| HS Code | 116946 |
| Chemical Name | Lithium Aluminium Titanium Phosphate |
| Chemical Formula | Li1.3Al0.3Ti1.7(PO4)3 |
| Appearance | white to off-white powder |
| Crystal Structure | NASICON-type rhombohedral (space group R-3c) |
| Electrochemical Stability Window V Vs Li Li | 2.2-4.2 |
| Thermal Stability Air | stable up to approximately 800°C |
| Moisture Sensitivity | reacts with water; requires dry handling |
| Typical Particle Size D50 | 0.5-5 µm |
| Specific Surface Area M2 Per G | 5-20 |
As an accredited Lithium Aluminium Titanium Phosphate factory, we enforce strict quality protocols—every batch undergoes rigorous testing to ensure consistent efficacy and safety standards.
| Packing | 25 g in a sealed polypropylene bottle, flushed with argon and stored with desiccant to prevent moisture uptake. |
| Container Loading (20′ FCL) | 20′ FCL loading of Lithium Aluminium Titanium Phosphate, packed in sealed bags on pallets, ensuring stable, safe transport. |
| Shipping | Lithium Aluminium Titanium Phosphate is shipped as a stable, inorganic solid powder. It is packed in sealed, moisture-resistant containers to prevent hydration and contamination. No special hazardous classification applies under normal conditions, though standard handling precautions, including dust control and avoidance of inhalation, are recommended during transport and storage. |
| Storage | Store Lithium Aluminium Titanium Phosphate in a tightly sealed, airtight container in a cool, dry, well-ventilated area. Protect from moisture and humidity, as exposure may degrade its properties. Keep away from incompatible materials such as strong acids and oxidizers. Use appropriate personal protective equipment when handling. |
| Shelf Life | Store in dry, inert atmosphere; stable for up to 12 months when sealed and moisture-free. |
Lithium aluminium titanium phosphate (Li1+xAlxTi2−x(PO4)3, x 0.3–0.5) is supplied as a submicron powder with D50 0.3–1.0 µm, BET surface area 5–15 m²/g, and ionic conductivity of 1×10⁻⁴–7×10⁻⁴ S/cm after densification. The material requires vacuum drying at 180–250 °C for 12–24 h before moisture-sensitive processing; unopened packaging is stored at ≤25 °C and RH ≤20%. The application routes below are limited to lithium-ion conduction segments where the phosphate-based NASICON structure is electrochemically compatible or separated from metallic lithium by a buffer layer. REACH (EC) No 1907/2006 and RoHS Directive 2011/65/EU Annex II compliance statements are issued with each production lot.
Ceramic tape casting of LATP for lithium-metal solid-state cells operates within a sintering window of 900–980 °C; excursions above 1000 °C produce AlPO4 secondary phase and lithium volatilization that reduce ionic conductivity from typical sintered values of 1×10⁻⁴–7×10⁻⁴ S/cm at 25 °C to below 3×10⁻⁵ S/cm. A production slurry is composed of 100 parts calcined LATP powder with D50 0.3–0.5 µm, 4–7 parts PVB binder, 2–4 parts benzyl butyl phthalate plasticizer, 0.5–1.5 parts phosphate ester dispersant, and 35–50 parts anhydrous ethanol/toluene solvent blend; solids loading is controlled at 28–35 wt%. The slurry is tape-cast onto silicone-coated Mylar using a doctor blade gap of 150–300 µm, dried at 60–90 °C to green tape thickness of 50–120 µm, and then subjected to a two-step debinding schedule of 0.2 °C/min to 400 °C with a 1 h hold, followed by 0.5 °C/min to 600 °C with a 1 h hold under flowing air. Sintering at 900–980 °C for 2–6 h yields ceramic sheets with density ≥93% of theoretical density when measured by ASTM C373-18 water absorption; final thickness after surface grinding is 150–300 µm. Because LATP is thermodynamically unstable against metallic lithium, a buffer interlayer of LiF, Li3PO4, or a lithium-conducting polymer is sputtered or coated onto the separator before assembly. Production-quality systems follow ISO 9001:2015 and IATF 16949:2016; cell-level transport validation is performed under UN Manual of Tests and Criteria Part III Section 38.3, and powder handling requires REACH (EC) No 1907/2006 safety data sheet compliance plus RoHS Directive 2011/65/EU Annex II substance verification. Terminal products are dense LATP separator sheets and die-cut discs for solid-state pouch cells, high-temperature lithium metal cells, and solid-state cell qualification platforms. Pre-drying at 180–250 °C for 12–24 h is mandatory when storage relative humidity exceeds 60%, and green tape must not be exposed to RH above 35% during printing because residual water promotes lithium phosphate hydrolysis.
