Patent Application
20060062715
This application claims priority of Japanese Patent Applications Nos. 2004-103083, 2004-268878, and 2004-347384, filed on Mar. 31, 2004, Sep. 15, 2004, and Nov. 30, 2004, respectively.
1. Technical Field
This invention relates to ultrathin carbon fibers comprising tubular laminates of ultrathin carbon sheets. Particularly, this invention relates to the ultrathin carbon fibers which are suitable for use as a filler to be added to resin or the like.
2. Background Art
Carbon fibers are well known in the art. These are carbons having fibrous appearance. Some of these are known as ultrathin carbon fibers, which may be classified by their diameters and have received wide attention. The ultrathin carbon fibers may also be referred to as, for instance, vapor phase grown carbon fiber, carbon nanofiber, carbon nanotube, etc.
Among carbon fibers, the carbon nanotubes are those typically having diameters of not more than 100 nm. Since carbon nanotubes have unique physical properties, they are expected to be used in various applications, such as nanoelectrical materials, composite materials, catalyst support for fuel cells, gas absorbents, etc.
Carbon nanotubes include single wall carbon nanotubes (SWNTs) and multi wall carbon nanotubes (MWNTs). Single wall carbon nanotubes (SWNTs) each comprise a tubular monolayer of a sheet, wherein carbon atoms are bonded to each other to form a network structure, i.e., a graphene sheet. Multi wall carbon nanotubes (MWNTs) each comprise several tubular graphene sheets, which are coaxially layered. Depending on the chiral index, which is related to the diameter and the geometrical arrangement of the rolled graphene sheet, the characteristics of a carbon nanotube may be metallic or semimetallic.
U.S. Pat. No. 4,663,230 and JP-H03-174018-A disclose carbon fibrils that comprise multiple continuous layers of regularly ordered carbon atoms, wherein the multiple continuous layers have a substantially graphite structure. Each layer and the core in the fibrils are disposed substantially concentrically about the cylindrical axis of the fibril, and the fibrils are graphitic. Further, U.S. Pat. No. 5,165,909 discloses catalytically grown carbon fibrils that comprise multiple continuous layers of regularly ordered carbon atoms, wherein the ordered carbon atoms have c-axes that are substantially perpendicular to the cylindrical axes of the fibrils. Each layer and the core in these fibrils are disposed substantially concentrically about the cylindrical axes of the fibrils, and the fibrils are graphitic. U.S. Pat. Nos. 4,663,230, and 5,165,909, and JP-H03-174018-A are incorporated herein by reference in their entireties. The fibers having the layered structure of concentric graphene sheets as disclosed in the prior art, however, are prone to deformations and may adhere to each other due to their van der Waals interactions. The bulk fibers, therefore, have a tendency to form aggregates, in which the fibers are mutually entangled in a complicated web. When such aggregate particles are added as a filler to a matrix material, it is difficult to disentangle the fibers of the aggregates. As a result, it is difficult to disperse the fibers throughout the matrix.
When carbon nanotubes are added as a filler to a matrix material to improve electrical conductivity of a material, it is preferable to use a minimum amount of the carbon nanotubes, so that the electrical conductivity of the material can be improved with little loss of the original properties of the matrix material. In order to improve the electrical conductivity of a matrix material with a minimum amount of carbon nanotubes, it would be desirable to have improved electrical conductivity of the carbon nanotubes by eliminating defects in the graphene sheets and to have improved dispersability of the carbon nanotubes so that they can be dispersed in random orientations throughout the matrix. Carbon nanotubes contribute conductive paths in the matrix by forming carbon fiber networks, and they are more effective when they are dispersed in random orientations in the matrix.
One aspect of the invention relates to ultrathin carbon fibers. Ultrathin carbon fibers in accordance with some embodiments of the invention may have physical properties suitable for use as fillers in composite preparations. They may have high dispersability in the matrix of the composite. They may have relatively straight shapes.
They may have high strength and/or have good electrical conductivity. Ultrathin carbon fibers in accordance with embodiments of the invention may have maximum diameters of not more than 100 nm.
Ultrathin carbon fibers manufactured by the chemical vapor deposition (CVD) process, when examined with a transmission electron microscope (TEM) may show a structure, wherein the graphene sheets are beautifully stacked. When these carbon fibers are analyzed with Raman spectroscopy, however, the D bands thereof may be large and many defects may be observed. Furthermore, in some cases, the graphene sheets produced by the CVD processes may not fully develop, resulting in patch-like structures.
