Phonon transport in helically coiled carbon nanotubes
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Transcript of Phonon transport in helically coiled carbon nanotubes
C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8
.sc ienced i rec t .com
Avai lab le a t wwwScienceDirect
journal homepage: www.elsevier .com/ locate /carbon
Phonon transport in helically coiled carbonnanotubes
http://dx.doi.org/10.1016/j.carbon.2014.05.0310008-6223/� 2014 Elsevier Ltd. All rights reserved.
* Corresponding author.E-mail address: [email protected] (I. Milosevic).
Zoran P. Popovic, Milan Damnjanovic, Ivanka Milosevic *
University of Belgrade, Faculty of Physics, Studentski trg 12, 11001 Belgrade, Serbia
A R T I C L E I N F O
Article history:
Received 31 March 2014
Accepted 13 May 2014
Available online 22 May 2014
A B S T R A C T
We perform theoretical studies on the phonon thermal transport in helically coiled carbon
nanotubes (HCCNTs). The Gruneisen parameter, as a function of the phonon wave vector
and phonon branch, is numerically evaluated for each vibrational mode, so that the
three-phonon Umklapp scattering rates can be calculated exactly by taking into account
all allowed phonon relaxation channels. We considered wide temperature range and heat
conductor lengths from nano- to macro-scale. We examine the crossover from ballistic to
diffusive transport regime and impact of HCCNT geometrical parameters on their heat con-
duction. Thermal conductivity in HCCNTs is found to be slightly lower than that in single
walled carbon nanotubes (SWCNTs). This is interpreted by the competition among three
factors. Firstly, threefold reduction of the Gruneisen parameter for the acoustic branches.
Secondly, lower phonon group velocities. Finally, availability of purely acoustic scattering
channels. Nevertheless, HCCNTs are predicted to be more suitable (than SWCNTs) for
thermal management applications due to their spring-like shape. HCCNTs are extremely
elastic, natural NanoVelcro material.
� 2014 Elsevier Ltd. All rights reserved.
1. Introduction
Since the early work of Ruoff and Lorents [1] where high ther-
mal conductivity of carbon nanotubes have been predicted on
the basis of the high in-plane thermal conductivity of graph-
ite and of bulk and thin film diamond, wealth of experimental
and theoretical research of heat transport in carbon nano-
tubes and related carbon nanostructured materials have been
done [2]. It has been experimentally evidenced that, at all
temperatures, thermal conductivity of single walled carbon
nanotubes (SWCNTs) is dominated by phonons rather than
electrons [3] and that in nanotube thermal conductors Fourier
empirical law of thermal conduction is violated even when
the phonon mean free path (MFP) is much shorter than the
nanotube length [4].
However, with the exception of the recent reports on the
molecular dynamics calculations of thermal conductivity [5]
and thermal expansion [6] of helically coiled carbon nano-
tubes (HCCNTs) [7], theoretical research of their thermal
properties is lacking, although the first synthesis [8,9] of the
coiled nanotubes followed soon after the discovery of the
straight ones [10]. Presumably, the lack of large-scale synthe-
sis method of coiled CNTs over the past decades has hindered
extensive research of their precious properties and further
realizations of their potentials for the nano-technological
applications [11–13]. However, several recent reports on the
catalytic chemical vapor deposition production of the
HCCNTs with controlled morphology [14,15] substantially
improve the prospects of fundamental and applied physics
research of these peculiar nanostructures.
282 C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8
Here, using the upgraded Klemens treatment of heat con-
duction in basal planes of graphite [16–18] we perform a detail
theoretical study of the intrinsic thermal conductivity of
HCCNTs.
Used is the model of HCCNTs based on the topological
coordinate method [19,20] which has significant advantages
over the scheme proposed in the pioneering work of Ihara
Fig. 1 – Model of HCCNTs. (a) Symmetry generating elements (h
translation F and twofold horizontal rotational axis, U-axis, wh
geometrical parameters of HCCNTs (tubular diameter d, coil pitc
the eyes one half of the monomer is highlighted; (b) Cohesive e
(lower panel) of the corrugated and un-corrugated models of HC
side: Initial LR triple connected graph (n6=1, ((3,0), (0,3))) of pentag
Super-cell ((3,0), (0,3)) is shown; rectangle denotes its unit cell. O
Super-cell ((3,0), (0,2)) is shown; rectangle denotes its unit cell. I
cells), n5 ¼ 2 columns of hexagons (between the pairs of pentag
(between the pairs of heptagons of adjacent unit cells) [19].
