Synthesis strategy toward microspheric carbon coated off-stoichiometric lithium—iron—phosphorus compound materials

Abstract

A cathode active material represented by the formula, LiFexPO4/C, wherein 0.9≦x<1, preferably 0.96≦x<1, which was obtained from carbon pre-coated off-stoichiometric FexPO4, wherein 0.9≦x<1, preferably 0.96≦x<1. The materials may be double-carbon-coated particles obtained by carbon coating a mixture of a lithium component and FexPO4/C sub-particles, wherein the FexPO4/C sub-particles may be obtained by carbon coating FexPO4.

Description

CROSS REFERENCE TO RELATED APPLICATIONS

This application claims the priority of Chinese Application No. 201110238095.7 filed on Aug. 18, 2011, the disclosure of which is incorporated by reference in its entirety.

BACKGROUND OF INVENTION

1. Field of the Invention

The present invention relates to the field of lithium batteries, particularly to materials for cathodes of lithium ion batteries.

2. Background Art

Lithium-ion batteries (LIBs) have received most attention at both fundamental and applied levels, and thus have had rapid development and occupied the main market of battery devices, owing to the higher operating voltage and energy density as compared to lead-acid or Ni-MH battery.

Since lithium-ion batteries (LIBs) were introduced into market, the application targets have evolved into other areas from the initial applications in various small portable devices, such as cell phones, camcorders, digital cameras and laptop computers, etc. The small-sized lithium-ion battery used for mobile devices is called the first generation lithium-ion battery. Currently, much concern has been devoted to the next generation large-scaled lithium-ion battery used for hybrid electric vehicles (HEVs) and electric vehicles (EVs).

Spinels, such as LiCoO₂, LiNiO₂, LiMn₂O₄ and LiNi_1-xCo_xO₂, have been preferred previously as cathode active materials because these materials have a high energy density and a high voltage p1-p2 (U.S. Pat. No. 5,130,211, issued to Wilkinson et al.; U.S. Pat. No. 5,418,090, issued to Koksbang et al.). However, such materials suffer from high cost and thermal instability. Moreover, these cathode active materials are higher in toxicity and liable to pollute the environment significantly. Therefore, it should be one of the most dominant research activities targeting the development of abundant resources as cathode materials in terms of power density (rate capability), energy density, stability (cycle life), safety and cost.

Since the pioneering work of Padhi et al. (Padhi et al., J. Electrochem. Soc. 1997, 144, 1188; see also, U.S. Pat. No. 5,910,382, issued to Goodenough et al.), olivine-typed LiFePO₄, with the merits of high stability and environmental safety, high theoretical capacity, and low cost (Ravet et al., Nat. Mater. 2003, 2, 702; Gaberscek et al., Electrochem. Commun. 2007, 9, 2778; U.S. Pat. No. 6,514,640, issued to Armand et al), has won the challenge to become the most promising cathode materials of the new generation of lithium-ion batteries needed for electric mobility.

However, the vital disadvantages of LiFePO₄ as an electrode material lie in its low intrinsic electronic conductivity and poor rate of performance. During the past decade, much effort has been devoted to the understanding and improvement of the performances of LiFePO₄.

Armand et al. were the first to show that LiFePO₄ with a carbon coating can achieve almost the theoretical capacity (Ravet et al., J. Electrochem. Soc. Abstr., 1999, 99-2, 172; Ravet et al., J. Power Sources, 2001, 97-98, 503; U.S. Pat. No. 6,085,015, issued to Armand et al). After this work, numerous studies have indicated that electronically conductive coating (mainly carbon) is one of the most efficient techniques to enhance the surface electronic conductivity of LiFePO₄ particles (Doherty et al., J. Drummond, Chem. Mater. 2009, 21, 5300). In addition, carbon coating can play a role in reducing the particle size of LiFePO₄ by inhibiting particle growth during sintering (Lin et al., J. Power Sources, 184 (2008) 444), and suppressing the oxidation of Fe²⁺ to Fe³⁺ during sintering and thus simplifying the atmosphere requirement in synthesis (Wang, R. Cai, T. Yuan, X. Yu, R. Ran, Z. Shao, Electrochem. Acta 54 (2009) 2861; U.S. Pat. No. 7,060,206, issued to Barker et al).