Inventors of the present invention have found that heat treatment of the ultrathin carbon fibers at high temperatures can reduce the magnitudes of the D bands and enhance the electrical conductivities of the ultrathin carbon fibers. The high-temperature treatment results in carbon fibers having polygonal cross sections (the cross section is taken in a direction orthogonal to the axes of the fibers). The high-temperature treatment also makes the resultant fibers denser and having fewer defects in both the layer stacking direction and the surface direction of the graphene sheets that comprise the carbon fibers. As a result, the carbon fibers have enhanced flexural rigidity (EI) and improved dispersability in a resin (or matrix material).
One aspect of the present invention relates to ultrathin carbon fibers comprising two or more tubular graphene sheets layered in a direction substantially orthogonal to the axis of the ultrathin carbon fiber, i.e., the tubular graphene sheets are substantially concentric (co-axial), wherein the tubular graphene sheets show a polygonal cross section (in a direction orthogonal to the carbon fiber axis), wherein the maximum diameters of the carbon fibers are in the range of 15 to 100 nm; an aspect ratio of the carbon fiber is no more than 105; and ID/IG (ratio of intensities of the D band and G band in a Raman spectrum) of the carbon fiber as determined by Raman spectroscopy is not more than 0.1.
Another aspect of the present invention relates to an ultrathin carbon fiber comprising two or more tubular graphene sheets layered in a direction that is substantially orthogonal to the axis of the ultrathin carbon fiber, i.e., the tubular graphene sheets are substantially concentric (co-axial), wherein the tubular graphene sheets show a polygonal cross section, wherein the maximum diameters of the carbon fibers are in the range of 15 to 100 nm; an aspect ratio of the carbon fiber is not more than 105; ID/IG of the carbon fiber as determined by Raman spectroscopy is not more than 0.2; and an anisotropic ratio of magneto resistances of the carbon fiber is not less than 0.85.
In some embodiments of the present invention, magneto resistances of the carbon fibers may have negative values in a range of magnetic flux density between 0 and 1 Tesla (T).
Further, an ultrathin carbon fiber according to embodiments of the present invention may be prepared by heating a mixture of a catalyst and a hydrocarbon at a temperature in the range of 800-1300° C. in a generation furnace to produce an intermediate, which is then treated in a heating furnace maintained at a temperature in the range of 2400-3000° C. to heat and refine the intermediate.
Alternatively, an ultrathin carbon fiber according to embodiments of the present invention may be prepared by heating a mixture of a catalyst and a hydrocarbon at a temperature in the range of 800-1300° C. in a generation furnace to produce a first intermediate, which is then treated in a first heating furnace maintained at a temperature in the range of 800-1200° C. to heat the first intermediate and transform it into a second intermediate, which is then treated in a second heating furnace maintained at a temperature in the range of 2400-3000° C. to heat and refine the second intermediate. Note that the “generation furnace,” the “heating furnace,” the “first heating furnace,” and the “second heating furnace” are described as separate units for clarity. However, one of ordinary skill in the art would appreciate that some or all of these furnaces may be the same physical unit set to different conditions (e.g., different temperatures). For example, the first heating furnace and the second heating furnace may be the same unit controlled at different temperatures in sequence.
The above mentioned catalyst may comprise a transition metal compound and sulfur (or a sulfur compound).
In accordance with some embodiments of the invention, in the second heating furnace, the second intermediate is subjected to a falling down process so that the bulk density of the carbon fibers may be selected to be about 5-20kg/m3.
In accordance with one embodiment of the present invention, the second intermediate may be heated for 5-25 minutes in the second heating furnace.
The ultrathin carbon fibers according to embodiments of the invention may have characteristics of high bending stiffness and sufficient elasticity. Thus, these fibers can restore their original shapes even after deformation. Therefore, the ultrathin carbon fibers according to embodiments of the present invention are less likely to intertwine in a state where the fibers are entangled with each other when they aggregate. Even if they happen to be entangled with each other, they can disentangle easily. Therefore, it would be easier to distribute these fibers in a matrix by mixing them with a matrix material because they are less likely to exist in an entangled state in the aggregate structure. Additionally, because carbon fibers according to some embodiments of the present invention have polygonal cross sections (in a direction orthogonal to the axis of the fiber), these carbon fibers can be more densely packed, and fewer defects will occur in both the stacking direction and the surface direction of the tubular graphene sheets that comprise the carbon fibers. This property gives these carbon fibers enhanced flexural rigidities (EI) and improved dispersability in the resin.
