U.S. patent application number 11/011207 was filed with the patent office on 2005-11-03 for nanocrystalline ceramic materials reinforced with single-wall carbon nanotubes.
This patent application is currently assigned to THE REGENTS OF THE UNIVERSITY OF CALIFORNIA. Invention is credited to Kuntz, Joshua D., Mukherjee, Amiya K., Wan, Julin, Zhan, Guodong.
Application Number | 20050245386 11/011207 |
Document ID | / |
Family ID | 32770859 |
Filed Date | 2005-11-03 |
United States Patent
Application |
20050245386 |
Kind Code |
A1 |
Zhan, Guodong ; et
al. |
November 3, 2005 |
Nanocrystalline ceramic materials reinforced with single-wall
carbon nanotubes
Abstract
Composites of ceramic materials, notably alumina or metal oxides
in general, with single-wall carbon nanotubes are consolidated by
electric field-assisted sintering to achieve a fully dense material
that has an unusually high fracture toughness compared to the
ceramic alone, and also when compared to composites that contain
multi-wall rather than single-wall carbon nanotubes, and when
compared to composites that are sintered by methods that do not
include exposure to an electric field.
Inventors: |
Zhan, Guodong; (Davis,
CA) ; Mukherjee, Amiya K.; (Davis, CA) ;
Kuntz, Joshua D.; (Lafayette, CA) ; Wan, Julin;
(Schenectady, NY) |
Correspondence
Address: |
TOWNSEND AND TOWNSEND AND CREW, LLP
TWO EMBARCADERO CENTER
EIGHTH FLOOR
SAN FRANCISCO
CA
94111-3834
US
|
Assignee: |
THE REGENTS OF THE UNIVERSITY OF
CALIFORNIA
OAKLAND
CA
|
Family ID: |
32770859 |
Appl. No.: |
11/011207 |
Filed: |
December 13, 2004 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
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11011207 |
Dec 13, 2004 |
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10356729 |
Jan 30, 2003 |
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6858173 |
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Current U.S.
Class: |
501/95.1 ;
501/103; 501/108; 501/120; 501/127; 501/152 |
Current CPC
Class: |
C04B 2235/322 20130101;
Y10S 977/842 20130101; C04B 2235/666 20130101; C04B 2235/72
20130101; C04B 2235/3217 20130101; C04B 35/053 20130101; C04B
35/443 20130101; C04B 2235/3229 20130101; B82Y 30/00 20130101; C04B
35/46 20130101; C04B 35/6261 20130101; C04B 2235/96 20130101; C04B
35/117 20130101; C04B 2235/549 20130101; C04B 35/64 20130101; C04B
2235/5445 20130101; C04B 2235/785 20130101; C04B 2235/5454
20130101; C04B 35/645 20130101; C04B 2235/77 20130101; C04B 35/488
20130101; C04B 2235/5288 20130101; C04B 35/50 20130101; C04B 35/505
20130101 |
Class at
Publication: |
501/095.1 ;
501/103; 501/108; 501/120; 501/127; 501/152 |
International
Class: |
C04B 035/80 |
Goverment Interests
[0001] This invention was made with financial support from the
United States Government under Contract No. DAAD19-00-1-0185,
awarded by the United States Army Research Office. The Federal
Government therefore has certain rights in this invention.
Claims
What is claimed is:
1-9. (canceled)
10. A high-performance ceramic material prepared by a process
comprising consolidating a mixture of ceramic particles of less
than 100 nm in diameter and single-wall carbon nanotubes into a
continuous mass by compressing said mixture while passing an
electric current through said mixture.
11. A high-performance ceramic material in accordance with claim 10
in which said ceramic oxide particles are alumina.
12. A high-performance ceramic material in accordance with claim 10
in which said single-wall carbon nanotubes constitute from about 3%
to about 25% by volume of said mixture.
