was achieved. The effect of crystallite size of the Prussian blue-based cathode on electrochemical performance was investigated by Nazar's group.78 They synthesized three samples with different crystallite sizes (nano (K1.69Fe[Fe(CN)6]0.90·0.4H2O, KFeHCF-S), submicron (K1.78Fe[Fe(CN)6]0.92·0.4H2O, KFeHCF-M), and micron (K0.68Fe[Fe(CN)6]0.89·0.7H2O, KFeHCF-L) crystallites) via a novel citrate chelation route for the first time. Compared with KFeHCF-M and KFeHCF-L, KFeHCF-S showed the highest reversible capacity of 140 mAh g−1. Noticeably, the KFeHCF-S cathode with nano-crystallite particles delivered a comparable energy density (∼500 Wh kg−1) to that of sodium HCF cathodes.

Mai's group synthesized ultrathin nanosheet-assembled flower-like hierarchical Prussian blue materials (K1.4Fe4[Fe(CN)6]3, PB-NSs) by a facile dissolution–recrystallization strategy.79 Benefiting from the hierarchical structure, more active sites were exposed and the diffusion path was greatly shortened, thereby promoting efficient K+ diffusion and leading to enhanced electrochemical performance of PB-NSs. In addition, the XRD results revealed that the lattice structure of PB-NSs during the charge/discharge process was well-maintained, indicating the superior stability of PB-NSs. Subsequently, Xu et al. obtained mesoporous single-crystalline iron hexacyanoferrate (K0.0216FeFe(CN)6·3.03H2O, MSC-FeHCF) micro-spheres by using a SiO2 template-assisted synthesis strategy (Fig. 6a–c).80 This unique mesoporous micro-structure not only facilitates the permeation of the electrolyte and fastens K+ migration, but also relieves the internal stress of MSC-FeHCF during cycling and restricts the interstitial water content inside the material (Fig. 6d and e). Meanwhile, the single crystal decreases grain boundaries, enabling fast charge transfer (Fig. 6f); therefore, MSC-FeHCF delivers superior cycling stability and rate performance of 86.7 mAh g−1 at 3 A g−1, retaining 85.8% of the specific capacity after 2000 cycles at 0.5 A g−1. As shown in Fig. 6g and h, in situ XRD revealed a reversible phase transition from the cubic phase to the monoclinic phase during the charge/discharge process.

Fig. 6. (a) Rietveld refinement of the XRD pattern of MSC-FeHCF. (b) and (c) SEM images of MSC-FeHCF microspheres. (d) BET analysis of MSC-FeHCF. (Inset) Pore size distribution. (e) Von Mises stress contours of MSC-FeHCF (top) and MSC-FeHCF (bottom) stress under complete potassiation. (f) Schematic illustration of stress dispersion, mesoporous confinement effect, electrolyte full wetting, and rapid K+ transportation in MSC-FeHCF. (g) Charge/discharge curves of MSC-FeHCF. (h) The relevant 2D contour plots of in situ XRD patterns. Reproduced with permission.80 Copyright 2025, Wiley-VCH.

Fig. 6

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3.2.2. Composites with conductive materials

In general, composites with conductive materials can enhance charge transfer efficiency and alleviate volume changes during charge and discharge processes, thereby effectively improving potassium storage performance. Xue et al. synthesized a polypyrrole-modified Prussian blue material K1.87Fe[Fe(CN)6]0.97·□0.03·0.84H2O (KHCF@PPy) through an in situ polymerization coating method.81 The introduction of conductive polypyrrole effectively enhanced the electronic conductivity of KHCF, resulting in improved rate capability of the KHCF@PPy cathode. In addition, ex situ XRD demonstrated the superior structural stability of KHCF@PPy during the charge/discharge process. Benefiting from the above merits, KHCF@PPy exhibited an initial discharge capacity of 88.9 mAh g−1 and superior cycling stability with a capacity retention of 85% after 500 cycles. Similarly, Zhou et al. designed a polypyrrole modified Prussian blue material K0.97Fe[Fe(CN)6]0.83·□0.17·0.28H2O (PB-PPY).82 They found that part of K+ remains in the PB-PPY framework and acts as pillars, ensuring fast K+ diffusion kinetics and strengthening the stability of the PB framework (Fig. 7a). Therefore, the as-prepared PB-PPY displayed a higher discharge capacity of 108.6 mAh g−1 for the first cycle than that of pure Prussian blue (55.5 mAh g−1) (Fig. 7b and c). Ex situ XRD analysis during the first two cycles of charge and discharge evidenced that there is no phase transition for the PB-PPY sample and the storage mechanism can be assigned to a solid solution reaction (Fig. 7d and e). Also, compared with pure PB, the PB-PPY sample exhibited better rate capability and obviously improved cycling stability (Fig. 7f and g).