It is commonly recognized that the rate capability of LiFePO₄ powder could be increased by minimizing the size of the particles as much as possible to improve the effective surface that is active for electrochemical reactions. Moreover, smaller size theoretically reduces the paths for the electrons and the Li⁺ ions inside the particles. However, from the standpoint of manufacturing, the excessive reduction in sizes causes a poor post-processing performance of cells, such as ultrahigh surface effects, low tap densities and over utilization of N-methyl-2-pyrrolidone (NMP) dosage. Therefore, large-scale and eco-efficient synthetic techniques with considerations of electrochemically activities, particle sizes, cation order, and post-processing performance are important to the success of the electrode material.

SUMMARY OF INVENTION

One aspect of the invention relates to cathode active materials. A cathode active material is represented by the formula, LiFe_xPO₄/C, wherein 0.9≦x<1, preferably 0.96≦x<1, which was obtained from carbon pre-coated off-stoichiometric Fe_xPO₄, wherein 0.9≦x<1, preferably 0.96≦x<1. The materials may be double-carbon-coated particles obtained by carbon coating a mixture of a lithium component and Fe_xPO₄/C sub-particles, wherein the Fe_xPO₄/C sub-particles may be obtained by carbon coating Fe_xPO₄.

Another aspect of the present invention relates to a novel strategy for the fabrication of the hierarchical mesoporous double-carbon-coated LiFe_xPO₄ microspheres. The synthetic approach synergistically combines the dual carbon coating and spray-drying processes. Double conductive coating can greatly improve the uniformity of the carbon layer on both the primary and secondary LiFe_xPO₄/C particles, and afford large capacities at high discharge rates. Moreover, two steps of spray-drying and post-annealing can realize the hierarchical microsized secondary particles containing nanoscale primary particles. This novel structure has the advantages of significantly reducing the diffusion paths of the lithium ions and high tapped density. In addition, embodiments of the present invention use water as a solvent, thereby avoiding the hidden safety problems and the high production and recycling costs of organic solvents.

A method for preparing a cathode active material in accordance with one embodiment of the invention includes drying an aqueous mixture containing Fe_xPO₄ and a carbon precursor to obtain a dried mixture, wherein 0.9≦x<1; sintering the dried mixture to obtain Fe_xPO₄/C microspheres; mixing the Fe_xPO₄/C microspheres with a lithium salt and a second carbon precursor in distilled water to form a second mixture; drying the second mixture to obtain a dried second mixture; and calcining the second dried mixture to obtain the cathode active material.

Embodiments of the invention also relate the as-synthesized hierarchical microspherical LiFe_xPO₄/C compositions for use as active cathode materials in lithium insertion-type electrodes. With these materials, fast charge and discharge rates are obtained at room temperature and an excellent energy density is observed.

BRIEF DESCRIPTION OF DRAWINGS

A complete appreciation of the invention will be readily obtained by reference to the following detailed description and the accompanying drawings.

FIG. 1 illustrates an Energy Dispersive X-ray Spectroscopy (EDS) spectrum of spots on a separator; inset is an EDS spectrum of a pure separator.

FIG. 2 illustrates SEM and TEM images of double-carbon-coated LiFe_0.98PO₄ microspheres produced in accordance with one embodiment of the present invention.

FIG. 3 illustrates XRD (Cu Kα) patterns of double-carbon-coated LiFe_0.98PO₄ powders according to one embodiment of the present invention.

FIG. 4 illustrates a particle size distribution (volume-based) of double-carbon-coated LiFe_0.98PO₄ powders produced in accordance with an embodiment shown in Example 1 of the invention.

FIG. 5 illustrates charge/discharge profiles of (a) single-carbon-coated LiFe_0.98PO₄ and (b) double-carbon-coated LiFe_0.98PO₄.

FIG. 6 illustrates discharge profiles of double-carbon-coated LiFe_0.98PO₄ at various C rates.

FIG. 7 illustrates cycling performance of a 10 Ah lithium ion battery made of double-carbon-coated LiFe_0.98PO₄.

FIG. 8 shows a flowchart illustrating one method in accordance with one embodiment of the invention.

DEFINITION

As used herein, the term “tapped density” has its normal meaning in the art of powder characterization. Specifically, “tapped density” is measured by mechanically tapping a measuring cylinder containing a powder sample. After observing the final volume, the cylinder is mechanically tapped, and volume readings may be taken until no or little further changes in the volume is observed.

As used herein, a “carbon precursor” refers to a carbon containing compound that can provide a carbon coating of the Fe_xPO₄/C or LiFe_xPO₄/C microspheres. Examples of carbon precursors include inorganic (C) or organic carbon source, such as sucrose (C₁₂H₂₂O₁), glucose (C₆H₁₂O₆), citric acid (C₆H₈O₇), ascorbic acid (C₆H₈O₆), acetylene black, and the like. A carbon precursor for the first carbon coating may be the same or different from the carbon source for the second carbon coating in accordance with embodiments of the invention.

