Magnetite (Fe.SUB.3.O.SUB.4.)—multiwalled carbon nanotube composite structures with performance as high rate electrode materials for Li-ion batteries

Abstract

A method of synthesizing an electrode material for lithium ion batteries from Fe.sub.3O.sub.4 nanoparticles and multiwalled carbon nanotubes (MWNTs) to yield (Fe.sub.3O.sub.4-NWNTs) composite heterostructures. The method includes linking the Fe.sub.3O.sub.4 nanoparticles and multiwalled carbon nanotubes using a π-π interaction synthesis process to yield the composite heterostructure electrode material. Since Fe.sub.3O.sub.4 has an intermediate voltage, it can be considered an anode (when paired with a higher voltage material) or a cathode (when paired with a lower voltage material).

Claims

1. A method of synthesizing an electrode material for lithium-ion batteries from Fe.sub.3O.sub.4 nanoparticles and acid-functionalized multiwalled carbon nanotubes (MWNTs) to yield composite heterostructures (Fe.sub.3O.sub.4-MWNTs), the method comprising: linking the Fe.sub.3O.sub.4 nanoparticles and the acid-functionalized multiwalled carbon nanotubes using a π-π interaction synthesis process to yield the composite heterostructure electrode material.

2. The method of claim 1, wherein the step of linking includes acid-functionalizing the multiwalled carbon nanotubes (MWNTs) includes oxidizing and coating surfaces of the MWNTs with oxygenated moieties comprising carboxylic acid.

3. The method of claim 2, wherein the linking anchors the Fe.sub.3O.sub.4 nanoparticles onto the surfaces of the acid-functionalized multiwalled carbon nanotubes.

4. The method of claim 1, wherein prior to linking, the Fe.sub.3O.sub.4 nanoparticles are first functionalized with 4-mercaptobenzoic acid (4-MBA) linker molecules.

5. The method of claim 4, wherein the functionalizing includes dispersing Fe.sub.3O.sub.4 nanoparticles in an ethanolic solution of 4-mercaptobenzoic acid (4-MBA) and stirring to facilitate either a mondentate or bidentate coordination mode between terminal carboxylic acid groups of 4-MBA linker molecules and corresponding Fe sites localized on the Fe.sub.3O.sub.4 surfaces.

6. The method of claim 5, further comprising isolating the functionalized Fe.sub.3O.sub.4 including removing any unbound 4-mercaptobenzoic acid (4-MBA) linker molecules.

7. The method of claim 4, wherein the anchoring includes sonicating a solution comprising the 4-mercaptobenzoic acid (4-MBA)functionalized Fe.sub.3O.sub.4, the oxidized multiwalled carbon nanotubes, ethanol and dimethyl sulfoxide (DMSO) to form stable π-π interactions between phenyl rings within the 4-MBA linker molecules and an underlying multiwalled carbon nanotube network of the multiwalled carbon nanotubes.

8. The method of claim 1, wherein the Fe.sub.3O.sub.4 nanoparticles (NPs) have an average size in a range of 8-10 nm.

9. The method of claim 8, wherein the Fe.sub.3O.sub.4 nanoparticles are provided in solution at a loading ratio of 50 wt %.

10. An anode fabricated with an electrode material synthesized by the method of claim 1.

11. A cathode fabricated with an electrode material synthesized by the method of claim 1.

12. An electrode for a lithium-ion cell or battery fabricated with an electrode material synthesized by the method of claim 1, wherein upon pairing the electrode with a pairing electrode fabricated with a higher voltage material during intended use in a lithium-ion cell or battery, the electrode functions as an anode and the pairing electrode of the higher voltage material functions as a cathode and wherein upon pairing the electrode with a pairing electrode fabricated with a lower voltage material, the electrode functions as an anode and the pairing electrode of higher voltage material functions as a cathode.

13. An electrode for a lithium-ion cell or battery, fabricated with an electrode material synthesized according to the method of claim 1.

14. A lithium-ion cell or battery comprising an electrode fabricated with the electrode material synthesized by the method of claim 1.

15. An electrode material for lithium-ion batteries, comprising Fe.sub.3O.sub.4 nanoparticles with attached 4-mercaptobenzoic acid (4-MBA) linker molecules and acid-functionalized multiwalled carbon nanotubes (MWNTs) linked by π-π interactions with the 4-MBA linker molecules, forming (Fe.sub.3O.sub.4-MWNTs) composite heterostructure electrode materials.

16. The electrode material of claim 15, wherein the 4-mercaptbenzoic acid (4-MBA) linker molecules include phenyl rings and the π-π interactions occur between the phenyl rings and the acid-functionalized multiwalled carbon nanotubes (MWNTs).

17. The electrode material of claim 15, wherein the surfaces of the acid-functionalized multiwalled carbon nanotubes (MWNTs) include an oxidized carboxylic acid coating.

18. The electrode material of claim 15, wherein the Fe.sub.3O.sub.4 nanoparticles have an average size in a range of 8-10 nm.

19. An electrode fabricated with the electrode material of claim 15.

20. An anode fabricated with an electrode material of claim 15.

21. A cathode fabricated with an electrode material of claim 15.

22. An electrode for a lithium-ion cell or battery fabricated with an electrode of claim 15, wherein upon pairing the electrode with a pairing electrode fabricated with a higher voltage material during intended use in a lithium-ion cell or battery, the electrode functions as an anode and the pairing electrode of the higher voltage material functions as a cathode and wherein upon pairing the electrode with a pairing electrode fabricated with a lower voltage material, the electrode functions as an anode and the pairing electrode of higher voltage material functions as a cathode.

23. A lithium ion battery including an electrode fabricated from with the electrode material synthesized according to the method of claim 1.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) Further features and advantages of the invention will become apparent from the description of embodiments that follows, with reference to the attached figures, in which:

(2) FIG. 1 illustrates a prior art covalent attachment process between magnetite (Fe.sub.3O.sub.4) nanoparticles and multi-wall carbon nanotubes (MWNTs);

(3) FIG. 2 illustrates the novel π-π interaction attachment process between magnetite (Fe.sub.3O.sub.4) nanoparticles and adjoining multi-wall carbon nanotubes (MWNTs), according to the invention;

(4) FIG. 3a is a TEM image depicting morphology at 100 nm of the Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the covalent attachment protocol of FIG. 1;

(5) FIG. 3b is a TEM image depicting morphology at 10 nm of Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the covalent attachment protocol of FIG. 1;

(6) FIG. 3c is depicts selected area electron diffraction (SAED) results for the Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the covalent attachment protocol of FIG. 1.

