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A simplified model to estimate thermal resistance between carbon nanotube and sample in scanning thermal microscopy
To cite this article before publication: Maxim Nazarenko et al 2017 J. Phys. D: Appl. Phys. in press https://doi.ora/10.1088/1361-6463/aa900e
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r V FAlrtcmi3
3 A simplified model to estimate thermal resistance between carbon
5 nanotube and sample in scanning thermal microscopy
10 Maxim Nazarenko1'2, Mark C. Rosamond^, Andrew J. Gallant1'4, Oleg V. Kolosov3, 12
13 Vladimir G. Dubroskii2,4 and Dagou A. Zeze1,4*
15 1 School of Engineering & Computing Sciences, Durham University, Durham DH1 3LE, UK
17 2 St Petersburg Academic University, Khlopina 8/3, 194021 St Petersburg, Russia
20 3 Department of Physics, Lancaster University, Lancaster LA1 4YB, UK
22 4 University of Information Technologies, Mechanics and Optics
24 §: Now at the School of Electrical and Electronic Engineering, University of Leeds, Leeds,
26 LS2 9JT UK
31 Abstract
34 Scanning Thermal Microscopy (SThM) is an attractive technique for nanoscale thermal
36 measurements. Multiwalled carbon nanotubes (MWCNT) can be used to enhance a SThM
38 probe in order to drastically increase spatial resolution while keeping required thermal
43 the MWCNT-enhanced probe tip and a sample under study is essential for the accurate
45 interpretation of experimental measurements. Unfortunately, there is very little literature on
47 Kapitza interfacial resistance involving carbon nanotubes under SThM configuration. We
40 propose a model for heat conductance through an interface between the MWCNT tip and the
52 sample, which estimates the thermal resistance based on phonon and geometrical properties
54 of the MWCNT and the sample, without neglecting the diamond-like carbon layer covering
56 the MWCNT tip. The model considers acoustic phonons as the main heat carriers and
sensitivity. However, an accurate prediction of the thermal resistance at the interface between
the M the M
account for their scattering at the interface based on a fundamental quantum mechanical approach. The predicted value of the thermal resistance is then compared with experimental data available in the literature. Theoretical predictions and experimental results are found to be of the same order of magnitude, suggesting a simplified, yet realistic model to approximate thermal resistance between carbon nanotube and sample in SThM, albeit low temperature measurements are needed to achieve a better match between theory and experiment. As a result, several possible avenues are outlined to achieve more accurate predictions and to generalize the model.
1. Introduction
Nanotechnology is an umbrella term covering the study and manipulation of matter at the nanoscale. Well-developed and diverse techniques are required to achieve this efficiently. Atomic force microscopy (AFM) developed in 1986 [1] provides for both the study and manipulation of nanometer objects. A number of nanoscale microscopy techniques based on the AFM were developed through the years [2-8]. In particular, scanning thermal microscopy (SThM) investigates the thermal properties of materials at the nanoscale [9-13]. Currently, thermal management problems are some of the most significant limiting factors not only for high-power electric devices, but even more importantly, for high-speed electronic components [14-16]. As characteristic device dimension shrinks while their thermal envelope remains roughly the same, the specific heat production is increased drastically. In order to optimize device design, astute measurement methods are required. Most current thermal measurement systems (such as infrared imaging, photoreflectance measurements, and Raman spectroscopy) are based on optical effects, limiting their resolution to micrometer scale [17-19]. SThM uses direct measurements techniques and s for tens of nanometer spatial resolution. However, classical SThM techniques are not
requirements for high spatial resolution, i.e. small contact area, inevitably result in a high
3 totally adequate for the study of high thermal conductivity materials such as semiconductors
5 [20] due to their diminished ability to differentiate between such materials. Moreover,
10 thermal resistance, which, in turn, lowers thermal resolution even more.