and Itoh [21]. Firstly, it allows for almost continual variation
of a single geometrical parameter while all the other param-
eters are kept fixed. Secondly, it matches geometrical param-
eters of the as-synthesized HCCNTs [22,23]. Finally, apart
from the previously defined smooth helical structure [19] we
here introduce also corrugated model of HCCNTs (Fig. 1), as
both circular and polygon-like shapes of the cross-sections
elical rotational angle 2p=Q which is followed by a fractional
ich interlinks pairs of atoms within a monomer) and
h p, inclination angle v and helical diameter D); as a guide to
nergies (upper panel) and relative difference of tubular radii
CNTs as a function of the graph parameter nr; (c) On the left
ons (black), hexagons (white) and heptagons (dark grey) [20].
n the right side: Augmented graph (1,2,2,2, ((3,0), (0,2))).
nserted are nr ¼ 2 rows of hexagons (between initial unit
ons within a unit cell) and n7 ¼ 2 columns of hexagons
Fig. 2 – Low energy phonon dispersion relations for a
(2,2,0,0, ((1,0), (0,5))) HCCNT, with geometrical parameters
D ¼ 2:2 nm; d ¼ 0:5 nm; p ¼ 2:6 nm; v ¼ 210. Acoustic
branches (green), the lowest optical branch (blue) and
scattering channels AAA (green solid line) and AAO (blue
solid line) are highlighted. Three-phonon Umklapp
scattering of the type I (II) is shown by solid (dashed) line.
Red diamond marks the considered phonon. (A colour
version of this figure can be viewed online.)
C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8 283
are evidenced in the as-synthesized samples of the coiled car-
bon nanotubes [7,24].
We perform calculations of thermal conductivity of
HCCNTs of finite lengths, from 10nm to 10mm. Apart from
the anharmonic three-phonon Umklapp processes which
are treated exactly, for all allowed phonon relaxation chan-
nels, backscattering is accounted for within relaxation time
approximation. We also examine temperature dependant
crossover from ballistic to diffusive transport regime, as well
as dependance of thermal conductivity on geometrical
parameters of HCCNTs.
The breakdown of the Fourier law of heat conduction
which was evidenced in SWCNTs [4] we also predict for
HCCNTs. Namely, we find that regularly distributed pentago-
nal and heptagonal ‘‘defects’’ do not to scatter the long-wave
length phonons to the extent enough to remove the thermal
conductivity divergence with nanotube length.
We predict that thermal conductivity of HCCNTs amounts
� 75% of that of the corresponding SWCNTs as the coil length
exceeds 500 lm. So good heat conducting properties in com-
bination with the unique mechanical qualities [13,25] make
HCCNTs promising candidates for thermal management
applications.
2. Phonon dispersion relations
We consider the model of HCCNTs which is obtained by roll-
ing up a triple connected graph of pentagons, hexagons and
heptagons, conventionally defined by a set of numbers
ðn6;nr;n7;n5; ðb1;b2ÞÞ, where ðb1;b2Þ are the super-cell vectors,
while the tiling pattern is given by the first four parameters,
Fig. 1. In addition to the relaxation procedure given in Ref.
[19], tubular radial coordinates of carbon atoms are also var-
ied and obtained is a model of corrugated HCCNTs. Compar-
ison of the cohesive energies of the corrugated and un-
corrugated HCCNTs together with the rate of corrugation
are given in Fig. 1. Geometrical structure of HCCNTs is charac-
terized by tubular diameter d, outer diameter of a helix D,
helical step p and inclination angle v.
Unlike the case of SWCNTs where phonon dispersion
curves are evaluated using the graphite force constants [26]
adopted to the nanotube geometry [27], dynamical sub-matri-
ces of HCCNTs are numerically derived out of Brenner inter-
atomic potential [28] by varying space coordinates of carbon
atoms and calculating the corresponding energy changes.
Since HCCNTs are complex systems which, in general, do
not have translational periodicity and contain thousands of
atoms within a single coil pitch, application of the line group
symmetry [29] and related symmetry based techniques [30] as
well as helical quantum number representation of phonon
modes were essential for carrying out numerical
computation1.
Symmetry of HCCNTs [19], described by a 5th family LG
L ¼ TQðFÞD1, which is generated by helical transformation
ðCQ jFÞ (i.e. rotation for 2p=Q followed by fractional translation
1 Quite recently, similar method which apply line group symmetryvibrations in MoS2 NTs [31].
2 In the literature, helical quantum numbers are, by convention, dennumbers. However, as herein we are dealing only with the helical qu
F) and by p-rotation around twofold horizontal axis (U-axis,
Fig. 1). Generally, parameters Q and F (which is determined
by the inclination angle v and monomer length a of the
HCCNT: F ¼ a sin v) are real and only in the special case of
the rational Q value (i.e. Q ¼ q=r, where q and r are co-primes
satisfying condition q > r), there is a translational symmetry
with period A ¼ qF. However, even in these special cases, heli-
cal quantum number representation of the phonon disper-
sions is more convenient since unit cell is always very large.