The upper filler loading in PEO/PVDF-HFP composite electrolyte membranes is limited by a viscosity cliff-edge: at LATP loading above 15 wt%, solvent-casting slurries exceed 5000 mPa·s at 25 °C, and slot-die coating becomes discontinuous below 0.5 m/min unless solids content is reduced below 20 wt%. A qualified free-standing electrolyte membrane formulation contains 5–25 wt% LATP, 20–35 wt% LiTFSI, 5–15 wt% succinonitrile, and 45–65 wt% polymer matrix; the LATP filler must be vacuum-dried at 200 °C for 12 h before compounding. Twin-screw extrusion uses a corotating extruder with L/D ratio of 40:1, barrel temperatures of 110–180 °C, screw speed 120–250 rpm, and a side-stuffer feed for LATP after the polymer melt seal. Dispersion is verified by laser diffraction according to ISO 13320:2020 after melt dilution; D90 must remain below 1.2 µm. Tensile properties are evaluated on Type V specimens according to ASTM D638-14 at 25 ± 2 °C: elongation at break falls below 5% when filler loading exceeds 25 wt%, producing slitting cracks; below 5 wt%, no continuous ionic percolation benefit is observed. Melt flow rate is measured by ISO 1133-1:2022 at 230 °C/2.16 kg, and the process window narrows because viscosity rises sharply above 15 wt% filler. Flame resistance is verified by UL 94 V-0 on free-standing films above 50 µm; calendered films must not shrink more than 2% at 100 °C for 1 h. Production is conducted in a dry room with dew point below −40 °C and RH below 0.5%, because LiTFSI and LATP surface hydroxyl groups generate acidic species that corrode slot-die lips. The terminal products are free-standing electrolyte membranes of 30–150 µm thickness used as polymer-ceramic separators in solid-state pouch cells, lithium-metal cells, and solid-state battery qualification stacks. REACH (EC) No 1907/2006 and RoHS Directive 2011/65/EU obligations are managed through the Article 33(1) communication pathway for components containing lithium salts.
In solid-state cathode manufacturing, LATP is mixed into NMP-based cathode slurries where the absence of liquid electrolyte requires the solid-state ion conductor to occupy ionic percolation channels between polycrystalline NMC particles. A 1 kg dry cathode batch contains 78–85 wt% NMC811 or NMC622, 10–15 wt% LATP, 2–4 wt% PVDF binder, and 3–5 wt% conductive carbon black; the LATP fraction is held below 15 wt% because aluminium and titanium dissolution into residual moisture creates acidic species that attack the 12–20 µm aluminium foil current collector during drying. Slurry viscosity at 25 °C is measured by Brookfield RV spindle 7 at 20 rpm and maintained between 3000–8000 mPa·s; 0.3–0.5 mm zirconia beads are used in a basket mill at 800–1200 rpm for 90–180 min for dispersion. The slurry is coated with a slot-die coater at 0.5–2.0 m/min, dried in a three-zone oven at 80–110–120 °C, and calendered to 3.0–3.4 g/cm³ electrode density. Coating adhesion is tested by a cross-cut method based on ASTM D3359-23 where a 5B classification is required before cell assembly. Slitting and stacking are performed under ISO 14644-1 Class 6 conditions; the dew point must remain below −40 °C because LATP adsorbs moisture rapidly and releases HF in the presence of LiPF6 during later formation cycles. The calendered cathode sheets are then laminated with a polymer or sulfide solid electrolyte; direct contact with sulfide electrolytes is avoided unless the LATP particles are surface-coated with LiNbO3, because Ti species catalyse sulfide oxidation and increase interfacial resistance. Terminal products are solid-state cathode sheets, composite cathodes for solid-state pouch cells, and dry-room-compatible electrode rolls for pilot cell lines. Cell-level transport validation under UN 38.3 applies to the assembled pouch cells; the electrode roll itself is supplied under ISO 9001:2015 and IATF 16949:2016 material traceability requirements.
