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Matthias Mecklenburg , Arnim Schuchardt , Yogendra
Rainer Adelung *, Andriy Lotnyk , Lorenz Kienle , and
Aerographite: Ultra Lightweight, Flexible Nanowall,
Carbon Microtube Material with O
Performance
The utilization of carbon nanomaterial’s fascinating properties,
like carbon nanotubes’ (CNTs’) tensile strength of 63 GPa [ 1 ] or
graphenes lowest electrical resistance [ 2 ] is typically limited by
the lack of advanced structural design. CNTs directly assem-
bled as macroscopic rope deliver ≈ 3 GPa. [ 3 ] Only if individual
tubes get interconnected higher values can be achieved. [ 4 ] For
graphene the underlying substrate is often limiting the conduc-
tivity. [ 2 ] Although 3D interconnected graphene networks were
recent
and li
not se
Furthe
from t
synthe
nectio
the sy
presen
< 200
lattice
Despi
scopic
Rec
tures
ductiv
applic
super
high p
high m
and unl
200–400
ited lifet
connecti
Aerog
robust t
rial prop
M. Me
Istitute
Hambu
Denick
A. Schu
Prof. R
Institu
Functio
University of Kiel
Kaiserstr
E-mail: ra
Dr. A. Lo
Institute
Synthesis
Universit
Kaiserstr
[+] Prese
Permose
DOI: 10
© 2012 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheimelibrary.com
tion as an electrode material. A super lightweight variant of
Aerographite is shown in Figure 1 e–h (SI, Figure S16). Here
the walls of the tubes introduce another hierarchy level; they are
formed from a hollow framework of ribbons which consists of
a transition state between amorphous carbon (with a very high
amount of sp 2 -hybridized bonds) and completely sp 2 -hybridized
vitreous carbon, as confi rmed by the electrical conductance and
the electron energy loss spectroscopy (EELS) spectra. [ 18 , 19 ] This
hollow framework structure (network with sub network) mate-
rial possesses the super low density of 180 μ g cm − 3 which is
. 2, D-24143 Kiel, Germany
@tf.uni-kiel.de
tnyk , [+] Prof. L. Kienle
for Materials Science
and Real Structure
y of Kiel
. 2, D-24143 Kiel, Germany
nt Address: Leibniz Institute of Surface Modifi cation (IOM)
rstr. 15, D-04318, Leipzig, Germany
.1002/adma.201200491
Adv. Mater. 2012, 24, 3486–3490
ly synthesized, they are only hypothetically free standing
ghtweight (2 mg cm − 3 ), without a second phase they are
lf-supporting and only stable as composite materials. [ 5 ]
rmore they tend to collapse even as single tubes. [ 6 ] Thus -
he engineering point of view - real life applications desire
sis methods which enable tailoring of materials intercon-
ns and morphological design, like recently presented by
nthesis of nickel microlattices [ 7 ] (0.9 mg cm − 3 ). Here we
t a novel cellular material called Aerographite (density
µg cm − 3 ), more than 4 times lighter than the Ni micro-
s, which were up to now the most lightweight materials.
te its low density it can be fabricated in various macro-
shapes in the order of several cubic centimeters.
ently published results about graphene network struc-
indicate the importance of highly porous, electrical con-
e, and mechanical stable foam like structures [ 5 , 8 ] for the
ations as electrode material for Li ion car batteries or
capacitors. For those applications low specifi c weight, a
enetrability, and accessibility of surfaces and especially
which is
freely ad
over the
Figure 1
cally opa
structur
adsorbin
Raman s
magnifi c
reveals t
intercon
that pro
than the
a simila
carbon n
meter. O
exhibit o
mation
of vanis
S3) that
dependi
be shape
Figure S
effect of
pure sp
bons [ 15 , 1
mechan
electrica
cklenburg , Prof. K. Schulte
of Polymers and Composites
rg University of Technology
estr. 15, D- 21073 Hamburg, Germany
chardt , Dr. Y. K. Mishra , S. Kaps ,
. Adelung
te for Materials Science
nal Nanomaterials
Kumar Mishra , Sören Kaps ,
Karl Schulte
utstanding Mechanical
echanical robustness are necessary. Cyclic loading
oading with Li ions easily leads to volume changes of
%. [ 9 ] Corresponding stresses are a major point of lim-
ime performance, [ 9 – 11 ] thus introduction of direct inter-
ons are advantageous.