In addition, helical angular momentum m is conserved in
Umklapp processes, regardless of whether reduced or
extended Brillouin zone scheme is applied [29]. Helical wave
vector k reflects helical periodicity and runs over the irreduc-
ible domain ½0; p=F�. Full symmetry assigned dispersion
curves, when shown over the irreducible domain, correspond
to doubly degenerated phonon states. On the other hand, first
Brillouin zone is given by the interval ð�p=F;p=F� and C-point
and edge-point phonon states are characterised by a parity
with respect to the U-axis. Lack of the rotational symmetry
implies vanishing helical angular momentum (m ¼ 0).
Although helical quantum number representation2 is
used, total number of phonon branches is still very large:
three times the number of atoms within a monomer, nF.
Therefore, for clarity, in Fig. 2, displayed is only the low
energy part of phonon dispersions (from 0 to 50�1012 rad/s
out of roughly 300� 1012 rad=sÞ for the HCCNT with relatively
small number of atoms in a monomer: nF ¼ 60.
Being quasi-one dimensional systems, HCCNTs have four
acoustic branches: In helical quantum numbers representa-
to empirical potential calculations has been used to study lattice
oted as ~k and ~m, in order to distinguish from the linear quantumantum numbers, tilde symbol is omitted for convenience.
284 C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8
tion, transverse acoustic (TA) modes are characterized by
finite wave number k ¼ 2p=Q (V point) and quadratic disper-
sion, while longitudinal acoustic (LA) and shear wave acoustic
modes (SWA) are represented by k ¼ 0 (C point) and show lin-
ear dispersions (Fig. 2) with the sound velocities of the same
intensity, vLA ¼ vSWA ¼ 3000 m/s, which is much lower than
the sound velocities in SWCNTs [27]. However, in contrast to
SWCNTs, the maximal acoustic band velocities in HCCNTs
are not the sound velocities. As illustrated in Fig. 2, over a
relatively large interval of the Brillouin zone, dispersions of
the acoustic phonons are linear with the band velocity of,
typically � 9000 m/s, corresponding to the intensity of the
TA sound velocity in SWCNTs [27] (whilst the TA acoustic
modes of HCCNTs have quadratic dispersion xTA ¼ ak2;
a ¼ 10�6 m2=s). Finally, the optical gap is an order of
magnitude lower than in the case of straight SWCNTs.
3. Phonon scattering
Different momentum non conserving scattering processes
contribute to the thermal resistance: anharmonic phonon
interaction, diffuse phonon scattering from rough bound-
aries, phonon-defect scattering, etc. In ideal cases (crystal
structures without defects and without boundaries, e.g.) the
intrinsic thermal conductivity is limited only by the pho-
non–phonon scattering due to the lattice anharmonicity
which can be theoretically interpreted by considering three-
phonon Umklapp processes.
Following the method of Klemens and Pedraza for evaluat-
ing theoretical values of phonon thermal conductivity (which
was applied originally to single crystals of graphite [16] and
later, by Balandin and co-workers [18], advanced and adapted
for calculation of thermal transport in graphene) we derive
expressions of intrinsic thermal conductivity of HCCNTs tak-
ing into account the three-phonon Umklapp scattering pro-
cesses in which: (I) a phonon xðkÞ leaves the state k as
being absorbed by another phonon from the heat flux, and
(II) a phonon comes to the state k, due to the decay of a pho-
non from the state k00. For these two types of Umklapp pro-
cesses energy conservation laws are: xðkÞ � xðk0Þ � xðk00Þ ¼ 0,
where the upper sign corresponds to the first and lower sign
to the second process.
In Umklapp processes, in general, quasi-momenta and
quasi-angular momenta are not conserved. However, unlike
the case of the straight SWCNTs, where the scattering phase
space is severely restricted [32] due to the chirality dependant
quasi-angular momenta selection rules [29], there is no such a
reduction of the scattering phase space of HCCNTs. Hence,
three phonons which pertain to any combination of the
branches can take part in an Umklapp process provided that
the energy is conserved and the condition imposed on the
quasi-momenta is fulfilled: k� k0 ¼ k00 þ K (where K is a reci-
procal lattice vector). This is in contrast to the achiral
SWCNTs where Umklapp scattering which involves three
acoustic phonons is not allowed [32]. Consequently, while
contribution of the normal scattering processes have consid-
3 In the previous theoretical studies of thermal conductivity of graphbetter agreement with experiment.
erable impact on the phonon transport in the straight
SWCNTs, they do not have the same effect in HCCNTs.
Namely, as normal processes indirectly affect thermal con-
ductivity through redistribution of the phonon modes, if they
would not be taken into account, many triples of phonons of
SWCNTs would be left trapped in the states which fulfill
momenta and energy conserving conditions but do not satisfy
the angular momenta selection rules. This however is not the
case with HCCNTs, where all the phonon scattering channels
are open.