13. A high-performance ceramic material prepared by a process
comprising consolidating a mixture of ceramic particles of less
than 100 nm in diameter and single-wall carbon nanotubes into a
continuous mass by compressing said mixture at a pressure of from
about 40 MPa to about 100 MPa and a temperature of from about
900.degree. C. to about 1,400.degree. C., while passing a pulsed
direct current of from about 500 A/cm2 to about 5,000 A/cm2 through
said mixture.
14. A high-performance ceramic material prepared by a process
comprising: (a) forming a mixture of alumina powder and single-wall
carbon nanotubes in which said single-wall carbon nanotubes
constitute from about 4% to about 20% by volume of said mixture;
and (b) consolidating said mixture so activated into a continuous
mass by compressing said mixture at a pressure of from about 40 MPa
to about 100 MPa while exposing said mixture to a pulsed direct
current of from about 500 A/cm.sup.2 to about 5,000 A/cm.sup.2.
Description
BACKGROUND OF THE INVENTION
[0002] 1. Field of the Invention
[0003] This invention resides in the field of ceramics, and
incorporates technologies relating to nanocrystalline materials,
carbon nanotubes, and sintering methods for densification and
property enhancement of materials.
[0004] 2. Description of the Prior Art
[0005] Ceramics that have a microstructure consisting of nano-sized
crystalline grains, i.e., grains that are less than 100 nm in
diameter, are known to have unique properties that set these
materials apart from ceramics with larger-grain microstructures. As
a result, nanocrystalline ceramics hold promise as high-performance
materials for a wide variety of applications extending from
microelectromechanical devices (MEMS) to materials of construction
for heat engines, cutting tools, wear and friction surfaces, and
space vehicles. Fulfillment of the promise of nanocrystalline
ceramics has been limited however by the brittleness of these
materials.
[0006] Among the various attempts to reduce the brittleness of
nanocrystalline ceramics, the most prominent have been the
development of composites in which secondary materials are
dispersed throughout the matrix ceramic material. In some of the
more recent developments, carbon nanotubes, specifically multi-wall
carbon nanotubes, have been used as the secondary material. A
description of "ceramic matrix nanocomposites containing carbon
nanotubes" is found in Chang, S., et al. (Rensselaer Polytechnic
Institute), U.S. Pat. No. 6,420,293 B1, issued Jul. 16, 2002 on an
application filed on Aug. 25, 2000. While the description
encompasses both single-wall and multi-wall carbon nanotubes, the
only carbon nanotubes for which test data is presented in the
patent are multi-wall carbon nanotubes. The description in the
patent of the sintering of the starting powders to form a dense
continuous mass is limited to hot isostatic pressing.
[0007] Single-wall carbon nanotubes possess extraordinary
electrical conductivity as well as a thermal conductivity that is
twice that of diamond. Thus, when single-wall carbon nanotubes have
been added to polymer matrices, the nanotubes have been shown to
give the polymer an electrical conductivity high enough to provide
an electrostatic discharge. Other extraordinary properties of
single-wall carbon nanotubes are mechanical properties such as
stiffness (a Young's modulus of 1,400 GPa) and strength (a tensile
strength well above 100 GPa). While the electrical properties have
been successfully exploited, the mechanical properties have not.
Iron-alumina composites that include carbon nanotubes, for example,
have demonstrated only marginally higher fracture strength than
alumina alone and markedly lower than carbon-free iron-alumina
composites. Nor has there been much improvement in fracture
toughness. The best results reported to date are those of Siegel,
R. W., et al., in Scripta mater. 44 (2001): 2061-2064, in which a
24% increase in fracture toughness of alumina was achieved by
nanosized alumina filled with multi-wall carbon nanotubes.
[0008] Of further relevance to this invention is the literature on
electric field-assisted sintering, which is also known as spark
plasma sintering, plasma activated sintering, and field-assisted
sintering technique. Electric field-assisted sintering is disclosed
in the literature for use on metals and ceramics, for consolidating
polymers, for joining metals, and for crystal growth and promoting
chemical reactions. The densification of alumina powder by electric
field-assisted sintering is disclosed by Wang, S. W., et al., J.