Slot-die coating of LATP onto 7–12 µm PE base film uses a ceramic coating slurry with 100 parts LATP, 3–6 parts PVDF-HFP, 1–2 parts phosphate ester dispersant, and NMP to achieve 15–25 wt% solids; aqueous CMC/SBR variants are processed only within a pH range of 6.5–7.5 and a slurry age below 6 h to suppress Li+/H+ exchange and phosphate hydrolysis. The LATP fraction in the dry coating is 90–95 wt% with a particle size D50 of 0.3–0.8 µm and a specific surface area of 5–10 m²/g; particles above 1.0 µm produce die streaks at coating speeds above 40 m/min. Coating thickness is controlled to 2–5 µm per side, yielding a total separator thickness of 10–18 µm after calendering at 60–90 °C and 10–25 N/mm line pressure. The coated separator must demonstrate heat shrinkage below 3% in MD and TD after 130 °C for 1 h, and tensile strength is verified by ASTM D882-18 on 15 mm wide strips. Gurley number is commonly specified at 200–450 s/100 mL for high-energy-density NMC cells; if the coating increases Gurley above 450 s/100 mL, the drying profile or solvent blend is adjusted. Slot-die equipment includes a 0.3 µm absolute filter and static mixer before the die; production runs are executed at 20–80 m/min with three-zone drying at 50–80 °C. Cell-level safety qualification is performed under UN 38.3, and separator production is governed by ISO 9001:2015 and IATF 16949:2016, with REACH (EC) No 1907/2006 and RoHS Directive 2011/65/EU Annex II declarations required for export. Terminal products are LATP-coated polyolefin separators for EV NMC and LFP pouch or prismatic cells, 3C-consumer cells, and high-power cells where thermal stability and lithium dendrite resistance are specified.
Direct contact between LATP and metallic lithium is electrochemically unstable because Ti4+ reduces at potentials below 1.5 V versus Li/Li+, forming Li3P and Li–Al regions that increase interfacial impedance. A polymer-based artificial interlayer is therefore used with 5–15 wt% LATP, 10–18 wt% PVDF-HFP, 55–70 wt% anhydrous DME/dioxolane, and 2–5 wt% fluoroethylene carbonate; the coating is applied at 5–20 µm dry thickness onto 20–50 µm lithium foil by reverse gravure coating. The production environment requires a dew point below −50 °C and oxygen below 10 ppm because surface hydroxyl groups on LATP react with lithium; a LiF or Li3PO4 buffer layer is sputtered or spray-coated before LATP-containing interlayer deposition. Coating tension is maintained at 5–15 N/100 mm, and ultraviolet-free lighting is used in the coating zone to prevent radical degradation of fluorinated compounds. In 1–5 Ah lithium-metal pouch cells, the interlayer limits short-circuit failure by maintaining interfacial impedance below 50 Ω cm² during formation; direct LATP contact without buffer can exceed 500 Ω cm² after 10 cycles. Published production-scale data for this specific configuration is limited outside cell maker qualification reports, so cell-level verification under UN 38.3 and ISO 9001:2015/IATF 16949:2016 traceability remains mandatory before export. REACH (EC) No 1907/2006 Annex II restrictions and RoHS Directive 2011/65/EU Annex II verification are required; lithium metal anode handling also falls under dangerous goods transport criteria. Terminal products are protected lithium metal anodes for high-energy-density solid-state or liquid-electrolyte pouch cells, lithium-sulfur and lithium-air research modules, and industrial power packs where anode thickness, interlayer thickness, and interface resistance are jointly specified.