Out of the general forms for matrix elements of the three-
phonon interaction [17], we evaluate the expressions for the
three-phonon Umklapp scattering rates in HCCNTs taking
into account all the phonon branches and their dispersions
as well as energy and momenta selection rules. At the tem-
perature T, Umklapp scattering rate s�1U (where sU is the pho-
non relaxation time) of a phonon from the state km of the
branch m and with energy �hxm is calculated according to the
following expression (upper/lower sign correspond to first/
second type of the Umklapp process):
s�1U ðm;km;TÞ ¼
2c2m �hxmðkmÞF
3nFMv2m ðkmÞ
Xa;b
Xka ;kb2X
xaðkaÞxbðkbÞjDx0�ðkaÞj
�
�ffT½xaðkaÞ� � fT½xbðkbÞ� þ12� 1
2g:
The summations are taken over the all 3nF phonon dispersion
branches and over the set
X ¼ fk 2 ð�p; p� jDx�ðkÞ ¼ 0 ^ Dx0�ðkÞ– 0g;
Dx�ðkaÞ ¼ xmðkmÞ � xaðkaÞ � xbðkbÞ;
cm is Gruneisen parameter of the branch m (calculated is mode-
dependant Gruneisen parameter which is then averaged over
the each phonon branch3); M is a carbon atom mass; vmðkÞ is
the phonon group velocity; fT is Bose–Einstein equilibrium
distribution function at temperature T.
Gruneisen parameter cmk of an individual phonon mode
xmðkÞ is defined as the negative logarithmic derivative of the
frequency of the mode with respect to the volume. Overall
Gruneisen parameter for the acoustic branches is calculated
as the weighted average of the individual Grunisen parame-
ters in which the contribution of each phonon is weighted
by its contribution to the specific heat [34,16] and the typical
value obtained for HCCNTs is �0.5 (which is for a factor 3
lower than in the case of SWCNTs).
The coiled nanotubes do not have surface which can pro-
vide boundary scattering except for the nanotube ends which
may lead to the backscattering. The backscattering rate s�1B ,
which is of relevance in the ballistic regime only, is calculated
within relaxation time approximation: s�1B ¼ vmð1� sÞ=L,
where vm is the group velocity of the phonon branch m; L is
NT length and s is adjustable parameter giving fraction of
phonons which scatter specularly from the boundaries (the
values zero and one correspond respectively to the absolutely
rough and ideally smooth boundaries). Value of the s-param-
eter depends on the quality of the end-contacts [35] and in
ene [18] and BN NTs [33] mode-specific Gruneisen parameter gave
Fig. 3 – Phonon MFP K vs. phonon wave-vector k at room
temperature. Dotted horizontal line indicates MFP threshold
K0. Arrows point to the particular values of the cut-off
frequencies, xCðLAÞ;xCðSWAÞ and xjðTAÞ, which correspond
to the given cut-off in the k-space.
Fig. 4 – Intrinsic MFP for the first two phonon branches of a
(1,3,2,0, ((1,0), (0,5))) HCCNT at temperatures of 100 K and
300 K. Dashed lines show the room temperature intrinsic
MFP of the acoustic modes of a (7,1) SWCNT. (A colour
version of this figure can be viewed online.)
C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8 285
our calculations nearly ideal contacts are assumed by taking
s ¼ 0:98.
The scattering rates we consider to be mutually indepen-
dent and apply the Matthiessen’s rule, taking thus the overall
scattering rate as a sum of the particular scattering rates.
4. Thermal conductivity
Thermal conductivity j is the sum of the individual phonon
conductivities jmðkÞ:
j ¼X
m
Xk
jmðkÞ ¼1V
Xm
Xk
cmðkÞvmðkÞKmðkÞ ð1Þ
where cmðkÞ ¼ �hxmðkÞ @@ T f TðxmðkÞÞ is the phonon specific heat,
KmðkÞ ¼ jvmðkÞjsmðkÞ is the phonon MFP and the summation is
taken over the entire phonon dispersions m and over the
wave-vectors k of the Brillouin zone (�p=F; p=F].
Calculations of thermal conductivity we perform on a
sample of HCCNTs with helical diameters D � 5 nm, helical
— tubular radii ratio D : d from 4 to 5.5 and helical steps p
between 2 and 6.2 nm.
Taking for the volume of the monomer of HCCNT
V ¼ 2prda, where d ¼ 3:4 A and r are the nanotube wall thick-
ness and tubular radius (averaged over the radii of the all
orbits of the corrugated model of HCCNT, Fig. 1), replacing
the summation over the 1D Brillouin zone with the integra-
tion over the irreducible domain of the reciprocal space, Eq.
