U.S. patent application number 13/214633 was filed with the patent office on 2012-05-31 for porous nanostructured polyimide networks and methods of manufacture.
This patent application is currently assigned to Aerogel Technologies, LLC. Invention is credited to Chakkaravarthy Chidambareswarapattar, Nicholas Leventis, Chariklia Sotiriou-Leventis.
Application Number | 20120134909 13/214633 |
Document ID | / |
Family ID | 46126818 |
Filed Date | 2012-05-31 |
United States Patent
Application |
20120134909 |
Kind Code |
A1 |
Leventis; Nicholas ; et
al. |
May 31, 2012 |
POROUS NANOSTRUCTURED POLYIMIDE NETWORKS AND METHODS OF
MANUFACTURE
Abstract
Porous three-dimensional networks of polyimide and porous
three-dimensional networks of carbon and methods of their
manufacture are described. For example, polyimide aerogels are
prepared by mixing a dianhydride and a diisocyanate in a solvent
comprising a pyrrolidone and acetonitrile at room temperature to
form a sol-gel material and supercritically drying the sol-gel
material to form the polyimide aerogel. Porous three-dimensional
polyimide networks, such as polyimide aerogels, may also exhibit a
fibrous morphology. Having a porous three-dimensional polyimide
network undergo an additional step of pyrolysis may result in the
three dimensional network being converted to a purely carbon
skeleton, yielding a porous three-dimensional carbon network. The
carbon network, having been derived from a fibrous polyimide
network, may also exhibit a fibrous morphology.
Inventors: |
Leventis; Nicholas; (Rolla,
MO) ; Sotiriou-Leventis; Chariklia; (Rolla, MO)
; Chidambareswarapattar; Chakkaravarthy; (Rolla,
MO) |
Assignee: |
Aerogel Technologies, LLC
Glendale
WI
|
Family ID: |
46126818 |
Appl. No.: |
13/214633 |
Filed: |
August 22, 2011 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
|
61375656 |
Aug 20, 2010 |
|
|
|
Current U.S.
Class: |
423/439 ; 216/56;
423/445R; 521/157; 521/89; 521/90; 977/700; 977/897 |
Current CPC
Class: |
C08G 18/7671 20130101;
B82Y 40/00 20130101; C01B 32/90 20170801; C08G 18/3243 20130101;
C08J 9/28 20130101; C08G 73/1003 20130101; C01B 32/30 20170801;
C08L 79/08 20130101; C01B 32/956 20170801; C01B 32/97 20170801;
C08J 2201/0502 20130101; C01B 32/00 20170801; H01G 11/38 20130101;
Y02E 60/13 20130101; C08G 73/1035 20130101; B82Y 30/00 20130101;
C08J 2205/026 20130101; C08G 18/346 20130101; C08G 73/1067
20130101; C08G 2110/0091 20210101; C08J 2375/04 20130101 |
Class at
Publication: |
423/439 ; 521/90;
521/89; 423/445.R; 521/157; 216/56; 977/700; 977/897 |
International
Class: |
C08G 73/10 20060101
C08G073/10; C01B 31/02 20060101 C01B031/02; C01B 31/00 20060101
C01B031/00; B44C 1/22 20060101 B44C001/22; C08J 9/28 20060101
C08J009/28; C01B 31/30 20060101 C01B031/30 |
Goverment Interests
FEDERALLY SPONSORED RESEARCH
[0002] Research leading to various aspects of embodiments presented
herein were sponsored, at least in part, by the National Science
Foundation, Grant No. CHE-0809562 and Grant No. CMMI-0653919. The
United States Government may have certain rights in the invention.
Claims
1. A method of manufacturing a three-dimensional nanostructured
polyimide network, the method comprising: mixing an anhydride and
an isocyanate in a solvent to form a sol-gel material; and drying
the sol-gel material to form the polyimide network.
2. The method of claim 1, wherein the solvent comprises at least
one of pyrrolidone and N-methyl-2-pyrrolidone.
3. The method of claim 1, wherein the anhydride is pyromellitic
dianhydride.
4. The method of claim 1, wherein the isocyanate is
4,4'-diisocyanatodiphenylmethane.
5. The method of claim 1, wherein the solvent further comprises at
least one of acetonitrile, acrylonitrile, or acetone.
6. The method of claim 1, further comprising a step of subjecting
the sol-gel material to solvent-exchange using at least one of a
pyrrolidone, acetonitrile, or acetone.
7. The method of claim 1, wherein the drying the sol-gel material
includes supercritical drying of the sol-gel material.
8. The method of claim 1, wherein the drying the sol-gel material
includes subcritical drying of the sol-gel material.
9. A fibrous aerogel comprising: a three dimensional network of
particles including polyimide, the three dimensional network having
a fibrous morphology.
10. An insulator, a lightweight structural material, an acoustic
insulating material, or an impact dampening material comprising the
aerogel of claim 9.
11. The method of claim 1, further comprising pyrolyzing the
polyimide network to form a carbon network.
12. The method of claim 11, wherein the carbon network is
chemically etched to produce a carbon network having increased
microporosity.
13. The carbon aerogel of claim 11.
14. A fibrous aerogel comprising: a three dimensional network of
nanoparticles including a carbon skeleton, the three dimensional
network having a fibrous morphology.
15. An electrode, a battery, a supercapacitor device, an insulator,
a ballistic material, an ablative material, an armor comprising the
aerogel of claim 14.
16. A method of manufacturing an aerogel, the method comprising:
mixing an anhydride and an isocyanate in a solvent in the presence
of a ceramic oxide to form a sol-gel material; drying the sol-gel
material to form the hybrid polyimide aerogel; and pyrolyzing the
hybrid polyimide aerogel to form at least one of a metal aerogel, a
metalloid aerogel, a metal carbide aerogel and a metalloid carbide
aerogel.
17. The method of claim 16, in which the ceramic oxide forms an
interpenetrating network throughout a polyimide network.
18. The method of claim 16, in which the ceramic oxide comprises
one or more of a metal oxide, a metalloid oxide, or silicon
oxide.
19. The aerogel of claim 16.
20. The method of claim 1, wherein the isocyanate comprises at
least one of a diisocyanate, triisocyanate, and a polyisocyanate.
Description
RELATED APPLICATION
[0001] This application claims the benefit of U.S. Provisional
Patent Application Ser. No. 61/375,656, filed Aug. 20, 2011,
entitled "Porous Nanostructured Polyimide Networks and Methods of
Manufacture," by Leventis et al.
BACKGROUND
[0003] 1. Field
[0004] Aspects herein relate to nanostructured polyimide networks,
carbonized derivatives, related materials, uses thereof, and
methods of manufacture.
[0005] 2. Discussion of Related Art
[0006] Three-dimensional porous architectures are a desirable form
factor for many materials as they allow installation of new
properties into a material not possessed by the non-porous form of
a material. Porous architectures possessing nanostructured
features, such as nanopores or nanoparticulate solid frameworks,
are further desirable in many cases as they can possess new and/or
more extreme properties than porous architectures without
nanostructured features.
[0007] Aerogels are an example of a porous architecture possessing
nanostructured features. Aerogels are materials comprised of
three-dimensional assemblies of nanoparticles or nanostructures
that exhibit high porosity materials and ultra-low densities
Aerogel materials are typically produced by forming a gel that
includes a porous solid component and a liquid component and then
removing the liquid component by supercritically, subcritically, or
freeze drying the wet gel to isolate the porous solid component.
This porous solid component is an aerogel. Supercritical drying
involves the liquid being transformed into a fluid above its
critical point and removing the fluid while leaving the porous
solid structure generally intact. Subcritical drying involves
evaporation of the liquid below its critical point in a way that
leaves the porous solid structure generally intact. Freeze drying
involves freezing of the liquid component and sublimation of the
resulting solid in a way that leaves the porous solid structure
generally intact.
[0008] The large internal void space in aerogels and other
nanostructured and non-nanostructured three-dimensional porous
networks generally provides for a low dielectric constant, a low
thermal conductivity, and a high acoustic impedance. These
materials have been considered for a number of applications
including thermal insulation, lightweight structures, and impact
resistance.
SUMMARY
[0009] Articles and methods for manufacturing three-dimensional
porous polyimide networks and three-dimensional porous carbon
networks are described.
[0010] Three-dimensional porous polyimide networks can be prepared
by mixing a dianhydride and a diisocyanate in a solvent comprising
a pyrrolidone and acetonitrile at room temperature to form a
sol-gel material and subsequently drying the sol-gel material to
form a polyimide aerogel. Drying may be performed supercritically,
subcritically, or by freeze drying. In some embodiments, a
polyimide aerogel manufactured by methods described herein may have
a fibrous morphology which may or may not also include particulate
features.
[0011] Three-dimensional porous carbon network aerogels may also be
manufactured through a conversion step from polyimide aerogels.
Once a polyimide aerogel is formed, the aerogel may be subjected to
a pyrolysis step, giving rise to a carbon skeleton in the aerogel,
hence, a carbon aerogel. In some embodiments, a polyimide aerogel
having a fibrous morphology that is subject to the pyrolysis step
may give rise to a carbon aerogel also having a fibrous
morphology.
[0012] In some cases, three-dimensional porous polyimide networks
not considered aerogels may be produced. Likewise,
three-dimensional porous carbon networks not considered aerogels
may be derived from such three-dimensional polyimide networks.
[0013] Various embodiments of the present invention provide certain
advantages. Not all embodiments of the invention share the same
advantages and those that do may not share them under all
circumstances.
[0014] Further features and advantages of the present invention, as
well as the structure of various embodiments of the present
invention are described in detail below with reference to the
accompanying drawings.