As used herein, a “lithium precursor” refers to a lithium containing compound that can provide lithium ion (Li⁺) in the LiFe_xPO₄/C microspheres. Examples of lithium precursors include any lithium organic salt or inorganic salts, such as lithium carbonate (Li₂CO₃), lithium bicarbonate (LiHCO₃) lithium acetate (CH₃CO₂Li), lithium hydroxide (LiOH), lithium nitrate (LiNO₃), lithium halide (LiX, wherein X is F, Cl, Br, or I), and the like.

As used herein, the term “off-stoichiometric” or “sub-stoichiometric” iron-lithium phosphate means that the ratio of iron to lithium (or phosphate) in the complex is less than 1—i.e., less iron than lithium (or phosphate), such as LiFe_0.98PO₄. Because the iron content is less than 1 equivalent, the complex may contain other elements, such as other metals (e.g., alkaline metals, alkaline earth metals, transition metals, and the like). Sub-stoichiometric or off-stoichiometric iron content is preferred based on the fact that there are plenty of spots on the separator after the experiments of cycling performances of the cells made of the stoichiometric lithium-iron-phosphate. Due to the potential risk of short circuit caused by high iron content dissolved in electrolytes, off-stoichiometric lithium-iron-phosphate is better. Therefore, the ratio of iron to phosphorus is off-stoichiometric in the raw ferric phosphate sources.

As used herein, the term a “double-carbon-coated” composite or particle refers to a composite or particle that is prepared by two-stage carbon coatings. First, a starting material (e.g., off-stoichiometric iron phosphate) is coated with carbon to produce carbon-coated sub-particles, which are then mixed with one or more other components (e.g., lithium salt) and then carbon coated one more time. In accordance with embodiments of the invention, the particles, for example, may be micrometer sized particles that comprise a plurality of nanometer sized sub-particles.

As used herein, the term “molar ratio” refers to the number of moles of component A relative to component B when the component B is present at 1.0 mole. For Example, “a molar ratio of a carbon precursor and Fe_xPO₄ is 0.15” means that there are 0.15 mole of the carbon precursor and 1.0 mole of Fe_xPO₄.

Note that disclosure of numerical ranges in the present description does intend to include individual numbers within the range, i.e., as if they were individually disclosed.

DETAILED DESCRIPTION

Having generally described the present invention, a further understanding can be obtained by reference to the specific preferred embodiments, which are provided herein for the purpose of illustration only and are not intended to limit the scope of the invention.

Embodiments of the present invention relate to cathode active materials for lithium-ion batteries with an appropriate off-stoichiometry in lithium-iron composite phosphorus oxide, having a formula of LiFe_xPO₄, wherein 0.9≦x<1, preferably about 0.94≦x<1, more preferably about 0.96≦x<1, and most preferably x is about 0.98. To obtain the LiFe_xPO₄, the ratio of iron to phosphorus in raw Fe_xPO₄ is very important. In accordance with embodiments of the invention, the LiFe_xPO₄ powders for use as cathode active materials are coated with dual carbon layers.

Conventional cells having cathodes made of stoichiometric lithium-iron-phosphate compounds may show a large number of spots on separators after multiple cycles of charges-discharges. As shown in FIG. 1, Energy Dispersive X-ray Spectroscopy (EDS) spectra show that the iron contents of the spots are much higher than the iron contents in other regions. It is believed that iron deposition occurred during long-term cycling of cells having cathodes made of stoichiometric lithium-iron-phosphate compounds, because the possibility of introducing iron from the environment is eliminated during the entire period of the electrochemical experiment shown in FIG. 1. Due to potential problems of short circuit caused by high iron contents and iron deposition (as shown in FIG. 1), embodiments of the invention involve off-stoichiometric (sub-stoichiometric) ratio of iron and phosphorus in the ferric phosphate composites.