Fig. 7. (a) The schematic illustration of the K ion storage mechanism of PB. Charge/discharge curves of (b) PB-PPY sample and (c) PB sample at 50 mA g−1. (d) Ex situ XRD patterns at different charge/discharge states. (e) The first two cycles of charge/discharge curves of PB-PPY. (f) Rate capability of PB-PPY at different current densities of 50–500 mA g−1. (g) Cycling comparison of PB and PB-PPY at a current density of 50 mA g−1. Reproduced with permission.82 Copyright 2023, Springer.

Fig. 7

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In addition, Zhu et al. created a synthesis method via transformation of the corrosion layer of rusty stainless-steel meshes (RSSM) into compact stacked layers of Prussian blue (PB) nanocubes; when further coated with reduced graphite oxide (RGO), they fabricated a flexible binder-free electrode (denoted as RGO@PB@SSM) for PIBs.83 The unique structure not only enhances the conductivity but also improves the structural stability of the electrode. Therefore, the RGO@PB@SSM cathode showed a high initial discharge capacity of 96.8 mAh g−1, good rate performance (43 mAh g−1 at 400 mA g−1) and enhanced cycling stability (a capacity retention of 75.1% after 305 cycles). Subsequently, Wei and co-workers investigated a series of PB/GO-based composites, K1.50Fe[Fe(CN)6]0.90·0.34H2O/GO (PB/GO), K1.56Fe[Fe(CN)6]0.91·0.33H2O/rGO (PB/rGO) and K1.59Fe[Fe(CN)6]0.90·0.30H2O/PVP-rGO (PB/PVP-rGO).84 Noticeably, some oxygen-containing functional groups were lost during GO reduction, thus weakening the PB and rGO interaction, leading to the structural destruction of PB with poor electrochemical performance. They found that the presence of PVP facilitated the restoration of interaction between rGO and PB, which ensured the integrity of the carbon-encapsulating structure and the conductivity of the PB/PVP-rGO cathode during long-term cycling. Among these composited materials, PB/PVP-rGO exhibited the best potassium storage performance, with a high-capacity retention of 96.5% after 800 cycles. Finally, they fabricated a potassium-ion full-cell with pre-potassiation intercalated graphite (KC8) as the anode, which exhibited outstanding rate performance (77.0 mAh g−1 at 10C) and excellent cycling ability (a high capacity retention of 88.1% after 150 cycles).

Recently, Liu et al. pointed out that hybrid cathode design may offer promising solutions for capacity improvement by introducing a novel anion–cation relay storage mechanism.85 Using MoS2/carbon fibers (CFs) as both a conductive additive and an anion host, they innovatively prepared a Prussian blue analogue-based hybrid cathode (PBAs-MoS2/CFs, Fig. 8a–f). As shown in Fig. 8g–i, the galvanostatic charge/discharge (GCD) profiles of the PBAs-MoS2/CFs hybrid cathode showed combined characteristics of both the MoS2/CFs cathode and the PBA cathode GCD profiles, which implied an anion–cation relay process within the hybrid cathode, that is K+ ions undergo insertion/extraction in the PBA component, while PF6− ions are inserted into/extracted from the MoS2/CFs part. This synergistic dual-ion mechanism within the hybrid cathode significantly enhances electrochemical performances in terms of capacity, rate capability and lifespan (Fig. 8j and k). Therefore, the PBAs-MoS2/CFs hybrid cathode exhibited an ultrahigh specific capacity of ≈143.8 mAh g−1 at 100 mA g−1 and a capacity retention of over 87.4% after 500 cycles at 1000 mA g−1.