12 This apparent contradiction may make the situation look hopeless. However, a possible
14 mitigating approach is to use a high thermal conductivity element, such as multiwalled
17 carbon nanotubes (MWCNT) to enhance the performance of the probe tip, in direct contact
19 with the sample under study [21-25]. The outstanding geometric and mechanical properties,
21 such as high aspect ratio, perfect crystalline structure and high Young's modulus [26] allow
23 MWCNT to probe into deep and steep recesses and to flex while avoiding mechanical
25 damage. If a relatively short conically shaped probe is used, similar to that explored later in
30 conductance due to the use of MWCNT may significantly improve the performance of
32 SThM.
39 proven experimentally [24]. It is now reported in the literature that MWCNT may drastically
41 increase spatial resolution while having sufficiently low thermal resistance as to keep
43 required thermal sensitivity [24, 27]. However, the unique properties of MWCNT are coupled
45 with new challenges. For instance, understanding the heat flow through the sample and probe
this paper, the mechanical stability is unlikely to be compromised. In turn, the high thermal
Early theoretical analysis confirmed the high potential of such an approach [25] that was then
remains a major challenge to achieve a better insight into thermal energy transport at the
50 nanometer scale. It is also essential to achieve simultaneously the competing objective of
52 high spatial resolution and high thermal sensitivity. This problem has many aspects, such as
54 ballistic heat transport through the MWCNT [28, 29] and high anisotropy of the nanotube
therm;
thermal conductivity. Here, we concentrate on the study of a significant component of the
heat transfer in SThM, i.e. the ultimate interface between the MWCNT tip and the sample. Difference in material parameters give rise to the so-called Kapitza thermal resistance [20]. Unlike bulk thermal resistance, Kapitza thermal resistance exists just at the interface between two different materials and does not depend on the thickness. Therefore, it makes a major contribution to thermal resistance of almost any nanoscale system. As such, the knowledge of the Kapitza resistance is crucial to the accurate measurement of materials thermal properties at the nanometer scale. It should be noted that there is very little literature on interfacial resistance involving carbon nanotubes under SThM configuration. For example, L Hu et al. [30] used molecular dynamics approach to study heat transport in CNT embedded in a matrix. H Zhong and coworkers [31] employed the same technique to investigate thermal resistance between overlapping CNTs, while Yann Chalopin et al. found significantly lower thermal conductivity of CNT pellets as compared to individual CNTs [32]. Mingo and Broido [29] studied ballistic heat transport in single-walled CNTs and found higher thermal resistance than thought earlier. While quite insightful, these studies do not directly address the research problem discussed in this paper.
An adequate interpretation of SThM measurements data requires one to account for interface thermal resistance. Unfortunately, direct experimental measurements of the Kapitza resistance are very challenging. Likewise, temperature change and phonon dispersion at the interface, temperature dependence measurements and current flow complicate further the prediction of the Kapitza resistance [33]. Moreover, most of the earlier studies, e.g. [34-37], consider bulk materials, where size effect are expected to play a significant role [28]. Here, we propose a simple theoretical model to estimate the thermal resistance at the interface between the MWCNT tip and the sample under study. Quantum consideration of the heat
3 transfer is explored to account for the submicron lateral dimensions of MWCNTs. The
5 developed is subsequently compared with the experimental results available in the lite
10 2. Methods: Theoretical model
12 It is assumed that the main contribution to the heat transfer near and at the interface is due to
15 bulk acoustic phonons [38,39]. However, the theoretical model, as shown below, is not
17 sensitive to the exact nature of heat carriers and can be expanded to consider other types of
19 carriers. Moreover, generalization for two distinct types of carrier is possible, provided they
21 do not influence each other's behavior.
26 [33]. For instance, the need to consider the interfacial temperature discontinuity, current flow
28 as well as temperature dependence measurements (i.e. realistic phonon dispersion and density
30 of states are required at higher temperatures in the acoustic diffusive model) makes the
32 accurate prediction of the Kapitza resistance challenging. Therefore, the model proposed
An accurate definition of thermal resistance is rather complex, as detailed in the literature
aims at offering a somewhat simplified, but still rigorous approach to address the problem
Let us consider two macroscopic media 1 and 2 in thermal contact and each at a constant
37 outlined above by providing a realistic estimate of the Kapitza resistance. This requires a
39 number of hypotheses described as follows.