In accordance with embodiments of the invention, Fe_xPO₄ or Fe_xPO₄.nH₂O, wherein n stands for the number of hydrates (i.e., n is an integer from 1 to 4), a lithium precursor, and a carbon precursor may be used as starting materials to synthesize the LiFe_xPO₄/C composites. In accordance with some embodiments of the invention, a method for preparing high purity products may include the following basic steps: (1) the Fe_xPO₄/C precursors are obtained through spray drying of a water-based mixture of Fe_xPO₄.nH₂O powder and a carbon precursor; (2) the dried mixture are calcined at 400-600° C. under a nitrogen atmosphere to form nanocrystalline microspheres; and (3) the as-obtained nanocrystalline Fe_xPO₄/C microspheres are mixed with a stoichiometric amount of a lithium salt and a carbon precursor to undergo lithiating and a second carbon-coating, via another spray-drying and calcination processes to provide double-carbon-coated LiFe_xPO₄ microspheres.

For example, FIG. 8 shows a flowchart illustrating a method in accordance with one embodiment of the invention. As show, a method 80 may start with preparing a mixture of Fe_xPO₄, wherein 0.9≦x<1.0, more preferably 0.96≦x<1.0, and a carbon precursor (step 81). The Fe_xPO₄ may be supplies as a hydrate, Fe_xPO₄.nH₂O, wherein n is the number of water molecules in the hydrate (i.e., n is an integer from 1 to 4). The carbon precursor can be any organic compound or inorganic compound that can generate carbon at high temperature. Examples of the carbon precursors such as sucrose (C₁₂H₂₂O₁₁), glucose (C₆H₁₂O₆), citric acid (C₆H₈O₇), ascorbic acid (C₆H₈O₆), acetylene black, and the like. A molar ratio of the carbon precursor and the Fe_xPO₄ may be 0.08-0.15. The mixture may be made as an aqueous slurry or solution. The use of water (such as distilled water) avoids organic solvents, which may pose safety concerns as well as environmental costs.

Then, the mixture is dried (step 82). The drying may be performed with any known techniques, such as air drying or spray drying. In accordance with embodiments of the invention, the drying is preferably performed with spray drying so that the products will have spherical morphology, which will have short paths for the ions to diffuse in and out from all directions. The dried mixture is then sintered at a high temperature (step 83). The sintering temperature, for example, may be from 400-600° C. Furthermore, the sintering may be performed under an inert atmosphere (e.g., a nitrogen atmosphere) to form nanocrystalline microspheres of Fe_xPO₄/C, in which each of the microspheres of Fe_xPO₄ may be coated with a thin layer of carbon.

The Fe_xPO₄/C microspheres are mixed with a lithium precursor and a second carbon precursor, which may be the same or different from the first carbon precursor, to form a second slurry or solution (step 84). The lithium precursor may be an organic or inorganic salt containing lithium as a cation, such as LiOH, LiCl, LiC₂O₃, LiCH₃CO₂, and the like. The molar ratio of lithium and phosphorus in the second mixture is 1.0-1.1. An amount of the second carbon precursor may be determined according to a carbon content of the Fe_xPO₄/C microspheres to provide a final carbon content of 2.0-5.0 wt %. The slurry or solution may use water (e.g., distilled water) as a solvent to avoid the problems and costs of organic solvents. The mixture slurry or solution is again dried (step 85). Again, the drying may be performed using any technique known in the art, including spray drying.

Finally, the dried mixture may be calcined at a high temperature to produce a double-carbon-coated LiFe_xPO₄/C powders or particles, which can be advantageously used as cathode active materials for lithium ion batteries (step 86). The calcining may involves annealing at a high temperature (e.g., about 400-600° C.) for a proper duration (e.g., for 2 hours). Furthermore, the calcining may also include treatment at a high temperature (e.g., 650-750° C.) by heating the annealed products at a rate of 2-10° C. per minute. The high temperature (e.g., 650-750° C.) treatment (curing) may be performed for a selected duration (e.g., 10-15 hours).

Using methods of the present invention, one may fabricate uniform spherical LiFe_xPO₄/C powders that have novel hierarchical microstructures composed of carbon-coated micrometer-sized secondary spheres that contain nano-sized carbon-coated primary spheres. This hierarchical spherical microstructure provides optimized performances by a combination of both advantages of two size scales. The nanoscale primary spheres have reduced path lengths for the electrons and the Li⁺ ions to move in and out of the particles and have increased effective surface areas that are active for electrochemical reactions, while the micrometer-scale secondary spheres would have higher tapped densities, and good post-processing performances (e.g., better flowability). Therefore, the hierarchical spherical microstructures in accordance with embodiments of the invention would have excellent electrochemical properties, as well as high producing and processing performances.