Mater. Res. 15 (4) (April 2000): 982-987.
SUMMARY OF THE INVENTION
[0009] It has now been discovered that a ceramic material of
unusually high fracture toughness and favorable mechanical
properties in general is achieved by combining single-wall carbon
nanotubes with nano-sized ceramic particles and consolidating the
resulting mixture into a continuous mass by electric field-assisted
sintering. The invention is illustrated by alumina as a
representative ceramic material, and the resulting single-wall
carbon nanotube-reinforced alumina possesses a toughness that is
nearly three times the toughness of pure nanocrystalline alumina
prepared in the same manner. The composite is also superior to
composites formed with multi-wall carbon nanotubes, despite the
fact that full density can be achieved both with ceramics sintered
with single-wall carbon nanotubes and with ceramics sintered with
multi-wall carbon nanotubes. This discovery that single-wall carbon
nanotubes offer a significant improvement relative to multi-wall
carbon nanotubes is thus a further aspect of this invention not
recognized in the prior art. A still further discovery is that
ceramic nanocomposites prepared by the process of this invention
are at least equal if not superior in mechanical properties to
ceramic nanocomposites that contain iron in addition to the carbon
nanotubes. Electric field-assisted sintering itself offers
advantages to the process by producing a fully dense product with
superior mechanical properties in much less processing time than
other sintering methods. This unique combination of the use of
single-wall carbon nanotubes and electric field-assisted sintering
produces a ceramic nanocomposite with the highest fracture
toughness reported to date.
[0010] These and other features, advantages and objects of this
invention will be apparent from the description that follows. All
literature references cited in this specification are incorporated
herein by reference for their descriptions of the subject matter in
the contexts of which the citations are made.
BRIEF DESCRIPTION OF THE FIGURE
[0011] FIG. 1 is a plot of fracture toughness of sintered alumina
vs. amount of carbon nanotubes incorporated into the alumina,
listing test results generated by the inventors herein together
with test results reported in the literature.
DETAILED DESCRIPTION OF THE INVENTION AND PREFERRED EMBODIMENTS
[0012] Carbon nanotubes are polymers of pure carbon. Both
single-wall and multi-wall carbon nanotubes are known in the art
and the subject of a considerable body of published literature.
Examples of literature on the subject are Dresselhaus, M. S., et
al., Science of Fullerenes and Carbon Nanotubes, Academic Press,
San Diego (1996), and Ajayan, P. M., et al., "Nanometre-Size Tubes
of Carbon," Rep. Prog. Phys. 60 (1997): 1025-1062. The structure of
a single-wall carbon nanotube can be described as a single graphene
sheet rolled into a seamless cylinder whose ends are either open or
closed. When closed, the ends are capped by either half fullerenes
or more complex structures including pentagons. The average
diameter of a single-wall carbon nanotube is within the range of
0.5 to 100 nm, and more typically, 0.5 to 10 nm, 0.5 to 5 nm, or
0.7 to 2 nm. The aspect ratio, i.e., length to diameter, can range
from about 25 to about 1,000,000, and preferably from about 100 to
about 1,000. Thus, a nanotube of 1 nm diameter may have a preferred
length of from about 100 to about 1,000 nm. (All ranges stated
herein are approximate.) Nanotubes frequently exist as "ropes," or
bundles of 10 to 100 nanotubes held together along their length by
van der Waals forces, with individual nanotubes branching off and
joining nanotubes of other "ropes." Multi-walled carbon nanotubes
are multiple concentric cylinders of graphene sheets. The cylinders
are of successively larger diameter to fit one inside another,
forming a layered composite tube bonded together by van der Waals
forces, with a typical distance of approximately 0.34 nm between
layers, as reported by Peigney, A., et al., "Carbon nanotubes in
novel ceramic matrix nanocomposites," Ceram. Inter. 26 (2000)
677-683.