BRIEF DESCRIPTION OF DRAWINGS
[0015] The accompanying drawings are not intended to be drawn to
scale. For purposes of clarity, not every component may be labeled
in every drawing. Various embodiments of the invention are
described, by way of example, in the accompanying drawings. In the
drawings:
[0016] FIG. 1 depicts chemical structures for PMDA, MDI and
MDA;
[0017] FIG. 2a shows a flow chart for the preparation of a
three-dimensional porous polyimide network in accordance with some
embodiments;
[0018] FIG. 2b shows another flow chart for the preparation of a
three-dimensional porous polyimide network in accordance with some
embodiments;
[0019] FIG. 3a depicts a flow chart for the preparation of a
three-dimensional porous polyimide network in accordance with some
embodiments;
[0020] FIG. 3b shows another flow chart for the preparation of a
three-dimensional porous polyimide network in accordance with some
embodiments;
[0021] FIG. 3c shows yet another flow chart for the preparation of
a three-dimensional porous polyimide network in accordance with
some embodiments;
[0022] FIG. 4 illustrates a reaction step in forming a
three-dimensional porous polyimide network in accordance with some
embodiments;
[0023] FIG. 5a depicts reactions where a polyimide is formed
through isocyanate and amine routes in accordance with some
embodiments;
[0024] FIG. 5b depicts more reactions where a polyimide is formed
through isocyanate and amine routes in accordance with some
embodiments;
[0025] FIG. 6a depicts a molecular structure of a three-dimensional
porous polyimide network formed through an amine route;
[0026] FIG. 6b illustrates a molecular structure of a
three-dimensional porous polyimide network formed through an
isocyanate route in accordance with some embodiments;
[0027] FIG. 7 shows a nuclear magnetic resonance (NMR) spectra of a
PMDA/MDI mixture in accordance with some embodiments;
[0028] FIG. 8 illustrates photographs of polyimide aerogels
synthesized in accordance with some embodiments;
[0029] FIG. 9 depicts an infrared (IR) spectra of polyimide
aerogels prepared in accordance with some embodiments;
[0030] FIG. 10 illustrates a NMR spectra of polyimide aerogels
prepared in accordance with some embodiments;
[0031] FIG. 11 depicts a shrinkage data for polyimide aerogels
prepared in accordance with some embodiments;
[0032] FIG. 12 shows nitrogen sorption data for polyimide aerogels
prepared in accordance with some embodiments;
[0033] FIG. 13 shows scanning electron microscope (SEM) images of
polyimide aerogels prepared in accordance with some
embodiments;
[0034] FIG. 14 shows more SEM images of polyimide aerogels prepared
in accordance with some embodiments;
[0035] FIG. 15 depicts small angle neutron scattering data of
polyimide aerogels prepared in accordance with some
embodiments;
[0036] FIG. 16 illustrates a compressive stress-strain curve of
polyimide aerogels prepared in accordance with some
embodiments;
[0037] FIG. 17 shows thermogravimetric analysis (TGA) data of
polyimide aerogels prepared in accordance with some
embodiments;
[0038] FIG. 18 shows Raman spectra polyimide aerogels prepared in
accordance with some embodiments;
[0039] FIG. 19 shows SEM images and nitrogen sorption data for
carbon aerogels prepared in accordance with some embodiments;
and
[0040] FIG. 20 shows more SEM images and nitrogen sorption data for
carbon aerogels prepared in accordance with some embodiments.
DETAILED DESCRIPTION
[0041] Porous three-dimensional networks of polyimide and porous
three-dimensional networks of carbon and methods of their
manufacture are described herein. In some embodiments,
three-dimensional porous polyimide networks (e.g., aerogels) are
prepared by mixing a dianhydride and a diisocyanate in a solvent
comprising a pyrrolidone and an acetonitrile at room temperature to
form a sol-gel material. The sol-gel material may be dried
supercritically or subcritically so as to form the
three-dimensional porous polyimide network. The three-dimensional
porous polyimide network may also exhibit a fibrous morphology. In
some embodiments, the three-dimensional porous polyimide network
may be subject to an additional step of pyrolysis resulting in the
three dimensional network of polyimide being converted to a carbon
skeleton, yielding a three-dimensional porous carbon network. The
three-dimensional porous carbon network, having been derived from a
fibrous three-dimensional porous polyimide network, may also
exhibit a fibrous morphology.
[0042] Three-dimensional porous polyimide networks may be prepared
via a one-step room-temperature synthesis route involving reaction
of a dianhydride with a diisocyanate. Using an isocyanate to form
the polyimide network using methods described herein provides
certain advantages: a) CO.sub.2 is the only substantial byproduct;
b) sacrificial dehydrating agents (e.g., acetic anhydride/pyridine)
are not required for gelation; c) gelation and imidization take
place at room temperature and, thus, post-gelation curing at high
temperatures (e.g., 190.degree. C.) in order to complete
imidization is not required; d) use of isocyanates is cheaper than
use of amines from the traditional route; e) higher density
bifunctional aerogels for dual-purpose applications (e.g. thermal
insulators that are also used as structural components; impact
dampening materials that are also used as structural components)
are easily accessible with no solubility issues in turn extending
the accessible density range upwards, while the polyamic acid route
encounters solubility issues at higher concentration sols; and f)
an entangled fiber nanomorphology stabilizes the nanostructure,
extending the accessible density range downwards.
[0043] Three-dimensional porous polyimide networks such as
polyimide aerogels may be manufactured using a route that involves
condensation of a dianhydride and a diamine to form a polyamic acid
solution that is dehydrated with an anhydride to form polyimide. In
some cases, use of a sacrificial dehydration step is generally
expensive with respect to the cost of materials and removal of the
byproducts. A further complication may be the kinetic formation of
isoimides which can be converted to more thermodynamically stable
imides by high-temperature treatment. To accommodate this, the
dehydration step may be carried out at elevated temperatures
directly (>130.degree. C.). Preparation of certain polyimide
aerogels are described in U.S. Pat. No. 7,074,880 entitled
"Polyimide aerogels, carbon aerogels, and metal carbide aerogels
and methods of making same" and is incorporated herein by reference
in its entirety.
[0044] Polyimide aerogels synthesized via a conventional route
using diamine (PI-AMN) as compared to routes contemplated by the
inventors and described herein using isocyanate (PI-ISO) may have
similar surface areas (e.g., for 20% solid formulation PI-ISO: 351
m.sup.2/g, density=0.196 g/cm.sup.3; PI-AMN: 377 m.sup.2/g,
density=0.291 g/cm.sup.3). However, the nanomorphologies of
polyimide aerogels prepared using isocyanate may be completely
different from nanomorphologies of polyimide aerogels prepared
using diamine. For example, for a similar chemical composition,
PI-ISO may have a fibrous morphology, while PI-AMN have a
particulate morphology. In general, PI-ISO may also be more robust
and may shrink less compared to PI-AMN. Upon pyrolysis, polyimide
aerogels can be converted to carbon aerogels which may retain the
main morphological characteristics (fibrous versus particulate) of
their parent polyimide aerogels.
[0045] Three-dimensional porous polyimide networks such as
polyimide aerogels synthesized through the isocyanate route are
less prone to shrinkage during processing compared to polyimide
aerogels synthesized through the diamine route, densities as low as
0.04 g/cm.sup.3 have been obtained. Further, owing to solubility
issues, PI-AMN aerogels generally cannot be made with sols above
20% w/w solids in the sol. Resulting PI-AMN aerogels had a density
of 0.291 g/cm.sup.3. However, more concentrated sols are possible
via the isocyanate route. For example, PI-ISO aerogels from sols
with 30% w/w solids had a density of about 0.304 g/cm.sup.3. Upon
carbonization at 800.degree. C., PI-ISO retain their parent
nanomorphology, which may be fibrous. The ability to prepare higher
density polyimide aerogels and other three-dimensional porous
polyimide networks extends the range of compressive strength and
stiffness attainable for polyimide networks and their carbonized
derivatives.
[0046] Three-dimensional porous polyimide networks such as
polyimide aerogels prepared in accordance with methods described
herein may exhibit a suitable degree of shrinkage. In some
embodiments, three-dimensional porous polyimide networks (e.g.,
polyimide aerogels) prepared with isocyanate may exhibit a
shrinkage of less than 30%, less than 20%, less than 10%, less than
5%, less than 2%, less than 1%. In some cases, the shrinkage of a
polyimide aerogel may be affected by the percent solids w/w. For
example, when the percentage of solids in the sol is lower, the
degree of shrinkage for the polyimide aerogel may be greater.
[0047] The density of three-dimensional porous polyimide networks
or three-dimensional porous carbon networks prepared from pyrolysis
of polyimide networks using methods described herein may be
between, for example, about 1 mg/cc and about 550 mg/cc, or between
about 100 mg/cc and about 400 mg/cc. In some embodiments, the
density of three-dimensional porous polyimide networks or
three-dimensional porous carbon networks prepared from pyrolysis of
polyimide networks may be greater than about 300 mg/cc.
[0048] Aerogels described herein may include a three-dimensional
porous network of secondary particles and primary particles. Porous
secondary particles having a diameter of between about 5-10 nm are
made up of nonporous primary particles having a diameter of less
than about 1 nm. While the primary particles are arranged in a
manner that forms micropores within the secondary particles, larger
mesopores arise through the arrangement of secondary particles
relative to one another. A silica nanoparticle network in the form
of an aerogel may include mesopores having voids that are between
2-50 nm in diameter between secondary particles. Primary particles
include voids that are less than 2 nm in diameter.