(1) takes the form:
j ¼ 14p2rda
Xm
Z p=F
0cmðkÞvmðkÞKmðkÞdk ð2Þ
In order to avoid the problem of vanishing scattering of the
long-wave length phonons [36] (which makes the thermal
conductivity to diverge as the heat conductor length
increases) we introduce the cut-off frequencies for the disper-
sions around C and V points, (xC and xV) exempting from the
heat flow the phonons with infinite MFP. The cut-off frequen-
cies are determined by analysing the wave-vector depen-
dance of the MFP, Fig. 3. In all the cases considered it holds
xCðLAÞ > xCðSWAÞ > xVðTAÞ.Frequency dependance of the phonon MFPs for the acous-
tic branches of a (2,2,0,0, ((1,0), (0,5))) HCCNT, and of the LA, TA
and TWA modes of a (7,1) SWCNT are presented in Fig. 4. In
the calculations, only the Umklapp scattering rates are
accounted for. Generally, phonon MFP in the coiled tubes is
of the same order of magnitude as in the straight tubes. If
long wave length phonons which are characterized by infinite
MFP are excluded, MFP of the acoustic modes of vibration at
room temperature spans to 10 lm. As the system is cooled
down to 100 K, acoustic phonon MFP is predicted to reach
1 mm.
According to the empirical Fourier law of heat conduction,
which refers to the diffusive regime of heat transport (i.e.
under condition that length of the conductor is considerably
larger than the phonon MFP), the thermal conductivity j
directly relates the heat energy flux U to the temperature gra-
dient: U ¼ �jrT. The Fourier law implicitly states that the
thermal conductivity is independent of the length of the con-
ductor. This was experimentally proved in all the cases of
three-dimensional (3D) materials considered thus far. How-
ever, there are many indications that the Fourier law in 1D
systems does not hold. Theoretical investigation of the heat
conduction in 1D chains of anharmonic oscillators suggests
that the chaotic behavior in 1D is not enough to attenuate
the free traveling long wave-length phonons [37]. From the
experimental side, the breakdown of the Fourier law in car-
bon and boron-nitride nanotubes has been evidenced [4]:
measured thermal conductivity data were fitted to a function
jðLÞ � Lb; and the b parameter, which measures the deviation
from the Fourier low behavior, was determined to be
b 2 ½0:6;0:8�. According to our calculations, HCCNTs are yet
another variety of 1D systems that violates the law of heat
conduction. Fit to the numerically results at zero cut-off fre-
quencies, (which is essentially equivalent to the long wave-
length approximation) predicts b 2 ½0:4;0:6� for HCCNTs and
b 2 ½0:3;0:5� for straight SWCNTs.
Fig. 6 – Length dependance of thermal conductivity of
(1,3,2,0, ((1,0), (0,5))) HCCNT (solid line) and (7,1) SWCNT
(dashed line) at T ¼ 200 K (navy), T ¼ 300 K (olive) and
T ¼ 400 K (wine). Dotted lines indicate thermal conductivity
of HCCNT along the helical axis. (A colour version of this
figure can be viewed online.)
286 C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8
In Fig. 5 presented is length dependance of the room tem-
perature thermal conductivity of a coiled (1,3,2,0, ((1,0), (0,5)))
CNT and of a straight (7,1) CNT having similar tubular diame-
ters. Dashed lines show the results obtained in the long wave-
length approximation and the parameters giving deviation
from the Fourier low are b ¼ 0:3 (SWCNT) and b ¼ 0:5
(HCCNT). If the frequency cut-off is introduced, thermal con-
ductivity saturates to finite value: j ¼ 3300 W/Km (matching
the conductivity of the purified diamond [38]) at L > 500 lm
(for the HCCNT) and j ¼ 4300 W/Km at L > 100 lm (for the
SWCNT). The latter is in excellent agreement with the previ-
ously reported results [39] (j � 4000 W/Km, L > 100 lm,
T ¼ 316 K, calculated for (10,0) NT).
The relative thermal conductivity of HCCNTs with respect
to the corresponding straight SWCNTs is length dependant.
Heat transfer through the coiled NTs over the distance of
10nm is �; 50% lower than through the straight counterparts.
However, relative thermal conductivity of HCCNTs rapidly
increases with the conductor length, being 70% at �100nm
and reaching the plateau of 75% at the lengths of the order
of 1 mm.
For the conductors shorter than phonon MFPs, scattering-
free phonon transport leads to linear dependance of the ther-
mal conductivity with length. The lower the temperature, the
larger is the phonon MFP (Fig. 4) and thus the limit of the bal-
listic conductor length is larger (Fig. 6).