FIG. 2 shows the SEM and TEM images of double-carbon-coated LiFe_0.98PO₄ microspheres in accordance with embodiments of the invention. As shown, the resulting materials have morphology of hierarchical mesocrystal spheres, which are formed by self-assembly of the primary LiFe_0.98PO₄ nanospheres. Successful uniform carbon coating on the surface of LiFe_0.98PO₄ is suggested by the transmission electron microscopy (TEM) image shown in FIG. 2b. The carbon content in the double-carbon-coated LiFe_0.98PO₄ microspheres is estimated to be about 2.38 wt %.

FIG. 3 shows an X-ray diffraction (XRD) pattern of double-carbon-coated LiFe_0.98PO₄ powders. It can be clearly seen that the diffraction peaks for LiFe_0.98PO₄/C are indexed to an orthorhombic olivine space group, Pmna (JCPDS 81-1173). This confirms the presence of LiFe_0.98PO₄ as a single-crystalline phase in the powder. Additionally, there is no evidence in the XRD pattern for the presence of carbon, due to its amorphous structure and its small amount with respect to the LiFe_0.98PO₄ phase.

The particle size distribution of the resultant double-carbon-coated LiFe_0.98PO₄ is shown in FIG. 4. To illustrate the advantageous particle size distribution and the absence of the disruptive larger particles in the products according to embodiments of the invention, the volume-based data are shown. The values based on the particle fraction (%) are as follows: D50 value about 24.0 μm; D10 value less than 10.8 μm; D90 value about 44.9 μm; and the difference between the D90 value and D10 value less than 34.1 μm.

In this example, the tapped density of the hierarchical double-carbon-coated LiFe_0.98PO₄ microspheres is measured to be 1.2 g·cm⁻³ (g/cm³), which is greater than those obtained for common (nanosized) LiFePO₄ morphologies of 1.0 g·cm⁻³. The higher tapped density may be of great importance to the transportation applications of lithium batteries, because it ensures a low reactivity and a high volumetric energy density. Embodiments of the invention typically have tapped densities greater than 1.0 g·cm⁻³, preferably greater than 1.1 g·cm⁻³, more preferably greater than 1.2 g·cm⁻³. In some embodiments, the tapped densities may be in the ranges of 1.0 g·cm⁻³-1.3 g·cm⁻³, more preferably in the range of 1.1 g·cm⁻³-1.3 g·cm⁻³, and most preferably in the range of 1.15 g·cm⁻³-1.25 g·cm⁻³. Any mention of a numerical range in this description intends to cover all numbers between the upper and lower limits.

Moreover, the double-carbon-coated LiFe_0.98PO₄ powders in accordance with embodiments of the invention have larger Brunauer-Emmett-Teller (BET) surface areas, as compared with carbon-free LiFePO₄ powders. In general, the double-carbon-coated LiFe_0.98PO₄ powders in accordance with embodiments of the invention may have BET surface areas in a range of 18 m²·g⁻¹-25 m²·g⁻¹, more preferably in a range of 20 m²·g⁻¹-23 m²·g⁻¹, and most preferably in a range of 21 m²·g⁻¹-23 m²·g⁻¹. For example, in some embodiments, the double-carbon-coated LiFe_0.98PO₄ powders may have Brunauer-Emmett-Teller (BET) surface areas of 21.53 m²·g⁻¹.

The electrochemical properties of single-carbon-coated LiFe_0.98PO₄ and double-carbon-coated LiFe_0.98PO₄ are investigated and compared, and results are shown in FIG. 5. The charge and discharge capacities of the double-carbon-coated LiFe_0.98PO₄ are much higher than the single carbon-coated powders. This result is not surprising because the slow kinetics is enhanced by the excellent electronic conductivity brought about by the double carbon coatings.

The rate capabilities of double-carbon-coated LiFe_0.98PO₄ are characterized by applying different current densities, and the results are shown in FIG. 6. In these tests, the cells were charged to 4.0 V at 0.2 C, and then discharged to 2.0 V at a rate of n C (wherein n=0.2, 1, 5, or 10). From FIG. 6, it can be seen that the LiFe_0.98PO₄/C material has good rate capabilities. At a 0.2 C rate, the material discharges to its estimated theoretical capacity of 152.6 mAh·g⁻¹. Even at the highest rate tested (10 C), the material achieves about 71% of its theoretical capacity.