Furthermore, according to embodiments of the present invention, electrical conductivities of the carbon fibers may be improved by reducing defects in the graphene sheets that comprise the carbon fibers. Therefore, the carbon fibers according to embodiments of the present invention can provide better electrical conductivity when mixed in a matrix material.
Other aspects and advantages of the invention will be apparent from the following description and the appended claims.
Now, the present invention will be described in detail with reference to some embodiments of the invention, which are not intended to be restrictive, but are disclosed for the purpose of facilitating the illustration and understanding of the present invention.
Ultrathin carbon fibers according to embodiments of the present invention may be prepared by subjecting initial products of carbon fibers, as shown in
The maximum diameters of the cross sections of these carbon fibers are in the range of 15 to 100 nm. The aspect ratios of the carbon fibers are not more than 105. The ID/IG of the carbon fibers, as determined by Raman spectroscopy, are not more than 0.1.
The fact that the carbon fibers may show polygonal figures as the cross sections is a result of annealing at a temperature of not less than 2400° C. Additionally, the density of the carbon fiber can be increased from 1.89g/cm3 to 2.1 g/cm3 by annealing. Therefore, the carbon fibers are denser and have fewer defects in both the stacking direction and the surface direction of the graphene sheets that comprise the carbon fibers. In addition, the flexural rigidity (EI) and the dispersibility in the resin of the carbon fibers are improved.
In order to enhance the strength and electrical conductivity of the carbon fibers, it is desirable that the graphene sheets that comprise the carbon fibers have minimum defect. In some embodiments of the invention, for example, the ID/IG ratios of the carbon fibers, as determined by Raman spectroscopy, are not more than 0.2, more preferably, not more than 0.1. In Raman spectroscopy, a large single crystal graphite has only a peak (G band) at 1580 cm−1. When the graphite crystals are small or have any lattice defects, a peak (D band) at 1360 cm−1 can appear. Thus, when the intensity ratio (R═I1360/I1580═ID/IG) of the D band and the G band is below the limits defined above, the graphene sheets have little defect.
In accordance with embodiments of the invention, it is desirable that the maximum diameters of the ultrathin carbon fibers lie between 15 nm and 100 nm. When the maximum diameter is less than 15 nm, the cross section of the carbon fiber does not have a polygonal shape. On the other hand, the smaller the diameters are, the longer the carbon fibers will be for the same amount of carbon. The longer carbon fibers will have enhanced electrical conductivities. Thus, it is not desirable to have the maximum diameters of the ultrathin carbon fibers greater than 100 nm for use as modifiers or additives to improve conductivity of a matrix, such as a resinous material, etc. Particularly, it is desirable to have the maximum diameters of the carbon fibers in the range of 20-70 nm. A carbon fiber having a diameter within the preferred range and having tubular graphene sheets layered one over another in a direction orthogonal to the fiber axis, i.e., a co-axial (concentric) multilayer carbon fiber, would have high bending stiffness and sufficient elasticity. This property would allow the carbon fiber to restore to its original shape after undergoing any deformation. Therefore, such fibers tend to adopt relaxed structures when dispersed in a matrix, even if it has been deformed before or during mixing into the matrix material.
Carbon fibers in accordance with embodiments of the invention preferably have aspect ratios of not more than 105. When the aspect ratio of a carbon fiber exceeds 105, undesirable effects may arise, such as heightened viscosity when mixed with a matrix material (such as resin), resulting in bad moldability.
An ultrathin carbon fiber according to embodiments of the present invention preferably has a magneto resistance that has a negative value in a range of magnetic flux density between 0 and 1 Tesla (T) and decreases with increasing magnetic flux density, and the maximum magneto resistance (Δ ρ/ρ)max at 1 tesla (T) is not more than −0.1%. (See
The magnitude (absolute value) of magneto resistance of a carbon fiber becomes small when more defects exist in the carbon material. When a carbon fiber contains microcrystals of graphite, the magneto resistance is positive and increases with increasing magnetic flux density, or the magneto resistance may temporarily have a negative value and then becomes positive and thereafter increases with increasing magnetic flux density. On the other hand, the absolute value of the magneto resistance becomes small when a carbon fiber contains no graphite structure or have many defects in the graphene sheet (For explanation, see “Carbon Family: Respective Diversities and Evaluation therefor,” Agune Shoufu Sha, 2001 ). The related part of this literature is incorporated herein by reference.