(7) FIG. 3d is a TEM image depicting morphology at 100 nm of the Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by a prior art physical sonication method;

(8) FIG. 3e is a TEM image depicting morphology at 10 nm of Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the prior art physical sonication method;

(9) FIG. 3f is depicts selected area electron diffraction (SAED) results for the Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the prior art physical sonication method;

(10) FIG. 3g is a TEM image depicting morphology at 100 nm of the Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the π-π interaction process of the invention, illustrated in FIG. 2;

(11) FIG. 3h is a TEM image depicting morphology at 10 nm of Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the π-π interaction process of the invention;

(12) FIG. 3i depicts selected area electron diffraction (SAED) results for the Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the π-π interaction process of the invention;

(13) FIG. 4 depicts IR spectra of (a) oxidized MWNTs, (b) APTES-functionalized Fe.sub.3O.sub.4, (c) MWNT-50 wt % Fe.sub.3O.sub.4 heterostructures synthesized by the covalent attachment process of FIG. 1, (d) 4-MBA functionalized Fe.sub.3O.sub.4, (e) MWNT-50 wt % Fe.sub.3O.sub.4 heterostructures synthesized using π-π interaction process of FIG. 2;

(14) FIG. 5a depicts first and second discharge and charge profiles of cells containing the Fe.sub.3O.sub.4-MWNT composite electrodes formed by π-π synthesis process of FIG. 2 tested at a C/10 rate;

(15) FIG. 5b depicts first and second discharge and charge profiles of cells containing the Fe.sub.3O.sub.4-MWNT composite electrodes formed by the prior art sonication (So) process tested at a C/10 rate;

(16) FIG. 5c depicts first and second discharge and charge profiles of cells containing the Fe.sub.3O.sub.4-MWNT composite electrodes formed by the covalent (co) attachment process of FIG. 1 tested at a C/10 rate;

(17) FIG. 5d depicts first and second discharge and charge profiles of cells containing the Fe.sub.3O.sub.4-MWNT-physically mixed control electrodes tested C/10 rate (control);

(18) FIG. 6 is a graph depicting average specific capacity versus cycle number of the cells fabricated by the Fe.sub.3O.sub.4-MWNT-π composite, the Fe.sub.3O.sub.4-MWNT-So composite, the Fe.sub.3O.sub.4-MWNT-Co composite and the Fe.sub.3O.sub.4-MWNT-Control composite;

(19) FIG. 7a depicts CV results of Fe.sub.3O.sub.4-MWNT-π heterostructure at a 0.1 mV/s scan rate;

(20) FIG. 7b depicts CV results of Fe.sub.3O.sub.4-MWNT-So heterostructure at a 0.1 mV/s scan rate;

(21) FIG. 7c depicts CV results of Fe.sub.3O.sub.4-MWNT-CO heterostructure at a 0.1 mV/s scan rate;

(22) FIG. 7d depicts CV results of Fe.sub.3O.sub.4-MWNT-control heterostructure at a 0.1 mV/s scan rate;

(23) FIG. 8A depicts an EIS Nyquist plot of the respective synthesized Fe.sub.3O.sub.4-MWNT-π, Fe.sub.3O.sub.4-MWNT-So, Fe.sub.3O.sub.4-MWNT-CO and Fe.sub.3O.sub.4-MWNT-control heterostructures at a 0.1 mV/s scan heterostructures collected before 30 galvanostatic cycles at a C/10 rate;

(24) FIG. 8B depicts an EIS Nyquist plot of the respective FIG. 8A synthesized heterostructures collected after 30 galvanostatic cycles at the C/10 rate, and including an equivalent circuit used to fit the results;

(25) FIG. 9A depicts Z.sub.re versus ω.sup.−0.5 data associated with electrodes formed with the respective synthesized Fe.sub.3O.sub.4-MWNT-π, Fe.sub.3O.sub.4-MWNT-So, Fe.sub.3O.sub.4-MWNT-CO and Fe.sub.3O.sub.4-MWNT-control composites of the samples analyzed, before 30 cycles of testing; and

(26) FIG. 9A depicts Z.sub.re versus ω.sup.−0.5 data associated with electrodes formed with the respective synthesized Fe.sub.3O.sub.4-MWNT-π, Fe.sub.3O.sub.4-MWNT-So, Fe.sub.3O.sub.4-MWNT-CO and Fe.sub.3O.sub.4-MWNT-physically mixed control composites of the samples analyzed, after 30 cycles of testing.

DETAILED DESCRIPTION OF THE INVENTION

(27) The following detailed description of embodiments of the invention will be made in reference to the accompanying drawings. In describing the invention, explanation about related functions or constructions known in the art are omitted for the sake of clarity in understanding the concept of the invention to avoid obscuring the invention with unnecessary detail.

(28) The inventive method effectively anchors magnetite (Fe.sub.3O.sub.4) nanoparticles (NPs), with average diameters of 8-10 nm, and a loading ratio of 50 wt %, onto multi-walled carbon nanotube (MWNT) sidewalls using a π-π interaction synthesis process, to yield Fe.sub.3O.sub.4-MWNT composite (heterostructures).

(29) Fe.sub.3O.sub.4-MWNT composite (heterostructures) fabricated using the prior processes, including Sonication process, Covalent process and the physically mixed Control process are compared with the heterostructures synthesized by the π-π interaction synthesis process of the invention. Sonication includes dispersing MWNTs in an H.sub.2O: dimethyl sulfoxide (DMSO) mixture by sonication. Covalent attachment process includes dispersing Fe.sub.3O.sub.4 nanoparticles in DMSO and further functionalizing with (3-aminopropyl) triethoxysilane (APTES) by reacting under an N.sub.2 atmosphere to yield amine-terminated Fe.sub.3O.sub.4 (amide formation as a linking bridge).