Electrochemical properties of the double-carbon-coated LiFe_0.98PO₄ composites are characterized using a prismatic lithium ion cell-100 Ah. The cathode active material is prepared using certain proportions of LiFe_0.98PO₄/C composite material (as-synthesized using a method of the present invention), polyvinylidene fluoride (PVDF), acetylene black, and graphite. These components are dispersed in N-methylpyrrolidone (NMP) and the resulting uniform slurry is applied to both faces of an aluminum foil, followed by a drying step. The anode is prepared by coating both faces of a copper foil with a slurried anode material, which is made by dispersing natural graphite, acetylene black, and carboxymethylcellulose (CMC) in water. Cells are constructed using the positive and negative electrodes with a polyethylene porous film as a separator. LiPF₆ (1 mol/L) is dissolved in a mixture of elthylene carbonate (EC) and methylethyl carbonate (MEC) (2:1 ratio by weight) to provide a non-aqueous electrolyte. The cells are tested at a rate of 0.5 C and cycled between 3.65 V and 2.0 V.

FIG. 7 shows the corresponding plot of discharge capacity vs. cycle number of the Ah lithium ion battery having a cathode made of LiFe_0.98PO₄/C. As can be seen, there is no obvious capacity fading even after over 350 cycles. The results demonstrate the superior cycling stability of cells having cathodes made of a hierarchically structured LiFe_0.98PO₄/C, in accordance with embodiments of the invention.

EXAMPLES

Embodiments of the invention are further illustrated in the following examples. One skilled in the art would appreciate that these examples are for illustration only and are not intended to limit the scope of the invention.

Example 1

For the preparation of Fe_0.98PO₄/C microspheres, a carbon precursor (e.g., sucrose) was dissolved in an aqueous solution of 1795.2 g Fe_0.98PO₄.2H₂O at 0.08 molar ratio of Fe_0.98PO₄.2H₂O. The mixed solution was pumped into a continuously stirred mill (capacity of 10 L) and agitated for about 2 hours. The resulting average particles size (D50 value) of the slurry was controlled to be less than 2.0 μm. Spray-drying of water-based mixture to give spherical Fe_0.98PO₄/C precursor; the solid volume density of the mixture was determined to be about 20-50%. The dried precursor was then sintered for 2 hours at a temperature of 600° C. under a nitrogen atmosphere to produce nanocrystalline Fe_0.98PO₄/C microspheres with the D50 value of 20 μm and specific surface area of 10-15 m²/g. The carbon content was measured to be about 1.0-2.0 wt %.

For the preparation of LiFe_0.98PO₄/C microspheres, the as-obtained nanocrystalline Fe_0.98PO₄/C microspheres were mixed with a stoichiometric amount of Li₂CO₃ and a carbon precursor (e.g., sucrose) to provide the lithium source and the second carbon-coating source, respectively. The molar ratio of Li and Fe may be maintained at a predetermined ratio (e.g., 1.02), while the amount of carbon precursor may be selected according to the carbon content of the Fe_0.98PO₄/C materials to provide a desired final carbon content (for example, 2.0 wt %). After continuously stirring, adjusting solid volume density and the second spray drying process, the mixture was calcined at an appropriate temperature for a selected duration (for example, at 400° C. for 2 hours). Then, the products may be heated (e.g., at a rate of 10° C. per minute) to a higher temperature (e.g., 700° C.) and remained at the higher temperature (e.g., 700° C.) for a selected period of time (e.g., 12 hours) under an inert atmosphere (e.g., nitrogen atmosphere) to cure the products. The final product had the D50 value of 5-25 μm and a specific surface area of 20-30 m²·g.

Example 2

In this example, Fe_0.96PO₄.2H₂O was selected as a ferric precursor. For the preparation of Fe_0.96PO₄/C microspheres, a carbon precursor (e.g., sucrose) was dissolved in an aqueous solution of Fe_0.96PO₄.2H₂O at 0.095 molar ratio of Fe_0.96PO₄.2H₂O. The mixed solution was pumped into a continuously stirred mill (capacity of 10 L) and agitated for about 2 hours. The resulting average particles size (D50 value) of the slurry was controlled to be less than 2.0 μm. The water-based mixture was spray dried to give a spherical Fe_0.96PO₄/C precursor. The solid volume density of the mixture was determined to be about 20-50%. The precursor was then sintered for 4 hours at a temperature of 400° C. under a nitrogen atmosphere to produce nano-crystalline Fe_0.96PO₄/C microspheres with a D50 value of 20 μm and a specific surface area of 10-15 m²/g. The carbon content was measured to be about 1.0-2.0 wt %.