raphite is designed to be most lightweight but extremely
o bear strong deformations. These challenging mate-
erties are achived by Aerographite’s hirachical design
realized by a novel single-step cvd sythesis based on
justable ZnO networks. Figure 1 gives a small overview
variety of the Aerographite family. The photograph of
a shows that the material is completely black and opti-
que despite its extreme low density. The open porous
e of Aerographite is orders of magnitudes more light
g than, e.g., carbon nanotube sponges as confi rmed in
pectroscopy experiments. Figure 1 b–d show in different
ations the distinct levels of the material. A closer look
hat this variant of Aerographite consists of a seamless
nected network of closed shell micro tubes, a structure
vides ultra-low densities of ≈ 2 mg cm − 3 already lower
lightest reported aerogels. [ 5 , 8 , 12 , 13 ] The walls possess
r nanoscopic thickness ( ≈ 15 nm) like thin multiwall
anotubes (MWCNTs) but have a microscale tube dia-
ther than MWCNTs, the relatively large graphite planes
rders of magnitude less curvature promoting the for-
of manifold tube junctions over the sintering bridges
hed template (Supporting Information (SI), Figure S2,
are exceptions for CNT materials. [ 14 ] Furthermore,
ng on the growth conditions, the graphite surface can
d in a wrinkled manner (surface in Figure 1 d and SI,
4) to give a higher mechanical stability. The stabilizing
wrinkled, e.g., non-hexagonal ring confi gurations, of
2 -carbon structures is also known from glass-like car-
6 ] (often called ‘vitreous carbons’), which have superior
ical properties and chemical resistance [ 17 ] but are still
lly conductive as it would be required for an utiliza-
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one or
other l
sized,
which
the ho
cies, se
graphi
face-ar
damag
or carb
The
and su
plate. T
in a br
and su
structu
some o
(SI, Fig
The
of vari
remov
by a h
to me
(SI, Fi
achieve
as we
S16 ribbons, S13-S15 fi lled) are highly con-
trollable by the CVD parameters respectively
Figure
thesis.
closed-s
archical l) Other
variants
Aerogra
surface
Adv. Mat
1 . Overview of different Aerographite morphologies by controlled derivations
a) Photograph of macroscopic Aerographite. b–d) 3D interconnected struc
hell graphitic Aerographite in different magnifi cations and TEM inset of wall. e–
hollow framework confi guration of Aerographite in different magnifi cations. i–
© 2012 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
der of magnitude lighter than all known aerogels and
ightweight materials. Many more variants can be synthe-
e.g. the low aspect ratio variant of interconnected spheres
is depicted in Figure 1 i (SI, Figure S5). Furthermore,
llow tubes can be fi lled with several kinds of carbon spe-
e Figure 1 j-k (SI, Figures S13-S15). Due to the internal
tic structure of these variants a much higher specifi c sur-
ea is given but with the disadvantage that fl exibility and
e tolerance are reduced to a level of conventional silica [ 13 ]
on aerogels. [ 8 , 12 ]
achieved structures of Aerographite adopt the network
rface structure of the individual tailorable ZnO [ 20 ] tem-
hus it is possible to tune the morphology of Aerographite
oad manner with respect to its aspect ratios, diameters,
rface structures (SI, Figure S5). To give a glimpse of the
ral variety of the template material, Figure 2 a–d show
f the templates, including the corrugated pipe structures
ures S7b, S11b).