45 t t
46 temperature Tt and T2, respectively. Let be the total heat flux per unit area transported
48 by all carriers arriving at the interface from medium 1 and passing into medium 2 (see
50 Figure 1). accounts for all heat carriers having any possible energy. Likewise, 02°*
55 from medium 2 and passing into medium 1. Both fluxes are determined by the material
57 parameters of the system and the temperature of the media which they originate from. The
represents the total heat flux per unit area transported by all carriers arriving at the interface
parame
observable total heat flux from media 1 into media 2 is simply ©12 — 021^ the interfacial thermal resistance p is then defined as:
0i°2t(7'l)-02Olt(7'2)'
Strictly speaking, the value of this interfacial resistance is governed by system involved as well as temperatures T and T2, i.e. p is a function of both T and
AT = 7\ - T2.
Normally, when studying heat transfer on the macroscopic scale, we assume that the temperature changes abruptly at the interface. While that is a natural and useful idealization at the macroscale, it is not applicable at the nanoscale, where interface thickness may be of the same order of magnitude as the characteristic dimensions of other objects under study, and carriers are not fully thermalized. Therefore, we adopt a more careful continuous approach with no singularities in the temperature distribution.
As the system approaches thermal equilibrium (i.e. 7 and T2 approach a given value of T), the change of the interfacial resistance due to varying AT becomes smaller, until it becomes negligible. At the same time, 0*2 and 02°* both approach an equivalent value 0. In practical SThM measurement modes, a high degree of non-equilibrium is detrimental to accurate mapping of the thermal contrast between sample and probe, be it at low or high temperature. Relevant calibration is subsequently adopted to estimate contact resistance [13,25]. Therefore, the thermal resistance at the interface may be calculated using Eq. (1):
p = (£i|<I>)-1. (2)
The value of T can be thought of as the temperature at the interface. Note also, that it makes ence which of the fluxes, 0-J21 or 02°l, is used in Eq. (2), since they are equal under equilibrium state.
e, the thern
10 11 12
20 21 22
3. Results and Discussion 3.1. Heat carriers scattering at the interface
The origin of the interface thermal resistance lies in incident carrier being scattered at the interface. Normally, two pathways for phonon scattering are considered: the acoustic mismatch model, and the diffuse mismatch model [33]. The first one assumes that phonons are governed by continuum acoustics, i.e., phonons are considered as plane waves propagating in the continuous medium, while the interface is assumed perfectly planar. In the diffuse mismatch model, on the other hand, the opposite assumption is made: all the incident phonons are believed to be diffusely scattered at the interface, while correlations at interfaces are assumed to be completely destroyed by diffuse scattering. Hence, the transmission probability is defined solely by the principle of detailed balance and densities of phonon states. In other words, the probability that the phonon will scatter into a given side of the interface is totally independent of where the phonon came from. Instead, the probability of scattering into a given side is proportional to the density of phonon states on that side (Fermi's "golden rule"). Those two mechanisms are illustrated in Figure 1 left and right panels, respectivel
10 11 12
20 21 22
Acoustic mismatch
Media 1
Diffusive mismatch
Interface
Media 2
Figure 1: Two possible pathways of phonon scattering: acoustic mismatch, where phonons behave as planar waves (left) and diffuse mismatch, where all correlations at interface are completely destroyed (right). Possible phonon propagation paths are denoted by arrows.
Figure 2: Close-up Transmission Electron Microscopy (TEM) image of a MWCNT tip (left) juivalent diffraction patterns for each of the four regions (right).