[0049] Three-dimensional porous networks discussed herein may have
fibrous morphologies where the networks may include nanofibers
having various diameters and lengths. In some embodiments, fibrous
morphologies of such networks include fibers having an average
diameter ranging between about 1 nm and about 500 nm (e.g., between
about 10 nm and about 400 nm, between about 100 nm and about 300
nm) or less than 500 nm (e.g., less than 400 nm, less than 300 nm,
less than 200 nm). In some embodiments, fibrous morphologies of
porous networks described herein include fibers having an average
length of at least 50 nm and may extend into the micron length
scale. The average aspect ratio of fibers in a three-dimensional
porous networks having a fibrous morphology, such as an aerogel may
be greater than 2, greater than 5, greater than 10, greater than
20, greater than 50, etc. Three-dimensional porous networks
described herein that exhibit a fibrous morphology may include both
fibrous and non-fibrous features (e.g., particulate), but, in some
embodiments, could also contain only fibrous features, free of
non-fibrous features.
[0050] Any appropriate isocyanate, such as a diisocyanate or
triisocyanate, may be used for forming a sol-gel material to
produce a three-dimensional porous polyimide network, such as a
polyimide aerogel. For example, suitable non-limiting diisocyanates
may include 4,4'-diisocyanatodiphenylmethane or methylene
di-p-phenyldiisocyanate (MDI).
[0051] Any appropriate dianhydride may be used to react with an
isocyanate (e.g., diisocyanate, triisocyanate) in forming a sol-gel
material to produce a three-dimensional porous polyimide network,
for example, a polyimide aerogel. In an embodiment, a suitable
non-limiting dianhydride includes pyromellitic dianhydride
(PMDA).
[0052] A suitable solvent may be used along with the isocyanate and
the dianhydride. In various embodiments, a pyrrolidone (e.g.,
N-methyl-2-pyrrolidone, NMP), acetonitrile, acrylonitrile, acetone,
and/or combinations thereof may be used to form a three-dimensional
porous polyimide network, such as a polyimide aerogel.
[0053] In some embodiments, monolithic polyimide aerogels (PI-ISO)
may be prepared by drying wet gels synthesized via a rather
underutilized room-temperature reaction of pyromellitic dianhydride
(PMDA) with 4,4'-methylene di-p-phenyldiisocyanate (MDI). The
reaction may be observed using liquid-phase .sup.13C-NMR in
DMSO-d.sub.6 which, for some cases, has indicated that the reaction
proceeds through a seven-member ring intermediate that collapses to
the imide by expelling CO.sub.2. PI-ISO may be characterized and
compared with aerogels obtained via the classic reaction of PMDA
and 4,4'-methylenedianiline (MDA), referred to as PI-AMN. The two
materials, PI-ISO and PI-AMN may be chemically identical, showing
similar degrees of crystallinity (30-45%, by XRD), and both
including similarly sized primary particles (6.1-7.5 nm, verified
by SANS). For some embodiments, they both may contain meso- and
macroporosity by N.sub.2-sorption porosimetry and may exhibit
similar BET surface areas (300-400 m.sup.2 g.sup.-1).
[0054] A major difference between PI-AMN and PI-ISO prepared using
methods described herein, however, is that PI-AMN are particulate
while PI-ISO may be fibrous in morphology. Without being limited to
any one particular mechanism, the difference in morphology may be
due to the rigidity of the seven-member ring intermediate of
PI-ISO. PI-AMN shrinks significantly during processing (up to 40%
in linear dimensions), but can exhibit stronger mechanical
properties than PI-ISO of the same density. Upon pyrolysis at
800.degree. C., both PI-ISO and PI-AMN have been observed to
convert to porous carbons. PI-AMN lose their nanomorphology and
more than 2/3 of their surface area, as opposed to PI-ISO, which
retains their nanomorphology and surface area. Etching with
CO.sub.2 at 1000.degree. C. increases the surface area of both
PI-AMN and PI-ISO, and improves the electrical conductivity of the
latter. In one embodiment, etching resulted in an increase of
surface area in PI-AMN to 417 m.sup.2/g and an increase in PI-ISO
to 1010 m.sup.2/g and an increase in electrical conductivity in
PI-ISO by a factor of 70. Etching for longer periods of times, with
higher flow rates of CO.sub.2, and higher temperatures can further
increase these values.
[0055] Among engineering plastics, polyimides demonstrate good
chemical resistance as well as excellent mechanical properties and
stability at high temperatures. For example, a special formulation
referred to as PMR-15 is emerging as an aerospace industry standard
for replacing metal components in jet engines and is rated at
290.degree. C. for 10,000 h. In that regard, polyimide aerogels
could be ideal materials for high-temperature low-k dielectrics for
fast electronics (where k stands for the dielectric constant), and
for high-temperature thermal insulation with advantages over blown
closed-cell macroporous polyimide foams already in use for that
purpose. As mentioned, polyimide aerogels may have synthesized
employing a conventional two-step DuPont route utilizing
dianhydrides and diamines. The two monomers react at room
temperature yielding a polyamic acid solution that subsequently is
dehydrated to the polyimide with acidic anhydride and a
base-catalyst (e.g., pyridine or triethylamine). A post-gelation
high-temperature treatment of wet gels ensures complete imidization
and conversion of undesirable isoimides to imides. Though chemical
dehydration of the polyamic acid is energy-intensive and introduces
by-products, industrially, dehydration and imidization are carried
out by direct heating of the polyamic acid at high temperatures
(.about.200.degree. C.). In an attempt to adapt this direct heating
method for the synthesis of aerogels, however, precipitates were
obtained rather than gels.
[0056] Polyimide aerogels described herein may also be synthesized
via a one-step room-temperature route that involves reaction of
anhydrides with isocyanates. In some embodiments, pyromellitic
dianhydride (PMDA) is reacted with 4,4'-methylene diphenyl
diisocyanate (MDI). For contrast, a route involving the reaction of
PDMA with 4,4'-methylenedianiline (MDA) will be considered.
Resulting aerogels from both routes are chemically identical (by IR
and solids CPMAS .sup.13C-NMR). However, despite similar degrees of
crystallinity and primary particle sizes (by XRD and SANS,
respectively), their nanomorphology (by SEM) may be quite
different: polyimides from the amine route (PI-AMN) are
particulate, while those from the isocyanate route (PI-ISO) are
fibrous. One of ordinary skill in the art would be able to
recognize the difference between a particulate and fibrous
morphology. Upon pyrolysis, both kinds of polyimide aerogels may be
converted to carbon aerogels, which, in the case of PI-ISO retain
the fibrous morphology of their parent polyimides.
EXAMPLES
Synthesis of PI-ISO Versus PI-AMN
[0057] FIG. 1 illustrates the chemical structures for a number of
polyimide aerogel precursors, namely PMDA, MDI and MDA. FIGS. 2a-2c
and 3a-3b summarize various embodiments of the synthesis of PI-AMN
and PI-ISO aerogels. Typical samples processed under the different
conditions discussed below are shown in the figures.
[0058] PI-AMN were prepared through a polyamic acid step (see FIGS.
5a and 5b) according to a modification of the Aspen Aerogels
adaptation of the classic DuPont route. According to the latter,
typically polyamic acid is not isolated from its preparation
solution (in N-methyl-2-pyrrolidone, NMP) and is dehydrated either
thermally (>190.degree. C.) or chemically at room temperature
with acetic anhydride/base (e.g., pyridine, triethylamine, etc.).
At first, to improve the Aspen Aerogels protocol that opts for
chemical dehydration, bypassing the latter step by direct heating
of NMP solutions of the polyamic acid may be performed, yet may
result in precipitation rather than gelation. Thus,
room-temperature (RT) chemical dehydration was used with acetic
anhydride/pyridine. The bulk density of the final aerogels may be
varied by successive dilutions of the polyamic acid solution before
adding the dehydrating agents. Although addition of the dehydrating
agents into the polyamic acid solution induces gelation, in general
polyimides obtained by that route required heating at elevated
temperatures in order to complete imidization and to convert any
kinetically formed isoimides to thermodynamically more stable
imides.
[0059] Room-temperature PI-AMN gels were solvent-exchanged with
ethanol and dried to aerogels (abbreviated as PI-AMN-RT) using
liquid CO.sub.2 extracted supercritically. Subcritical drying of
the aerogels may also be performed. According to IR, PI-AMN-RT
aerogels do not contain detectable amounts of isoimide (with
expected absorption at 1800 cm.sup.-1), but the absorption at
.about.3500 cm.sup.-1 indicates that they may contain amides and
therefore unreacted polyamic acid. Heating PI-AMN-RT aerogels at
190.degree. C. causes extensive shrinkage and results into
xerogel-like materials with a loss in surface area. Hence, PI-AMN
was heated in a solvent-swollen state, and thus imidization was
completed before drying by transferring wet gels into NMP followed
by heating at 190.degree. C. Subsequently, wet gels may be cooled
to RT, NMP was exchanged with ethanol, and ethanol-filled wet-gels
may be supercritically dried with CO.sub.2 yielding PI-AMN-190
aerogels. In some cases, even though absorption at .about.3500
cm.sup.-1 decreases, it did not disappear. Further, even by heating
in the solvent-swollen state, PI-AMN samples shrink significantly
relative to their molds (up to 40% in linear dimensions)
irrespective of their bulk density; shrinkage is not caused by the
heat treatment at 190.degree. C., as aerogel samples either dried
directly after gelation (PI-AMN-RT) or after heating at 190.degree.
C. in NMP according to FIGS. 2a and 3a (PI-AMN-190) are similar in
size. Rather, shrinkage of PI-AMN samples may be attributed to the
innate chemistry of the gel-forming process.