Therefore, the criteria described above, i.e., (1) the magneto resistance of a carbon fiber has a negative value and decreases with increasing magnetic flux density up to 1 Tesla (T), and (2) the maximum magneto resistance (Δ ρ/ρ)max at 1 Tesla (T) is not more than −0.1%, may be used to show that the respective layers, or graphene sheets, that comprise a carbon fiber have two dimensional structures with few defects and do not form three dimensional graphite structure between adjacent layers.
Incidentally, the magneto resistance is a value that depends not only on the crystallinity of the graphene sheet, such as, size, integrity, etc., of the graphene sheet, but also on the orientation of the graphene sheet, due to its anisotropy. Therefore, by measuring azimuthal dependence of the magneto resistance, the crystallinity of graphene sheet and its orientation may be determined.
The aforementioned maximum magneto resistance (Δρ/ρ)max is, as known in the art, a value that can be determined by applying a constant magnetic flux density having a fixed magnitude to a sample, in three orthogonal directions, and measuring respective magneto resistances in the three directions of the magnetic fields. The “Tmax” direction, which is the direction of the magnetic field that produced the maximum magneto resistance, is determined. Then, (Δρ/ρ)max is defined as the value of the magneto resistance in the Tmax direction.
Moreover, the (Δρ/ρ)TLmin is the minimum value of magneto resistances that are measured by giving a rotation (TL rotation) in the direction of the magnetic field from the Tmax direction along the electrical current direction under a constant magnetic flux density and as a function of rotational angle φ. Additionally, the (Δρ/ρ)Tmin is the minimum value of magneto resistances that are measured by giving a rotation (T rotation) in the direction of the magnetic field in a plane perpendicular to the electrical current direction and as a function of rotational angle θ. Dependence of the magneto resistance values (Δρ/ρ) on the rotational angles φ and θ is related to the selective orientations of the graphene sheet. Therefore, anisotropy ratios γT and γTL, which are defined as follows, can be used as parameters to show the selective orientation of a graphene sheet.
γT=(Δρ/ρ)Tmin/(Δρ/ρ)max
γTL=(Δρ/ρ)TLmin/(Δρ/ρ)max
As for the ultrathin carbon fibers according to embodiments of the present invention, it is desirable that both these anisotropy ratios of the magneto resistance are not less than 0.85. When the magneto resistance (Δρ/ρ) is a negative, as described above, and each of these anisotropy ratios has a value close to 1, it is found that the graphene sheets are not oriented in any particular direction, i.e., they are randomly oriented.
As for the ultrathin carbon fibers according to embodiments of the present invention, it is also desirable that the spacing for the (002) faces, as determined by X ray diffraction, is in the range of 3.38-3.39 angstroms.
That the ultrathin carbon fibers according to embodiments of the present invention have such structures as described above is likely due to how they are made. The intermediate (first intermediate) prepared by heating a mixture of a catalyst and a hydrocarbon at a temperature in the range of 800-1300° C. in a generation furnace has a structure comprising patch-like sheets of carbon atoms laminated together (i.e., some sheets are still in incomplete condition). See,
When the above-mentioned intermediate is subjected to heat treatment at a temperature in the range of 2400-3000° C., the patch-like sheets of carbon atoms are rearranged to associate with each other and form multiple graphene sheet-like layers. Under these circumstances, the respective layers cannot self-align to form the graphite structure because the layers are forced to adopt the tubular three-dimensional structure of the intermediate as a whole. When heat treatment is run at a temperature sufficiently higher than 3000° C., the carbon atoms may have a high degree of freedom and may rearrange because the carbon bonds may be broken at such a high temperature. When at a temperature of not more than 3000° C., the carbon atoms cannot move freely. Instead, they may have limited movement while being bound to each other in the patch-like structure. As a result, although the defects may be repaired within individual graphene sheets, some defects may remain in the layers or at alignments and realignments of the layers due to excess or deficiency of carbon atoms.
Next, techniques for the production of ultrathin carbon fibers according to embodiments of the present invention will be described.