[0013] Carbon nanotubes are commonly prepared by arc discharge
between carbon electrodes in an inert gas atmosphere. The product
is generally a mixture of single-wall and multi-wall nanotubes,
although the formation of single-wall nanotubes can be favored by
the use of transition metal catalysts such as iron or cobalt.
Single-wall nanotubes can also be prepared by laser ablation, as
disclosed by Thess, A., et al., "Crystalline Ropes of Metallic
Carbon Nanotubes," Science 273 (1996): 483-487, and by Witanachchi,
S., et al., "Role of Temporal Delay in Dual-Laser Ablated Plumes,"
J. Vac. Sci. Technol. A 3 (1995): 1171-1174. A further method of
producing single-wall nanotubes is the HiPco process, as disclosed
by Nikolaev, P., et al., "Gas-phase catalytic growth of
single-walled carbon nanotubes from carbon monoxide," Chem. Phys.
Lett. 313, 91-97 (1999); and by Bronikowski M. J., et al.,
"Gas-phase production of carbon single-walled nanotubes from carbon
monoxide via the HiPco process: A parametric study," J. Vac. Sci.
Technol. 19, 1800-1805 (2001).
[0014] The ceramic materials that form the major component of the
composites of this invention include any known ceramics, although
preferred ceramics are metal oxides. Examples of metal oxide
ceramics are alumina, magnesium oxide, magnesia spinel, titania,
cerium oxide, yttria, and zirconia. Further examples are
combinations of two or more of these metal oxides, and combinations
that include other oxides such as silica and other metal and
non-metal oxides, as well as mixed metallic oxides such as SiAlON,
AlON, spinels, and calcium aluminate. A metal oxide that is
currently of particular interest is alumina, including both
.alpha.- and .gamma.-alumina.
[0015] The starting materials for the nanocomposites of this
invention are preferably powder mixtures of the ceramic and the
single-wall carbon nanotubes. It is preferred that the mixtures,
and the final product as well, be free of multi-wall carbon
nanotubes, or if multi-wall carbon nanotubes are present, that the
amount of multi-wall nanotubes relative to the amount of
single-wall nanotubes be so small that the presence of the
multi-wall nanotubes does not obliterate or significantly reduce
the beneficial properties attributable to the single-wall
nanotubes. It is also preferred that the nanocomposites be free of
iron or contain no more than a negligible amount that will not
affect the properties of the product.
[0016] The relative amounts of ceramic material and single-wall
carbon nanotubes can vary, although the mechanical properties and
possibly the performance characteristics may vary with the
proportion of single-wall carbon nanotubes present. In most cases,
best results will be achieved with nanocomposites in which the
single-wall carbon nanotubes constitute from about 1% to about 50%
by volume of the starting powder mixture, and preferably from about
3% to about 25% by volume. The volume percents referred to herein
are measured on the bulk starting material, i.e., the volumes of
non-consolidated powders.
[0017] The ceramic material used as a starting material is
preferably in the form of nano-sized particles, i.e., particles
whose diameters are less than 100 nm in diameter on the average,
and preferably from about 10 nm to about 90 nm on the average. The
single-wall carbon nanotubes can be dispersed through the ceramic
powder by conventional means to form a uniformly dispersed powder
mixture, although a preferred method is one involving the use of
suspensions of the two materials in a liquid suspending medium. The
ceramic powder and the carbon nanotubes can thus be suspended in
separate volumes of a low molecular weight alcohol (ethanol, for
example), followed by combining of the two suspensions. Carbon
nanotubes are available from commercial suppliers in a paper-like
form, and can be dispersed in ethanol and other liquid suspending
agents with the assistance of ultrasound.