[0060] On the other hand, PMDA/MDI solutions gel directly at room
temperature without use of additional reagents. The reaction was
followed up to the gelation point using liquid-phase .sup.13C-NMR
in DMSO-d.sub.6. As shown in FIGS. 5a and 5b, it can be seen that
the reaction proceeds through a seven-member ring intermediate
which collapses to the imide by expelling CO.sub.2. At the gelation
point (.about.7.5 h), a significant amount of the seven-member ring
intermediate remains and still reacts. On the other hand, the
reaction may proceed much slower in NMP at RT and gelation may take
up to 48 h depending on the monomer concentration. Gelation may be
carried out at RT in DMSO. Although PI aerogels are opaque, their
wet gel precursors are generally translucent allowing visual
inspection of their interior. It can be seen that PI-ISO aerogels
obtained from DMSO sols at RT may contain large bubbles (CO.sub.2)
entrapped in their bulk.
[0061] In some embodiments, the seven-member intermediate may be
considered an in-situ foaming agent leading to foam-like PI-ISO
architectures defined by porous walls. Macroscopically void-free
(i.e., bubble-free) PI-ISO aerogel monoliths were obtained by two
methods (shown in FIGS. 2b, 3b-3c): either, (a) by RT gelation of
PMDA/MDI in mixtures of NMP with DMSO or acetonitrile (samples
referred to as PI-ISO-RT); or, (b) by gelation in pure NMP at
slightly elevated temperatures by stepwise heating from 60.degree.
C. to 90.degree. C. (see FIGS. 2b, 3b-3c, samples referred to as
PI-ISO-90). It can be appreciated that other heating arrangements
may be possible. The first method combines sufficiently
low-viscosity sols with affordable gelation times (30-33 h for the
15% w/w solids formulation) allowing CO.sub.2 to be dissipated and
bubble formation to be avoided. The second method has the advantage
of comparing PI-ISO and PI-AMN prepared in environments of similar
polarity (both in NMP); step-wise heating of the PMDA/MDI sol in
NMP ensured defect-free monoliths, while direct heating at
90.degree. C. led to foams qualitatively similar to those obtained
in DMSO at RT (i.e., with bubbles). All gels were aged
.about.4.times. their gelation time in their molds, were
solvent-exchanged with ethanol, and supercritically dried with
CO.sub.2.
[0062] IR spectra of PI-ISO-RT look essentially identical to IR
spectra of PI-AMN-190, but the solid-state .sup.13C-NMR spectra of
the two materials show differences in the relative peak intensities
which are attributed to differences in polymer length and therefore
to the polarity of the sol (as a reminder, PI-ISO-RT were prepared
in NMP/acetonitrile or NMP/DMSO mixtures, while PI-AMN-190 were
prepared in pure NMP). FIG. 9 shows IR spectra of polyimide aerogel
samples where peak assignments include: a, b (1777 cm.sup.-1 and
1723 cm.sup.-1) asymmetric and symmetric stretching vibrations of
C.dbd.O; c (1511 cm.sup.-1) aromatic ring breathing modes; d (1366
cm.sup.-1) C--N--C imide ring stretching; e, f (1123 cm.sup.-1 and
780 cm.sup.-1) imide ring vibrations; and g (723 cm.sup.-1) imide
ring bending.
[0063] FIG. 10 shows solids CPMAS .sup.13C-NMR of samples as
indicated. Samples shown are prepared using the 15% solids
formulation (Table 1) with PI-AMN and PI-ISO-90 prepared in NMP;
and PI-ISO-RT prepared in NMP/CH.sub.3CN (3:1 w/w). Notably, the
peak in the .sup.13C-NMR spectrum of PI-AMN-190 at 142 ppm (carbon
number 16, see FIGS. 5a and 5b) appears only as a shoulder in the
spectrum of PI-ISO-RT. According to .sup.13C-NMR spectra
simulations of the PMDA/MDI dimer transition to pentamer, an
upfield shift for the resonance of carbon number 16 as the polymer
becomes longer is expected, suggesting that PI-ISO-RT consists of
longer polymer chains than PI-AMN-190. The .sup.13C-NMR spectrum of
PI-ISO-90, (which was also prepared in NMP just like PI-AMN-190),
is identical to the spectrum of the latter, signifying the
importance of the solvent polarity in the nucleation and growth
mechanism by which the two materials are formed. FIG. 7 shows room
temperature (20 C) liquid .sup.13C-NMR in DMSO-d6 of a PMDA/MDI
mixture (1:1 mol:mol, 12% w/w solids formulation). The bottom two
spectra are of the monomers. Times reported refer to the time
lapsed after mixing. The last spectrum at the top corresponds to
the point just before gelation. FIGS. 5a and 5b show peak
assignment (by spectra simulation).
Experimental Methods
[0064] Pyromellitic dianhydride (PMDA) (e.g., obtained from
Chriskev Company, Inc.); 4,4'-diisocyanatodiphenylmethane
(4,4'-methylene diphenyl diisocyanate, MDI),
4,4'-methylenedianiline (MDA), and acetic anhydride ((Ac).sub.2O)
(e.g., obtained from Acros Chemicals); and pyridine (e.g., obtained
from Fisher Scientific) may be used. Anhydrous
N-methyl-2-pyrrolidone (NMP), acetonitrile, dimethylsulfoxide
(DMSO), and absolute ethanol were used (e.g., obtained from Aldrich
Chemical Co). Deuterated DMSO (DMSO-d.sub.6) was also used (e.g.,
obtained from Cambridge Isotope Laboratories, Inc).
[0065] Preparation of polyimide aerogels via the anhydride/diamine
route (PI-AMN) will now be described.
[0066] Pyromellitic dianhydride (15.696 g, 0.072 mol) and
4,4'-methylenedianiline (14.256 g, 0.072 mol) were added in
variable amounts of NMP in a 250 mL round bottom flask under
magnetic stirring. For example, for the 15% w/w solids formulation
(samples referred to as PI-AMN-15) the amount of NMP was 169.7 g.
The solution was stirred at room temperature under nitrogen for 12
h and the color changed from colorless to yellow. At that point,
acetic anhydride (in 6.3 mol excess to pyromellitic dianhydride)
and pyridine (1:1 mol ratio to acetic anhydride) were added to the
resulting polyamic acid solution, and the new solution (sol) was
poured into molds and was allowed to gel at room temperature. As
molds for samples used for general chemical and physical
characterization, Wheaton 4-mL Polypropylene Omni-Vials with a
1.04-cm inner diameter were used (Fisher part No. 225402), and for
samples used for mechanical testing 30-mL Fisherbrand Class B Amber
Glass Treaded Vials were used, 2.1-cm inner diameter (Fisher part
No. 03-339-23E). The gelation time depends on the formulation: for
2.5%, 5%, 10% and 20% w/w solids (PMDA+MDA) in the original NMP
solution the gelation time was .about.4 h, .about.1.5 h, 15 min and
<15 min, respectively. The gels were aged in the molds for 12 h,
subsequently they were washed with NMP (3.times., 8 h each time,
using 4.times. the volume of the gel each time), cured at
190.degree. C. for 3 h in the last NMP wash solution, cooled to
room temperature, washed with ethanol (4.times., 8 h each time,
using 4.times. the volume of the gel for each wash) and dried into
polyimide aerogels in an autoclave with liquid CO.sub.2, taken out
at the end supercritically.
[0067] Preparation of polyimide aerogels via the isocyanate route
(PI-ISO) at room temperature and at 90.degree. C. will now be
described.
[0068] At room temperature, MDI (2.50 g, 0.01 mol) was added under
stirring to a mixture of NMP and acetonitrile (3:1 w/w), or NMP and
DMSO (1:1 w/w) in a three-neck round bottom flask under N.sub.2 at
room temperature. Once the isocyanate was dissolved, pyromellitic
dianhydride (2.18 g, 0.01 mol) was added. For example, for a 15%
w/w solids formulation the amount of NMP and acetonitrile were
19.88 g (19.34 mL) and 6.62 g (8.43 mL), respectively. Similarly
for a 10% w/w solids formulation, the amounts of NMP and DMSO were
21.06 g and 21.06 g respectively. The reaction mixture was stirred
under nitrogen for 1 h. The resulting sol was poured in molds (see
above), which were allowed to stand at room temperature. Gelation
takes usually 6 h-48 h depending on the formulation. For example,
in NMP:CH.sub.3CN (3:1 w/w), the 10%, 15%, 20% and 30% w/w solids
formulations take 2 days, 36 h, 18 h, and 12 h, respectively. By
comparison, a 15% w/w solids formulation in NMP takes 48 h for
gelation at RT. Gels were aged in the molds for 24 h-8 days
depending on the gelation time, typically four times the gelation
time. Subsequently, gels were removed from the molds and were
initially washed (solvent-exchanged) with NMP:acetonitrile (3:1
v/v), then with NMP:acetonitrile:acetone (2:1:1 v/v/v), NMP:acetone
(1:1 v/v), and finally with pure acetone. Similarly, gels
synthesized in NMP/DMSO were placed in pure NMP, the second wash
was carried out with NMP:acetone (3:1 v/v) the third with
NMP:acetone (1:1 v/v), and finally gels were placed in pure
acetone. After 4 acetone washes (8 h each time, using 4.times. the
volume of the gel for each wash) wet gels were dried into polyimide
aerogels in an autoclave with liquid CO.sub.2, taken out at the end
supercritically.
[0069] At 90.degree. C., a more time-efficient synthesis of PI-ISO
was carried out at slightly (by polyimide standards) elevated
temperatures as follows: pyromellitic dianydride (2.18 g, 0.01 mol)
and MDI (2.50 g, 0.01 mol) were added in variable amounts of NMP in
a three-neck round bottom flask under nitrogen at room temperature.
