Background of the Invention Nanostructures, such as nanotubes and nanowires, exhibit technologically important electronic properties and have shown promising applications, including nanoscale electronic and optical devices, high strength materials, electron field emission devices, tips for scanning probe microscopy, and chemical sensors. Boron nanostructures have recently attracted much attention because they are predicted to possess special properties superior to those of other one-dimensional nano-materials.

For example, boron nanotubes appear to be stable and, independent of structural helicity, have metallic conductivities exceeding those of carbon nanotubes. Metallic nanotubes can carry large current densities and, by themselves, may be useful for providing electrical interconnects and switches.

Boron compounds have also received renewed interest as a result of the discovery of superconductivity in MgB2. Measurements of the upper critical field, Hc2 (T), the thermodynamic critical field, He (T), and the critical current, Jc, indicate that MgB2 is a type-II superconductor with a superconducting transition temperature of To =40 K and properties that are consistent with an intermetallic superconductor. Measurements of

the boron isotope effect in this compound are consistent with the superconductivity being mediated via electron-phonon coupling.

Recent band structure calculations point to the importance of two-phonon pairing for resonant exchange between Cooper pairs in boron compounds such as MgB2. The band structure is also known to depend on the dimensionality of the electron and phonon system. For example, the electron pairing potential can be enhanced in MgB2- nanotubes by several gaps in the phonon density of states, thereby synergetically enhancing both Tc and Je. Such high-temperature superconductors are expected to be important, for example, for efficient lossless transmission of electric power.

It would therefore be desirable to provide a process for the growth of boron-based one-dimensional and two-dimensional nanostructures, such as nanowires and nanotubes, in particular singe-wall nanotubes, with controlled chemical and physical properties and dimensionality in or on a suitable framework material, as well as devices using such nanowires and nanotubes with properties that are superior to those found in three-dimensional structures made from the same or a similar material.

Summary of the Invention The invention relates to the growth of boron nanostructures, such as nanotubes and nanowires, with a controlled diameter, a narrow diameter distribution, and controlled chemical and physical properties on mesoporous siliceous frameworks, such as MCM-41. Devices made with the process of the invention can exhibit unique electronic properties due to their low dimensionality, such as high-temperature superconductivity.

According to one aspect of the invention, one-dimensional superconducting

device includes a boron nanostructure that has a diameter of less than 100 nm and is impregnated with an electron donor element, wherein the boron nanostructure exhibits a superconducting transition temperature greater than 36 degrees K.

According to another aspect of the invention, an arrangement of superconducting single-wall boron nanotubes includes a framework made of mesoporous silica having pores with a pore size that has a predetermined dimensional relationship with a diameter or cross-sectional area of the boron nanotubes. An element capable of forming a boron complex is dispersed in the pores, and single-wall boron nanotubes are disposed in the pores of the framework and doped with an electron donor element.

The boron nanotubes exhibit a superconducting transition temperature greater than 36 degrees K.

According to yet another aspect of the invention, a method for producing a boron nanostructure includes the steps of specifying a diameter or cross-sectional area of the boron nanostructure, selecting a framework having pores with a pore size that has a predetermined dimensional relationship with the diameter or cross-sectional area of the boron nanostructure, wherein the framework includes an element capable of forming a complex with boron, and contacting, in a reactor, the framework with a boron precursor at a temperature sufficient to produce the boron nanostructures with the specified diameter or cross-sectional area.

Embodiments of the invention may include one or more of the following features. The electron donor element can be an element of Group la or Group IIa of the periodic table of elements, such as Lithium, Beryllium and/or Magnesium, for example, in form of a metal vapor. The boron nanostructure can be a nanowire having a diameter of, for example, less than 50 nm or a nanotube, for example a single-wall

nanotube, with a diameter of, for example, less than 10 nm. The nanostructure can also be a nanofiber with a diameter of, for example, less than 1 nm. The boron atoms of the nanofibers can be arranged in a polyethylene-like chain structure, with the nanofibers aligned in a parallel fashion or intertwined.

The as-grown boron nanostructure can also be exposed to an ambient containing magnesium to form magnesium diboride (MgB2), which is a superconductor with a reported superconducting transition temperature of around 35 K in crystalline form.

The element dispersed in pores can be Mg, B, Ni, Pd, Ce, Co, Mn, Mo and/or Al, or mixtures thereof, which tend to form complexes with boron. Before growth of the nanostructures, the mesoporous silica can be exposed to a precursor of the electron donor element, optionally with the addition of hydrogen.

To increase the selectivity for nanotubes, the as-grown nanostructure, which can also include nanowires, fibers and needles, can be oxidized and subsequently exposed to an alkaline solution, for example a mixture of NaOH and ethanol/water, thereby retaining predominantly boron nanotubes.