(30) The π-π interaction process of the invention, includes dispersing Fe.sub.3O.sub.4 nanoparticles in an ethanolic solution of 4-mercaptobenzoic acid (4-MBA) linker molecules, then stirring to facilitate either a monodentate or bidentate coordination mode between the terminal carboxylic acid groups of the 4-MBA and corresponding Fe sites localized on Fe.sub.3O.sub.4 surfaces. The resulting slurry is then reacted with o-MWNTs through sonication in ethanol and DMSO solvents, resulting in stable π-π interactions between the phenyl rings within the aromatic 4-MBA linker molecules and the underlying conjugated MWNT network.

(31) The inventors have verified that electrodes fabricated with composites synthesized through π-π interaction synthesis process provide for efficient charge transfer due to a presence of a conjugated aromatic system, fast Li-ion diffusion rate owing to a relatively short linker length and a favorable retention of a greater degree of physical integrity after cycling. Since Fe.sub.3O.sub.4 has an intermediate voltage, it can be utilized as an anode (when paired with a higher voltage material) or as a cathode (when paired with a lower voltage material).

Examples

(32) Functionalization of MWNTs—Pristine MWNTs (95%, SES Research) are dispersed in concentrated HNO.sub.3 by sonication and subsequently heated to 120° C. for 4 h to remove metal catalysts and carbonaceous impurities, and to correspondingly oxidize and coat the surfaces of the MWNTs with oxygenated moieties, such as carboxylic acid functional groups. The resulting purified and oxidized MWNTs (o-MWNTs) were filtered through a 200 nm polycarbonate membrane (Millipore), thoroughly washed with excess water, and ultimately dried at 80° C. for 18 hours.

(33) Synthesis of Fe.sub.3O.sub.4 NPs—Magnetite (Fe.sub.3O.sub.4) is synthesized using a co-precipitation method similar to that described in S. Zhu, A. C. Marschilok, E. S. Takeuchi, and K. J. Takeuchi, Electrochem. Solid-State Lett., 12, A91 (2009), in which a solution of iron (II) chloride tetrahydrate (FeCl.sub.2.Math.4H.sub.2O) and iron (III) chloride hexahydrate (FeCl.sub.3.6H.sub.2O) were added to a solution containing trimethylamine [N(CH.sub.2CH.sub.3).sub.3] under a nitrogen atmosphere. The isolated powder samples were dried prior to subsequent characterization.

(34) Synthesis of Fe.sub.3O.sub.4-MWNT Composites—

(35) MWNT-Fe.sub.3O.sub.4 synthesized by physical sonication method—Oxidized MWNTs (o-MWNTs) were dispersed in a H.sub.20: dimethyl sulfoxide (DMSO) mixture by sonication to obtain a uniform, well-dispersed black solution. Fe.sub.3O.sub.4 aqueous solution was the added to the black solution (o-MWNTs dispersed in a H.sub.2O: DMSO mixture) in a drop-wise manner (1 mL/min), and the resulting mixture further sonicated for 2 hours. As-prepared heterostructures were then isolated by vacuum filtration and ultimately dried in a vacuum oven at 80° C.

(36) MWNT-Fe.sub.3O.sub.4 synthesized by a “covalent” attachment protocol—As-prepared Fe.sub.3O.sub.4 nanoparticles (NPs) were initially dispersed in DMSO and further functionalized with (3-aminopropyl) triethoxysilane (APTES) by reacting at 85° C. for 18 h under a N.sub.2 atmosphere, followed by thermal curing at 120° C. for 24 h in N.sub.2 in order to generate amine-terminated Fe.sub.3O.sub.4. The scheme incorporates: (i) an acid treatment of MWNTs; (ii) surface functionalization of Fe.sub.3O.sub.4 with APTES molecules; and (iii) heterostructure generation involving amide formation as the linking bridge between the constituent components, i.e. the MWNTs and the Fe.sub.3O.sub.4. The reaction procedures constituting the covalent attachment process are illustrated in FIG. 1.

(37) Specifically, o-MWNTs were dispersed in a H.sub.2O: DMSO mixture by sonication, followed by the addition of 1-ethyl-3-(3-dimethylaminopropyl) carbodiimide (EDC) and N-Hydroxysuccinimide (NBS) in 2-morpholinoethanesulfonic acid (MES) buffer. The mixture was sonicated for 1 h, a process allowing for activation of the surface carboxylic groups on the exterior of the o-MWNTs. NH.sub.2-terminated Fe.sub.3O.sub.4 NPs were dispersed in water to obtain a homogeneous solution and then added into a solution of MWNTs, drop-wise with vigorous stirring for 24 h. The product was later collected using vacuum filtration, washed with excessive water, and ultimately dried in a vacuum oven. EDC, NHS, and MES reagents were purchased from Sigma Aldrich, and used without additional purification.

(38) MWNT-Fe.sub.3O.sub.4 synthesized by a π-π interaction synthesis process—The reaction procedures for attachment utilizing the π-π synthesis process of the invention are depicted in FIG. 2. This synthesis process includes dispersing as-synthesized Fe.sub.3O.sub.4 nanoparticles (NPs) in an ethanolic solution of 4-mercaptobenzoic acid (4-MBA) (Aldrich, 99%) linker molecules, forming a mixture. The mixture was subsequently stirred at 60° C. for 18 h to facilitate either a monodentate or bidentate coordination mode between the terminal carboxylic acid groups of the 4-MBA and the corresponding Fe sites localized on the Fe.sub.3O.sub.4 NP surface. A. Raman, R. Quinones, L. Barriger, R. Eastman, A. Parsi, and E. S. Gawalt, Langmuir, 26, 1747 (2010).

(39) The resulting functionalized product was isolated by vacuum filtration and further washed with ethanol for multiple times to remove any remaining, unbound 4-MBA linkers. The 4-MBA functionalized Fe.sub.3O.sub.4 microspheres were further reacted with the oxidized MWNTs (o-MWNTs), through sonication in a mixture of ethanol and DMSO (in a 3:1 volume ratio) solvents for 2 h. This process formed stable π-π interactions between the phenyl rings within the aromatic 4-MBA linker molecules and the underlying conjugated MWNT network. The resulting composites were subsequently vacuum filtered, washed, and ultimately dried in a vacuum oven at 80° C.