For example, for a 15% w/w solids formulation the amount of NMP was
26.52 g. The flask was placed in a 60.degree. C. bath and the
solution was stirred under N.sub.2 for 0.5 h. The resulting sol was
poured into molds (see above), which were heated in an oven
successively at 60.degree. C., 70.degree. C. and 80.degree. C. for
3 h at each temperature. Although gelation of the PMDA/MDI/NMP
mixture may occur even at room temperature over longer periods of
time as described above, according to this protocol, gelation
usually occurs at the early stages of the 60.degree. C. heating.
Gels were first aged at 90.degree. C. for 12 h in their molds, and
subsequently they were removed from the molds and they were placed
directly in fresh ethanol. After four ethanol washes (8 h each
time, using 4.times. the volume of the gel for each wash) wet gels
were dried into polyimide aerogels in an autoclave with liquid
CO.sub.2, taken out at the end supercritically.
[0070] Conversion of polyimide aerogels into carbon aerogels will
also be described.
[0071] PI-AMN and PI-ISO aerogels were pyrolyzed at 800.degree. C.
for 3 h in a tube furnace under a flowing stream of Ar. Before
heating, the tube was purged with Ar for 10 min, and the heating
rate was set at 5.degree. C. min.sup.-1. At the end of the heating
period, the power to the furnace was disconnected and the tube was
allowed to cool slowly back to room temperature under flowing
Ar.
[0072] Carbon aerogels were etched by placing the aerogels in a
tube furnace under flowing argon and were heated at 1000.degree. C.
The flowing gas was switched to CO.sub.2 and the temperature was
maintained at that level for 3 h. Subsequently the flowing gas was
switched back to Ar and the power to the furnace was disconnected,
allowing for slow cooling back to room temperature.
[0073] Drying with supercritical fluid CO.sub.2 was conducted in an
autoclave (SPI-DRY Jumbo Supercritical Point Dryer, SPI Supplies,
Inc. West Chester, Pa.). Aerogel bulk densities (.rho..sub.b) were
calculated from the weight and physical dimension of the samples.
Skeletal densities (.rho..sub.s) were determined with helium
pycnometry using a Micromeritics AccuPyc II 1340 instrument.
Porosities, .PI., were determined from .rho..sub.b and .rho..sub.s
according to:
P=100.times.[(1/.rho..sub.b)-(1/.rho..sub.s)]/(1/.rho..sub.b). BET
surface areas (.sigma.) and pore size distributions were measured
with nitrogen adsorption/desorption porosimetry using a
Micromeritics ASAP 2020 Surface Area and Porosity Analyzer. Samples
for surface area and skeletal density determination were outgassed
for 24 h at 80.degree. C. under vacuum before analysis. Average
pore diameters were determined by the 4.times.V.sub.Total/.sigma.
method, where V.sub.Total is the total pore volume per gram of
sample. V.sub.Total is calculated either from the single highest
volume of N.sub.2 adsorbed along the adsorption isotherm or from
the relationship V.sub.Total=(1/.rho..sub.b)-(1/.rho..sub.s). The
single point N.sub.2 adsorption method tends to underestimate
V.sub.Total significantly when macropores are involved, and thus
numerical proximity of the values determined by the two methods is
used as a semi-quantitative criterion for evaluating macroporosity.
Scanning electron microscopy (SEM) was conducted using a Hitachi
S-4700 Field Emission instrument. Chemical characterization of all
polyimide aerogels was based on IR and solid state .sup.13C NMR.
Infrared spectra were obtained in KBr pellets using a Nicolet-FTIR
model 750 Spectrometer. Solid-state .sup.13C NMR spectra were
obtained with samples ground in fine powders on a Bruker Avance 300
spectrometer (75.475 MHz carbon frequency), using magic angle
spinning (5 kHz) with broadband proton suppression and the CPMAS
TOSS pulse sequence for spin sideband suppression. .sup.13C NMR
spectra were externally referenced to the carbonyl of glycine
(176.03 ppm relative to tetramethylsilane). .sup.13C-NMR peak
assignment was aided by NMR spectra simulations using ChemDraw
Ultra 7.0. Thermogravimetric analysis (TGA) was conducted under
nitrogen with a TA Instrument, model Hi-Res-TGA 2950 using
.about.10 mg samples and a heating rate of 10.degree. C.
min.sup.-1. The reaction between PMDA and MDI was monitored in
DMSO-d.sub.6 at room temperature up to the gelation point by liquid
.sup.13C NMR using a 400 MHz Varian Unity Inova NMR instrument. The
crystallinity of the polyimide samples was determined by x-ray
diffraction (XRD) using a Scintag 2000 diffractometer with Cu
K.alpha. radiation and a proportional counter detector equipped
with a flat graphite monochromator. The identity of the fundamental
building blocks of the two materials was probed with small angle
neutron scattering (SANS) using .about.2 mm thick discs cut with a
diamond saw from cylinders, on a time of flight, low-Q
diffractometer, LQD, at the Manuel Lujan Jr. Scattering Center of
the Los Alamos National Laboratory. The scattering data are
reported in the absolute units of differential cross section per
unit volume (cm.sup.-1) as a function of Q, the momentum
transferred during a scattering event. Quasi-static mechanical
testing under compression was conducted on an Instron 4469
universal testing machine frame, following the testing procedures
and specimen length/diameter ratio (equal to one) in ASTM D1621-04a
(Standard Test Method for Compressive Properties of Rigid Cellular
Plastics). The recorded force as a function of displacement
(machine-compliance corrected) was converted into stress as a
function of strain. Four-point-probe conductivity measurements were
conducted on flat surface of rectangular block of carbon aerogel
samples (made with a fine sand paper) using an Alesis contact probe
station model CPS-06 with a Cascade Microtech electrode model
C4S-44/5S. The reliability of the probe was confirmed with silicon
wafers and indium-tin-oxide coated glass slides of known sheet
resistance.
Macroscopic Characterization of PI-ISO Versus PI-AMN
[0074] General materials properties of polyimide aerogels
synthesized by methods shown in FIGS. 2a and 2b are summarized in
Table 1. FIG. 8 shows photographs of polyimide aerogels synthesized
with 15% solids under various conditions also summarized in Table
1. Despite that sols are formulated based on weight percent of
solids in solvents of different densities, attention was paid so
that the molar monomer concentrations in the different sols, ([C],
see Table 1), remained about equal, allowing for a direct
comparison. PI-AMN aerogels appear mechanically stronger than the
corresponding PI-ISO, but as mentioned above they also shrink
significantly with respect to their molds (from 42% at the lowest
gelation limit of 2.5% w/w solids, to 25% at the maximum solubility
limit of 20% w/w solids). On the other hand, PI-ISO samples are
also robust but soft, and shrink significantly less than PI-AMN
under any preparation conditions--in some cases even less than 1%.
Shrinkage is reflected upon the bulk densities (.rho..sub.b) of the
final aerogels. FIG. 11 summarizes data for shrinkage in a linear
dimension (e.g., the cylinder diameter) of samples of Table 1.
PI-AMN samples shrink much more than PI-ISO prepared using similar
monomer concentrations (see Table 1). At similar solids
concentration formulations, the density of the PI-ISO samples is
lower than that of the PI-AMN samples (e.g., at 20% w/w solids
formulation, which is the highest solubility recorded of PI-AMN,
the density of the PI-ISO samples is 0.2 g cm.sup.-3 versus 0.3 g
cm.sup.-3 for the PI-AMN samples). Further, the lowest .rho..sub.b
values with PI-AMN attainable are .about.0.09 g cm.sup.-3, while
easy-to-handle PI-ISO monoliths with .rho..sub.b as low as 0.05 g
cm.sup.-3 are readily prepared.
TABLE-US-00001 TABLE 1 Materials characterization data for
polyimide aerogels Same Name (Composition- Process- Linear Bulk
Skeletal Temperature-% Shrinkage Density, Density, Crystallinity
w/w Solids).sup.a [C], M (%).sup.e .rho..sub.b (g cm.sup.-3)
.rho..sub.s (g cm.sup.-3).sup.g (%) [.degree.2.theta.] PI
-AMN-190-2.5.sup.d 5.78 .times. 10.sup.-5 41.6 0.090 1.547 .+-.
0.104 45 [21, 29] PI-ISO-RT -2.5.sup.c,d 5.14 .times. 10.sup.-5
35.3 .sup.f 1.595 .+-. 0.102 .sup.f PI-AMN-190-5 1.17 .times.
10.sup.-4 38.0 .+-. 0.1.sup.j 0.142 .+-. 0.021.sup.j 1.478 .+-.
0.045 37 [21, 28] PI -ISO-RT-5.sup.b 1.18 .times. 10.sup.-4 5.0
.sup.f 1.526 .+-. 0.045 42 [19, 25] PI-ISO-RT-5.sup.c 1.04 .times.
10.sup.-4 18.87 .+-. 0.02.sup.j 0.047 .+-. 0.002.sup.j 1.534 .+-.
0.080 37 [18] PI-AMN-190-10 2.37 .times. 10.sup.-4 30.04 .+-.
0.02.sup.k 0.186 .+-. 0.016.sup.k 1.453 .+-. 0.015 41 [21, 29, 42]
PI-ISO-RT-10.sup.b,k 2.33 .times. 10.sup.-4 2.1 .+-. 0.9.sup.k
0.112 .+-. 0.003.sup.k 1.490 .+-. 0.023 23 [18]
PI-ISO-RT-10.sup.c,k 2.11 .times. 10.sup.-4 10.03 .+-. 0.03.sup.k
0.090 .+-. 0.006.sup.k 1.473 .+-. 0.022 59 [43, 49] PI-AMN-190-15
3.61 .times. 10.sup.-4 28.24 .+-. 0.01.sup.k 0.232 .+-. 0.008.sup.k
1.474 .+-. 0.024 35 [22, 26] PI-AMN-RT-15 3.61 .times. 10.sup.-4
35.0 .+-. 0.3.sup.k 0.376 .+-. 0.006.sup.k 1.432 .+-. 0.018 37 [35,
48] PI -ISO-90- 15 3.43 .times. 10.sup.-4 17.48 .+-. 0.02.sup.k
0.223 .+-. 0.014.sup.k 1.551 .+-. 0.037 33 [22, 27, 44] Pl-ISO-RT
-15.sup.b 3.54 .times. 10.sup.-4 .sup. <1.0.sup.k 0.167 .+-.