developed CVD process allows a single-step synthesis
ous carbon species with a simultaneous and complete
al of the whole template material. This is introduced
ydrogen gas fl ow, which reduces ZnO (SI, Figure S6)
tallic Zn, which is precipitated to the exhaust system
gures S7-S10). It is important to point out that the
d carbon structures and degree of crystalline order
ll as the morphology (SI, Figures S2-S4 graphitic,
ments a
structur
measur
structur
rarely reported and challen
impressive low density of
framework structure (Fi
exhibits outstanding mec
and tensile strength and th
Aerographite reacts with a
unidirectional tensile and
ible plastic deformation
As a demonstration of th
even possible to regain th
Aerographite bulk body
100 micrometers, by subs
shape, indicating an extre
leading to marginal differ
stress. These features a
mechanical tensile loads w
disentangling of CNTs or
shows a sponge like behav
the modulus increased to
see SI, Figure S20. A te
duces a pronounced self-s
nism behind this could b
the hollow amorphous ca
load direction. The hollow
ρ = 0.180 mg cm − 3 exhib
ultimate tensile strength (
of Aerographite. i) Aerographite network in low aspect bubble-like confi guration. j-k)
phite with nano porous graphite fi lling. l) Hollow corrugated pipe design of Aerographite
by detailed adoption of template shape.
er. 2012, 24, 3486–3490
3487wileyonlinelibrary.com
nd Van der Waals forces. In fact this
al defi ciency is the reason why tensile
ements of CNT-assembled graphitic
es and also silica aerogels are just
ging to measure. [ 22 ] Just owing to the
< 200 μ g cm − 3 the hierarchical hollow
gure 1 e–g), fortifi ed by sp 3 -bonds,
hanical robustness, specifi c stiffness,
erefore superior merit indices. [ 23 ] The
viscoelastic deformation behavior on
compression stresses with a revers-
part, see Figure 3 a (SI, Figure S21).
is mechanical robust behavior, it is
e full shape of an initial 3 mm high
after compression down to a few
equent expansion back to its original
me low Poisson ratio (SI, Video S1),
ences between true and engineering
llow the application of remarkable
ithout losing structural integrity, e.g.,
small fl akes of graphite. The material
ior under compression, for 95% strain
160 kPa in a 8.5 mg cm − 3 sample,
nsile and compression cycling intro-
tiffening (inset Figure 3 c). A mecha-
e a reorganization and alignment of
rbon ribbon structure parallel to the
framework variant with a density of
its a smooth fracture behavior at an
UTS) of 1 kPa what is superior to all
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by the design of the ZnO templates (SI,
Figure S6). Microscopy of an evolutionary
state (SI, Figures S7-10) and the results
of TEM (SI, Figures S4, S12), EFTEM (SI,
Figures S10,S12), XRD, Raman spectros-
copy, and TGA measurements at different
Aerographite types are discussed in the sup-
porting information where one can also fi nd
suggested growth model (SI, Figure S1).
For mechanical testing distinct examples
of the Aerographite family were created and
loaded under cyclic compression and tensile
stress. Tests with different geometries showed
that cylindrical test specimens provided the
lowest experimental error (see Experimental
Section). SI, Figure S19 shows a viewgraph of
the Young’s modulus in compression versus
the density. This graph indicates the change
in the Young’s modulus in compression for
different densities and the corresponding
structure types. It must be pointed out that
Aerographite can carry signifi cant tensile
loads as its network structure exhibits tube
junctions which originate from the ZnO tem-
plate. This robustness in tensile loading is
an exception for foam like carbon structures
which are usually kept together by entangle-
of syn-
ture of
h) Hier-
3488
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N the amount of the stored electrolyte, the ion
mobility and the volume of the individual
report
relatio
higher
deliver
more,
obtain
ical Ae
tion is
fi rst pl
resp. 2
S18). W
of Aer
are st
low de
could
shield
stand
First e
double
confi rm
An Ae
the rec
is evap
of the
Figure O tem-
plates w
tural va
interme
plate re
pattern
Aerogra
Aerogra
2 . Growth process and analysis of Aerographite. a) Photograph of utilized Zn
inelibrary.com © 2012 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
Aerogra
conduct
pression
samples
inset) t
porosity
epoxy s
turing (
We have here introdu
lightweight, electrically c
fl exible graphite based m
lished synthesis for other
graphene, the here used
plate for the synthesis o
has been proved that thi
able substrate/template m
e.g., CNTs and graphene.