For the preparation of LiFe_0.96PO₄/C microspheres, the as-obtained nano-crystalline Fe_0.96PO₄/C microspheres were mixed with a stoichiometric amount of Li₂CO₃ and a carbon precursor (e.g., glucose) to provide the lithium source and the second carbon-coating source, respectively. The molar ratio of Li and Fe was maintained at about 1.00, while the amount of carbon precursor was determined according to the carbon content of Fe_0.96PO₄/C materials to provide a final carbon content of 2.5 wt %. After continuously stirring, adjusting the solid volume density, and the second spray drying process, the mixture was calcined at a temperature of 400° C. for 2 hours, and then at a rate of 10° C. per minute to 700° C. and remained at 700° C. for another 12 hours under a nitrogen atmosphere. The final product had the D50 value of 5-25 μm and a specific surface area of 20-30 m²/g.

Example 3

In this example, Fe_0.98PO₄.4H₂O was selected as a ferric precursor. For the preparation of Fe_0.98PO₄/C microspheres, a carbon precursor (e.g., glucose) was dissolved in an aqueous solution of Fe_0.98PO₄.4H₂O at 0.15 molar ratio of Fe_0.98PO₄.4H₂O. The mixed solution was pumped into a continuously stirred mill (capacity of 10 L) and agitated for about 2 hours. The resulting average particles size (D50 value) of the slurry was controlled to be less than 2.0 μm. The water-based mixture was spray dried to give a spherical Fe_0.98PO₄/C precursor. The solid volume density of the mixture was determined to be about 20-50%. The precursor was then sintered for 3 hours at a temperature of 500° C. under a nitrogen atmosphere to produce nano-crystalline Fe_0.98PO₄/C microspheres with a D50 value of 20 μm and a specific surface area of 10-15 m²/g. The carbon content was measured to be about 1.0-2.0 wt %.

For the preparation of LiFe₉₈PO₄/C microspheres, the as-obtained nano-crystalline Fe_0.98PO₄/C microspheres were mixed with a stoichiometric amount of LiOH and a carbon precursor (e.g., glucose) to provide the lithium source and the second carbon-coating source, respectively. The molar ratio of Li and Fe was maintained at 1.07, while the amount of carbon precursor was determined according to the carbon content of the Fe_0.98PO₄/C materials to provide a final carbon content of 5.0 wt %. After continuously stirring, adjusting solid volume density, and the second spray drying process, the mixture was calcined at temperature of 400° C. for 2 hours, and then at a rate of 10° C. per minute to 700° C. and remained at 700° C. for another 12 hours under a nitrogen atmosphere. The final product had a D50 value of 5-25 μm and a specific surface area of 20-30 m²/g.

Example 4

In this example, Fe_0.98PO₄.2H₂O was selected as a ferric precursor. For the preparation of Fe_0.98PO₄/C microspheres, a carbon precursor (e.g., sucrose) was dissolved in an aqueous solution of Fe_0.98PO₄.2H₂O at 0.125 molar ratio of Fe_0.98PO₄.2H₂O. The mixed solution was pumped into a continuously stirred mill (capacity of 10 L) and agitated for about 2 hours. The resulting average particles size (D50 value) of the slurry was controlled to be less than 2.0 μm. The water-based mixture was spray dried to give a spherical Fe_0.98PO₄/C precursor. The solid volume density of the mixture was determined to be about 20-50%. The precursor was then sintered for 4 hours at a temperature of 400° C. under a nitrogen atmosphere to produce nano-crystalline Fe_0.98PO₄/C microspheres with a D50 value of 20 μm and specific surface area of 10-15 m²/g. The carbon content was measured to be about 1.0-2.0 wt %.

For the preparation of LiFe_0.98PO₄/C microspheres, the as-obtained nano-crystalline Fe_0.98PO₄/C microspheres were mixed with a stoichiometric amount of LiNO₃ and a carbon precursor (e.g., citric acid) to provide the lithium source and the second carbon-coating source, respectively. The molar ratio of Li and Fe was maintained at 1.05, while the amount of carbon precursor was determined according to the carbon content of Fe_0.98PO₄/C materials to provide a final carbon content of 3.0 wt %. After continuously stirring, adjusting the solid volume density, and the second spray drying process, the mixture was calcined at temperature of 600° C. for 2 hours, and then at a rate of 2° C. per minute to 750° C. and remained at 750° C. for another 10 hours under a nitrogen atmosphere. The final product had a D50 value of 5-25 μm and a specific surface area of 20-30 m²/g.