0.002.sup.k 1.447 .+-. 0.021 17 [17] PI-ISO-RT-15.sup.c 3.22
.times. 10.sup.-4 3.19 .+-. 0.01.sup.k 0.124 .+-. 0.001.sup.k 1.398
.+-. 0.009 42 [43, 49] PI-AMN-190-20 4.89 .times. 10.sup.-4 24.89
.+-. 0.02.sup.k 0.291 .+-. 0.022.sup.k 1.437 .+-. 0.016 31 [21, 29]
PI-ISO-90 -20 4.64 .times. 10.sup.-4 5.87 .+-. 0.01.sup.k 0.266
.+-. 0.011.sup.k 1.454 .+-. 0.009 33 [18] PI-ISO-RT-20.sup.b 4.77
.times. 10.sup.-4 2.78 .+-. 0.03.sup.k 0.208 .+-. 0.001.sup.k 1.415
.+-. 0.022 22 [18] PI-ISO-RT-20.sup.c 4.36 .times. 10.sup.-4 1.27
.+-. 0.01.sup.k 0.196 .+-. 0.001.sup.k 1.461 .+-. 0.014 31 [17, 19]
PI-ISO-90 -30 7.17 .times. 10.sup.-4 .sup. 4.71 .+-. 0.001.sup.l
0.382 .+-. 0.003.sup.l 1.473 .+-. 0.031 31 [17] PI-ISO-RT-30.sup.c
6.78 .times. 10.sup.-4 .sup. <1.0.sup.l 0.285 .+-. 0.027.sup.l
1.445 .+-. 0.009 33 [17, 20] PI-ISO-90-40 9.84 .times. 10.sup.-4
.sup. 4.90 .+-. 0.001.sup.l 0.513 .+-. 0.011.sup.l 1.432 .+-. 0.009
32 [17, 19] PI-ISO-RT-40.sup.c 9.36 .times. 10.sup.-4 3.8 .+-.
0.2.sup.l 0.417 .+-. 0.008.sup.l 1.443 .+-. 0.007 42 [27, 43]
PI-ISO-90-50 1.27 .times. 10.sup.-3 .sup. 5.50 .+-.
0.00.sub.3.sup.l 0.679 .+-. 0.002.sup.l 1.452 .+-. 0.014 33 [19,
25] Same Name (Composition- BET Average Average Process- Porosity,
Surface Pore Pore Temperature-% .pi. (% void Area, Diameter
Diameter w/w Solids).sup.a space) .sigma.(m.sup.2 g.sup.-1)
(nm).sup.h (nm).sup.i PI -AMN-190-2.5.sup.d 94 385 17.0 [108.5]
42.7 [60.4] PI-ISO-RT -2.5.sup.c,d .sup.f 297 14.7 [.sup.f] 35.5
[55.0] PI-AMN-190-5 90 412 29.6 [62.0] 47.0 [11.4] PI
-ISO-RT-5.sup.b .sup.f 374 13.8 [.sup.f] 36.3 [67.3]
PI-ISO-RT-5.sup.c 97 333 23.0 [250.4] 36.3 [45.7] PI-AMN-190-10 87
431 29.5 [45.8] 40.7 [22.1] PI-ISO-RT-10.sup.b,k 93 373 28.9 [88.9]
41.7 [37.1] PI-ISO-RT-10.sup.c,k 94 316 25.6 [131.6] 39.8 [38.4]
PI-AMN-190-15 84 413 26.5 [35.3] 31.6 [17.1] PI-AMN-RT-15 74 299
11.2 [26.2] 14.5 [9.4] PI -ISO-90- 15 85 244 14.2 [62.6] 39.8
[66.6] Pl-ISO-RT -15.sup.b 88 391 25.5 [54.3] 31.6 [28.4]
PI-ISO-RT-15.sup.c 91 315 33.5 [93.2] 52.5 [34.3] PI-AMN-190-20 80
378 18.2 [29.0] 24.0 [11.9] PI-ISO-90 -20 80 246 20.0 [50.0] 24.0
[11.8] PI-ISO-RT-20.sup.b 85 366 23.0 [44.7] 30.9 [30.8]
PI-ISO-RT-20.sup.c 87 352 22.7 [84.7] 39.8 [26.1] PI-ISO-90 -3 74
303 13.2 [51.2] 24.5 [30.0] PI-ISO-RT-30.sup.c 80 339 22.4 [33.3]
40.7 [32.2] PI-ISO-90-40 64 278 10.7 [17.8] 14.1 [25.6]
PI-ISO-RT-40.sup.c 71 171 12.0 [39.7] 39.8 [40.2] PI-ISO-90-50 53
222 6.3 [14.1] 8.5 [7.2] .sup.aPI-AMN: Polyimide samples
synthesized through the amine route; PI-ISO: polyimide samples
synthesized through the isocyanate route; PI-AMN-190: samples cured
in NMP at 190.degree. C. before drying; PI-AMN-RT: samples dried
supercritically without further curing at 190.degree. C.;
PI-ISO-90: samples synthesized at 60-90.degree. C. in NMP;
PI-ISO-RT: samples synthesized at room temperature. .sup.bPI-ISO-RT
samples synthesized in NMP/DMSO. .sup.cPI-ISO-RT samples
synthesized in NMP/acetonitrile). .sup.dSingle sample.
.sup.eShrinkage = 100 .times. (mold diameter - sample
diameter)/(mold diameter). .sup.fIrregular shape, was not measured.
.sup.gSingle sample, average of 50 measurements. .sup.hBy the 4
.times. V.sub.Total/.sigma.method. For the first number,
V.sub.Total was calculated by the single-point adsorption method;
for the number in brackets, V.sub.Total was calculated via
V.sub.Total = (1/.rho..sub.b) - (1/.rho..sub.s). .sup.iFrom the BJH
plots: The first numbers are the peak maxima; the numbers in
brackets are the width at half maxima of the BJH plots.
.sup.jAverage of 2 samples. .sup.kAverage of 4 samples.
.sup.lAverage of 3 samples.
[0075] Partly owing to the similar chemical composition of the two
materials, partly to their similar degree of crystallinity (30-45%
by XRD, see Table 1), and partly to similar packing distances
within the crystalline phases (expressed by similar 2.theta.
values, see Table 1), skeletal densities, .rho..sub.s, of all
samples are in the 1.4-1.5 g cm.sup.-3 range, which is comparable
with the density of bulk polyimides obtained from PMDA and MDA
(1.357 g cm.sup.-3). The similar .rho..sub.s values but the
different .rho..sub.b's are reflected in the porosities, which are
higher for the PI-ISO aerogels relative to the corresponding PI-AMN
samples. However, BET surface areas, .sigma., from N.sub.2-sorption
data show an opposite trend from the porosities: despite higher
shrinkage, higher bulk densities and lower porosities, PI-AMN
samples have about equal or higher surface areas than PI-ISO
samples. These data point to significant differences in the
nanomorphology of the PI-AMN versus the PI-ISO samples, which are
discussed in the next section. FIG. 12 shows representative
N.sub.2-sorption data (insets showing BJH plots) of polyimide
aerogels prepared using the 15% w/w solids formulations (Table 1).
FIG. 12(A) depicts PI-AMN-190 (.rho..sub.b=0.23 g cm.sup.-3); and
FIG. 12(B) shows PI-ISO-RT prepared in NMP/DMSO1:1 w/w
(.rho..sub.b=0.17 g cm.sup.-3).
Structural Characterization of PI-ISO Versus PI-AMN
[0076] The microstructure of polyimide aerogels was evaluated in
terms of their pore-size distribution and the nanomorphology of
their skeletal frameworks. The pore-size distribution at the
meso/macro scale was evaluated semi-quantitatively by analysis of
the N.sub.2-sorption data in combination with SEM, while the
elementary building blocks of the skeletal framework were probed
with SANS. Data shown concern samples obtained with the 15% w/w
solids formulation. Similar data and trends have been observed with
samples prepared with all other solids formulations (Table 1).
[0077] For both PI-AMN and PI-ISO samples, N.sub.2-sorption
isotherms show a rapid increase of the volume adsorbed at relative
pressures above 0.9, which in combination with the narrow
desorption loop indicates the presence of both meso- and
macroporosity. Indeed, pore size analysis via the relationship
(pore diameter)=4.times.V.sub.Total/.sigma., where V.sub.Total is
calculated either from the maximum adsorption point in the
isotherm, or the relationship
V.sub.Total=(1/.rho..sub.b)-(1/.rho..sub.s), gives quite different
values (Table 1), which get progressively closer as the bulk
density increases, as expected by the fact that more dense
materials should have smaller pores. The BJH-desorption method
reflects the mesoporosity and yields pore diameters closer to those
obtained by the single point absorption method (Table 1), but it
also shows quite broad pore size distributions (evaluated by the
width at half maxima of the BJH plots, see Table 1). Overall, the
N.sub.2-sorption method indicates that both PI-AMN and PI-ISO
aerogels are meso/macroporous materials. SEM, however, shows that
their pore structures are quite different: at all densities PI-AMN
are particulate while PI-ISO are fibrous. At high magnifications,
there was a discernible primary/secondary particle structural
hierarchy in the case of PI-AMN, while in some cases it can be also
claimed that the PI-ISO ribbons consist of particles. FIG. 13
illustrates SEM data at two different magnifications of polyimide
aerogels prepared using the 15% w/w solids formulations (Table 1).