Dry electrode lines replace NMP with PTFE fibrillation, and LATP is added at 1–5 wt% to the dry cathode mixture to create ionic conduction paths along the NMC grain boundaries. A dry cathode composition comprises 85–92 wt% NMC, 2–6 wt% conductive carbon, 2–4 wt% PTFE, and 1–5 wt% LATP; loadings above 5 wt% make the calendered sheet too stiff for lamination, while loadings below 1 wt% produce no measurable ionic percolation. The powders are pre-dried at 150–200 °C for 6–10 h and mixed in a 5 L shear mixer at 2000–4000 rpm for 8–15 min before jet milling at 0.5–1.0 MPa compressed air; final particle size is checked by ISO 13320:2020, with D90 held below 1.2 µm to avoid electrode divots. The dry powder is fed into a calender at 60–120 °C and 10–30 m/min and pressed onto 12–20 µm aluminium foil to a density of 3.0–3.3 g/cm³. Electrode and polymer electrolyte layers are hot-pressed at 120–180 °C and 5–20 MPa to form a continuous solid-state cell stack; water content after drying is below 200 ppm, and the production room meets ISO 14644-1 Class 5 at dew point below −40 °C. The process eliminates NMP and reduces energy input because no drying oven is required, but powder flow and segregation become critical control variables; aerated bulk density is tested by ISO 3923-2:2016 after jet milling. Compliance is maintained under ISO 9001:2015 and IATF 16949:2016, with UN 38.3 cell-level transport testing after pouch cell assembly and REACH/RoHS documentation for the dry electrode sheets where applicable. Terminal products are dry-processed solid-state cathode sheets, self-supporting electrolyte-cathode laminates, and dry electrode rolls intended for solid-state pouch cell lines.
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Lithium Aluminium Titanium Phosphate is placed within the NASICON family of oxide solid electrolytes by its stoichiometric series Li1+xAlxTi2−x(PO4)3, with the substitution level 0.3 corresponding to Li1.3Al0.3Ti1.7(PO4)3. A model designation LATP-0.3/1.7 is used for that specific aluminium-for-titanium substitution. The partial replacement of Ti4+ by Al3+ increases the mobile Li+ population and widens the framework bottleneck for ion migration. Published total ionic conductivities for dense pellets typically fall between 10−4 and 10−3 S/cm at 25 °C; the bulk lattice contribution can approach 1.5 × 10−3 S/cm when grain-boundary impedance is minimised. The theoretical density is approximately 2.9 g/cm³, whereas tap density after comminution is commonly 0.8–1.2 g/cm³. The powder is supplied as a white to off-white free-flowing solid, and it is selected for solid-state separator layers, composite cathodes, and protective coatings in cells where oxide chemical stability is preferred over sulfide chemistries.
Because the material is a ceramic-ion conductor, powder processing dominates final separator resistivity. Batches comminuted in high-energy planetary mills with yttria-stabilised zirconia media of 0.3 mm diameter exhibit increased specific surface area and a corresponding rise in grain-boundary resistance if the amorphous surface layer is not removed during sintering. Production-scale tape-casting operations using slot-die coaters and solvent-based dispersions require tight particle size distribution control; a bimodal distribution can create differential sintering and closed porosity in a green tape. Moisture content of as-received powder is checked by Karl Fischer titration according to ASTM E203-24, because adsorbed water lowers the pH of aqueous dispersions and may hydrolyse phosphate groups. Pre-drying at 150 °C for 2 h under vacuum is applied when storage relative humidity has exceeded 60 %. In dry-room coating, anhydrous ethanol or aprotic solvents such as N-methyl-2-pyrrolidone are preferred to water.
Particle-size distribution also determines the minimum achievable separator thickness. A D90 below 3 μm is required for a 20 μm separator tape; larger particles dominate the wet-film thickness and create pinholes. Laser diffraction reports D10, D50, and D90 values; a span below 1.5 is preferred for tape casting. Bimodal distributions produced by blending two milled lots can increase green density but complicate binder burnout because fine particles trap decomposition products. On a production-scale slot-die line, a tape with a span above 2.0 commonly shows edge cracking during drying. These constraints are addressed by classifying the powder through an air classifier or by controlled milling in a fluidised-bed opposed-jet mill, which reduces contamination from grinding media. D50 values from 0.5 μm to 5 μm are therefore not interchangeable across applications; separator tapes require the lower end of the range, while composite cathodes may tolerate coarser powders to avoid excessive slurry viscosity.