Modifications of the helical-tubular diameter ratio, D : d,
induce the modifications of the phonon dispersions of HCCNTs
which are further reflected in the thermal and mechanical
properties. Namely, the lower D : d is, the higher are the both
thermal conductivity and elastic modulus. As apart from the
high thermal conductance it is important that theraml inter-
face materials are also highly elastic, in order to quantify the
optimal helical-tubular diameter ratio for heat-sinking appli-
cations of HCCNTs, thorough calculations of the both proper-
Fig. 5 – Room temperature thermal conductivity j of (1,3,2,0,
((1,0), (0,5))) HCCNT (black) and (7,1) SWCNT (gray) as a
function of the conductor length L. Solid lines show the
results obtained introducing the cut-off frequencies (Fig. 3),
while long wave-length approximation is indicated by the
dashed lines. Dotted line gives thermal conductivity of the
HCCNT along the helical axis. Inset highlights the conductor
length range: 0–10 lm.
ties are to be performed on a large and representative sample
of the modeled HCCNTs. However, this task is beyond the scope
of this paper and will be presented elsewhere.
As illustrated in Fig. 7, HCCNTs with lower helical-tubular
diameter ratio are characterized by higher acoustic phonon
velocities which are further reflected in the higher thermal
conductivity (under condition that other structural parame-
ters are not changed notably).
4.1. Thermal conductance
The heat flow rate through a single ballistic phonon channel
at temperature T is given by the quantum of thermal conduc-
tance [40]: rthðTÞ ¼ p2k2BT=3h. In the ballistic limit, thermal
Fig. 7 – Thermal conductivity of HCCNTs: (3,3,0,0, ((1,0), (0,5)))
(red); (1,3,2,4, ((1,0), (0,5))) (green); (1,4,2,2, ((1,0), (0,5))) (blue);
with different helical-tubular diameter ratio D : d, as a
function of the length of the helix (solid line) and of the
length of the helical axis (dotted line). Inset shows the
corresponding low energy phonon dispersions. (A colour
version of this figure can be viewed online.)
Fig. 8 – Temperature dependance of thermal conductance r
for 1lm long (2,2,0,0, ((1,0), (0,5))) HCCNT. Ballistic r � T (red)
and diffusive r � T�1 (blue) regimes are highlighted. Arrow
indicates that two quanta of conductance do not extrapolate
to zero at T ¼ 0 K. (A colour version of this figure can be
viewed online.)
C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8 287
conductance r is an integer multiple of rth and thus more
appropriate measure of the heat transport than thermal con-
ductivity j. The conductance is related to the conductivity as:
r ¼ ðS=LÞj, where S is the area of the cross-section of the heat
conductor. Temperature dependance of the thermal conduc-
tance of one micrometer long (2,2,0,0, ((1,0), (0,5))) HCCNT is
shown in Fig. 8.
The quantized ballistic conductance is characterized by a
linear temperature dependance rðTÞ � T and holds until
T � 30 K. At temperatures higher than several Kelvins,
HCCNTs carry two quanta of thermal conductance,
rHCCNT ¼ 2rthðTÞ, i.e. a half of the energy flux through the
straight SWCNTs [41] in a scattering-free transport regime.
Only in the zero temperature limit HCCNTs have four trans-
port channels, Fig. 8. The peak of the conductance is reached
at T ¼ 55 K when a balance between specific heat increase
and increased scattering rate is established. At higher tem-
peratures scattering processes dominate and at T > 200 K dif-
fusive transport regime rule rðTÞ � T�1 holds.
5. Conclusion
Presented is the theoretical study of phonon heat conduction
in helically coiled carbon nanotubes. Flexible atomistic model
in which the coiling arises as an intrinsic property of the
structure [42] and which matches the geometrical parameters
of the as-synthesized HCCNTs is proposed.
Phonon dispersions of HCCNTs are found to substantially
differ from that of SWCNTs: The coiled tubes are character-
ized by narrow acoustic bands and by relatively low phonon
group velocities. In addition, since lacking pure rotational
symmetry, they allow for three-phonon Umklapp scattering
of solely acoustic modes of vibration (by contrast to the
straight SWCNTs, where such kind of processes are forbidden
by selection rules). Due to the balance of the low anharmonic-
ity of acoustic modes, on the one side, and lack of the restric-
tions on the type of the scattering channels, on the other side,
MFP of the acoustic phonons in HCCNTs is of the same order
as in the case of straight SWCNTs: from one to ten microme-
ters at room temperature.
Room temperature thermal conductivity of HCCNTs is pre-
dicted to match that of the purified diamond as the nanotube
length exceeds 0.5 mm. For many applications, vertically
aligned CNT arrays are promising as thermal interface mate-
rials and thermal conductance is a crucial measure of their
performance. However the optimal interfaces need to have
a variety of other characteristics like e.g. high elasticity. In
this respect, the coiled nanotubes are superior to the straight
ones. Besides, HCCNTs naturally form VelcroTM-like contact
[43] where the tubes mechanically entangle, so that the load
transfer efficiency in composites [11] made of the coiled CNTs
(rather than of the straight ones) is expected to be substan-
tially larger (as the coiled shape spontaneously induces
mechanical interlocking when the composite is subjected to
loading).