FIG. 13(A) shows PI-AMN-190 (.rho..sub.b=0.23 g cm.sup.-3); and
FIG. 13(B) shows PI-ISO-RT prepared in NMP/CH3CN 3:1 w/w
(.rho..sub.b=0.12 g cm.sup.-3). FIG. 14 shows SEM data of (A)
PI-AMN (.rho..sub.b=0.186 g/cm3, porosity=87%, .rho..sub.s=1.456
g/cm.sup.3, BET surface area=431 m.sup.2/g); and (B) PI-ISO
(.rho..sub.b=0.090 g/cm.sup.3, porosity=94%, .rho..sub.s=1.473
g/cm.sup.3, BET surface area=315 m.sup.2/g.
[0078] The make-up of the skeletal frameworks in PI-AMN and PI-ISO
was probed quantitatively with SANS. To exclude the effect of the
solvent, which controls phase-separation, and therefore affects the
size of the particles, the specific materials compared were both
prepared in NMP (PI-ISO-90 and PI-AMN-190). While scattering from
PI-AMN and PI-ISO is distinct, there are similarities. To
facilitate analysis, and as shown in FIG. 15, scattering has been
broken down into four regions. Each material displays two
length-scales (regions I and III) and two power-law regions (linear
sections on a log-log plot, regions II and IV). In region IV both
materials display power-law scattering with exponents of .about.5
(PI-ISO: 5.0.+-.0.1; PI-AMN: 5.1.+-.0.1). FIG. 15 shows SANS data
of PI-AMN-190 (black line, .rho..sub.b=0.23 g cm.sup.-3) and of
PI-ISO-90 (red line, .rho..sub.b=0.22 g cm.sup.-3) both prepared in
NMP using the 15% w/w solids formulation. Vertical lines separate
the power-law regions (II and IV) from the "knee" regions (I and
III). For smooth interfaces, the exponent in this region is
typically 4, while for fractally-rough interfaces it is 3-4.
Exponents>4 are largely attributed to rapidly changing density
at the interface. In region III, both materials display a "knee,"
which is indicative of a fundamental length-scale and may relate to
small pores, the cross section of a foam strut, or the primary
particle size of aggregates forming the material. The first two
possibilities are excluded based on the similar skeletal densities
of the two materials (absence of small pores) and the quite
different SEM microstructures (different cross-sections of the
skeletal frameworks). Region III knees are attributed to the
primary particles forming the materials. Analysis according to the
Unified Model provides the radius of gyration (R.sub.g), where for
spherical particles R.sub.g.apprxeq.0.77R (R is the average radius
of the particles). For PI-AMN, R.sub.g=5.8 nm and for PI-ISO,
R.sub.g=4.7 nm. In region II, both materials exhibit power-law
scattering again. PI-AMN exhibits a power-law with an exponent of
.about.2 and PI-ISO exhibits an exponent of .about.1. For fractal
systems, an exponent of 2 would indicate pore (or mass) fractals,
while for simple shapes it is indicative of a sheet- or disk-like
morphology; an exponent of 1 is indicative of a cylindrical-like
morphology, which would describe the fibers of PI-ISO. Finally, in
region I both materials display "knees," which may again relate to
larger pores, the cross section of a foam strut or the size of an
aggregate of particles. For PI-AMN, R.sub.g=35 nm and for PI-ISO,
R.sub.g=41.6 nm. Based on SEM, in the case of PI-AMN those
structural elements are attributed to secondary particles and in
the case of PI-ISO to the diameter of the fibers. It is noted that
length-scales identified by SANS agree well with feature sizes seen
at the higher magnification SEM.
[0079] Overall, chemically identical (case of PI-AMN-190 and
PI-ISO-90) and structurally very similar primary particles (in
terms of crystallinity and size) seem to form secondary particles
in the case of PI-AMN, and fibers in the case of PI-ISO. The size
of the primary particles may be controlled by the common solvent
(NMP). Then, the variable that remains different in the two systems
is the actual chemistry of the two processes, which is translated
into the surface functionality of the primary particles. It is
suggested that the flexible amic acid bridges between PI-AMN
primary particles allows pivoting, closer packing, and a 3D growth
resulting into secondary particles; on the other hand, the rigidity
of the seven-member ring between PI-ISO primary particles, in
combination with steric hindrance from neighboring particles,
imposes growth at the exposed ends of the assembly resulting in
directional growth and fibers. FIGS. 6a and 6b illustrate a
molecular schematic of the interfacial chemistry of primary
particles in PI-AMN and PI-ISO.
[0080] The 3D growth in PI-AMN create numerous crosslinks between
secondary particles while in the case of PI-ISO, crosslinking may
take place only at the contacts between fibers. This model for
PI-AMN versus PI-ISO aerogels is supported by the higher shrinkage
of PI-AMN, and may serve as an explanation for their high
compressive mechanical strength, which compares favorably with that
of structurally analogous polymer crosslinked silica aerogels at
the same densities. On the other hand, at similar percent solids
formulations, PI-ISO aerogel monoliths are mechanically much weaker
materials, undergoing premature catastrophic failure to large
pieces with much smaller loads. In some embodiments, entangled
nanofibrous structures are generally mechanically stronger (the
bird-nest effect).
[0081] FIG. 16 depicts behavior under compression (ASTM D1621-04a)
of a PI-AMN-190 sample prepared using the 20% w/w solids
formulation (Table 1): a short linear elastic range (at
<(1.175.+-.0.075) % strain, magnified and shown as an inset) is
followed by plastic deformation (up to 50% strain) and inelastic
hardening thereafter. The samples did not fail under compression.
Other data pertinent to mechanical characterization (averages of
two samples): bulk density .rho..sub.b=0.291.+-.0.006 g cm.sup.-3;
maximum strength (at 86% engineering strain): 99.27.+-.3.64 MPa;
specific energy at maximum load (at 86% engineering strain):
48.04.+-.2.48 J g.sup.-1; Young's modulus (from the slope of the
linear elastic range in the inset): 27.25.+-.0.84 MPa; yield
strength (stress at 0.2% offset strain): 1.525.+-.0.388 MPa
(calculated by drawing a parallel line to the slope of the linear
elastic range in the inset, starting from engineering
strain=0.002); yield stain (i.e., strain at yield strength):
3.10.+-.0.45; linear elastic to total deformation at the yield
point: 0.38.
Pyrolysis of Polyimide Aerogels and Conversion to Carbon
[0082] Porous carbons are pursued as electrodes for fuel cells and
batteries. Polyimides generally have good carbonization yields, and
in fact the first PI-AMN aerogels reported were also investigated
for their conversion to carbon aerogels (pyrolytically) and metal
carbide aerogels (carbothermally, after doping with selected
sol-gel derived metal oxides). Carbonizable polymers are capable of
either cyclizing, or undergoing ring fusion and chain coalescence
by heating. For this the chain should either contain aromatic
moieties or be aromatizable (usually by oxidation). In the former
case, there is one carbon atom between aromatic rings; otherwise,
pyrolytic chain scission will prevail leading to loss of fragments.
The PMDA/MDI or MDA polyimides herein fulfill the last criterion.
By thermogravimetric analysis under N.sub.2 (TGA) both PI-AMN and
PI-ISO are stable up to about 550.degree. C., subsequently loosing
40-50% of their mass before 650.degree. C. (presumably by loss of
small molecules like CO and CO.sub.2). FIG. 17 shows comparative
TGA data for samples indicated prepared using 15% w/w solids
formulations. The additional gradual mass loss at higher
temperatures is attributed to loss of nitrogen-containing
fragments. Carbonization pyrolysis was carried out at 800.degree.
C. under Ar for 3 h. Pertinent data concerning the resulting carbon
aerogels are summarized in Table 2 for various samples prepared
with the 15% w/w and the 10% w/w solids formulations (for
comparison, refer to Table 1).
TABLE-US-00002 TABLE 2 Properties of PI-AMN and PI-ISO derived
carbon aerogels.sup.a Precursor for Pyrolytic Carbonization Carbon
Linear Bulk Skeletal BET Surface (Sample-Additional Yield %
Shrinkage Density, Density, Porosity, Area, Processing) (w/w)
(%).sup.g .rho..sub.b (g cm.sup.-3) .rho..sub.s (g cm.sup.-3).sup.j
.pi. (% v/v) .sigma.(m.sup.2 g.sup.-1) PI-AMN-190-15 58 .+-.
2.sup.e 48.0 .+-. 0.5 [63] 1.018 .+-. 0.153.sup.h 1.896 .+-. 0.070
46 113 PI-ISO-90-15 55 .+-. 2.sup.e 40.8 .+-. 0.4 [52] 0.665 .+-.
0.064.sup.h 1.998 .+-. 0.057 67 279 PI-ISO-RT-10.sup.b 53 .+-.
2.sup.e 61.6 .+-. 0.9 [64] 1.012 .+-. 0.117.sup.i 1.863 .+-. 0.034
46 336 PI-ISO-RT-10.sup.c 53.6 .+-. 0.4.sup.e 62 .+-. 2 [66] 0.967
.+-. 0.160.sup.i 1.729 .+-. 0.021 44 361 PI-AMN-190-15 79.sup.f 3
[63] 0.701 2.114 .+-. 0.069 67 417 3 h-CO.sub.2.sup.d PI-ISO-RT-10
59.sup.f 8.7 [65] 0.670 2.310 .+-. 0.052 71 1010 3
h-CO.sub.2.sup.b,d .sup.aPI-AMN and PI-ISO samples as indicated,
processed at 800.degree. C. under Ar for 3 h. .sup.bPI-ISO-RT
samples synthesized at in NMP/DMSO. .sup.cPI-ISO-RT samples
synthesized in NMP/acetonitrile. .sup.dResulting carbon samples
processed for an additional 3 h at 1000.degree. C. under flowing
CO.sub.2. .sup.eAverage of four samples. .sup.fSingle sample; yield
relative to the sample before treatment with CO.sub.2 at
800.degree. C. for 3 h. .sup.gShrinkage = 100 .times. (sample
diameter before pyrolysis - sample diameter after
pyrolysis)/(sample diameter before pyrolysis); for the number in
the brackets, shrinkage was calculated with respect to the original
mold diameter. .sup.hAverage of two samples. .sup.iAverage of 3
samples. .sup.jSingle sample, average of 50 measurements.