Fig. 8. (a–c) Optical images of PBAs-MoS2/CFs. (d and f) High-resolution TEM images of MoS2 and PBAs, respectively. (e) SEM image of the PBAs-MoS2/CFs hybrid electrode. (g–i) Charge/discharge curves of MoS2/CFs, PBAs and PBAs-MoS2/CFs at a current density of 100 mA g−1. (j) Rate performance of PBAs-MoS2/CFs at different current densities of 100 to 1000 mA g−1. (k) Cycling stabilities of PBAs-MoS2-CFs at a current density of 1000 mA g−1. Reproduced with permission.85 Copyright 2025, Wiley-VCH.

Fig. 8

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3.2.3. Electrolyte modification

Electrolytes, often regarded as the “blood” of batteries, critically determine their electrochemical performance. Jeschull and co-workers presented a poly(ethylene oxide)-potassium bis(trifluoromethanesulfonyl)imide (PEO-KFTSI) solid polymer electrolyte (SPE) for the Prussian blue analogue cathode (K2Fe[Fe(CN)6]).86 Compared with traditional organic liquid electrolytes, the K2Fe[Fe(CN)6] cathode with SPE exhibited significantly improved potassium storage performance. Moreover, Lin et al. proposed a dual stabilization strategy to improve the reversible capacity and electrochemical stability of potassium Prussian blue (KPB).87 They applied ethylenediaminetetraacetic acid dipotassium salt (EDTA-2K) as the chelating agent to adjust the crystallization process during co-precipitation. Meanwhile, potassium bis(fluorosulfonyl) imide (KFSI) was employed to construct a robust cathode/electrolyte interface. As a result, the KPB‖graphite full cell exhibited a high reversible capacity of 102.4 mAh g−1, good rate performance (40.4 mAh g−1 at 1.5 A g−1) and superior cycling stability (88% capacity retention from cycle 25 to 400). Subsequently, Wang and colleagues developed a dual additive modification strategy to regulate the interfacial chemistry of Fe-based Prussian blue analog (KFeHCF) cathodes.88 The theoretical calculations and CV analysis evidenced that potassium selenocyanate (KSeCN) is more easily oxidized on the cathode surface and facilitates the formation of a robust cathode electrolyte interphase (CEI) (Fig. 9a–c), which can remarkably inhibit side reactions during the electrochemical process and therefore gives improved cycling stability. They proposed that the dual-additive can dramatically alleviate Fe dissolution and stabilize the KFeHCF structure (Fig. 9d–f). The K‖KFeHCF cell with optimized electrolyte achieved superior cycling performance (a high capacity retention of 81.5% after 5000 cycles) compared with the electrolyte without additives (17.7% of its original capacity after 1000 cycles) and other reported studies (Fig. 9g and h).

Fig. 9. (a) Calculation of the HOMO and LUMO of conventional solvent components, KSeCN and LiDFOB. CV tests of the KFeHCF electrode measured at a scan rate of 0.2 mV s−1 in (b) base electrolyte and (c) electrolyte with 0.5 wt% KSeCN + 0.5 wt% LiDFOB. (d) Raman analysis of the KFeHCF cathode with base and optimized electrolytes after 100 cycles. (e) ICP-OES results of the base and optimized electrolytes after 100 cycles. (f) Ex situ XRD curves of the KFeHCF cathode at different cycles with base and optimized electrolytes. (g) Cycling performance comparison of base and dual-additive electrolytes at 5C charge and discharge rates. (h) Comparison of the cycling life of K‖KFeHCF batteries with that reported in previous studies. Reproduced with permission.88 Copyright 2025, Wiley-VCH.

Fig. 9

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4. Conclusions and perspectives

Owing to its cost-effectiveness, open framework, and high theoretical capacity, FeHCF has emerged as a promising cathode material for PIBs. This review has comprehensively summarized the recent advancements in FeHCF, highlighting its potential while critically addressing the key challenges that impede practical application (such as low electronic conductivity, the presence of interstitial water, and structural vacancies), all of which lead to inadequate capacity reversibility, limited cycling stability and unsatisfactory rate performance. From a commercial application standpoint, we have discussed a range of strategic modification approaches to effectively mitigate these issues. To enable the practical application of FeHCF cathodes in PIBs, they should meet the following performance milestones in the future: reversible capacity ≥130 mAh g−1 and capacity retention ≥80% after 2000 cycles. Furthermore, to facilitate a clear comparison of the development status of various FeHCF-based materials, the electrochemical performance metrics of representative candidates are systematically summarized in Table 1. Generally, crystal structure engineering and elemental doping can effectively enhance the structural stability of the FeHCF cathode, thereby extending its cycle life. In addition, morphology control and hybridization with conductive materials can significantly improve charge transfer kinetics, thus enhancing the rate capability of FeHCF.