In this paper we gave insight into the mechanisms which
govern intrinsic heat conduction in HCCNTs. However, in
order to come to real applications, many questions are still
to be resolved. One of these, a heat dissipation along the
nanotubes and from the nanotubes to the substrate, is critical
to developing and improving CNT-based electronic devices
[44,45].
Acknowledgments
The authors acknowledge funding of Serbian Ministry of Sci-
ence (ON171035) and Swiss National Science Foundation
(SCOPES IZ73Z0–128037/1).
Appendix A. Supplementary data
Supplementary data associated with this article can be found,
in the online version, at http://dx.doi.org/10.1016/
j.carbon.2014.05.031.
R E F E R E N C E S
[1] Ruoff RS, Lorents DC. Mechanical and thermal properties ofcarbon nanotubes. Carbon 1995;33:925–30.
[2] Marconnet AM, Panzer MA, Goodson KE. Thermal conductionphenomena in carbon nanotubes and related nanostructuredmaterials. Rev. Mod. Phys. 2013;85:1295–327.
[3] Hone J, Whitney M, Piskoti C, Zettl A. Thermal conductivity ofsingle-walled carbon nanotubes. Phys. Rev. B1999;59:R2514–6.
[4] Chang CW, Okawa D, Garcia H, Majumdar A, Zettl A.Breakdown of Fouriers law in nanotube thermal conductors.Phys. Rev. Lett. 2008;101. 075903.
[5] Zhao J, Wu J, Jiang J-W, Lu L, Zhang Z, Rabczuk T. Thermalconductivity of carbon nanocoils. Appl. Phys. Lett. 2013;103.233511.
[6] Popovic ZP, Damnjanovic M, Milosevic I. Anisotropy ofthermal expansion of helically coiled carbon nanotubes.Phys. Status Solidi B 2013;250:2535–8.
[7] Fejes D, Hernadi K. A Review of the properties and CVDsynthesis of coiled carbon nanotubes. Materials2010;3:2618–42.
288 C A R B O N 7 7 ( 2 0 1 4 ) 2 8 1 – 2 8 8
[8] Zhang XB, Zhang XF, Bernaerts D, Van Tendeloo G, AmelinckxS, Van Landuyt J, et al. The texture of catalytically grown coil-shaped carbon nanotubules. Europhys. Lett. 1994;27:141–6.
[9] Amelinckx S, Zhang XB, Bernaerts D, Zhang XF, Ivanov V,Nagy JB. A formation mechanicsm for catalytically grownhelix-shaped graphite nanotubes. Science 1994;265:635–9.
[10] Iijima S. Helical microtubules of graphitic carbon. Nature1991;354:56–8.
[11] Lau KT, Lu M, Hui D. Coiled carbon nanotubes: synthesis andtheir potential applications in advanced compositestructures. Composites: Part B 2006;37:437448.
[12] Yang S, Chen X, Motojima S. Tactile sensing properties ofprotein-like single-helix carbon microcoils. Carbon2006;44:3352–5.
[13] Volodin A, Buntinx D, Ahlskog M, Fonseca A, Nagy JB, VanHaesendonck C. Coiled carbon nanotubes as self-sensingmechanical resonators. Nano Lett. 2004;4:1775–9.
[14] Fejes D, Nemeth Z, Hernadi K. CVD synthesis of spiral carbonnanotubes over asymmetric catalytic particles. React. Kinet.Catal. Lett. 2009;96:397–404.
[15] Fejes D, Forro L, Hernadi K. Catalyst preparation with ballmilling for catalytic synthesis of coiled carbon nanotubes.Phys. Status Solidi B 2010;247:2713–6.
[16] Klemens PG, Pedraza DF. Thermal conductivity of graphite inthe basal plane. Carbon 1994;32:735–41.
[17] Han YJ, Klemens PG. Anharmonic thermal resistivity ofdielectric crystals at low temperatures. Phys. Rev. B1993;48:6033–42.
[18] Nika DL, Pokatilov EP, Askerov AS, Balandin AA. Phononthermal conduction in graphene: role of Umklapp and edgeroughness scattering. Phys. Rev. B 2009;79:155413.
[19] Milosevic I, Popovic ZP, Damnjanovic M. Structure andstability of coiled carbon nanotubes. Phys. Status Solidi B2012;249:2442–5.
[20] Laszlo I, Rassat A. The geometric structure of deformednanotubes and the topological coordinates. J. Chem. Inf.Comput. Sci. 2003;43:519–24.