Median particle size is measured by laser diffraction under ISO 13320:2020; representative grades have D50 values from 0.5 μm to 5 μm. Specific surface area, determined by nitrogen adsorption according to ISO 9277:2022, falls between 5 m²/g and 15 m²/g. Tap density obtained by ASTM B330-20 is typically 0.8–1.2 g/cm³. These inputs are not independent; a powder with a D50 of 1 μm and a BET surface area above 12 m²/g usually contains aggregated fines that reduce die-fill uniformity. X-ray diffraction with Rietveld refinement is used to quantify the NASICON phase fraction and secondary phases such as AlPO4, Li3PO4, and TiO2. A target NASICON fraction above 95 wt% with total detectable secondary phases limited to 2 wt% is common for bulk separator grades, although published specifications for particular milled lots vary with the calcination profile and raw-material purity.
| Parameter | Method | Typical range | Processing relevance |
|---|---|---|---|
| Median particle size D50 | ISO 13320:2020 | 0.5–5 μm | Controls green packing and sintering shrinkage |
| Specific surface area | ISO 9277:2022 | 5–15 m²/g | Higher values lower sintering onset but increase moisture uptake |
| Tap density | ASTM B330-20 | 0.8–1.2 g/cm³ | Affects die filling and pressed pellet thickness |
| NASICON phase fraction | XRD Rietveld refinement | ≥95 wt% | Secondary phases raise grain-boundary impedance |
| Total ionic conductivity at 25 °C | Electrochemical impedance spectroscopy | 1 × 10−4–1 × 10−3 S/cm | Measured on dense pellets with blocking electrodes |
| Activation energy | EIS temperature sweep | 0.28–0.35 eV | Indicates bulk migration bottleneck |
Uniaxial pressing at 200–400 MPa followed by air sintering is used to make separator discs. The processing window is narrow: densification accelerates above 900 °C, but lithium loss and AlPO4 segregation become measurable above 1000 °C. A representative profile of 2 h at 950 °C with ramps of 2 °C/min yields relative densities of 92–96% in laboratory pellet studies. Published data for specific production-scale roller-hearth kiln profiles is limited; furnace loading, saggar material, and oxygen partial pressure shift the upper temperature boundary by roughly ±15 °C. Alumina saggars are preferred over mullite because mullite can introduce siliceous surface contamination under long soak times. Sintered pellets are dry-polished before impedance testing to remove surface layers that form during furnace cooling.
Impedance analysis of sintered pellets distinguishes bulk and grain-boundary contributions. In a Nyquist spectrum collected from 1 MHz to 0.1 Hz on blocking stainless-steel electrodes in a sealed Swagelok cell, the high-frequency intercept gives ohmic resistance, and the middle-frequency semicircle is assigned to grain-boundary impedance. Total conductivity is therefore strongly influenced by sintering atmosphere; a slightly lithium-rich powder can compensate for Li loss, but excess Li3PO4 segregates at grain boundaries and depresses conductivity. Pellets sintered in oxygen rather than air may retain more Ti4+ and show lower electronic leakage. Published data for the optimum oxygen partial pressure is limited, with some studies reporting no benefit above 21 vol% O2 when carbon removal is complete.
Batch-to-batch variance is evaluated by ignition loss, particle size, and conductivity witness pellets. Ignition loss after 1 h at 1000 °C should remain below 0.5 wt%; higher values indicate adsorbed moisture or organic residue from milling aids. Conductivity witness pellets are prepared from each lot by pressing at 300 MPa and sintering at 950 °C for 2 h. Acceptance limits are typically 5 × 10−4 S/cm minimum total conductivity at 25 °C. This measurement is not equivalent to final separator performance because grain size and lithium loss vary with the thermal history of the final part, but it provides a reproducible lot-release criterion.