(40) Structural Characterization

(41) X-ray diffraction (XRD)—Fe.sub.3O.sub.4 samples were characterized by X-ray powder diffraction (XRD) using a Rigaku SmartLab X-ray powder diffractometer. CuKα radiation was utilized with a Bragg-Brentano focusing geometry. The full width at half maximum (FWHM) of the (311) peak was determined using the Peak Fit software. Crystallite sizes were determined using the Scherrer equation after correcting for instrumental broadening using a lanthanum hexaboride (LaB6) standard. P. Scherrer, Nachr. Ges. Wiss. Gottingen, 96 (1918).

(42) Electron microscopy—As-synthesized Fe.sub.3O.sub.4-MWNT samples prepared by the three different attachment protocols were dispersed in ethanol and sonicated for 2 minutes to ensure a uniform dispersion. One drop of the solution was evaporated onto a 300 mesh Cu grid, which was coated with a lacey carbon film. TEM characterization, including data associated with morphology and selected area electron diffraction, was performed on a JEOL JEM 2100F TEM instrument, equipped with a field-emission electron gun operating at 200 kV and a high-resolution pole-piece with a 0.19 nm point-to-point resolution.

(43) Thermo-gravimetric analysis (TGA)—Data were acquired using a TGA Q500 instrument over a relatively broad temperature range spanning from 30 to 800.0 under an air atmosphere, using a set heating rate of 10° C./min.

(44) FT-mid-IR—Relevant data were obtained on a Nexus 670 (Thermo Nicolet) spectrometer equipped with a single-reflectance zinc selenide (ZnSe) ATR accessory, a KBr beam splitter, and a DTGS KBr detector. Specifically, solid samples were placed onto a ZnSe crystal. Measurements were obtained in reflectance mode by using the Smart Performer module.

(45) Electrochemical Methods

(46) Preparation of Fe.sub.3O.sub.4 electrodes—Tape cast electrodes of Fe.sub.3O.sub.4-MWNT were prepared on copper foil using a combination of 80% active material (MWNT-Fe.sub.3O.sub.4 50 wt % heterostructures), 10% carbon black, 7% polyvinylidene fluoride (PVDF) binder, and 3% graphite by weight. A control sample was prepared by physically mixing together 40% Fe.sub.3O.sub.4, 40% MWNT, 10% carbon black, 7% PVDF, and 3% graphite by weight.

(47) Electrochemical testing—The electrodes prepared as noted above were used to assemble two-electrode coin type cells. The cells were assembled using a lithium foil electrode and an electrolyte containing 1.0 M of lithium hexafluorophosphate (LiPF.sub.6) in ethylene carbonate and dimethyl carbonate (30/70, v/v).

(48) Cycling tests were conducted using a Maccor Battery Tester at 30° C. Lithium/magnetite (Li/Fe.sub.3O.sub.4) cells were initially discharged to 0.2 V at a C/10 (92.6 mA/g) discharge rate for 30 cycles, followed by a rate capability test with discharge rates applied in the sequence of 200, 400, 800, 100, 1200, 1600, and 2000 mA/g with the C/10 rate used again for the next 50 cycles. All of the charge rates were set at C/10 using voltage limits of 0.2 and 2.5 V. Cyclic voltammetry (CV) data were collected using a two-electrode configuration wherein the reference and counter electrodes were both lithium metal. Voltage limits for the CV test were 0.1 V and 2.5 V at a scan rate of 0.1 mV/s. Electrochemical impedance spectroscopy (EIS) data were collected over a frequency range of 100 kHz to 10 mHz with a 10 mV amplitude.

(49) Results and Analysis:

(50) In these examples, we demonstrated that Fe.sub.3O.sub.4 nanoparticles (NPs) with an average size of 8-10 nm and a loading ratio of 50 wt % have been successfully attached onto the external surfaces of multi-walled carbon nanotubes (MWNTs) by means of three different preparative approaches, namely a sonication method, a covalent attachment protocol, as well as a π-π interaction strategy. Specifically, the Fe.sub.3O.sub.4 NPs associated with the sonication method lie directly on the outer surfaces of the MWNTs. Particles covalently attached onto the MWNTs formed amide chemical bonds through the mediation of the amorphous (3-minopropyl) triethoxysilane (APTES) linker. Finally, particles were anchored onto the underlying conjugated MWNTs via an aromatic 4-mercaptobenzoic acid (4-MBA) linker.

(51) Both structural and electrochemical characterization protocols have been used to systematically correlate the electrode performance with the corresponding attachment strategies. Fe.sub.3O.sub.4-MWNT composites generated by the π-π interaction strategy delivered 813, 768, 729, 796, 630, 580, 522, and 762 mAh/g under rates of 200, 400, 800, 100, 1200, 1600, 2000, and 100 mA/g, with 72% retention between cycles 2 and 80, demonstrating both higher capacity and better cycling stability as compared with analogues derived from the physical sonication as well as covalent attachment strategies. This finding may be attributed to the enhanced charge and ion transport coupled with retention of physical contact with the underlying MWNTs after a large volume change during cycling. Our collective results suggest that the π-π attachment modality is a more effective preparative strategy for enhancing the performance of MWNT-Fe.sub.3O.sub.4 composite electrodes after a full discharge process.

(52) Structure and morphology of the MWNT-Fe.sub.3O.sub.4 Heterostructures—Pristine MWNTs, obtained from SES Research, possess an overall nanotube content of 95 wt %, and measure 10-30 nm in diameter as well as ˜1-2 μm in length. The major impurities in the pristine MWNTs consist of amorphous carbon. After chemical functionalization, the oxidized MWNTs evince a relatively clean tube-like morphology with no observable impurities. The XRD pattern of as-prepared Fe.sub.3O.sub.4 NPs was recorded and showed excellent correspondence to a literature pattern of Fe.sub.3O.sub.4. In this study, all of the magnetite powder samples possessed crystallite sizes of 8-10 nm.