Further features and advantages of the present invention will be apparent from the following description of preferred embodiments and from the claims.

Brief Description of the Drawings The following figures depict certain illustrative embodiments of the invention in which like reference numerals refer to like elements. These depicted embodiments are to be understood as illustrative of the invention and not as limiting in any way.

FIG. 1 shows a high-resolution TEM image of an exemplary boron single wall nanotube grown on Mg-MCM-41;

FIG. 2 shows a high-resolution TEM image of a boron nanopipe grown at a higher temperature than the nanotube in FIG. 1; FIG. 3 shows a high-resolution TEM image of bundles of nanowires ; FIG. 4 shows a high-resolution TEM image of groups of nanotubes with uniform diameters; FIG. 5A shows a high-resolution electron micrograph of a boron nanostructure on a carbon-coated grid; FIG. 5B shows boron-K-edge mapping of the boron nanostructure of FIG. 5A ; FIG. 5C shows carbon-K-edge mapping of the boron nanostructure of FIG. 5A ; FIG. 6 shows Raman spectra of a boron nanostructure at two excitation wavelengths indicative of a nanotube configuration.

Detailed Description of Certain Illustrated Embodiments The process described herein is directed, inter alia, to the growth of boron-based nanotubes and nanowires with a controlled diameter and with controlled chemical (such as composition, doping) as well as physical (such as electrical and superconducting) properties.

The process for the growth of boron nanotubes of controlled and uniform diameter uses a templated technique for nanotube synthesis similar to the process that was successfully applied to the grow of aligned single walled carbon nanotubes with a uniform diameter, as described, for example, in commonly assigned US Patent Application Ser. No. 10/328857, filed 18-Dec-2002, and US Patent Application Ser.

No. 10/726394, filed 02-Dec-2003, the contents of which are incorporated herein by reference in their entirety. The template employs a mesoporous silica framework, for example MCM-41, with a parallel system of cylindrical pores having a very narrow distribution of diameters ( : L 0. 1 nm full width at half maximum-FWHM) centered at a preselected pore diameter ranging from 1.5-3. 5 nm. The pore size of the framework can be controlled by a surfactant and a swelling agent used in the preparation of the framework. The growth of carbon nanotubes disclosed in the above-referenced patent applications is initiated by incorporating an atomically dispersed catalyst or catalyst precursor into substitutional sites in or on the pore walls of the MCM-41 material.

The template pore diameter can be modified independently of the chemical composition of the pore wall.

Boron nanotubes were grown by using a magnesium-substituted MCM-41 template with a uniform pore diameter of 3.6 (0. 1) nm. A 6 mm internal diameter quartz reactor was loaded with 200 mg of freshly prepared Mg-MCM-41 template supported in the reactor on an alumina plug. The reactor was placed into an electric furnace and heated under continuous flow of hydrogen to 870°C. When a steady state temperature was reached, BC13 from Air Products and Chemicals, Inc. (99.9 wt. % purity; 10 ppmw of phosgene impurity) was added to the reactor feed and allowed to flow over the template at a BC13 : H2 volumetric ratio of approximately 1: 6 for 45 minutes. The total flow rate during reaction was 1.5 I/min (standard temperature and pressure). The reactor was then cooled to room temperature under flowing helium.

The material recovered from the reactor showed a grayish color and a significantly higher hardness compared to the fresh Mg-MCM-41 sample, suggesting metallic boron is embedded in the template material. It should be mentioned here that the

described reaction conditions are significantly milder than those used in other studies of BC13 reaction with hydrogen to form boron films. Experimental results suggest that magnesium in the Mg-MCM-41 is the catalyst or the catalyst precursor for the growth of single walled boron nanotubes, since a pure siliceous MCM-41 catalyst did not produce boron nanotubes under identical operating conditions. The reaction setup was mounted in the fume hood and the unreacted BCl3 was burnt in a hydrogen flare to prevent releasing the highly toxic BC13 into the atmosphere.

The boron loaded template was ground in an agate mortar, suspended in ethanol and sonicated for approximately 30 minutes. 0.05 ml of this suspension was dropped on a copper mesh coated with an amorphous holeycarbon film and the ethanol evaporated prior to transmission electron microscopy (TEM) analysis.

FIG. 1 shows a high-resolution TEM image of an exemplary boron single wall nanotube grown with the process described above. FIG. 2 shows a high-resolution TEM image of a boron nanopipe grown at a higher temperature and having a wall thickness of approximately 20 nm (nanopipes with wall thicknesses between 3 nm and 40 nm have been observed). FIG. 3 shows a high-resolution TEM image of bundles of nanowires with greater outside diameters than nanopipes. FIG. 4 shows groups of nanotubes that demonstrate the achieved diameter uniformity.

