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NASICON
NASICON
NASICON
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2×2 unit cell of Na3Zr2(SiO4)2(PO4) (x = 2), which is the most common NASICON material;[1] red: O, purple: Na, light green: Zr, dark green: sites shared by Si and P
One unit cell of Na2Zr2(SiO4)(PO4)2 (x = 1); red: O, purple: Na, light green: Zr, dark green: sites shared by Si and P

NASICON is an acronym for sodium (Na) super ionic conductor, which usually refers to a family of solids with the chemical formula Na1+xZr2SixP3−xO12, 0 < x < 3. In a broader sense, it is also used for similar compounds where Na, Zr and/or Si are replaced by isovalent elements. NASICON compounds have high ionic conductivities, on the order of 10−3 S/cm, which rival those of liquid electrolytes. They are caused by hopping of Na ions among interstitial sites of the NASICON crystal lattice.[2]

Properties

[edit]

The crystal structure of NASICON compounds was characterized in 1968. It is a covalent network consisting of ZrO6 octahedra and PO4/SiO4 tetrahedra that share common corners. Sodium ions are located at two types of interstitial positions. They move among those sites through bottlenecks, whose size, and thus the NASICON electrical conductivity, depends on the NASICON composition, on the site occupancy,[3] and on the oxygen content in the surrounding atmosphere. The conductivity decreases for x < 2 or when all Si is substituted for P in the crystal lattice (and vice versa); it can be increased by adding a rare-earth compound to NASICON, such as yttria.[1]

NASICON materials can be prepared as single crystals, polycrystalline ceramic compacts, thin films or as a bulk glass called NASIGLAS. Most of them, except NASIGLAS and phosphorus-free Na4Zr2Si3O12, react with molten sodium at 300 °C, and therefore are unsuitable for electric batteries that use sodium as an electrode.[2] However, a NASICON membrane is being considered for a sodium-sulfur battery where the sodium stays solid.

Development and potential applications

[edit]

The main application envisaged for NASICON materials is as the solid electrolyte in a sodium-ion battery. Some NASICONs exhibit a low thermal expansion coefficient (< 10−6 K−1), which is useful for precision instruments and household ovenware. NASICONs can be doped with rare-earth elements, such as Eu, and used as phosphors. Their electrical conductivity is sensitive to molecules in the ambient atmosphere, a phenomenon that can be used to detect CO2, SO2, NO, NO2, NH3 and H2S gases. Other NASICON applications include catalysis, immobilization of radioactive waste, and sodium removal from water.[2]

The development of sodium-ion batteries is important since it makes use of an earth-abundant material and can serve as an alternative to lithium-ion batteries which are experiencing ever-increasing demand despite the limited availability of lithium. Developing high-performance sodium-ion batteries is a challenge because it is necessary to develop electrodes that meet the requirements of high-energy density and high cycling stability while also being cost-efficient. NASICON-based electrode materials are known for their wide range of electrochemical potentials, high ionic conductivity, and most importantly their structural and thermal stabilities.[4] NASICON-type cathode materials for sodium-ion batteries have a mechanically robust three-dimensional (3D) framework with open channels that endow it with the capability for fast ionic diffusion.[5] A strong and lasting structural framework allows for repeated Na+
 ion de-/insertions with relatively high operating potentials. Its high safety, high potential, and low volume change make NASICON a promising candidate for sodium-ion battery cathodes.[6]

NASICON cathodes typically suffer from poor electrical conductivity and low specific capacity which severely limits their practical applications. Efforts to enhance the movement of electrons, or electrical conductivity, include particle downsizing[7] and carbon-coating[8] which have both been reported to improve the electrochemical performance.

It is important to consider the relationship between lattice parameters and activation energy as the change in lattice size has a direct influence on the size of the pathway for Na+
 conduction as well as the hopping distance of the Na+
 ions to the next vacancy. A large hopping distance requires a high activation energy.[9]

NASICON-phosphate Na
3V
2(PO
4)
3 compounds are considered promising cathodes with a theoretical specific energy of 400 W h kg−1. Vanadium-based compounds exhibit satisfactory high energy densities that are comparable to those of lithium-ion batteries as they operate through multi-electron redox reactions (V3+/V4+ and V4+/V5+) and a high operating voltage.[10] The use of vanadium is toxic and expensive which introduces a critical issue in real applications. This concern holds true for other electrodes based on costly 3d transition metal elements such as Ni- or Co-based electrodes. The most abundant and non-toxic 3d element, iron, is the favored choice as the redox center in the polyanionic or mixed-polyanion system.[11]

Lithium analogues

[edit]

Some lithium phosphates also possess the NASICON structure and can be considered as the direct analogues of the sodium-based NASICONs.[12] The general formula of such compounds is LiM
2(PO
4)
3, where M identifies an element like titanium, germanium, zirconium, hafnium, or tin.[2][13] Similarly to sodium-based NASICONs, lithium-based NASICONs consist of a network of MO6 octahedra connected by PO4 tetrahedra, with lithium ions occupying the interstitial sites among them.[14] Ionic conduction is ensured by lithium hopping among adjacent interstitial sites.[14]