Table 1. The electrochemical performance of some representative iron-based hexacyanoferrates for PIBsa.

Classification Materials Voltage range (V versus K+/K) Initial discharge capacity (mAh g−1) Rate performance (mAh g−1)/current density (mA g−1) Cycling stability (capacity retention %/cycles) Initial Coulombic efficiency (%) Electrolyte Ref.
Direct regulation Crystal structure engineering K1.72Fe[Fe(CN)6]0.96·0.342H2O 2.0–4.5 124.2 82.7/500 89.2/500 92.1 5.0 M KFSI DEGDME 63
K1.43Fe[Fe(CN)6]0.94·0.42H2O 2.5–4.3 109.8 54.1/1000 86.5/1000 — 0.5 M KPF6 EC/DEC 64
K1.56Fe[Fe(CN)6]0.89·□0.11·1.86H2O 2.0–4.4 118 82/1550 76/503 105.3 0.8 M KPF6 EC/DEC + 1 wt% FEC 65
K1.74FeFe(CN)6 2.0–4.0 79.4 45/200 57.5/250 97 0.8 M KPF6 EC/DEC + 1% FEC 66
K1.64FeFe(CN)6 2.0–4.3 113.1 60.4/1000 93/1000 — 2.5 M KFSI TEP 67
K1.61Fe[Fe(CN)6]0.88·0.43H2O 2.0–4.0 77.0 60.1/100 61.3/5000 104 2.5 M KFSI TEP 68
K1.69Fe[Fe(CN)6]0.95□0.05·0.74H2O 2.0–4.3 124.8 73/1000 71.3/2500 — 2.5 M KFSI TEP 69
K1.68Fe1.09Fe(CN)6·2.1H2O 2.0–4.5 110.5 — 81/100 105.1 0.8 M KPF6 PC + 4 wt% FEC 89
Transition metal element doping K1.90Fe0.67Mn0.16Cu0.09□0.09[Fe(CN)6]·1.78H2O 2.0–4.5 127.5 63.7/200 ∼70/350 — 1.0 M KPF6 EC/DEC/PC 36
K1.63Ni0.05Fe0.95[Fe(CN)6]0.92·0.42H2O 2.0–4.5 ∼135 81/400 94.4/50 — 0.8 M KPF6 EC/DEC + 1 wt% FEC 73
K1.81Fe0.90Mn0.10[Fe(CN)6]0.95·0.92H2O 2.01–4.5 76/800 40/300 — 0.8 M KPF6 EC/DEC + 5 wt% FEC 74
K1.47Fe0.5Mn0.5[Fe(CN)6]·1.26H2O 2.0–4.5 155.3 55.9/200 68.5/450 — 1.0 M KPF6 EC/DEC/PC 75
K1.23Fe0.42Mn0.45Sn0.13[Fe(CN)6]0.94·1.35H2O 2.0–4.5 97.4 47.1/200 61/300 — 1.0 M KPF6 EC/DEC/PC 76
Indirect regulation Morphology design KFe[Fe(CN)6]0.82·2.87H2O 2.0–4.5 118.7 71.9/200 80.49/1000 — 1.0 M KPF6 EC/DEC/PC 77
K1.69Fe[Fe(CN)6]0.90·0.4H2O 2.0–4.5 140 120/100 85/100 — 0.5 M KPF6 EC/DEC + FEC 78
K1.4Fe4[Fe(CN)6]3 2.0–4.0 71 24.9/600 75.2/100 — 0.5 M KPF6 EC/DEC + 5 wt% FEC 79
K0.0216FeFe(CN)6·3.03H2O 2.0–4.5 127.2 86.7/3000 85.8/2000 — 1.0 M KPF6 EC/PC + 5 wt% FEC 80
K0.220Fe[Fe(CN)6]0.805·□0.195·4.01H2O 2.0–4.0 76.7 36.0/400 ∼86.5/150 44 0.8 M KPF6 EC/DEC 90
Hybridization with conductive materials K1.87Fe[Fe(CN)6]0.97·□0.03·0.84H2O 2.0–4.2 88.5 72.1/1000 86.8/500 72.67 0.8 M KPF6 EC/DEC 81
K0.97Fe[Fe(CN)6]0.83·□0.17·0.28H2O 1.5–4.0 108.6 35.5/500 — 62.8 0.8 M KPF6 EC/DEC + 2 wt% FEC 82
K1.59Fe[Fe(CN)6]0.90·0.30H2O 2.5–4.3 121.8 — 96.5/800 — 0.5 M KPF6 EC/DEC 84
— 2.0–4.5 ≈143.8 81.3/1000 87.4/500 — 3.0 M KPF6 DEGDME 85
Electrolyte modification K2Fe[Fe(CN)6] 2.5–4.3 ∼106 — 90/50 ∼85 PEO-KTFSI 86
K1.92 Fe[Fe(CN)6]0.94·0.5H2O 2.0–4.4 76.2/200 81.3/600 86.6 1.0 M KFSI MeTMS/TTE 91
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a