The boron nanotubes can be removed from the Mg-MCM-41 silica template by boiling in water that is either slightly acidic or basic. Tests have shown that a solution of NaOH in ethanol/water can be used to remove the silica without damaging the boron nanotubes. The Mg is almost atomically dispersed in the template and can be washed out with a mild HC1 treatment.

Unwanted boron structures other than nanotubes can be removed from the

cleaned boron nanomaterials by chemical methods. For example, boron nanopipes and wires have been found to oxidize over time in air, whereas boron nanotubes are stable in air over many months. Treatment of the samples in an oxidizing environment can therefore be used to convert the nanowires/pipes to boron oxide which can then been dissolved in the same type of boiling alkaline solution used to remove the silica template.

Care has to be taken to eliminate from the reactants or from the subsequent chemical treatment traces of materials that can interact with the growth of the boron nanostructures or their physical properties, because boron forms stable compounds with many other compounds due to its short covalent radius and 7r-type valence orbitals. For this reason, in particular any source of oxygen, nitrogen, and carbon should be eliminated.

FIG. 5A shows a high-resolution TEM image of a boron nanowire placed on a carbon-coated support to determine its chemical composition. FIG. 5B shows an x-ray absorption image at the boron K-edge, clearly demonstrating that the nanostructure is indeed made of boron. FIG. 5C is a corresponding image, with the absorption detected at the K-edge of carbon. The experimental results were checked against a boron nitride standard.

The presence of tubular structures has been also confirmed by the presence of spectral features in the Raman breathing mode region at wave numbers below 500 cm' 1. The spectrum shown in FIG. 6 was recorded, with a catalyst sample removed from the reactor, without any purification or pre-treatment on a Raman spectrometer equipped with an Olympus confocal microscope using a 532 nm excitation wavelength. The peak at 210 cm-1 (labeled a in Fig. 3) is typical for tubular structures

and corresponds to the characteristic radial breathing mode. The spectral features between 300 caf and 500 em-1 (labeled b in Fig. 3) are also likely attributable to tubular structures, since similar peaks have been reported for single walled carbon nanotubes. However, the absence of Raman peaks characteristic for the tangential vibration mode of ordered carbon visible in the 1580-1600 caf region peak indicated that the tubular structure is not carbon. The peaks observed at 525 caf and higher frequencies are believed to be due to a-boron clusters. The inset in FIG. 3 shows a boron nanotube with a clearly apparent single-walled tubular structure.

All boron nanotubes found in this sample appear in close proximity of the Mg- MCM-41 template support, suggesting that the growth of the nanotubes is initiated at the template support, most likely at the magnesium sites incorporated into the pore walls.

Instead of a Mg-MCM-41 framework, a B-MCM-41 framework, i. e. , an MCM-41 framework having pores"loaded"with boron can also be used as a template. No boron nanotube growth has been observed on"pure"MCM-41 framework structures, although growth of nanofibers was detected. In addition to incorporating boron and magnesium in or on the pore walls of the MCM-41 framework pores, other metal atoms, such as Ni, Pd, Ce, Co, Mn, Mo and Al, and mixtures thereof, can also be incorporated. These metal atoms form combinations with boron, such as borides, that have a low enough decomposition temperature of, for example, less than approximately 950°C, and are small enough to be incorporated into the MCM-41 pore structure without disturbing the structural uniformity of the framework. Stated differently, to take advantage of the templating technique provided by the MCM-41 framework and to thereby control the structures formed, a strong interaction between

the boron precursor and the nucleation sites on or in the pore walls is desired.

The pores of the B-MCM-41 and Mg-MCM-41 templates provide geometric constraints for the growth of nanowires and nanotubes with diameters small enough to promote one-dimensional physical properties. Reaction of BC13 with H2 at temperatures ranging from 700°C-900°C over the MCM-41 template doped with either Mg or B can produce single walled boron nanotubes and other interesting boron nanostructures. Mg-MCM-41 was found to be most selective for single-walled nanotubes. One proposed growth mechanism is the decomposition of a boron complex formed in the geometrically confined pore environment leading to the formation of uniform nanostructures with the diameter controlled by the pores.

Although representative data are presented only for a pore size of approximately 3.5 nm, experimental results obtained with Mg-MCM-41 frameworks with other pore sizes have shown that the diameter of the boron nanotubes produced is coincident with the template pore size. As mentioned above, the pore size can be controlled, for example, by a suitable selection of the surfactant or swelling agent used in the preparation of the MCM-41 template.