Lithium NASICONs are promising materials to be used as solid electrolytes in all-solid-state lithium-ion batteries.[15]

Relevant examples

[edit]

The most investigated lithium-based NASICON materials are LiZr
2(PO
4)
3, LiTi
2(PO
4)
3,[2] and LiGe
2(PO
4)
3.[16]

Lithium zirconium phosphate

[edit]

Lithium zirconium phosphate, identified by the formula LiZr
2(PO
4)
3 (LZP), has been extensively studied because of its polymorphism and interesting conduction properties.[2][17] At room temperature, LZP has a triclinic crystal structure (C1) and undergoes a phase transition to rhombohedral crystal structure (R3c) between 25 and 60 °C.[17] The rhombohedral phase is characterized by higher values of ionic conductivity (8×10−6 S/cm at 150 °C) compared to the triclinic phase (≈ 8×10−9 S/cm at room temperature):[17] such difference may be ascribed to the peculiar distorted tetrahedral coordination of lithium ions in the rhombohedral phase, along with the large number of available empty sites.[2]

The ionic conductivity of LZP can be enhanced by elemental doping, for example replacing some of the zirconium cations with lanthanum,[17] titanium,[2] or aluminium[18][19] atoms. In case of lanthanum doping, the room-temperature ionic conductivity of the material approaches 7.2×10−5 S/cm.[17]

Lithium titanium phosphate

[edit]

Lithium titanium phosphate, with general formula LiTi
2(PO
4)
3 (LTP or LTPO), is another lithium-containing NASICON material in which TiO6 octahedra and PO4 tetrahedra are arranged in a rhombohedral unit cell.[16] The LTP crystal structure is stable down to 100 K and is characterized by a small coefficient of thermal expansion.[16] LTP shows low ionic conductivity at room temperature, around 10−6 S/cm;[12] however, it can be effectively increased by elemental substitution with isovalent or aliovalent elements (Al, Cr, Ga, Fe, Sc, In, Lu, Y, La).[12][16][20] The most common derivative of LTP is lithium aluminium titanium phosphate (LATP), whose general formula is Li
1+xAl
xTi
2-x(PO
4)
3.[16] Ionic conductivity values as high as 1.9×10−3 S/cm can be achieved when the microstructure and the aluminium content (x = 0.3 - 0.5) are optimized.[12][16] The increase of conductivity is attributed to the larger number of mobile lithium ions necessary to balance the extra electrical charge after Ti4+ replacement by Al3+, together with a contraction of the c axis of the LATP unit cell.[16][20]

In spite of attractive conduction properties, LATP is highly unstable in contact with lithium metal,[16] with formation of a lithium-rich phase at the interface and with reduction of Ti4+ to Ti3+.[15] Reduction of tetravalent titanium ions proceeds along a single-electron transfer reaction:[21]

Both phenomena are responsible for a significant increase of the electronic conductivity of the LATP material (from 3×10−9 S/cm to 2.9×10−6 S/cm), leading to the degradation of the material and to the ultimate cell failure if LATP is used as a solid electrolyte in a lithium-ion battery with metallic lithium as the anode.[15]

Lithium germanium phosphate

[edit]
LGP crystal structure.[22]

Lithium germanium phosphate, LiGe
2(PO
4)
3 (LGP), is closely similar to LTP, except for the presence of GeO6 octahedra instead of TiO6 octahedra in the rhombohedral unit cell.[16] Similarly to LTP, the ionic conductivity of pure LGP is low and can be improved by doping the material with aliovalent elements like aluminium, resulting in lithium aluminium germanium phosphate (LAGP), Li
1+xAl
xGe
2-x(PO
4)
3.[16] Contrary to LGP, the room-temperature ionic conductivity of LAGP spans from 10−5 S/cm up to 10−3 S/cm,[20] depending on the microstructure and on the aluminium content, with an optimal composition for x ≈ 0.5.[13] In both LATP and LAGP, non-conductive secondary phases are expected for larger aluminium content (x > 0.5 - 0.6).[16]

LAGP is more stable than LATP against lithium metal anode, since the reduction reaction of Ge4+ cations is a 4-electron reaction and has a high kinetic barrier:[21]

However, the stability of the lithium anode-LAGP interface is still not fully clarified and the formation of detrimental interlayers with subsequent battery failure has been reported.[23]

Application in lithium-ion batteries

[edit]

Phosphate-based materials with a NASICON crystal structure, especially LATP and LAGP, are good candidates as solid-state electrolytes in lithium-ion batteries,[16] even if their average ionic conductivity (≈10−5 - 10−4 S/cm) is lower compared to other classes of solid electrolytes like garnets and sulfides.[15] However, the use of LATP and LAGP provides some advantages:

  • Excellent stability in humid air and against CO2, with no release of harmful gases or formation of Li2CO3 passivating layer;[15]
  • High stability against water;[16]
  • Wide electrochemical stability window and high voltage stability, up to 6 V in the case of LAGP, enabling the use of high-voltage cathodes;[23]
  • Low toxicity compared to sulfide-based solid electrolytes;[16]
  • Low cost and easy preparation.[16]