Annotation: diethylene glycol dimethyl ether (DEGDME), ethylene carbonate/diethyl carbonate (EC/DEC), fluoroethylene carbonate (FEC), triethyl phosphate (TEP), propylene carbonate (PC), polyethylene oxide (PEO), 3-methylsulfolane (MeTMS), and 1,1,2,2-tetrafluoroethyl-2,2,3,3-tetrafluoropropylether (TTE).

To further advance the electrochemical performance of these materials, we suggest the following aspects should be taken into consideration: irst, precise regulation of defects and crystalline water content is essential. For example, optimizing synthesis conditions through coprecipitation, such as slow dropwise addition and low-temperature reaction, is expected to reduce [Fe(CN)6]4− vacancy defects. In addition, the introduction of coordination protectants (e.g., citric acid or EDTA-2K) can be utilized to preferentially coordinate with Fe2+, thereby suppressing hydrolysis side reactions and lowering crystalline water content. Second, constructing a composite conductive network is an effective strategy to enhance charge transport. Compositing iron-based Prussian blue analogues with carbon materials or modifying their surface with conductive polymers can significantly reduce interfacial impedance, improve surface charge transfer kinetics, and thereby enhance rate capability. Meanwhile, a thin and uniform coating strategy using conductive materials should be developed to minimize the amount of non-electrochemically active conductive additives. Third, electrolyte formulation and interface stability require systematic optimization. Exploring novel electrolyte systems or incorporating sulfur-containing additives can help stabilize the electrode–electrolyte interface, mitigate side reactions and enhance overall battery performance. Fourth, rational doping with metal elements (e.g., transition metal elements Mn, Co, and Ni) can disorder atomic arrangement and generate anisotropic stress fields, which effectively dissipate mechanical stresses, thereby improving the structural integrity of the electrode as well as the electrochemical performances. Finally, a deeper understanding of material behavior and potassium storage mechanisms should be pursued through advanced characterization techniques such as in situ XRD and EXAFS, combined with theoretical modeling (e.g., DFT calculations) to probe structural and electronic influences on performance. On this basis, using artificial intelligence for material screening and optimization (such as predicting defect formation energies and ion diffusion energy barriers) is also expected to accelerate the research and development of next-generation FeHCF cathodes.

Author contributions

M. Z. and M. Z. performed the literature search, analyzed the published results, and wrote the manuscript. Q. Z., H. D., X. M. and H. F. structured this review. X. C., J. S., L. L. and X. Z. provided key advice and supervised the preparation of the text.

Conflicts of interest

There are no conflicts to declare.

Acknowledgments

This work was supported by the National Natural Science Foundation of China (52202286 and 22309002), the open research fund of the Guangxi Key Laboratory of Advanced Structural Materials and Carbon Neutralization (GXAMCN25-1), the Natural Science Foundation of Zhejiang Provincial (LY24B030006), the Science and Technology Plan Project of Wenzhou Municipality (ZG2024055), the China National Postdoctoral Program for Innovative Talents (BX20250118), the Anhui Postdoctoral Scientific Research Program Foundation (2025B1045), the Fundamental Research Funds of Zhejiang Sci-Tech University (26202157-Y), the Qingchuang Technology Support Program of the University in Shandong Province (2024KJH080), the Shandong Provincial Natural Science Foundation (ZR2024MB153), and the Yantai Science and Technology Innovation Development Program (Basic Research Category, 2024JCYJ042).

Data availability

No primary research results, software or code have been included and no new data were generated or analysed as part of this review.

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