Example 5

In this example, Fe_0.96PO₄*2H₂O was selected as a ferric precursor. For the preparation of Fe_0.96PO₄/C microspheres, a carbon precursor (e.g., glucose) was dissolved in an aqueous solution of Fe_0.96PO₄.2H₂O at 0.11 molar ratio of Fe_0.96PO₄.2H₂O. The mixed solution was pumped into a continuously stirred mill (capacity of 10 L) and agitated for about 2 hours. The resulting average particles size (D50 value) of the slurry was controlled to be less than 2.0 μm. The water-based mixture was spray dried to give a spherical Fe_0.96PO₄/C precursor. The solid volume density of the mixture was determined to be about 20-50%. The precursor was then sintered for 2 hours at a temperature of 600° C. under a nitrogen atmosphere to produce nano-crystalline Fe_0.96PO₄/C microspheres with a D50 value of 20 μm and a specific surface area of 10-15 m²/g. The carbon content was measured to be about 1.0-2.0 wt %.

For the preparation of LiFe_0.96PO₄/C microspheres, the as-obtained nanocrystalline Fe_0.96PO₄/C microspheres were mixed with a stoichiometric amount of Li₂CO₃ and a carbon precursor (e.g., citric acid) to provide the lithium source and the second carbon-coating source, respectively. The molar ratio of Li and Fe was maintained at 1.1, while the amount of carbon precursor was determined according to the carbon content of Fe_0.96PO₄/C materials to provide a final carbon content of 4.0 wt %. After continuously stirring, adjusting the solid volume density, and the second spray drying process, the mixture was calcined at a temperature of 500° C. for 2 hours, and then at a rate of 6° C. per minute to 650° C. and remained at 650° C. for another 15 hours under a nitrogen atmosphere. The final product had a D50 value of 5-25 μm and a specific surface area of 20-30 m²/g.

Embodiments of the present may have one or more of the following advantages. First, because spherical particles may have higher tapped densities than those with irregular shapes, which generally result in a lot of vacant space between the particles and bad fluidity (flowability) of the powders, the spray-drying approach is employed to form microspherical particles with highly homogeneous morphology. Secondly, dual carbon coating processes are utilized to produce high porosity and to assure the uniformity of the carbon layers on both the primary and secondary LiFe_xPO₄ particles. The carbon coating layers play a role in improving the conductivity of LiFe_xPO₄, as well as acting as a nucleating agent to decrease the particle sizes of the final products and a reductant to avoid formation of undesirable ferric impurities. A complete, homogeneous, thin coating of carbon ensures that the LiFe_xPO₄ particles can receive electrons from all directions and that the Li⁺ ions can penetrate through the carbon layer without appreciable polarization. In addition, the more the carbon content, the lower the tapped density. Accordingly, the carbon precursor concentrations are importance and preferably are precisely controlled. Other advantages of embodiments of the invention include: suitable for kilogram-scale industrialized production, and using water-based synthetic systems, which avoid the safety problems and reduce the production and organic solvent recycling costs.

While this invention has been described in terms of certain embodiments thereof, it is not intended that it be limited to the above description, but rather only to the extent set forth in the following claims. The embodiments of the invention in which an exclusive property or privilege is claimed are defined in the following claims.

Claims

1. A method for preparing the cathode active material, comprising: drying an aqueous mixture containing FexPO4 and a carbon precursor to obtain a dried mixture, wherein 0.9≦x<1;sintering the dried mixture to obtain FexPO4/C microspheres;mixing the FexPO4/C microspheres with a lithium salt and a second carbon precursor in distilled water to form a second mixture;drying the second mixture to obtain a dried second mixture; andcalcining the dried second mixture to obtain the cathode active material, wherein an amount of the second carbon precursor is determined, according to a carbon content of the FexPO4/C microspheres, to provide a final carbon content of 2.0-5.0 wt %.

2. The method according to claim 1, wherein a molar ratio of the carbon precursor and the FexPO4 is 0.08-0.15.

3. The method according to claim 1, wherein the drying comprises spray-drying.

4. The method according to claim 1, wherein a molar ratio of lithium and phosphorus in the second mixture is 1.0-1.1.

5. The method according to claim 1, wherein the sintering comprises annealing at a temperature of about 400-600° C. for a duration in a range from 2 to 4 hours.

6. The method according to claim 1, wherein the calcining comprises annealing at a temperature of about 400-600° C. for 2 hours, and then at a rate of 2-10° C. per minute to 650-750° C. and remained at 650-750° C. for another 10-15 hours.

7. The method according to claim 1, wherein the calcining is carried out under a non-oxidizing atmosphere.