A high-capacity lithium metal anode could not be coupled with a LATP solid electrolyte, because of Ti4+ reduction and fast electrolyte decomposition;[15] on the other hand, the reactivity of LAGP in contact with lithium at very negative potentials is still debated,[21] but protective interlayers could be added to improve the interfacial stability.[23]

Considering LZP, it is predicted to be electrochemically stable in contact with metallic lithium; the main limitation arises from the low ionic conductivity of the room-temperature triclinic phase.[18] Proper elemental doping is an effective route to both stabilize the rhombohedral phase below 50 °C and improve the ionic conductivity.[18]

See also

[edit]

References

[edit]
Revisions and contributorsEdit on WikipediaRead on Wikipedia

NASICON

View on Grokipedia
from Grokipedia
NASICON, an for Sodium Super Ionic CONductor, is a class of phosphate-based inorganic solid electrolytes characterized by their rhombohedral and exceptional sodium-ion conductivity, typically ranging from 0.1 to 1.2 mS cm⁻¹ at , enabling efficient ion transport through a three-dimensional framework of polyanions and metal cations. The prototypical composition follows the general formula Na₁₊ₓZr₂SiₓP₃₋ₓO₁₂ (0 ≤ x ≤ 3), where the rigid skeletal array of ZrO₆ octahedra interconnected by PO₄ and SiO₄ tetrahedra provides pathways for mobile Na⁺ ions while maintaining high chemical and electrochemical stability. These materials were first reported in 1976 by H.Y.-P. Hong, who described their crystal structures in compounds like Na₃Zr₂Si₂PO₁₂. Concurrently, J.B. Goodenough and colleagues explored skeleton structures for rapid Na⁺ transport, confirming conductivities up to 10⁻³ S cm⁻¹ and emphasizing the role of the open lattice in facilitating superionic behavior. This discovery built on earlier interest in electrolytes for applications, positioning NASICON as a benchmark for sodium-based systems due to its thermal stability up to 1000°C and compatibility with sodium metal anodes. NASICON electrolytes have become central to the development of all-solid-state sodium-ion batteries, offering advantages over electrolytes such as enhanced , reduced flammability, and longer cycle life, with recent doping strategies (e.g., with Sc or Hf) achieving conductivities exceeding 1 mS cm⁻¹ at 25°C. Beyond batteries, they serve in sodium-sulfur cells, ion-selective membranes, and gas sensors, leveraging their wide (up to 5 V vs. Na/Na⁺) and mechanical robustness. Ongoing research focuses on optimizing synthesis methods like solid-state reactions or tape casting to minimize resistance and improve scalability for commercial .

History and Development

Early Discovery

The rhombohedral structure of compounds with the general formula NaM₂(PO₄)₃, where M is a tetravalent cation such as Ge, Ti, or Zr, was first synthesized and characterized in 1968 by researchers at the . Lars-Olof Hagman and Per Kierkegaard reported the preparation of NaZr₂(PO₄)₃, NaTi₂(PO₄)₃, and NaGe₂(PO₄)₃ through solid-state reactions, determining their crystal structures via . These materials exhibited a three-dimensional framework of corner-sharing PO₄ tetrahedra and MO₆ octahedra, forming open channels that could potentially accommodate mobile ions, though their ionic conductivity was not extensively investigated at the time. The discovery of exceptional sodium-ion conductivity in these phosphate frameworks occurred in 1976, marking the birth of NASICON (sodium superionic conductor) materials. H.Y.-P. Hong at the synthesized a series Na₁₊ₓZr₂SiₓP₃₋ₓO₁₂ (0 ≤ x ≤ 3) by partially substituting Si⁴⁺ for P⁵⁺, which expanded the framework and increased the sodium content, thereby enhancing Na⁺ mobility. This compositional tuning resulted in bulk conductivities approaching 10⁻³ S/cm at for x ≈ 2, comparable to liquid electrolytes, due to the percolating three-dimensional pathways for Na⁺ diffusion. Concurrently, J.B. Goodenough, Hong, and J.A. Kafalas explored the structural rationale for this fast-ion transport, emphasizing the rigid skeletal framework that maintains stability while allowing rapid Na⁺ hopping between interstitial sites. Their work coined the term "NASICON" and highlighted the material's potential for solid-state sodium batteries, sparking widespread interest in phosphate-based superionic conductors. These seminal studies laid the foundation for subsequent optimizations, demonstrating how subtle doping could achieve superionic behavior without compromising the host lattice integrity.