Briefly, an organic compound, such as a hydrocarbon, is thermally decomposed in a chemical vapor deposition (CVD) process in the presence of ultra fine particles of a transition metal as a catalyst. The residence time for ultrathin carbon fiber nucleus, intermediate product, and fiber product in the generation furnace is preferably short in order to produce carbon fibers (hereinafter, referred to as “intermediate” or “first intermediate”). The intermediate thus obtained is then heated at high temperature in order to produce the ultrathin carbon fibers having the desirable properties.
(1) Synthesis Method
Although the intermediate or first intermediate may be synthesized using a hydrocarbon and a CVD process conventionally used in the art, the following modifications of the process are desired:
To manufacture the ultrathin carbon fiber according to embodiments of the present invention efficiently, the intermediate or first intermediate obtained with the above method is subjected to high temperature heat treatment at 2400-3000° C. in an appropriate way. The fibers of the intermediate or first intermediate include a lot of adsorbed hydrocarbons because of the process described above. Therefore, in order to have useable fibers, it is necessary to separate the adsorbed hydrocarbons from the fibers. To separate the unnecessary hydrocarbons, the intermediate may be subjected to heat treatment at a temperature in the range of 800-1200° C. in a heating furnace. However, defects in the graphene sheet may not be repaired to an adequate level in the aforementioned hydrocarbon separation process. Therefore, the resultant product from this process may be further subjected to another heat treatment in a second heating furnace at a temperature higher than the synthesis temperature (e.g., 2400-3000° C.). The second heat treatment may be performed on the powdered product as-is, without subjecting the powder to any compression molding (or compacting).
For the high temperature heat treatment at 2400-3000° C., any process conventionally used in the art may be used, except that the following modifications are desirable.
In this process, it is possible to add a small amount of a reducing gas or carbon monoxide gas into the inert gas atmosphere to protect the material structure.
As raw material organic compounds, carbon monoxide (CO), hydrocarbons such as benzene, toluene, xylene, or alcohols such as ethanol may be used. As an atmosphere (carrier) gas, hydrogen, inert gases such as argon, helium, xenon may be used.
As catalysts, a transition metal or a mixture thereof such as iron, cobalt, molybdenum, or a transition metal compounds, such as ferrocene, metal acetate, and sulfur or a sulfur compound, such as thiophene or ferric sulfide, may be used.
In an embodiment of the invention, a mixture of raw material organic compound and a transition metal or transition metal compound and sulfur or sulfur compound as a catalyst are heated to a temperature of not less than 300° C. along with an atmosphere gas in order to gasify them. Then, the gasified mixture is added to the generation furnace and heated therein at a temperature in the range of 800-1300° C., preferably, in the range of 1000-1300° C., in order to synthesize ultrathin carbon fibers from the fine particles of catalyst metal and the hydrocarbon. The carbon fiber products (as the intermediate or first intermediate) thus obtained may include unreacted raw materials, nonfibrous carbons, tar, and catalyst metal.
Next, the intermediate (or first intermediate) in its as-is powder state, without subjecting it to compression molding, is subjected to high temperature heat treatment either in one step or two steps.
In the one-step operation (one heating furnace), the intermediate is conveyed into a heating furnace along with the atmosphere gas, and then heated to a temperature (preferably a constant temperature) in the range of 800-1200° C. to remove the unreacted raw material, adsorbed carbon, and volatile flux, such as tar, by vaporization. Thereafter, it may be heated to a temperature (preferably a constant temperature) in the range of 2400-3000° C. to improve the structures of the multilayers in the fibers, and, concurrently, to vaporize the catalyst metal included in the fibers to produce refined ultrathin carbon fibers. In the refined ultrathin carbon fibers, the respective layers therein have graphitic, two-dimensional structures. On the other hand, between the layers, there is substantially no regular, three-dimensional structure. Therefore, the layers in such refined carbon fibers are substantially independent of each other.