[0018] Once the mixture of ceramic powder and single-wall carbon
nanotubes is formed, the mixture is preferably mixed prior to
electric field-assisted sintering. Mechanical mixing can be
performed by ball-milling in conventional rotary mills that mix the
powder mixture with the assistance of tumbling balls. The sizes of
the balls, the number of balls used per unit volume of powder, the
rotation speed of the mill, the temperature at which the milling is
performed, and the length of time that milling is continued can all
vary widely. Best results will generally be achieved with a milling
time ranging from about 4 hours to about 50 hours. The degree of
mixing may also be affected by the "charge ratio," which is the
ratio of the mass of the balls to the mass of the powder. A charge
ratio of from about 5 to about 20 will generally provide proper
mixing. The milling can be performed on the powders while suspended
in the liquid suspending agent referred to above.
[0019] Electric field-assisted sintering is performed by passing a
pulsewise DC electric current through the powder mixture while
pressure is applied. A description of this method and of apparatus
in which the method can be applied is presented by Wang, S. W., et
al., "Densification of Al.sub.2O.sub.3 powder using spark plasma
sintering," J. Mater. Res. 15 (4), 982-987 (2000). While the
conditions may vary, best results will generally be obtained with a
densification pressure exceeding 10 MPa, preferably from about 10
MPa to about 200 MPa, and most preferably from about 40 MPa to
about 100 MPa. The preferred current is a pulsed DC current of from
about 250 A/cm.sup.2 to about 10,000 A/cm.sup.2, most preferably
from about 500 A/cm.sup.2 to about 1,500 A/cm.sup.2. The duration
of the pulsed current will generally range from about 1 minute to
about 30 minutes, and preferably from about 1.5 minutes to about 5
minutes. Preferred temperatures are within the range of from about
800.degree. C. to about 1,500.degree. C., and most preferably from
about 900.degree. C. to about 1,400.degree. C. Densification is
typically performed by isostatic compression under an inert gas
atmosphere, and preferred gas pressures for the densification are
within the range of from about 0.01 Torr to about 10 Torr, and most
preferably from about 0.03 Torr to about 1.0 Torr.
[0020] The term "nanocomposite" as used herein is intended to
include composites whose grain sizes are in the nano-size range,
i.e., less than 100 nm in diameter, as well as composites formed
from powders in the nano-size range that have undergone limited
grain growth during sintering. Accordingly, certain nanocomposites
referred to herein will have grain sizes that exceed the nano-size
range by as much as 500 nm due to the grain growth.
[0021] The following example is offered for purposes of
illustration and is not intended to limit the scope of the
invention.
EXAMPLE
Materials, Equipment, and Experimental Procedures
[0022] Purified single-wall carbon nanotubes produced by a
continuous catalytic process with more than 90% of the catalyst
removed were obtained from Carbon Nanotechnologies Incorporated
(Houston, Tex., USA). The nanotubes were obtained in paper form,
and once obtained were dispersed in ethanol with the assistance of
ultrasound. The ceramic material used was a mixture of alumina
powders consisting of 80% .alpha.-Al.sub.2O.sub.3 and 20%
.gamma.-Al.sub.2O.sub.3 with particle sizes of 300 nm (40 nm
crystallite size) and 20 nm respectively, obtained from Baikowski
International Corporation (Charlotte, N.C., USA). The alumina
powder was added to the alcohol suspension of the carbon nanotubes,
and a portion of the alcohol was then removed. Separate mixtures
representing 5.7 volume percent and 10 volume percent,
respectively, of carbon nanotubes relative to total solids, were
prepared in this manner. Each powder mixture, still suspended in
ethanol, was then passed through a 200-mesh sieve and placed in
milling jars with zirconia milling balls {fraction (5/16)}-inch in
diameter at a charge ratio of 10. The jars were then placed on a
rotary ball mill and milling was performed for 24 hours. All
ethanol was then removed by evaporation while the temperature was
maintained below 70.degree. C.