The reactant for the growth of the nanotubes and nanowires was diborane and/or BC13, with and without H2 as a co-reactant. It was observed that a higher base pressure in the reactor produced a greater selectivity for longer boron nanotubes.

The Mg-MCM-41 framework used in the aforedescribed experiments contained 1 % Mg loading. Larger concentrations of Mg can be incorporated without changing the pore structure; varying the pH during template synthesis can change the surface characteristics of the pore wall. The uniform pore size distribution can be controlled within 0. 1 nm FWHM by maintaining the pH level at, for example, pH = 11 iL 0.1

throughout the entire synthesis process. The addition of the antifoaming agent improves the structural order of the framework.

Selectivity to the particular boron nanostructures is affected by the growth temperature, with nanotubes formed at the lowest temperatures between approximately 700°C and 875°C, nanopipes formed at an intermediate temperature of approximately 900°C, and nanowires at higher temperatures. The selectivity may be caused by the tendency of boron to form clusters at higher temperatures.

"Pure"boron nanostructures may not be intrinsically stable because the boron bonds lack two electrons in order to satisfy Wade's rule; however, they appear nevertheless be close enough to Wade's rule to form stable structures. One approach for stabilizing the boron nanostructures, i. e. , nanotubes and nanowires, is to incorporate into the nanostructures during the growth of the nanostructures an electron donor, such as elements from the Group Ia or Group IIa of the periodic table of elements. Suitable donor atoms are, for example, Lithium, Beryllium, and Magnesium. Alternatively or in addition, the as-grown nanotubes and nanowires can also be exposed to an ambient that contains these elements and/or mixtures thereof.

Both the boron precursors (boron halides, diborane) as well as the compounds containing the donor elements can also be activated, for example, by photodissociation.

Metallic nanotubes, such as the aforedescribed boron nanotubes, provide the unusual opportunity to achieve confinement at much smaller dimensions beyond the reach of lithography. The confinement effects in metallic nanotubes can be tuned through changes in the diameter, chirality, doping and temperature. Dramatic alteration of both the phonon and electron structure of one-dimensional nanotubes

offers the possibility of novel superconducting behavior that cannot be accessed in higher dimensions.

In carbon compounds, 7r band eleckons lie at the top of the Fermi sea and are known to couple only weakly to the powerful zone-centered phonons, such as the C60 breathing mode. Conversely, in superconducting MgB2, holes in the a-band are the primary charge carriers, which couple very strongly (and preferentially) to the optical planar bond-stretching modes of the boron layers. Since Al-B2 type compounds are essentially isoelectronic forms of graphite, with the graphite-like boron planes being stabilized by charge injected from the cation, this mechanism of superconductivity may indicate interesting possibilities for other graphite-related compounds. For example, superconductivity has been reported below 4 K in boron-doped diamond, and in Li-doped bulk a-boron at 35 K. The possibility to attach or incorporate various cations in boron nanotubes could offer novel possibilities for useful superconducting materials.

As mentioned above, electron donor atoms, such as Li, Be and Mg, added to the boron nanostructures are expected to affect their electronic and superconducting properties. Pure boron nanotubes can be converted into MgB2 nanotubes by heating in Mg vapor at temperatures between 850°C and 1000°C. This conversion can be done either with the nanotubes removed from the B-MCM-41 or Mg-MCM-41 template, or with the nanotubes still attached to the template. In the latter case, the template with nanotubes is heated to between 900-1000°C The same process also converts nanowires and nanopipes to MgB2 structures.

Boron nanostructures can also be doped with Li using lithium borohydride or organo-lithium reagents, such as t-butyl lithium. Since lithium borohydride is more

volatile than Mg vapor, the reactor is a closed reactor rather than a flow reactor, with the nanotubes being mixed with lithium borohydride and heated to between 400°C andl 000°C while still in the template, i. e. , after synthesis but before template removal.

Beryllium can be incorporated by similar methods, starting, for example, with an organo-beryllium compound, and produces similar physical properties. It will be understood, however, that the particular method for incorporating the dopant atoms depends on the dopant and the selected precursor. Ideally, the precursors should only contain the metal to be incorporated and H and or boron. Donor metal halides have also been shown to have little detrimental effect on the produced nanostructures.

Preliminary data based on magnetic susceptibility measurements have shown that the superconducting transition temperature Te (H=0) of Mg-doped boron nanotubes is noticeably higher (on the order of 100 K) than the transition temperature of around 36 K observed for polycrystalline MgB2 and thicker MgB2 wires (around 100, um diameter).

While the invention has been disclosed in connection with the preferred embodiments shown and described in detail, various modifications and improvements thereon will become readily apparent to those skilled in the art. Accordingly, the spirit and scope of the present invention is to be limited only by the following claims.