Key Advancements

Following the initial discovery of NASICON materials in , subsequent research focused on optimizing the composition to enhance sodium-ion mobility and conductivity. In the late and early 1980s, variations in the Si/P ratio within the general formula Na_{1+x}Zr_2Si_xP_{3-x}O_{12} (0 ≤ x ≤ 3) were explored, with x ≈ 2 yielding the highest room-temperature conductivity of approximately 10^{-3} S cm^{-1}, attributed to an optimal balance of framework rigidity and interstitial sites for Na^{+} hopping. These refinements built on the rhombohedral structure, enabling faster ion transport through enlarged bottlenecks in the diffusion pathways. A major advancement in the 1980s and 1990s involved aliovalent doping to stabilize the structure and increase Na^{+} vacancy concentration. For instance, partial substitution of Zr^{4+} with lower-valence cations like Al^{3+} or Sc^{3+} in compositions such as Na_{1+x}Zr_{2-x}M_xSi_xP_{3-x}O_{12} (M = Al, Sc) improved bulk conductivity by up to an order of magnitude, reaching 10^{-3} S cm^{-1} at room temperature, while reducing grain boundary resistance. In the 2000s, yttrium doping emerged as a high-impact strategy, with Na_3Zr_{1.88}Y_{0.12}Si_2PO_{12} demonstrating a conductivity of 2.7 × 10^{-3} S cm^{-1} at due to enhanced phase purity and reduced impedance. By the , these doped NASICONs were integrated into prototype all-solid-state sodium batteries, such as those pairing Na_3Zr_2Si_2PO_{12} with Na_3V_2(PO_4)_3 cathodes, enabling stable cycling and paving the way for practical applications. Co-doping strategies in the , such as with Sc and Ge, have achieved conductivities up to 4.6 × 10^{-3} S cm^{-1} at , emphasizing interfacial engineering for device-level performance.

Structure and Composition

Crystal Structure

NASICON materials possess a rhombohedral crystal structure with space group R3‾cR\overline{3}c, consisting of a three-dimensional open framework that facilitates high sodium-ion mobility. This structure was first elucidated through crystallographic studies on compositions such as \ceNa1+xZr2SixP3−xO12\ce{Na1+xZr2SixP3-xO12} (0 ≤ x ≤ 3), revealing a rigid skeleton formed by corner-sharing \ceMO6\ce{MO6} octahedra and \ceXO4\ce{XO4} tetrahedra, where M typically denotes Zr or Ti and X represents P or Si. The framework creates interconnected channels for Na⁺ ions, with the octahedra linking to form chains along the c-axis and the tetrahedra bridging these chains to yield a stable, skeletal architecture. Within the unit cell, sodium ions occupy two primary crystallographic sites: the 6b site, located at the center of the framework cavities with high coordination, and the 18e site, positioned in the interstitial spaces along the diffusion pathways. These sites enable three-dimensional Na⁺ percolation through triangular bottlenecks (T1 and T2), where the T1 bottleneck involves a smaller cross-section for inter-cavity hopping. The ideal structure assumes undistorted polyhedra, but real compositions exhibit distortions due to cation size mismatches and compositional variations, influencing lattice parameters (e.g., a ≈ 9.0–9.5 Å, c ≈ 22.0–23.0 Å in rhombohedral setting). At lower temperatures or specific stoichiometries (e.g., Na₃Zr₂Si₂PO₁₂), the can transition to a monoclinic phase with C2/c, where the Na(2) site splits into two distinct positions, slightly distorting the framework and potentially reducing ionic conductivity. This arises from ordering of Na⁺ ions and framework tilting, but the high-temperature rhombohedral form remains dominant for superionic applications. The versatility of the allows substitution at M and X sites (e.g., M = Fe, Sc; X = Ge, ), maintaining the core topology while tuning properties like thermal stability.

General Formula and Variations

The general formula for NASICON (Sodium Super Ionic CONductor) materials is Na1+x_{1+x}Zr2_2Six_xP3−x_{3-x}O12_{12}, where 0≤x≤30 \leq x \leq 3. This composition derives from the parent compound NaZr2_2P3_3O12_{12} (x=0x=0), with silicon substitution for phosphorus enabling tunable sodium content and ionic conductivity. The structure accommodates interstitial sodium ions in rhombohedral channels, facilitating fast Na+^+ diffusion. NASICON can be broadly represented as Nax_xM2_2(AO4_4)3_3, where M denotes transition or main-group metal cations (e.g., tetravalent Zr4+^{4+}, Ti4+^{4+}, or trivalent Sc3+^{3+}) and A is tetrahedral anions like P5+^{5+} or Si4+^{4+}. This framework allows compositional flexibility, with sodium stoichiometry xx ranging from 1 to 4 depending on charge balance from substitutions. For instance, the archetypal NASICON Na3_3Zr2_2Si2_2PO12_{12} (x=2x=2) exhibits high Na+^+ conductivity due to optimized interstitial sites. Variations often involve partial substitution of Zr or the Si/P framework to enhance stability or conductivity. Scandium-doped variants, such as Na3+x_{3+x}Sc2_2Six_xP3−x_{3-x}O12_{12} (x=0.2−0.8x=0.2-0.8), improve sinterability and reduce grain boundary resistance. Manganese-based NASICONs, like Na1−4_{1-4}M'M''(PO4_4)3_3 with M' = Mn2+^{2+}, offer cost-effective alternatives but require careful phase control to avoid impurities. Recent high-entropy designs, such as Nax_x(Mn,Fe,Ti,Nb)2_2(PO4_4)3_3, incorporate multiple cations at M sites to improve phase stability and ionic pathways. These modifications prioritize electrochemical compatibility in batteries, with seminal studies emphasizing defect for optimal ion pathways.