of the Aerographite fam
network of microstructu
ness. Variants come as fi
or as a super lightweigh
struts from amorphous c
tuned from graphitic to
advantage of remarkable
lightweight material rea
specifi c moduli observed
parameters like, e.g., pore
bridges keeps the opportu
mechanical performance
like conductivity, fl exibilit
structural integrity, high o
high temperature stability
ed graphene or CNT based macroscopic bulk samples. In
n to its density Aerographite bears an at least 35 times
force as compared to the best silica based aerogel, which
s an UTS of 16 kPa at density of 100 mg cm − 3 . [ 13 ] Further-
a Young’s modulus of 15 kPa (slope in Figure 3 c) can be
ed. This modulus at such a low density brings a hypothet-
rographite free bending bar (min. defl ection if cross sec-
variable by E/ ρ 2 or if the height is variable by E/ ρ 3 ) to the
ace in every density selection map (0.463 × 106 m 5 kg − 1 s − 2
.572 × 106 m 8 kg − 2 s − 2 ), see Figure 3 b (SI, Figures S17,
hile a straight forward free standing panel application
ographite is more of academic interest, these numbers
ill very important in technological applications where
nsities lead to low acceleration induced forces. These
be microelectromechanical systems (MEMS), electrical
ing or conductive electrode applications that should with-
high accelerations, e.g., caused by vibrations or impacts.
xperiments with Aerographite electrodes in an electric
-layer capacitor (EDLC, also known as supercapacitor)
ed the mechanical robustness in a real life application.
rographite electrode loaded with electrolyte even endures
rystallization of the salt, which occurs when the solvent
orated during drying. This procedure induced cracking
activated carbon reference electrode. In order to optimize
ith a volume of 1.77 cm 3 . b-d) SEM micrographs showing two examples for the struc-
riety of ZnO crystal templates, here with a corrugated surface. e) Photograph of an
diate state of a sample on its way from ZnO to Aerographite. f-h) SEM revealing tem-
moval and formation of carbon layers (Figures S7-S10). i-k) TEM micrograph, SAED
, and EELS spectrum revealing graphitic state and sp 2 -hybridization of closed shell
phite. l-n) TEM micrograph, SAED pattern, and EELS spectrum of hollow framework
phite revealing amorphous carbon with a high content of sp 2 -hybridization. [ 19 ]
phite family exhibit a much higher
ivity of 37 S m − 1 at a mechanical com-
of 24%. The cm-scaled Aerographite
are super hydrophobic (Figure 3 b
herefore their properties and high
enable an excellent wetting with
ystems for nanocomposite manufac-
SI, Figure S22).
ced the novel synthesis of an ultra-
onductive, mechanical robust, and
aterial. In contrast to already estab-
carbon nanostructures like CNTs or
CVD process employs ZnO as tem-
f bulk samples on the cm 3 -scale. It
s inorganic semiconductor is a suit-
aterial for sp 2 hybridized carbons,
[ 25 , 26 ] The common structural motive
ily is the completely interconnected
res with a nanoscopic wall thick-
lled and unfi lled, corrugated walls,
t example of a hollow framework of
arbon. The atomic structure can be
glass-like pyrolytic carbon, with the
mechanical properties. This most
ches the highest merit indices for
until now. Further optimization of
size and volume density of sintering
nity for future improvements of the
of Aerographite. Further properties
y and compressibility without losing
ptical adsorption and X-ray opacity, a
and chemical resistance, the bearing
Adv. Mater. 2012, 24, 3486–3490
electrode, an electrolyte loaded Aerographite
electrode can be compressed till it has the
optimal balance between these parameters.