[0023] Each milled powder mixture was placed on a graphite die of
inner diameter 20 mm and cold-pressed at 200 MPa. The cold-pressed
powder mixtures were then sintered on a Dr. Sinter 1050 Spark
Plasma Sintering System (Sumitomo Coal Mining Company, Japan) under
vacuum. Electric field-assisted sintering was then performed at an
applied pressure of 63 MPa with a pulsed DC current of 5,000 A
maximum and a maximum voltage of 10 V, with a pulse duration time
of 12 ms separated by intervals of 2 ms. Once the pressure was
applied, the samples were heated to 600.degree. C. in 2 minutes and
then raised to 1,150.degree. C. for 3 minutes at a heating rate of
550.degree. C./min. The temperature was monitored with an optical
pyrometer focused on a depression in the graphite die measuring 2
mm in diameter and 5 mm in depth.
[0024] The final densities of the sintered compacts were measured
by the Archimedes method using deionized water as the immersion
medium. The density of the single-wall carbon nanotubes used as a
starting material was 1.8 g/cm.sup.3. Microstructure determinations
of the sintered compacts were performed with an FEI XL30-SFEG
high-resolution scanning electron microscope with a resolution
better than 2 nm and magnification of greater than 600 k. Grain
sizes were estimated by high-resolution scanning electron
microscope of fractured surfaces. Indentation tests were performed
on a Wilson Tukon hardness tester with a diamond Vickers indenter.
Bulk specimens were sectioned and mounted in epoxy, then polished
through 0.25-micron diamond paste. The indentation parameters for
fracture toughness (K.sub.IC) were a 2.5 kg load with a dwell time
of 15 s. The fracture toughness was calculated by the Anstis
equation as disclosed by Anstis, G. R., et al., "A Critical
Evaluation of Indentation Techniques for Measuring Fracture
Toughness: I, Direct Crack Measurement," J. Am. Ceram. Soc. 64 (9):
533-538 (1981).
[0025] In addition to the 5.7% and 10% (by volume) single-wall
carbon nanotube composites, pure alumina was processed in parallel
manner for comparison. The results were also compared with data
from the literature representing composites prepared by methods of
the prior art. All such results are presented below.
Results
[0026] The sintered materials whose preparation is described above
are listed in Table I together with nanocomposites selected from
the prior art as representative of the state of the art preceding
this invention. For each entry, the table lists composition,
expressed in terms of components and volume percents of each; the
sintering method, expressed as either electric field-assisted
sintering or hot pressing, together with the temperature reached
and the amount of time at that temperature; the relative density;
the grain size of the sintered product; the fracture toughness; and
the source of the data, i.e., either the inventors herein or the
literature citation. To obtain the relative density, the
theoretical density is first calculated as the total of the
densities of the components multiplied by their volume percents,
and the measured density is then expressed as a percent of the
theoretical density. In this Table, "SWCN" denotes single-wall
carbon nanotubes, "MWCN" denotes multi-wall carbon nanotubes, "SPS"
denotes spark plasma sintering (i.e., electric field-assisted
sintering), and "HP" denotes hot pressing (i.e., sintering in the
absence of an electric field).
1TABLE I Compositions, Processing Conditions and Relative Densities
of SWCN-Reinforced Alumina vs. Pure Alumina Composition Relative
Grain Fracture (additive volume %; Processing Density Size
Toughness balance Al.sub.2O.sub.3) Conditions (%) (nm)
(MPam.sup.1/2) Source 0% (pure Al.sub.2O.sub.3) SPS/1,150.degree.