[21] Ihara S, Itoh S. Helically coiled and toroidal cage forms ofgraphitic carbon. Carbon 1995;33:931–9.
[22] Fejes D, Popovic ZP, Raffai M, Balogh Z, Damnjanovic M,Milosevic I et al. Synthesis, model and stability of helicallycoiled carbon nanotubes. ECS Solid State Lett. 2013;2:M21–M23.
[23] Hernadi K, Thien-Nga L, Forro L. Growth and microstructureof catalytically produced coiled carbon nanotubes. J. Phys.Chem. B 2001;105:12464–8.
[24] Fonseca A, Hernadi K, Nagy JB, Lambin P, Lucas AA. Modelstructure of perfectly graphitizable coiled carbon nanotubes.Carbon 1995;33:1759–75.
[25] Chen X, Motojima S, Iwanga H. Vapor phase preparation ofsuper-elastic carbon micro-coils. J. Cryst. Growth2002;237:1931–6.
[26] Jishi RA, Venkataraman L, Dresselhaus MS, Dresselhaus G.Phonon modes in carbon nanotubules. Chem. Phys. Lett.1993;209:77–82.
[27] Dobardzic E, Milosevic I, Nikolic B, Vukovic T, DamnjanovicM. Single-wall carbon nanotubes phonon spectra: symmetry-based calculations. Phys. Rev. B 2003;68. 045408.
[28] Brenner DW, Shenderova OA, Harrison JA, Stuart SJ, Ni B,Sinnott SB. A second-generation reactive empirical bondorder (REBO) potential energy expression for hydrocarbons. J.Phys. C 2002;14:783–802.
[29] Damnjanovic M, Milosevic I. Line groups in physics: theoryand applications to nanotubes andpolymers. Berlin: Springer; 2010.
[30] M. Damnjanovic, I. Milosevic, E. Dobardzic, T. Vukovic, B.Nikolic. Symmetry based fundamentals of carbon nanotubes.In: Rotkin SV, Subramoney S, editors. Ch. II in Applied physicsof nanotubes: fundamentals of theory, optics and transportdevices, Springer–Verlag, Berlin; 2005.
[31] Jiang J-W, Wang B-S, Rabczuk T. Phonon modes in single-walled molybdenum disulphide nanotubes: lattice dynamicscalculation and molecular dynamics simulation.Nanotechnology 2014;25:105706. 9pp.
[32] Lindsay L, Broido DA, Mingo N. Lattice thermal conductivityof single-walled carbon nanotubes: beyond the relaxationtime approximation and phonon–phonon scatteringselection rules. Phys. Rev. B 2009;80:125407. 7.
[33] Jiang J-W, Wang J-S. Theoretical study of thermalconductivity in single-walled boron nitride nanotubes. Phys.Rev. B 2011;84:085439. 7.
[34] Ashcroft NW, Mermin ND. Solid state physics. CBSPublishing Asia Ltd; 1976.
[35] Ma H, Pan L, Zhao Q, Zhao Z, Qiu J. Thermal conductivity of asingle carbon nanocoil measured by field-emission inducedthermal radiation. Carbon 2013;50:778783.
[36] Pomeranchuk I. On the thermal conductivity of dielectrics.Phys. Rev. 1941;60:820–1.
[37] Lepri S, Livi R, Politi A. Heat conduction in chains ofnonlinear oscillators. Phys. Rev. Lett. 1997;78:1896–9.
[38] Berman R. Thermal conductivity of isotopically enricheddiamonds. Phys. Rev. B 1992;45:5726–8.
[39] Mingo N, Broido DA. Length dependence of carbon nanotubethermal conductivity and the problem of long waves. NanoLett. 2005;5:1221–5.
[40] Schwab K, Henriksen EA, Worlock JM, Roukes ML.Measurement of the quantum of thermal conductance.Nature, 404. Springer; 2000. p. 974–7.
[41] Yamamoto T, Watanabe S, Watanabe K. Universal features ofquantized thermal conductance of carbon nanotubes. Phys.Rev. Lett. 2004;92. 075502.
[42] Szabo A, Fonseca A, Nagy JB, Lambin P, Biro LP. Structuralorigin of coiling in coiled carbon nanotubes. Carbon2005;43:16281633.
[43] Berber S, Kwon YK, Tomanek D. Bonding and energydissipation in a nanohook assembly. Phys. Rev. Lett. 2003;91.165503.
[44] Rotkin SV, Perebeinos V, Petrov AG, Avouris P. An essentialmechanism of heat dissipation in carbon nanotubeelectronics. Nano Lett. 2009;9:1850–5.
[45] Perebeinos V, Rotkin SV, Petrov AG, Avouris P. The effects ofsubstrate phonon mode scattering on transport in carbonnanotubes. Nano Lett. 2009;9:312–6.