Properties

Ionic Conductivity

NASICON materials, known as sodium super ionic conductors, exhibit high ionic conductivity for Na⁺ ions due to their three-dimensional framework structure, which provides open pathways for ion migration. The prototype compound, Na₁₊ₓZr₂SiₓP₃₋ₓO₁₂ (0 ≤ x ≤ 3), was first reported in 1976, achieving a conductivity of approximately 0.2 S cm⁻¹ at 300 °C for x = 2, marking a significant advancement in solid electrolytes for sodium-ion transport. This high conductivity arises from the rhombohedral (R-3c) , where Na⁺ ions occupy interstitial sites connected by triangular bottlenecks, enabling fast with activation energies typically below 0.3 eV. The ion transport mechanism in NASICON involves correlated Na⁺ hopping through a percolating network of channels, rather than isolated jumps, which lowers the energy barrier and enhances mobility at elevated temperatures. At , undoped Na₃Zr₂Si₂PO₁₂ displays a bulk conductivity of about 0.67 mS cm⁻¹, but total conductivity is often limited by grain boundaries, contributing up to 50% of the resistance in polycrystalline samples. Doping strategies, such as partial substitution of Zr⁴⁺ with trivalent (e.g., Sc³⁺) or pentavalent (e.g., Nb⁵⁺) cations, increase the Na⁺ concentration to optimize site occupancy (ideally 3.3–3.55 Na per ) and enlarge bottleneck sizes, thereby boosting room-temperature conductivity to values exceeding 5 mS cm⁻¹ in compositions like Na₃.₃Zr₁.₉Nb₀.₁Si₂.₄P₀.₆O₁₂. Factors influencing conductivity include the Si/P ratio, with higher silicate content generally improving Na⁺ mobility by expanding the lattice and reducing phonon scattering, though excessive substitution (x > 2) can lead to phase instability. Sintering aids like NaF enhance densification, reducing grain boundary impedance and achieving relative densities over 95%, which correlates positively with overall conductivity. Recent computational and experimental efforts, including density functional theory-guided doping, have identified optimal cation radii around 0.72 Å for the B-site (e.g., Sc, Mg), yielding conductivities up to 1.2 mS cm⁻¹ at 25 °C in Na₃.₄Hf₀.₆Sc₀.₄ZrSi₂PO₁₂. These enhancements position NASICON as a competitive solid electrolyte, surpassing traditional sodium β-alumina in chemical stability while maintaining comparable or superior ionic performance.

Chemical and Thermal Stability

NASICON-type materials, particularly Na1+xZr2SixP3-xO12 (NZSP), exhibit robust that supports their use as solid electrolytes in sodium-based batteries. They demonstrate kinetic stability against sodium metal anodes despite thermodynamic instability, forming a self-limiting solid electrolyte interphase (SEI) with decomposition products such as Na4SiO4, Na2ZrO3, Na3P, and ZrSi, which limits further reactivity. The electrochemical stability window spans approximately 1.11–3.41 V versus Na+/Na, with oxidation stability extending beyond 5.0 V due to sluggish kinetics, enabling compatibility with high-voltage cathodes like NaxCoO2 and Na3V2(PO4)3. Additionally, NZSP shows resistance to moisture and humid air, as well as stability in aqueous environments, attributed to the robust phosphate-based framework. The chemical stability is further enhanced by compositional variations, such as substitutions with rare-earth elements or other cations, which maintain the rhombohedral structure while improving interface compatibility with electrodes and reducing dendrite formation. Reaction energies with sodium are relatively low at -0.27 eV/atom, lower than those for thiophosphate (-1.25 eV/atom) or LiPON (-0.66 eV/atom) electrolytes, contributing to safer operation. However, challenges arise at interfaces, where strategies like thin interlayers (e.g., Au or ) are employed to minimize impedance and enhance long-term stability during sodium /stripping. Thermally, NASICON materials display high stability, with phase transitions from monoclinic to rhombohedral occurring at 420–450 (147–177 °C), beyond which the rhombohedral phase predominates for optimal ionic conduction. They withstand temperatures up to 1200 °C without , though sodium loss can occur during prolonged high-temperature annealing, necessitating controlled atmospheres. This resilience supports applications at elevated temperatures, such as up to 300 °C, where ionic conductivity remains viable (e.g., 0.2–0.4 S cm-1 for related beta-alumina analogs), and enables robust performance in demanding environments. Overall, the combination of chemical and stability underscores NASICON's suitability for safe, durable solid-state sodium batteries.