(53) FIGS. 3a-c are images depicting morphology, at 100 nm (FIG. 3a) and 10 nm (FIG. 3b) and phase (FIG. 3c) of Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the covalent attachment protocol. FIGS. 3d-f are images depicting morphology, at 100 nm (FIG. 3d) and 10 nm FIG. 3e) and phase (FIG. 3f) of Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by physical sonication. FIGS. 3g-i are images depicting morphology, at 100 nm (FIG. 3g) and 10 nm FIG. 3h) and phase (FIG. 3i) of Fe.sub.3O.sub.4-MWNT composites with a 50 wt % of Fe.sub.3O.sub.4 loading, synthesized by the π-π interaction procedure.

(54) The Fe.sub.3O.sub.4 loading ratio in each composite formed by the three respective methods was confirmed by TGA profile, where nearly all of the Fe.sub.3O.sub.4 NPs were found to be 8-10 nm, and preferentially adhered onto external surfaces of the MWNTs.

(55) The spatial distribution of Fe.sub.3O.sub.4 NPs is more uniformly dispersed and these NPs are in direct contact with the underlying MWNTs in the composite generated by sonication (FIG. 3d). By contrast, a more uneven, aggregated and cluttered distribution of NPs is found in heterostructures prepared using the covalent-attachment method (FIG. 3a) and the π-π interaction synthesis process protocol (FIG. 3g). High resolution TEM images show that the Fe.sub.3O.sub.4 NPs associated with the sonication method lie directly on the outer surface of the MWNTs (FIG. 3c), whereas covalently attached particles apparently and presumably show a presence of AOTES coating (FIG. 3b). Selected area electron diffraction (SAED), as presented in FIGS. 3c, 3f and 3i, confirm that the NPs within the heterostructures synthesized by all three methods can be ascribed to pure magnetite phase.

(56) Electrodes fabricated with composites synthesized through π-π interaction synthesis process provide for efficient charge transfer due to a presence of a conjugated aromatic system, fast Li-ion diffusion rate owing to a relatively short linker length and a favorable retention of a greater degree of physical integrity after cycling. Using both structural and electrochemical characterization protocols, the 3 attachment modalities were correlated to the corresponding electrode (fabricated with composite material synthesized by the 3 attachment methods or modalities) performances.

(57) The observed differences are understood to be due to the attachment strategy employed. Physical sonication induces adsorption of nanoparticles (NPs) onto the MWNT surface, where inherently weak and more randomized van der Waals interactions exist between the NPs and the MWNTs. Consequently, these randomized van der Waals interactions may be more easily destroyed upon rigorous processing of the resulting nanocomposite, i.e., by the full discharge process. By contrast, electrodes formed with Fe.sub.3O.sub.4-MWNT composites generated by attaching the Fe.sub.3O.sub.4 to the MWNTs, through the mediation of bridging 4-mercaptobenzoic acid (4-MBA) linker molecules, is found to promote (i) an efficient charge transfer process due to the presence of a conjugated aromatic system, (ii) a fast Li-ion diffusion rate, owing to a relatively short length of the linker, and (iii) favorable retention of a greater degree of physical integrity after cycling.

(58) The FT-IR spectra of o-MWNTs, of APTES and 4-MBA functionalized Fe.sub.3O.sub.4, and covalently-formed and π-π stacking formed MWNT-50 wt % Fe.sub.3O.sub.4 composites are depicted in FIG. 4 (a-e, respectively). The IR spectra shown in (a) of FIG. 4 confirms the success of acid functionalization of the MWNTs (Y. Si and E. T. Samulski, Nano Lett., 8, 1679 (2008).), where the IR spectra in (b) of FIG. 4 confirms effective functionalization with APTES. R. Villalonga, M. L. Villalonga, P. Diez, and J. M. Pingarron, J. Mater. Chem., 21, 12858 (2011). IR spectra depicted in (c) of FIG. 4 confirms formation of a chemical bond between the MWNTs and the Fe.sub.3O.sub.4. IR spectra depicted in (d) confirms successful functionalization (C+O bond associated with the 4-MBA linker) and that of (e) of FIG. 4 confirms that the attachment is the result of strong π-π stacking interactions between the phenyl ring in the MBA linker and the underlying conjugated MWNT network.

(59) The 4-MBA coated Fe.sub.3O.sub.4 sample (see (d) of FIG. 4) gave rise to a sharp peak located at 1680 cm−1, corresponding to the stretching mode of the C═O bond associated with the 4-MBA linker. Peaks located at 1592 and 1400 cm−1 are due to the phenyl ring stretching mode derived from 4-MBA, an observation suggestive of a successful functionalization process. After attaching MBA-coated Fe.sub.3O.sub.4 onto the MWNTs (see (e) of FIG. 4), the two ring stretching peaks shifted from 1592 and 1400 cm−1 to 1589 cm−1 and 1394 cm−1, respectively, a result which was likely induced mainly by the presence of strong π-π stacking interactions between the phenyl ring within the MBA linker and the underlying conjugated MWNT network. This shift implies a ‘softening’ of the C═C bonds, and has been linked to an expansion of the C—C bonds. D.-Q. Yang, J.-F. Rochette, and E. Sacher, J. Phys. Chem. B, 109, 4481 (2005); Y. Zhang, S. Yuan, W. Zhou, J. Xu, and Y. Li, J. Nanosci. Nanotechnol., 7, 2366 (2007).

(60) Electrochemical evaluation of Fe.sub.3O.sub.4-MWNT composite heterostructures—Cells prepared using a two electrode configuration with the three variously prepared MWNT-Fe.sub.3O.sub.4 composites, generated by sonication (Fe.sub.3O.sub.4-MWNT-So, 50% of Fe.sub.3O.sub.4 wt.), covalent attachment (Fe.sub.3O.sub.4-MWNT-Co, 50% of Fe.sub.3O.sub.4 wt.) and π-π interaction synthesis process (Fe.sub.3O.sub.4-MWNT-π, 50% of Fe.sub.3O.sub.4 wt.), were discharged to 0.2 V and then charged to 3.0 V at a C/10 rate (IC=926 mAh/g). FIGS. 5a-d highlight the first two discharge/charge cycles profiles of all three of the cells together with that of the control sample, as shown, respectively. All of the Fe.sub.3O.sub.4-MWNT samples are found to evince similar discharge/charge profiles. FIG. 5a in particular indicates some critical points during the initial discharge process of Fe.sub.3O.sub.4.