C./3 min 100 349 3.3 herein 5.7% SWCN SPS/1,150.degree. C./3 min
100 200 7.9 herein 10% SWCN SPS/1,150.degree. C./3 min 100 200 9.7
herein 10% MWCN HP/1,300.degree. C./60 min 100 .about.500 4.2 (i)
6.4% SWCN; 2.5% Fe HP/1,475.degree. C./15 min 91 .about.500 4.8
(ii) 11.6% SWCN; 2.5% Fe HP/1,475.degree. C./15 min 97.5 .about.500
2.8 (ii) 4.7% SWCN; 5.3% Fe HP/1,475.degree. C./15 min 97.8
.about.500 3.6 (ii) 17.2% SWCN; 5.0% Fe HP/1,500.degree. C./15 min
99.2 .about.500 2.7 (ii) 8.5% SWCN; 4.3% Fe HP/1,500.degree. C./15
min 88.7 300 5.0 (iii) 10% SWCN; 4.3% Fe HP/1,500.degree. C./15 min
87.5 300 3.1 (iii) (i) Siegel, R. W., et al., "Mechaqnical Behavior
of Polymer and Ceramic Matrix Nanocomposites," Scripta Mater. 44:
2061-2064 (2001) (ii) Peigney, A., et al., "Carbon Nanotubes in
Novel Ceramic Matrix Nanocomposites," Ceram. Inter. 26: 677-683
(2000) (iii) Flahaut, E., et al., "Carbon Nanotubes-Metal-Oxide
Nanocomposites: Microstructure, Electrical Conductivity, and
Mechanical Properties," Acta Mater. 48: 8303-3812 (2000)
[0027] The fracture toughness data is also shown in FIG. 1, in
which the fracture toughness is plotted vs. the volume percent of
carbon nanotubes for each of the data entries in the Table. The
symbols used in FIG. 1 are: circles for the data generated by the
inventors herein, squares for the data taken from Siegel et al.,
triangles tapering at the top for the data taken from Peigney et
al., and triangles tapering at the bottom for the data taken from
Flahaut et al.
[0028] Comparison of the relative density values in the second and
third rows in Table I (the data representing the present invention)
with the relative density in the first row (and a comparison of the
circles in FIG. 1) indicates that the SWCN-containing
nanocomposites sintered by electric field-assisted sintering were
able to reach full density. This demonstrates that the addition of
SWCN had no adverse effect on the densification. Comparison of the
grain sizes among the various entries shows that the grain growth
was considerably lower in the second and third samples than in the
others, all of which used nano-scale powders as starting materials.
The smallest final grain size in the prior art entries was about
300 nm, but this was obtained at the expense of density, which was
only 88.7% of the theoretical density (ninth row of data). The only
other full-density sample was that achieved with multi-wall carbon
nanotubes (fourth row of data) but the grain size grew to 500
nm.
[0029] The microstructures observed by high-resolution scanning
electron micrograph of fractured surfaces for the composites shown
in the second and third rows of the table showed that the carbon
nanotubes were homogeneously dispersed through the alumina matrix
in both cases, although some agglomerations were observed in the
10% sample. Fracture surfaces were textured and rough in both
nanocomposites. No separation of the carbon nanotubes was observed.
Instead, the nanotube ropes were entangled with the alumina grains
to form a network structure. This has not been observed in the
prior art.
[0030] Comparison of the values in the fracture toughness column of
the Table and in the Figure shows that for the samples within the
scope of the present invention (the second and third rows in the
Table), the fracture toughness significantly increases with an
increase in the amount of single-wall carbon nanotubes present. The
sample containing 10 volume percent SWCN exhibited a fracture
toughness that was nearly three times that of pure nanocrystalline
alumina (shown in the first row of the table). The 10% SWCN sample
is also more than two and a half times tougher than a similar
sample from the literature (Siegel et al.) with the same content
but in multi-wall carbon nanotubes rather than single-wall (third
row vs. fourth row) and obtained by hot-pressing rather than
electric field-assisted sintering. In its own comparison with pure
alumina, the Siegel et al. paper reports only a 24% increase, and
other investigators, notably Laurent, C., et al., "Carbon
Nanotubes-Fe-Alumina Nanocomposites. Part I: Influence of the Fe
Content on the Synthesis of Powders," J. Euro. Ceram. Soc. 18:
2005-2013 (1998), report no toughening effect at all when carbon
nanotubes are incorporated into Fe-Al.sub.2O.sub.3. In sharp
contrast, the comparison performed by the inventors herein shows a
194% increase over pure alumina (third row vs. first row).
[0031] The foregoing is offered primarily for purposes of
illustration and explanation. Further variations, modifications and
substitutions that, even though not disclosed herein, still fall
within the scope of the invention may readily occur to those
skilled in the art.
* * * * *