Synthesis Methods

Solid-State Reactions

Solid-state reactions represent a conventional and widely adopted method for synthesizing NASICON materials, particularly the archetypal composition Na₃Zr₂Si₂PO₁₂ (NZSP), through high-temperature of solid precursors. This dry synthesis route involves intimate mixing of stoichiometric oxide or carbonate precursors, followed by controlled thermal treatment to promote phase formation and densification, yielding ceramics with rhombohedral structure suitable for solid electrolytes. Typical precursors include (Na₂CO₃), (ZrO₂), (SiO₂), and (NH₄H₂PO₄), often mixed in a molar ratio of 1.5:2:2:1 to account for the decomposition of NH₄H₂PO₄ into equivalents. The process begins with mechanical mixing, such as wet ball milling in or isopropanol using zirconia media at 250–300 rpm for 4–12 hours, to ensure homogeneity and reduce particle agglomeration. The mixture is then dried at 80°C and pre-calcined at 400–600°C for 4–5 hours to decompose volatile components like carbonates and salts, followed by grinding and a higher-temperature at 1100–1200°C for 4–12 hours to form the NASICON phase. Pellets are pressed uniaxially or isostatically (250–3000 MPa) and sintered at 1125–1300°C for 10–40 hours in air or inert atmospheres like , with heating rates of 5°C/min to minimize defects. Optimizations in solid-state synthesis significantly influence microstructure and ionic performance. Using nanoparticle precursors (e.g., ZrO₂ with surface areas >6 m²/g) enhances reaction kinetics, leading to finer grains (2–4 μm), higher relative densities (up to 96%), and improved Na⁺ conductivity compared to macroscale powders. Incorporating 5–10% excess sodium (e.g., via additional Na₂CO₃) compensates for volatilization losses during sintering, promoting phase purity and boosting room-temperature conductivity to ~4.7 × 10⁻⁴ S/cm for NZSP sintered at 1175°C. Prolonged sintering (e.g., 40 hours at 1230°C) further densifies the material, achieving conductivities as high as 1.16 × 10⁻³ S/cm, though excessive duration risks grain coarsening. Despite its simplicity and scalability, solid-state synthesis faces challenges such as the formation of secondary phases like monoclinic ZrO₂ due to incomplete reactions or Na/P evaporation, which can degrade conductivity to below 10⁻⁴ S/cm if not mitigated by precise and atmosphere control. Doping strategies, such as aliovalent substitution with Sc³⁺ or Al³⁺ during precursor mixing, have been integrated into this method to expand the NASICON stability window and enhance conductivity up to 1.2 mS/cm in variants like Na₃.₄Hf₀.₆Sc₀.₄ZrSi₂PO₁₂. Overall, this approach remains foundational for producing high-performance NASICON electrolytes, balancing cost-effectiveness with the need for rigorous parameter tuning.

Solution-Based Techniques

Solution-based techniques for synthesizing NASICON materials, such as Na₃Zr₂Si₂PO₁₂, offer advantages over traditional solid-state reactions by enabling atomic-level mixing of precursors, lower processing temperatures, and improved phase purity and homogeneity. These methods typically involve dissolving metal salts or alkoxides in solvents to form sols or precipitates, followed by gelation, drying, , and . They are particularly useful for producing fine powders that enhance densification and ionic conductivity in the final ceramics. The sol-gel method is a prominent solution-based approach, where precursors like zirconium propoxide, , , and are mixed in alcohols such as and to form a sol at controlled pH (around 3.0). The sol undergoes and to form a , which is then dried, calcined at temperatures like 750–800 °C for 1 hour, and sintered at 1000–1200 °C for 6–10 hours. This process yields high- discs with relative densities up to 95% and minimizes impurities when is slow, resulting in nearly pure monoclinic NASICON phases. Ionic conductivities achieved can reach 1.7 × 10⁻³ S cm⁻¹ at 25 °C when combined with spark plasma sintering (SPS), surpassing conventional due to nanoscale grain sizes and higher density. However, rapid may introduce zirconia impurities, reducing phase purity compared to other wet methods. Co-precipitation is another effective technique, involving the simultaneous precipitation of NASICON precursors from a solution of sodium, , , and sources (e.g., NaOH, Zr(OC₃H₇)₄, Si(OC₂H₅)₄, and NH₄H₂PO₄) in ethanol-water mixtures under stirring. The precipitate is filtered, washed, dried, at 800 °C, and sintered, often at 1000 °C for 10 hours. This method provides superior phase purity with minimal residual zirconia, higher crystallinity at lower calcination temperatures (e.g., 900 °C), and better powder reactivity than sol-gel, leading to denser ceramics. For Na₃Zr₂Si₂PO₁₂, co-precipitation followed by SPS has demonstrated ionic conductivities of 1.7 × 10⁻³ S cm⁻¹ at , attributed to intimate precursor mixing and reduced resistance. It is scalable and cost-effective for producing nanostructured powders suitable for solid electrolytes. Both methods lower the required temperatures compared to solid-state synthesis (typically >1200 °C), promoting energy efficiency and preserving sodium volatility, while enabling doping variations for optimized conductivity. For instance, sol-gel synthesis of Na₃Zr₂Si₂PO₁₂ at 1050 °C with excess sodium flux yields phase-pure materials with conductivities around 10⁻⁴ S cm⁻¹ at . These techniques have been pivotal in advancing NASICON for applications by improving microstructural control.