(61) Fe.sub.3O.sub.4 possesses an inverse spinel structure, with Fe.sup.3+ occupying tetrahedral sites (Wyckoff position 8a). The octahedral sites (Wyckoff position 16d) are occupied by both Fe.sub.3+ and Fe.sub.2+ in a cubic close packed array of 0.sup.2− ions. M. E. Fleet, J. Solid State Chem., 62, 75 (1986).

(62) During the initial stage of lithiation (x<2, where ‘x’=lithiation amount), Li.sup.+ ions insert into vacant octahedral (16c) sites. M. M. Thackeray, W. I. F. David, and J. B. Goodenough, Mater. Res. Bull., 17, 785 (1982); J. Fontcuberta, J. Rodriguez, M. Pernet, G. Longworth, and J. B. Goodenough, J. Appl. Phys., 59, 1918 (1986).

(63) At low Li.sup.+ concentrations, 8a Fe ions are displaced into the 16c site by electrostatic repulsion. Additional Li ions fill the octahedral holes (16c) and the now empty tetrahedral holes. The result of this initial electrochemical insertion mechanism is the transformation of the A[B.sub.2]O.sub.4 spinel phase into a (LiA)[B.sub.2]O.sub.4 rock salt type phase. The initial lithiation via the insertion mechanism yields a theoretical capacity of 230 mAh/g of Fe.sub.3O.sub.4. Further lithiation is proposed to form Li.sub.2O and Fe metal, as supported by recent X-ray absorption spectroscopy results. M. C. Menard, K. J. Takeuchi, A. C. Marschilok, and E. S. Takeuchi, Phys. Chem. Chem. Phys., 15, 18539 (2013).

(64) From points A to B, less than one Li+ ion can get into Fe.sub.3O.sub.4. At this level of lithiation, a rock salt type phase Li.sub.xFe.sub.3O.sub.4 (0<‘x’<2) is formed and at this discharge level, the lithiation process occurs via the insertion mechanism. The cubic close packed array of oxygen atoms remains intact. After lithiation of more than 2 equivalents of electrons (>point C), the conversion reaction becomes the dominant lithiation mechanism and is accompanied by dramatic structural changes during the advanced discharge process. This proposed transformation process can occur through the formation of a (LiA)[B.sub.2]O.sub.4 rock salt type phase followed by conversion to Fe metal, thereby resulting in an additional 690 mAh/g of capacity. W. Zhang, D. C. Bock, C. J. Pelliccione, Y. Li, L. Wu, Y. Zhu, A. C. Marschilok, E. S. Takeuchi, K. J. Takeuchi, and F. Wang, Adv. Energy Mater., (2016).

(65) The majority of the Fe.sub.3O.sub.4 conversion likely takes place between points C and D. The heterostructure incorporating MWNT starts to contribute additional capacity to the initial discharge at ˜0.8 V, in which the large irreversible capacities measured for Fe.sub.3O.sub.4-MWNT at cycle 2 are consistent with the formation of a solid electrolyte interface (SEI) at low voltage. D. T. Welna, L. Qu, B. E. Taylor, L. Dai, and M. F. Durstock, J. Power Sources, 196, 1455 (2011); Y. W. E. P. B. Balbueng, Lithium-Ion Batteries: Solid Electrolyte Interphase, Imperial College Press, London (2004).

(66) Among the four types of cell generated, the Fe.sub.3O.sub.4-MWNT-π sample yielded the highest initial capacity at ˜1700 mAh/g. By contrast, the analogous capacities of Fe.sub.3O.sub.4-MWNT-So heterostructures, Fe.sub.3O.sub.4-MWNT-Co heterostructures, and physically mixed Fe.sub.3O.sub.4-MWNT control samples were noticeably lower, and in fact, were measured to be ˜1600 mAh/g, ˜1350 mAh/g, and 1500 mAh/g, respectively (FIG. 5a-d). This trend was also observed in the 2nd cycle (FIG. 5a-d), wherein the highest capacity was observed with the Fe.sub.3O.sub.4-MWNT-π sample, as compared with all other types of attachment modalities analyzed.

(67) Specific capacity versus cycle number. The average specific capacity versus cycle number of the cells is shown in FIG. 6. A total of 80 cycles using sequential rates of C/10 (92.6 mA/g), 100, 200, 400, 8OO, 1200, 1600, and 2000 mA/g rate were tested. A galvanostatic cycling test with a C/10 rate was applied for the first 30 cycles to evaluate the reversibility of different Fe.sub.3O.sub.4-MWNT attachment modalities. The Fe.sub.3O.sub.4-MWNT-π sample delivered ˜1100 mAh/g in cycle 2 and ˜S50 mAh/g in cycle 30 (80% retention). The other analogous samples yielded less capacity and demonstrated a lower capacity retention. For example, the Fe.sub.3O.sub.4-MWNT-So heterostructures yielded ˜916 mAh/g on cycle 2 but only ˜718 mAh/g in cycle 30 (i.e. ˜73% retention). The Fe.sub.3O.sub.4-MWNT-Co heterostructures gave rise to ˜883 mAh/g on cycle 2 but merely about 570 mA/g on cycle 30 (i.e. 65% retention). Finally, the physically mixed Fe.sub.3O.sub.4-MWNT control samples furnished ˜900 mAh/g in cycle 2 but a much lower about 553 mAh/g with cycle 30 (i.e. 61% retention).

(68) Hence, the π-π stacking Fe.sub.3O.sub.4-MWNT materials delivered not only higher capacity but also exhibited better capacity retention as compared with the series of physically sonicated, covalently attached, and control samples over 30 cycles. After 30 cycles, the second rate capability test was applied. The discharge rates were increased between 200 mA/g to 2000 mA/g, while the charge rates for all cycles were maintained at C/10 (92.6 mA/g) until the 80.sup.th cycle. As the rates were increased, larger differences in capacities were observed for the cells with different modes of Fe.sub.3O.sub.4-MWNT attachment. Notably, the Fe.sub.3O.sub.4-MWNT-π sample exhibited both higher capacity and capacity retention as compared with the series of physically sonicated, covalently attached, and control samples after 30 cycles. In particular, the Fe.sub.3O.sub.4-MWNT-π sample gave rise to 813, 76S, 729, 796, 630, 580, 522, and 762 mAh/g under rates of 200, 400, 800, 100, 1200, 1600, 2000, and 100 mA/g, with 72% retention after 80 cycles.