Relative to other solid electrolyte classes, LATP occupies a position between oxide stability and moderate ionic conductivity. Cubic Li7La3Zr2O12 (LLZO) offers comparable conductivity but generally requires sintering above 1100 °C and forms a Li2CO3 surface film in humid air. Sulfide electrolytes such as Li6PS5Cl can achieve conductivity in the 10−3–10−2 S/cm range but require dry-room processing with dew points below −50 °C because of H2S release. The unsubstituted LiTi2(PO4)3 parent structure exhibits lower conductivity in the 10−5–10−4 S/cm range, demonstrating the effect of Al substitution on carrier concentration and framework geometry. LISICON frameworks such as Li14Zn(GeO4)4 share brittle ceramic handling behaviour but lack the conductivity and cost profile of aluminium-containing NASICON materials. These differences are summarised in Table 2.
| Material class | Total ionic conductivity at 25 °C | Air stability | Primary processing constraint | Critical incompatibility |
|---|---|---|---|---|
| LATP NASICON | 10−4–10−3 S/cm | Stable in dry air; slow moisture uptake | Sintering at 900–1000 °C | Ti4+ reduction at low potential |
| Cubic LLZO | 10−4–10−3 S/cm | Li2CO3 surface formation in humid air | Sintering above 1100 °C; grain-boundary control | High interfacial resistance at cathode |
| Li6PS5Cl sulfide | 10−3–10−2 S/cm | H2S release; dry-room required | Cold pressing; solvent sensitivity | Narrow electrochemical window; lithium metal interface |
| LiTi2(PO4)3 parent | 10−5–10−4 S/cm | Air stable | Sintering at moderate temperature | Lower conductivity limits separator thickness |
Direct contact with lithium metal or with negative-electrode potentials below approximately 1.5 V versus Li+/Li reduces Ti4+ to Ti3+. The resulting mixed electronic-ionic conductivity can promote self-discharge and internal shorting in separator layers. For cells with lithium metal negative electrodes, a passivating interlayer of LiF, Li3PO4, or a compliant polymer is required. The same redox limitation applies to LiTi2(PO4)3, which explains the use of graphite or insertion anodes in LATP-based cells rather than bare lithium metal. In humid air, the surface adsorbs water and can slowly form phosphoric acid species; aqueous slurry preparation is therefore not recommended unless the pH is monitored and the dispersion is used within 4 h. For dry-room coatings, anhydrous ethanol or aprotic solvents such as N-methyl-2-pyrrolidone are preferred. Published data for the specific humid-slurry degradation rate is limited; the safe boundary is best established by measuring slurry pH and viscosity drift on the coating line.
Slurry rheology and coating defects are governed by particle surface chemistry and binder selection. Polyvinylidene fluoride in N-methyl-2-pyrrolidone is used for separator coatings, but acidic phosphate surfaces can dehydrofluorinate PVDF under shear; neutralising the powder surface or adding a small Li3PO4 coating mitigates viscosity drift. Slurry viscosity is measured by rotational rheometry under ISO 3219:2021, with typical values of 3,000–8,000 mPa·s at 25 °C and a shear rate of 100 s−1. Viscosity above 10,000 mPa·s reduces slot-die coatability and promotes air entrapment. A high-shear planetary mixer operating at 2,000 rpm for 30 min with 0.3 mm zirconia beads reduces agglomerates, but over-milling beyond 60 min can amorphise the surface and lower sintered conductivity. Slot-die coating of a 20–40 μm wet film onto polyester carrier foil, followed by drying at 80 °C, is typical for free-standing green tapes. The dried green tape is then uniaxially pressed or calendered at 50–100 MPa before sintering to improve particle contact. Binder burnout at 450 °C for 1 h in flowing air is required prior to sintering to avoid residual carbon that blocks grain growth.
In composite cathodes, LATP is blended with layered oxide or phosphate active materials at 5–15 wt% to provide ionic percolation while preserving electronic contact. The blend is ball-milled dry or in non-aqueous solvent, then cast and dried. Interfacial reactions with cathode materials become measurable above 700 °C; therefore co-sintering is limited to low-temperature routes, or the cathode layer is infiltrated after the separator is densified. For LiFePO4-based cathodes, adding 10 wt% LATP can reduce cycle resistance but also increases cell mass. Mixed-cathode processing in a twin-screw extruder with an L/D ratio of 40:1 has been reported for ceramic-polymer hybrids, but published data for dry extrusion of all-ceramic LATP composites is limited. The electrolyte is then integrated into cell builds with a lithium anode behind a protective coating or with graphite anodes in bipolar stacks.