Applications in Energy Storage

Solid Electrolytes for Sodium-Ion Batteries

NASICON-type materials, with the general formula Na1+xZr2SixP3-xO12 (0 ≤ x ≤ 3), were first reported as sodium superionic conductors in and have emerged as leading candidates for electrolytes in all-solid-state sodium-ion batteries (ASSBs) due to their three-dimensional framework that facilitates fast Na+ . The archetypal composition, Na3Zr2Si2PO12 (often abbreviated as NZSP or NSP), exhibits a rhombohedral structure ( R-3c) composed of ZrO6 octahedra linked by PO4 and SiO4 tetrahedra, forming interstitial sites for Na+ ions that enable isotropic conduction pathways with low energies around 0.3 eV. This structure provides room-temperature Na+ conductivities typically in the range of 0.5–1 mS cm-1, comparable to liquid electrolytes, making NASICON suitable for replacing flammable organic solvents in sodium-ion systems to enhance and . The electrochemical stability of NASICON electrolytes is a key advantage for ASSBs, with a wide stability window of approximately 1.1–3.4 V versus Na/Na+, allowing compatibility with sodium metal anodes and common cathodes like Na32(PO4)3 without significant decomposition. Kinetically, a stable solid (SEI) forms on the NASICON surface in contact with sodium metal, preventing penetration and enabling reversible Na plating/stripping for over 200 hours in symmetric cells. However, challenges persist at electrode-electrolyte interfaces, where poor leads to high impedances (often >1000 Ω cm2); strategies such as applying ion-conducting interlayers (e.g., Na3PO4 or coatings) or adopting 3D scaffold designs have reduced these resistances to below 100 Ω cm2, improving overall cell performance. Doping and compositional tuning further optimize NASICON for battery applications, with substitutions like Sc3+ for Zr4+ or increased silicate content boosting conductivities up to 1.2–5.5 mS cm-1 at 25°C by enlarging conduction channels and reducing bottleneck sizes. In practical ASSBs, NASICON-based cells with Na3V2(PO4)3 cathodes have demonstrated capacities of ~110 mAh g-1 at 0.2C rates, retaining over 90% after 10,000 cycles, highlighting their potential for long-life, high-rate sodium storage. Thermal stability up to 1000°C also supports operation in elevated-temperature environments, though grain boundary resistance and moisture sensitivity remain areas for refinement through advanced sintering aids.
CompositionDopant/SubstitutionRoom-Temperature Conductivity (mS cm-1)Reference
Na3Zr2Si2PO12None0.67
Na3.4Hf0.6Sc0.4ZrSi2PO12Sc for Zr1.2
Na3.3Zr1.9Nb0.1Si2.4P0.6O12Nb for Zr5.5

Cathode Materials

NASICON-type materials, particularly polyanionic phosphates, serve as promising cathode candidates for due to their three-dimensional open frameworks, which enable fast Na⁺ diffusion channels and superior structural stability during repeated sodiation/desodiation cycles. These frameworks, composed of corner-sharing PO₄ tetrahedra and octahedra, minimize volume changes (typically <5%) and provide high thermal and chemical stability, making them suitable for high-power and long-life applications. A prototypical example is Na₃V₂(PO₄)₃, which exhibits a theoretical specific capacity of 117.6 mAh g⁻¹ based on the reversible extraction/insertion of one Na⁺ per formula unit at an average voltage of 3.4 V versus Na/Na⁺. This material benefits from a high Na⁺ ionic conductivity of approximately 10⁻³ S cm⁻¹ at room temperature, though its intrinsic electronic conductivity is low (∼1.6 × 10⁻⁶ S cm⁻¹), often necessitating modifications like carbon coating or nanostructuring to enhance rate performance. Recent advances include ion doping and composite formation; for instance, Cr and Fe co-doping in Na₃V₁.₅Cr₀.₄Fe₀.₁(PO₄)₃ improves electronic conductivity and stabilizes the structure, delivering ∼71 mAh g⁻¹ at an ultrahigh rate of 100 C and retaining 95% capacity over 10,000 cycles. Iron-based NASICON variants offer cost-effective alternatives, leveraging abundant Fe precursors. Na₄Fe₃(PO₄)₂(P₂O₇), a pyrophosphate-modified structure, provides an operating voltage of ∼3.0 V and achieves 80.3 mAh g⁻¹ at 20 C, with 69% capacity retention after 4,400 cycles, attributed to its air stability and low volume expansion (∼4%). Compositional tuning across NaₓMM′(PO₄)₃ (where M, M′ are 3d transition metals like V, Fe, Mn) allows tailoring of redox potentials from 2.5–4.0 V, enabling multi-voltage platforms for higher energy density, though challenges like phase instability in Ni/Co-rich variants persist. Overall, these cathodes prioritize safety and sustainability over layered oxide counterparts, with ongoing research focusing on high-entropy designs to further boost voltage windows and cycle life beyond 100 mAh g⁻¹ at practical rates.