(69) The corresponding data for the other samples tested can be summarized as follows. The Fe.sub.3O.sub.4-MWNT-So heterostructures yielded 733, 665, 624, 658, 492, 497, 472, and 576 mAh/g; the Fe.sub.3O.sub.4-MWNT-Co heterostructures delivered 606, 528, 474, 519, 330, 318, 285, and 418 mAh/g; and finally, the physically mixed control samples produced 556, 467, 399, 460, 269, 265, 246, and 360 mAh/g at cycles 31, 36, 41, 45, 56, 61, 66, and 71, respectively. In addition, there was less capacity variation for the cells derived from the Fe.sub.3O.sub.4-MWNT-π sample, during the cycling testing, as compared with the other types of CNT attachment.

(70) In effect, the Fe.sub.3O.sub.4-MWNT-π sample compared favorably with what has been previously reported in the literature. Specifically, the Fe.sub.3O.sub.4-MWNT-π sample was found to deliver higher capacities than both (i) the porous Fe.sub.3O.sub.4/MWCNT composites generated by Pang, et al., which yielded 601 mAh/g and 450 mAh/g under rates of 100 and 2000 mA/g (X.-J. Pang, J. Zhang, G.-W. Qi, X.-H. Dai, J.-P. Zhou, and S.-Y. Zhang, J. Alloys Compd., 640, 8 (2015)), as well as (ii) the MWCNT-Fe.sub.3O.sub.4-rGO nanocomposites, developed by Yang, et al., which produced measured capacities of 680 mAh/g and 250 mAh/g under rates of 200 and 1200 mA/g. S. Yang, C. Cao, G. Li, Y. Sun, P. Huang, F. Wei, and W. Song, Nano Research, 8, 1339 (2015).

(71) Cyclic voltammetry—In order to further probe the implications of the different attachment modalities, cyclic voltammetry (CV) data of the Fe.sub.3O.sub.4-MWNT samples, generated using π-π stacking, sonication, and covalent attachment protocols, were collected and analyzed in the context of Li.sup.+ insertion/extraction as well as of Fe.sub.3O.sub.4 conversion, as depicted in FIGS. 7a-f, as shown, respectively. The first three cycles were scanned at 0.1 m V/s within a voltage window of 0.1 and 2.5 V. The π-π stacking, sonication-mediated, and covalently attached Fe.sub.3O.sub.4-MWNT cells gave rise to three peaks located at about 1.7 V, ˜1.2 V, and 0.7 V for the initial discharge step. This observation is consistent with the galvanostatic initial discharge step characterized by three discharge plateaus.

(72) With respect to a comparison of the two composites derived from the use of different chemical linkers, i.e. APTES and 4-MBA, the MBA-mediated, π-π stacked Fe.sub.3O.sub.4-MWNT-π cell possesses a sharper cathodic peak at about 2500 mA/g with a peak positioned at ˜0.7 V as compared with the corresponding cathodic peak of the APTES-derived, covalently attached Fe.sub.3O.sub.4-MWNT-Co structure, at about 0.74 V at about 2100 mA/g. The observation of a “sharp” cathodic peak can be explained by the conversion of Fe.sub.3O.sub.4 to Fe and the formation of Li.sub.2O in addition to some irreversible reaction of electrolyte. D. C. Bock, K. C. Kirshenbaum, J. Wang, W. Zhang, F. Wang, J. Wang, A. C. Marschilok, K. J. Takeuchi, and E. S. Takeuchi, ACS Appl. Mater. Interfaces, 7, 13457 (2015).

(73) A broad anodic peak was observed at ˜1.80 V, corresponding to the reversible oxidation of Fe.sup.o.fwdarw.Fe.sup.2+ during the anodic process. In the 2.sup.nd cycle (FIG. 7a-d), both reduction and oxidation peaks were shifted to more positive voltages, thereby indicating an increased polarization of the electrode materials in the initial cycles. L. Ji, Z. Tan, T. R. Kuykendall, S. Aloni, S. Xun, E. Lin, V. Battaglia, and Y. Zhang, Phys. Chem. Chem. Phys., 13, 7170 (2011). The π-π stacked, Fe.sub.3O.sub.4-MWNT heterostructures exhibit higher peak currents as compared with their covalently-attached Fe.sub.3O.sub.4-MWNT heterostructure counterparts.

(74) In order to explain the better electrode performance associated with the Fe.sub.3O.sub.4-MWNT-π heterostructure sample, as compared with the other three analogues, the structural differences amongst the various Fe.sub.3O.sub.4-MWNT composites prepared using different attachment modalities were considered. Specifically, the conjugated 4-MBA linker contains an aromatic π-electron system together with terminal carboxylic acid and thiol groups; it possesses the characteristics of a conductive binder. Not surprisingly, MBA molecules have been used in surface enhanced Raman scattering applications associated with silver and gold (A. Michota and J. Bukowska, J. Raman Spectrosc., 34, 21 (2003); F. Wang, R. G. Widejko, Z. Yang, K. T. Nguyen, H. Chen, L. P. Fernando, K. A. Christensen, and J. N. Anker, Anal. Chem., 84, 8013 (2012), as well as in the context of self-assembled monolayers (SAMs) for bio-sensing. S. M. Rosendahl and I. J. Burgess, Electrochim. Acta, 53, 6759 (2008). It is believed that there have been no studies considering the application of MBA in battery electrode design.