Alternatively, the high temperature heat treatment may be performed in two steps (in two heating furnaces), the first intermediate is conveyed, along with the atmosphere gas, into a first heating furnace that is maintained at a temperature (preferably a constant temperature) in the range of 800-1200° C. to produce a ultrathin carbon fiber (hereinafter, referred to as “second intermediate”). The heat treatment removes unreacted raw materials, adsorbed carbons, and volatile flux such as tar by vaporization. Next, the second intermediate is conveyed, along with the atmosphere gas, into a second heating furnace that is maintained at a temperature (preferably a constant temperature) in the range of 2400-3000° C. to improve the structures of the multilayers in the fibers, and, concurrently, to vaporize the catalyst metal that is included in the second intermediate to produce refined ultrathin carbon fibers. It is desirable that the heating period for the second intermediate in the second heating furnace is in the range of 5-25 minutes, and the bulk density of the second intermediate in the second heating furnace is adjusted to be not less than 5 kg/m3 and not more than 20 kg/m3, preferably, not less than 5 kg/m3 and not more than 15 kg/m3. When the bulk density of the intermediate is less than 5 kg/m3, the powder does not flow easily so as to achieve good heat treatment efficiency. When the bulk density of the intermediate is more than 20 kg/m3, the final product does not readily disperse on mixing with resins, although the heat treatment efficiency of the intermediate is good.
The generation furnace used in this process is preferably a vertical type. The high temperature heating furnaces used in this process may be a vertical type or horizontal type; however, the vertical type is preferred because it allows the intermediate to fall down. The fall down process may be used to select intermediates having desired bulk density.
The ultrathin carbon fibers according to embodiments of the present invention may have one or more of the following properties:
Ultrathin carbon fibers of the invention may be used as fibers by themselves, or as powders added to other materials. When used as fibers alone, they may be used, for example, as field emission devices (FED), electron microscope elements, semiconductor devices, and others devices, utilizing their electron emission ability, electrical conductivity, superconductivity, etc. When used as powders, depending on the form utilized, it can be classified as: 1) zero dimensional composite materials, such as a slurry, in which the carbon fiber powder is dispersed; 2) one dimensional composite materials that are processed into a linear form; 3) two dimensional composite materials that are processed into a sheet form, such as cloth, film, or paper; and 4) three dimensional composite materials in a complex form or block. By combining such forms and functions, ultrathin carbon fibers of the invention may have a very wide range of applications. The following describes examples of the applications of these carbon fibers according to their functions.
1) Composites having Electrical Conductivity
Ultrathin carbon fibers of the invention may be mixed with a resin to produce a conductive resin or conductive resin molded body, which may be used as wrapping material, gasket, container, resistance body, conductive fiber, electrical wire, adhesive, ink, paint, and etc. In addition to resin composites, similar effects can be expected with a composite material that results from adding the carbon fibers to an inorganic material, such as ceramic, metal, etc.
2) Composites having Heat Conductivity
Ultrathin carbon fibers of the invention may be added to a matrix material to improve its heat conduction, similar to the above-described applications based on electrical conductivity.
3) Electromagnetic Wave Shields
Ultrathin carbon fibers of the invention may be mixed with a resin (or an inorganic material) and used as electromagnetic wave shielding materials, in the form of paints or other molded shapes.
4) Composites having Unique Physical Characteristics
Ultrathin carbon fibers of the invention may be mixed with a matrix, such as a resin or metal, to improve slidability of the matrix. Such materials may be used in, for example, rollers, brake parts, tires, bearings, lubricating oil, cogwheel, pantograph, etc.
Also, due to its light-weight and toughness characteristic, ultrathin carbon fibers of the invention can also be used in wires, bodies of consumer electronics or cars or airplanes, housings of machines, etc.
Additionally, it is possible to use these carbon fibers as substitutes for conventional carbon fibers or beads, and they may be used in a terminal or poles of a battery, switch, vibration damper, etc.
5) Carbon Fibers as Fillers
Ultrathin carbon fibers of the invention have excellent strength, and moderate flexibility and elasticity. Thus, they may be advantageously used as fillers in various materials, for example, to form a network structure. Based on these characteristics, it is possible to use these carbon fibers, for example, to strengthen the terminals of power devices such as a lithium ion rechargeable battery or a lead-acid battery, a capacitor, and a fuel cell, and to improve cycle characteristics of these power devices.
Hereinafter, embodiments of this invention will be illustrated in detail with practical examples. However, it is to be understood that the examples are given for illustrative purpose only, and the invention is not limited thereto.
The measurement methods used to assess the individual physical properties described hereinafter include the following.
(1) X Ray Diffraction
Because graphite has three-dimensional regularity, the graphite crystal lattice diffracts X-ray to give readily discernable diffraction peaks for the (101) and (112) faces. If a sample contains no graphite, the diffraction peaks for the (112) face would not appear. Therefore, if the diffraction peaks for the (112) face are absent, graphite is not included in the carbon material analyzed.