From CNT based electrodes [ 24 ] it is known
that increasing electrode length decreases
the capacity. CNT electrodes with 600 μ m
length show a power density of ≈ 2.3 Wh kg − 1
while 4000 μ m long Aerographite electrodes
still show 1.25 Wh kg − 1 which is a promising
starting point for the optimization. Besides
the structural properties, the application as
electrode material requires a good electrical
conductivity. Referring to this, Aerographite
reaches a conductivity of 0.2 S m − 1 at a den-
sity of 180 μ g cm − 3 .
By increasing the density under compres-
sion in air, e.g., to reach optimal free volume
to surface ratios, the conductivity increases
to 0.8 S m − 1 (0.2 mg cm − 3 ), see inset of
Figure 3 a. The increase for this light weight
material is mainly linear over a wide defor-
mation range of at least ε ≈ 30% which gives
chance for easy electro-mechanical sensing
applications. However samples of the heavy
(50 mg cm − 3 ) closed shell modifi cations of
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mm; d = 110 mm): At a constant temperature profi le
of 200 ° C in injection zone and 760 ° C in main
of
bici
to o
for
sup
from
of
deg
to s
sion
stru
Exp
T
disc
poly
1 to
rate
typi
esta
in. [ 2
0.8
10 m
C
grap
tem
Figu
test
max
con
den
drop
Aero
effe
mod
Adv.
re 3 . Mechanical and electrical properties of Aerographite. a) Tensile and comp
of the 180 μ g cm − 3 Aerographite variant (Figure 1e, SI, Figure S16), under tensile l
imum force and displacement was 31.1 mN and 0.4 mm. The inset shows the e
ductivity against compression. b) Material selection map, plotting the Young’s mo
sity 3 against the specifi c volume, parameters obtained from. [ 7 , 8 , 21 ] The inset shows
let on the surface of an Aerographite sample proving the superhydrophobicity
graphite. c) Tensile test of Aerographite (180 μ g cm − 3 ) until fracture. Inset: self-st
© 2012 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
Online Library or from the author.
Acknowledgements
We gratefully acknowledge par
Z1, R. A. DFG Heisenberg pro
grant and M. M. the Landesex
Joachim Herz Stiftung.
tensile and compressive loads, and the super hydropho-
ty making it a remarkable multifunctional material. Next
thers, potential applications might be electrode materials
the increasing demand of batteries and high surface area
ercapacitor materials. Proper designed carbon materials
the family of Aerographites could avoid typical problems
electrode materials like low mechanical cycling stability,
enerating electrical contacts, or non-optimized electrolyte
urface ratio which might be tuned in by simple compres-
due to the negligible Poisson’s ratio of these sponge-like
ctures.
erimental Section
emplates preparation : The ZnO templates were produced in a recently
overed method. [ 27 ] Zn powder (grain size 1–5 μ m) was mixed with
vinyl butyral powder (Kuraray Europe GmbH) in a mass ratio of
2. This mixture was heated in a muffl e furnace with a heating
of 60 ° C min − 1 to 900 ° C. After 30 min a loose powder of
cally ZnO tetrapods was obtained. Further synthesis methods and
blished recipes for the fabrication of ZnO structures can be found
0 ] Compressed powder (densities ranging from 0.15 g cm − 3 to
g m − 3 ) was reheated for 3 to 4 h at 1200 ° C in ceramic rings (h =
m, d = 15 mm) to form junctions.
VD-Synthesis : Basic Aerographite confi guration (hollow, with closed
hitic shells) can be gained by