[0083] Polyimide aerogels remain as quite sturdy monoliths after
pyrolysis. Carbon aerogels are also black in color. PI-AMN-derived
carbons, however, have a metallic luster, while PI-ISO derived
samples are dull. The carbonization yield generally is between
51-56% w/w. Carbon aerogels shrink further beyond their initial
imidization shrinkage (Table 1), but PI-ISO-RT samples shrink more
(.about.60%) than the PI-AMN samples (.about.50%), so that the
total shrinkage calculated from the initial molds (Table 2) is
approximately the same for both kinds of samples (63-66%). The
PI-ISO-90 samples seem to have a small advantage over the rest in
terms of shrinkage (overall 52% relative to the molds).
[0084] Chemically, pyrolytic samples consist only of carbon (as
determined by EDS). XRD shows very broad diffractions. Typical
Raman spectra show both the G (graphitic) and D (disordered) peaks
at 1352 cm.sup.-1 and 1597 cm.sup.-1, respectively. FIG. 18 shows
Raman spectra of polyimide aerogels prepared by the two routes. The
ratios of the integrated peak intensities (I.sub.D/I.sub.G) are
1.12 and 0.98 for carbon aerogels obtained from PI-ISO and PI-AMN,
respectively, indicating that all carbons are
nanocrystalline/amorphous. Indeed, the skeletal densities of all
samples are in the 1.7-2.0 g cm.sup.-3 range (Table 2), which is
what is expected from amorphous carbon (1.8-2.0 g cm.sup.-3).
Combination of bulk and skeletal densities yields porosities in the
range of .about.45% v/v of empty space, which are significantly
lower than the porosities of the parent polyimide aerogels (compare
Tables 1 and 2). An exception is the PI-ISO-90 samples where the
porosity is 67% v/v of empty space and is attributed to their lower
pyrolytic shrinkage (Table 2).
[0085] Microscopically (by SEM) PI-AMN-derived carbons are
different from their parent polyimide aerogels. FIG. 19 shows SEM
at two different magnifications and N.sub.2-sorption data for
carbon aerogels produced by pyrolysis at 800.degree. C. under
nitrogen. FIG. 19(A) shows PI-AMN-190 prepared by the 15% w/w
solids formulation in NMP; and FIG. 19(B) shows PI-ISO-RT prepared
by the 10% w/w solids formulation in NMP/CH3CN 3:1 w/w. FIG. 20
shows SEM data (scale bars at 200 nm) and N.sub.2-sorption data for
carbon aerogels after etching at 1000.degree. C. under flowing
CO.sub.2 for 3 h. FIG. 20(A) shows carbon aerogel from PI-AMN-190
prepared by the 15% w/w solids formulation in NMP; and FIG. 20(B)
shows carbon aerogel from PI-ISO-RT prepared by the 10% w/w solids
formulation in NMP/DMSO 1:1 w/w. There is a notable rapid rise of
the volume adsorbed at low relative pressures, indicating
microporosity (pore sizes<2 nm). The structure is dominated by
large macropores surrounded by "solid" walls, although
N.sub.2-sorption isotherms show the presence of all three kind of
pores: micropores (significant quick rise of the volume adsorbed at
low partial pressures), mesopores (presence of a hysteresis loop),
and macropores (second quick rise of the volume adsorbed above
P/P.sub.o.about.0.9). The lower BET surface area relative to that
of PI-AMN samples before pyrolysis (113 m.sup.2 g.sup.-1 versus 413
m.sup.2 g.sup.-1, respectively) is consistent with the changes
observed by SEM. On the other hand, PI-ISO-derived carbons retain
the fibrous nanomorphology of the parent polyimide aerogels, but
the fine structure that could be seen on the fibers of the parent
PI-ISO aerogels has been erased. Again, N.sub.2-sorption isotherms
indicate the presence of all three kinds of pores, while the BET
surface area of the PI-ISO-derived carbon aerogels has been
increased somewhat relative to that of the parent polyimides
(compare Tables 1 and 2). This pyrolytic behavior of both PI-AMN
and PI-ISO samples is consistent with the model of FIGS. 6a and 6b:
at the early stages of pyrolysis bond breaking and reforming at the
surfaces of the primary and secondary particles (case of PI-AMN),
leads to rearrangement and a more compact structure.
Macroscopically, that mechanism is expected to lead to shrinkage,
and microscopically into large voids defined by compact walls (case
of PI-AMN). On the other hand, in the case of PI-ISO bond breaking
and reforming leads to smoother thinner fibers, but the pore
structure is retained.
[0086] The presence of micropores indicated by the N.sub.2-sorption
isotherms suggests that a significant gain in surface area could be
achieved by etching. That was carried out under flowing CO.sub.2 at
1000.degree. C. (carbon and CO.sub.2 comproportionate to CO.) The
results are included in Table 2. CO.sub.2-treated samples lose
20-40% of their mass, shrink 3-9% and remain monolithic.
Consequently, bulk densities decrease, however, skeletal densities
increase to the 2.1-2.3 g cm.sup.-3 range (density of graphite at
2.26 g cm.sup.-3). The porosity is dominated by the bulk density
decrease, reaching up to .about.70% v/v of empty space.
Microscopically, PI-ISO samples remain fibrous, while PI-AMN
samples show macropores similar in shape to those observed before
etching. The number of those macropores has increased and
surrounding walls seem rougher; considering these data together
suggests that before etching many pores are masked by a thin porous
crust of carbon. After CO.sub.2-etching, the N.sub.2-sorption
isotherms indicate that the majority of the empty space is
attributed to micropores, while the BET surface areas of the
samples increases dramatically, reaching the levels of the parent
polyimide aerogels in the case of PI-AMN-derived carbons (417
m.sup.2 g.sup.-1), or far surpassing those levels in the case of
PI-ISO-derived samples (1010 m.sup.2 g.sup.-1). For reasons not
well understood yet, despite the mass loss CO.sub.2-etching
increases the electrical conductivity of PI-ISO-derived carbon
aerogels by .about.70.times., from 0.013 mho cm.sup.-1 (at
.rho..sub.b=0.967 g cm.sup.-3) to 8.697 mho cm.sup.-1 (at
.rho..sub.b=0.670 g cm.sup.-3). (By comparison the electrical
conductivity of CO.sub.2-etched PI-AMN-derived carbon aerogels is
4.491 mho cm.sup.-1 at .rho..sub.b=0.701 g cm.sup.-3.) Those values
render polyimide-derived carbon aerogels particularly attractive as
electrochemical electrodes.
[0087] Three-dimensional porous polyimide and carbon networks
derived therefrom, such as polyimide and carbon aerogels, are high
value-added materials and may be useful for a number of
applications. For example, such porous polyimide networks may be
useful in high-temperature thermal insulation (e.g., architectural,
automotive industrial applications, aircraft, spacecraft,
clothing), lightweight structures, acoustic insulation (e.g.,
buildings, automobiles, aircrafts), impact dampening, dielectrics
(e.g., for fast electronics), supports for catalysts, and as hosts
of functional reactants for chemical, electronic and optical
applications. In some embodiments, three-dimensional porous
networks described may be used as insulation material for apparel,
such as clothing, astronaut suits, and armor.
[0088] Described herein are three-dimensional porous polyimide
networks synthesized via a low temperature process through a
reaction of dianhydrides with diisocyanates. Although MDI has been
used, other monomers such as 4,4'-oxybis(phenylisocyanate) may
behave similarly and resulting polyimides may have the chemical
composition of Kapton. Three-dimensional porous polyimide networks
(e.g., polyimide aerogels) derived from PMDA/MDI may exhibit
fibrous morphologies and can be converted pyrolytically to
isomorphic three-dimensional porous carbon networks (e.g., carbon
aerogels), which, owing to their large surface area, may be useful
for their reactivity with nanoparticulate oxidizing agents.
[0089] Three-dimensional porous polyimide networks including
polyimide aerogels may be useful in applications that involve, for
example, absorption of oil or other hydrophobic materials. In some
instances, such materials may be capable of absorbing 5, 15, 20,
25, or more times their weight in oil or other hydrophobic
material. In some instances, the majority of the substance absorbed
may be retrieved by chemical and/or mechanical methods.
Three-dimensional porous carbon networks derived from
three-dimensional porous polyimide networks may also be useful for
a number of applications including, for example, manufacture of
electrodes, batteries, supercapacitors, high-temperature
insulators, high-temperature ballistics materials, ablative
materials and infrared blocking armor. In some embodiments, doping
PI-ISO with cerium oxide and pyrolysis to carbon under argon may
lead to materials that are self ignited when exposed to air, giving
rise to potential energetic materials applications.
[0090] Having thus described several aspects of at least one
embodiment of this invention, it is to be appreciated various
alterations, modifications, and improvements will readily occur to
those skilled in the art. Such alterations, modification, and
improvements are intended to be part of this disclosure, and are
intended to be within the spirit and scope of the invention.
Accordingly, the foregoing description and drawings are by way of
example only.
* * * * *