If a graphite contains turbostratic structures, the diffraction peaks in the direction of the C-axis, which is perpendicular to the graphene sheet, such as the peaks for the (002) and (004) faces, as well as the diffraction peaks in the direction of the a-axis, which is in-plane of the graphene sheet, such as the peaks for the (100) and (110) faces, are detectable.
An ideal graphite crystal has a three dimensional regular structure wherein the flat graphene sheets are regularly layered, and each plane is closely packed with the next with a spacing of 3.354 angstroms. On the other hand, if the graphite structure is not ideal, this regularity is disrupted and the graphite may include “turbostratic” structure, in which the spacing between the layers is larger than that of graphite crystal. When the spacing lies between 3.38 angstroms and 3.39 angstroms, the carbon material includes the turbostratic structure.
(2) Magneto Resistance
It is possible to judge whether or not carbon fibers contain any graphite structure based on the electromagnetic characteristic of graphite. The method determines graphitization degree, which is sensitive to the extent of lattice defects. Briefly, at a selected temperature, magneto resistance is measured with respect to magnetic flux density.
Magneto resistance Δρ/ρ is defined by the following equation:
Δρ/ρ=[ρ(B)−ρ(0)]/ρ(0)
wherein B denotes the magnetic flux density, ρ(0) denotes the electrical resistivity under the condition of no magnetic field, and ρ(B) denotes the electrical resistivity under the condition of a constant magnetic field B.
The magneto resistance takes a positive value when the sample is single crystal graphite, and the value decreases when the defects in the sample increase. When the sample includes microcrystalline graphite, the magneto resistance increases (maybe in the positive value range) with increasing magnetic flux density, or the magneto resistance may temporarily become negative, then returns to positive, and thereafter increases in the positive value range with increasing magnetic flux density. With carbon fibers not containing graphite, the magneto resistance decreases in the negative value range with increasing magnetic flux density. Further, because the magneto resistance values vary with orientations of the graphite crystal, the orientation of the graphite crystal can be determined by measuring magneto resistance of the sample with appropriate rotation of the sample.
The magneto resistance can be used to determine the crystallinity of the graphite with a high sensitivity, as compared to electrical resistance measurements, Raman spectroscopy analysis, peak analysis of the (002) face from X ray diffraction, etc.
(3) Raman Spectroscopy
In Raman spectroscopy, a large single crystal of graphite has only one peak (the G band) at 1580 cm−1 up to 2000 cm−1. When the graphite crystals are of finite minute sizes or have any lattice defects, another peak (D band) at 1360 cm−1 also appears. Thus, graphite defects may be analyzed with the intensity ratio (R═I1360/I1580═ID/IG) of the D band and the G band. It is known in the art that a correlation exists between the crystal size La and R in the graphene sheet plane. R=0.1 is supposed to be equivalent to La=500 angstroms.
The respective physical properties described later are measured according to the following parameters.
(1) X Ray Diffraction
Using the powder X ray diffraction equipment (JDX3532, manufactured by JEOL Ltd.), carbon fibers after high temperature treatment (or annealing processing) were determined. Kα ray, which was generated with a Cu tube at 40 kV, 30 mA was used, and the measurement of the spacing was performed in accordance with a standard method, such as the method defined by The Japan Society for the Promotion of Science (JSPS), described in “Latest Experimental Technique For Carbon Materials (Analysis Part),” Edited by the Carbon Society of Japan, (2001). Silicon powder was used as an internal standard. The related parts of this literature are incorporated herein by reference.
(2) Magneto Resistance
First, on a resin sheet, a mixture of an analyte and an adhesive was coated as a line. The thickness, width and length were about 1 mm, 1 mm, and 50 mm, respectively. Next, the sample was put into the magnetic field measuring equipment. Magnetic flux was applied in various directions, and the resistances of the sample were measured. During measurements, the measuring equipment was cooled with liquid helium, etc. Separately, another magneto resistance at the room temperature was also determined.
(3) Raman Spectroscopic Analysis
Raman spectroscopic analysis was performed with LabRam 800™, which is manufactured by HORIBA JOBIN YVON, S.A.S. The measurements were performed with 514 nm light from an argon laser.