(75) In the inventive method, the MBA-coated Fe.sub.3O.sub.4 attaches onto MWNTs through π-π electron conjugated interactions, which allow for more efficient electron transfer between the 2 species. This results in a lower charge transfer resistance. By contrast, covalently-produced Fe.sub.3O.sub.4-MWNT heterostructures were prepared using bulky, long-chain, and insulating APTES linkers in order to chemically connect the Fe.sub.3O.sub.4 NPs with the pendant carboxylic groups on the functionalized MWNTs. A prior report examined the use of the APTES linker for Fe.sub.3O.sub.4 immobilized onto a glassy carbon substrate and reported on an increased charge transfer resistance due to the presence of the linker. H. Yin, Y. Zhou, T. Liu, T. Tang, S. Ai, and L. Zhu, J. Solid State Electrochem., 16, 731 (2012).

(76) In addition, additional studies suggest that the presence of unwieldy, bulky, and non-conjugated ligands can act to deter charge transport between adjacent nanoparticles and nanostructures. L. Wang, J. Han, B. Sundahl, S. Thornton, Y. Zhu, R. Zhou, C. Jaye, H. Liu, Z. Q. Li, G. T. Taylor, D. A. Fischer, J. Appenzeller, R. J. Harrison, and S. S. Wong, Nanoscale, 8, 15553 (2016); T. Virgili, I. S. Lopez, B. Vercelli, G. Angella, G. Zotti, J. Cabanillas-Gonzalez, D. Granados, L. Luer, R. Wannemacher, and F. Tassone, J. Phys. Chem. C, 116, 16259 (2012).

(77) By contrast with their non-conjugated counterparts, the presence of electron-rich, conjugated systems, such as the 4-MBA in our work, is more efficacious at enabling, assisting, and ultimately promoting the charge transfer process. Thus, a higher specific capacity of the Fe.sub.3O.sub.4-MWNT-π cells as compared with their Fe.sub.3O.sub.4-MWNT-Co cell analogues can be rationalized as emanating from the reduced charge transfer resistance, due to the presence of the aromatic 4-MBA linkage. When comparing the performance of sonication-mediated Fe.sub.3O.sub.4-MWNT heterostructures as well as of the Fe.sub.3O.sub.4-MWNT-control composites, the Fe.sub.3O.sub.4-MWNT-π heterostructure sample delivered not only a higher capacity but also a better cycling stability, understandably due to more robust and stabilizing interactions between the Fe.sub.3O.sub.4 and the adjoining MWNTs, made possible by the presence of the 4-MBA linker molecules. The Fe.sub.3O.sub.4-MWNT-π cells understandably, readily accommodate for the drastic volume change occurring during the cycling process itself.

(78) Electrochemical impedance spectroscopy (EIS)—EIS data were collected before and after 30 galvanostatic cycles for the Fe.sub.3O.sub.4-MWNT-π, Fe.sub.3O.sub.4-MWNT-So, Fe.sub.3O.sub.4-MWNT-Co and Fe.sub.3O.sub.4-MWNT-control heterostructures to gain insight into the reaction kinetics and the effect of the different attachment methods (used to synthesize the respective composites) on the transfer of lithium ions. FIGS. 8A and 8B depict EIS Nyquist plots of the respective synthesized heterostructures collected before and after 30 galvanostatic cycles. An equivalent circuit (part of FIG. 8B) was used to fit the results. As shown, the sum of R1 and R2 represents the charge transfer resistance R.sub.ct; CPE is the constant phase element; and W.sub.o is the Warburg impedance. Before cycling of the cells, the EIS data showed that the Fe.sub.3O.sub.4-MWNT-π (−23Ω), Fe.sub.3O.sub.4-MWNT-So (−11Ω), Fe.sub.3O.sub.4-MWNT-Co (−15Ω), and Fe.sub.3O.sub.4-MWNT-Control (about 11Ω) samples gave rise to small semicircles, thereby indicating all materials had relatively small R.sub.ct values before electrochemical cycling.

(79) All of the cells nevertheless revealed larger R.sub.ct values after 30 cycles. Notably, the R.sub.ct values of the Fe.sub.3O.sub.4-MWNT-Co heterostructures increased more significantly as compared with the other samples to a value of −145Ω. By contrast, Fe.sub.3O.sub.4-MWNT-π exhibited a R.sub.ct value of only −30Ω. These data indicate that the Fe.sub.3O.sub.4-MWNT-π heterostructure sample possessed smaller charge transfer resistance values as compared with the corresponding sonication-mediated Fe.sub.3O.sub.4-MWNT-So and covalently processed Fe.sub.3O.sub.4-MWNT-Co samples.

(80) The EIS and Z.sub.re versus ω.sup.−0.5 data associated with the electrodes corresponding to all of the Fe.sub.3O.sub.4-MWNT-π, Fe.sub.3O.sub.4-MWNT-So, Fe.sub.3O.sub.4-MWNT-Co and Fe.sub.3O.sub.4-MWNT-control heterostructures samples analyzed, before and after 30 cycles, are shown in FIGS. 9A and 9B, respectively. By comparing the behavior of cells before and after 30 cycles, a trend of increasing slope for the Warburg impedance (σ) was observed for each of the samples. The diffusion coefficients calculated from Equations 1 and 2 below indicate that the larger the σ, the smaller the magnitude of the lithium ion diffusion coefficient for the Fe.sub.3O.sub.4-MWNT materials. The fitting summary for R.sub.s, R.sub.ct, σ, as well as the diffusion coefficient number (D.sub.Li.sup.+) for all of the materials analyzed has been put together. The fitting results suggest that the Fe.sub.3O.sub.4-MWNT-π heterostructure sample exhibited the highest effective lithium ion diffusion rate, after cycling (i.e. 2.06×10.sup.−11 cm2/s).
D.sub.Li+=(R.sup.2T.sup.2)/(2A.sup.2n.sup.4F.sup.4C.sup.2σ.sup.2)  (Equation 1)
Z.sub.re ασω.sup.−1/2  (Equation 2)

(81) Additional embodiments of the compositions and method described herein are provided in the enclosed appendices.

(82) While the invention has been described in connection with a manufacture of Fe.sub.3O.sub.4 based electrodes for cells and batteries, it is intended that these materials may also be used for other electrodes, i.e., cathodes and anodes. As shown and described with reference to certain embodiments, it will be understood by those skilled in the art that various changes in from and details may be made to these embodiments without departing from the spirit and scope of the present invention and equivalents thereof.