Lithium-Based Analogues

Composition and Examples

Lithium-based analogues of materials are phosphate-based solid electrolytes characterized by a rhombohedral structure that facilitates fast lithium-ion conduction through interconnected channels formed by PO₄ tetrahedra and MO₆ octahedra, where M is a tetravalent cation. The general composition follows the formula LiM₂(PO₄)₃, with M typically Ti, Ge, Zr, or Hf, enabling high ionic mobility due to the open framework similar to sodium but adapted for Li⁺ ions. These structures were first synthesized via solid-state reactions in 1986, demonstrating initial lithium-ion conductivities on the order of 10⁻⁵ S cm⁻¹. To improve conductivity and stability, partial substitution with trivalent cations such as Al³⁺ or Sc³⁺ is commonly employed, yielding compositions like Li_{1+x}M'xM{2-x}(PO₄)₃ (where M' is the trivalent dopant and 0 < x ≤ 0.5). This doping increases the lithium content and creates vacancies that enhance ion hopping. A seminal example is LiTi₂(PO₄)₃ (LTP), which exhibits a total room-temperature conductivity of approximately 10⁻⁵ S cm⁻¹ (bulk ~10⁻³ S cm⁻¹) and serves as a baseline for further modifications, as reported in early electrochemical studies. Prominent doped variants include Li_{1.3}Al_{0.3}Ti_{1.7}(PO₄)₃ (LATP), introduced through partial replacement of Ti⁴⁺ with Al³⁺ to achieve bulk conductivities up to 10^{-3} S cm⁻¹ at room temperature, making it suitable for thin-film applications in solid-state batteries. Another key example is Li_{1.5}Al_{0.5}Ge_{1.5}(PO₄)₃ (LAGP), a glass-ceramic form with total conductivity around 10^{-4} S cm⁻¹, valued for its chemical stability against moisture and ease of processing via melt-quenching. Zirconium-based analogues, such as LiZr₂(PO₄)₃ and its Al-doped derivative Li_{1+x}Al_xZr_{2-x}(PO₄)₃ (LAZP), offer enhanced electrochemical windows up to 6 V vs. Li/Li⁺ but lower conductivities (∼10^{-5} S cm⁻¹) without further optimization, highlighting trade-offs in stability versus ion transport. These examples underscore the versatility of lithium analogues, with ongoing refinements focusing on partial silicate substitution to lower sintering temperatures while maintaining phase purity. Recent advancements as of 2025 include arsenic doping in LATP frameworks, such as Li_{1.3+x}Al_{0.3}As_x Ti_{1.7-x}(PO₄)₃, achieving conductivities exceeding 10^{-3} S cm^{-1}, and high-entropy designs incorporating multiple cations for improved ionic transport and stability.

Applications in Lithium-Ion Batteries

Lithium-based NASICON analogues, such as Li₁.₃Al₀.₃Ti₁.₇(PO₄)₃ (LATP) and Li₁.₅Al₀.₅Ge₁.₅(PO₄)₃ (LAGP), serve primarily as solid electrolytes in all-solid-state lithium-ion batteries (ASSLIBs), enabling enhanced safety, higher energy density (up to ~500 Wh/kg), and elimination of flammable liquid electrolytes. These materials leverage their three-dimensional framework to facilitate rapid lithium-ion transport, with room-temperature ionic conductivities typically ranging from 10⁻⁴ to 10⁻³ S/cm for optimized compositions. For instance, LATP achieves conductivities up to 7 × 10⁻⁴ S/cm at 25°C, while co-doped variants like Li₁.₅Al₀.₄Cr₀.₁Ge₁.₅(PO₄)₃ reach 6.6 × 10⁻³ S/cm, supporting stable operation in thin-film or composite forms. In ASSLIBs, these electrolytes are paired with lithium metal anodes and oxide cathodes like LiNi₀.₈Co₀.₁₅Al₀.₀₅O₂, demonstrating cycling stability exceeding 500 hours at 0.1 mA/cm² with capacities around 156 mAh/g over 50 cycles when coated with protective layers such as ZnO or Li₃PO₄ to mitigate interfacial reactions. LAGP-based electrolytes, often integrated with reduced graphene oxide (rGO)/ZnO composites, reduce interfacial resistance to ~32 Ω and enable over 800 cycles in full cells, addressing dendrite formation and poor contact issues inherent to rigid ceramic structures. Additionally, water-stable variants like Li₁.₄₅Al₀.₄₅Ge₀.₂Ti₁.₃₅(PO₄)₃ (conductivity 1.0 × 10⁻³ S/cm) function as protective coatings for lithium metal in hybrid aqueous-non-aqueous systems, preventing moisture-induced degradation. Beyond electrolytes, NASICON-type phosphates act as insertion-type cathode and anode materials in conventional lithium-ion batteries. Li₃V₂(PO₄)₃, for example, operates at ~4 V vs. Li/Li⁺ with theoretical capacities of 197 mAh/g, enhanced by carbon nanofiber coatings for high-rate performance (e.g., 100 mAh/g at 10C) and cyclability over 1000 cycles. Similarly, LiTi₂(PO₄)₃ serves as a zero-strain anode at ~2.5 V, with carbon-coated versions (LiTi₂(PO₄)₃/C) delivering ultrafast charging (capacity retention >90% at 20C) due to minimal volume change during lithiation. Doping strategies, such as Al or Sn in these frameworks, further improve electronic conductivity and stability, positioning them as viable alternatives for high-power applications. Despite these advances, challenges persist, including chemical instability with lithium metal (e.g., reduction of Ti⁴⁺ or Ge⁴⁺ to form insulating layers) and high interfacial impedance, which limit practical energy densities to below 300 Wh/kg in prototype cells. Interface engineering via of Al₂O₃ or polymer-ceramic composites has shown promise in extending cycle life, as evidenced by LATP-based cells retaining 80% capacity after 200 cycles at . Overall, these materials contribute to safer, more durable -ion systems, with ongoing research focusing on scalable synthesis for commercialization.

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