Using the CVD process, ultrathin carbon fibers are synthesized from toluene as a raw material. The synthetic system used is shown in
The synthesis was carried out in the presence of a mixture of ferrocene and thiophene as the catalyst, and under a reducing atmosphere of hydrogen gas. Toluene and the catalyst were heated to 375° C. along with the hydrogen gas, and then they were supplied to the generation furnace to react at 1200° C. for a residence time of 8 seconds. The atmosphere gas was separated by a separator in order to use the atmosphere gas repeatedly. The hydrocarbon concentration in the supplied gas was 9% by volume.
The tar content as a percentage of the ultrathin carbon fibers in the synthesized intermediate (first intermediate) was determined to be 10%.
Next, the fiber intermediate was heated to 1200° C., and kept at that temperature for 30 minutes in order to effectuate the hydrocarbon separation. Thereafter, the fibers were subjected to high temperature heat treatment at 2500° C. Shown in
The synthetic system used for this example is shown in
Next, the carbon fibers (first intermediate) were subjected to heat treatment at 1200° C. for 35 minutes. After the heat treatment, the specific surface area of the resultant carbon fibers (second intermediate) were determined to be 33m2/g. The ID/IG ratio, which was measured by Raman spectroscopy, was found to be 1.0.
Further, the carbon fibers (second intermediate) were subjected to high temperature heat treatment at 2500° C. The ultrathin carbon fibers after the high temperature heat treatment have negative magneto resistance values, which decrease (first derivative is negative with respect to the magnetic flux density B) with increasing magnetic flux density. The ID/IG ratio, which was measured by Raman spectroscopy, was found to be 0.08.
The ultrathin carbon fibers obtained in Example 1 was analyzed with an X ray diffraction. For comparison, a graphite sample was also subjected to X ray diffraction analysis. The X ray diffraction patterns obtained from these determinations are shown in
From the comparison, it was found that both samples had a peak corresponding to the diffraction of the (110) face lying at approximately 77°. It was also found that the graphite sample had a peak corresponding to the diffraction of the (112) face lying at approximately 83°, while the sample of the ultrathin carbon fibers of Example 1 did not have such a peak. Therefore, this result shows that the ultrathin carbon fibers according to the present invention do not have a regular, three-dimensional structure like that of graphite.
Additionally, the spacing between the layers of the ultrathin carbon fibers, as measured from X-ray diffraction result, was found to be 3.388 angstroms.
To 1.00 g of the ultrathin carbon fibers produced in Example 1, 19.00 g (CNT 5%) or 49.0 g (CNT 2.0%) of a thickener (e.g., a heat-resistant inorganic adhesive, such as ThreeBond® 3732, manufactured by Three Bond Co., Ltd.) was added, and then the mixture was kneaded using a centrifugal mixer at 2000 rpm for 10 minutes. The resultant mixture was applied on a 125 μm thick polyimide resin film (e.g., UPILEX®-S, manufactured by UBE Industries, Ltd.) as a line of 1 mm wide, and allowed to dry.
Next, the magneto resistance changes of this polyimide resin as a function of magnetic flux density at selected temperatures were determined. The results are shown in Table 1 and
In a like manner, an epoxy resin coating film was prepared to have 0.5% by weight of the carbon fiber content in the coating film. An optical microphotograph of the resultant film is shown in
While embodiments of the invention have been illustrated with a limited number of examples, the present invention may be embodied in other forms without departing from the scope of the invention. The above embodiments and examples are therefore to be considered in all respects as illustrative and not restrictive, the scope of the invention should be limited only by the appended claims, rather than by the foregoing description, and all changes which come within the meaning and range of equivalency of the claims are therefore intended to be embraced therein.
The ultrathin carbon fibers according to embodiments of the present invention have excellent electron emission ability, electrical conductivity, heat conductivity, and can be used, for example, as semiconductor device, FED, electron microscope element, fuel cells, and in the applications as composite materials, such as electrical conductive fiber, electromagnetic wave shielding material, and housings for various mechanical devices, etc.
While the invention has been described with respect to a limited number of embodiments, those skilled in the art, having benefit of this disclosure, will appreciate that other embodiments can be devised which do not depart from the scope of the invention as disclosed herein. Accordingly, the scope of the invention should be limited only by the attached claims.
| Number | Date | Country | Kind |
|---|---|---|---|
| JP2004-103083 | Mar 2004 | JP | national |
| JP2004-268878 | Sep 2004 | JP | national |
| JP2004-347384 | Nov 2004 | JP | national |