Since the interface between a SThM tip and the sample under study is generally rough on the nanometer and atomic scale, the diffuse mismatch model would be more appropriate: while exact nature of phonon transport along the MWCNT comprises both diffusive and istic transport [13,29], a phonon behavior at the interface, due to random reflections on
the exa
3 irregularities, is assumed to depend solely on phonon energy. This assumption is reinforced
5 by the experimental evidences of amorphous diamond-like carbon layer covering the
7 MWCNT tip (Figure 2). Therefore, the transmission probability p12 of a single phonon from
10 the medium 1 to medium 2 depends on phonon's energy E, but not on its direction (by
12 definition of the diffuse scattering): p12 = p12(E). Since the transmission probability does
14 not depend on phonon polarization, the mode of the phonon is irrelevant in this case.
Therefore, only one mode can be considered. In order to simplify the following calculations,
19 Let 012(E) be the heat flux carried by phonon having energy E going through the interface
21 from medium 1 to medium 2 per unit area. From geometrical considerations, we have
23 012(E) =^^/o2"d0jo7r/2d0sin(0)cos(0)ri(E)Fi(E,T)ai(E)pi2(E), (3)
26 where r1(E) is the carrier propagation speed, F1(E, T) the occupation probability and 01(E)
29 the density of states, while subscript "1" denotes medium 1. An analytical expression is then
31 obtained by solving the double integration shown in Eq. (3).
33 012(E,T) =iv1F1(E,T)0i(E)p12(E). (4)
36 The flux in the opposite direction is given by changing 1^2 in Eq. (4), where the subscript
38 "2" denotes medium 2. The detailed balance consideration states that 012(E) = 021(E) in
40 equilibrium, yielding a relation between the p12 and p21. Moreover, the diffusion scattering
42 means that p21(E) = p11(E), leading to the following relation for the transmission
45 probability:
47 , (E) = ^(^(gT^CE) (5)
50 On the other hand, the total energy flux 012 transported by incident carriers arriving at the
52 interface from medium 1 and passing into medium 2 is
Q™ = F)o"1(F)p12(F)dF.
Substituting Eq. (6) into Eq. (2) leads to a general expression for the thermal interface resistance. For the case considered, a significant simplification can be made. Phonons in both media obey the Bose-Einstein statics with zero chemical potential, i.e. F1(E,T) = F2(E,T) = (exp(E/kT) — 1)"1. For a low energy, the propagation speed can be assumed constant. These considerations lead to the following final expression for the interface
resistance:
0-i = viv2 f_q1(E)Q2(E)E2__(7)
0 AkT2f (v1<j1(E)+v2<j2(E))sinh2(E/2kT) ' ( )
ie density
In order to find a value of the contact thermal resistance, the density of states both in the sample and MWCNT tip must be calculated. This is performed using approach described below.
3.2. Density of states in sample
For simplicity, a uniform substrate is considered where g2(E) = dVk/dE, where Vk is the volume of a sphere containing all wavevectors smaller than k. For a 3D case, this results in
a2(E)=-TTT- (8)
In turn, for a 2D sample with axial energy levels Ei, the density of state is as follows:
°2(E) = ^JiziiE - Ei)H(E - Ed, (9)
where H(x) is the ide step function.
3.3. Density of states in MWCNT
Based on the typical SEM images (Figure 3), the MWCNT tip was modeled as an upside-down sharp truncated cone with a radius R:
R = R0 + kz, (10)
10 11 12
20 21 22
where z is the axial coordinate counted from the small facet upwards, Ro the MWCNT small facet radius, R the MWCNT radius at height z and k the tangent of half of the taper angle
(k = tan(a/2); Figure 3).
Figure 3: SEM of MWCNT as used to enhance a SThM probe tip; a is the taper angle.
Since phonons are confined in the MWCNT but free to travel within it, an infinite potential barrier at the boundary with zero potential inside is assumed. Given an axial symmetry of the problem, cylindrical coordinates (r, 0, z) can be introduced, with z along the MWCNT axis. The Schrodinger equation associated with the phonons takes the form
>oundary condi
— — A0r(r, 0, z) = £0(r, 0, z),
coor coor
with zero boundary conditions at the MWCNT boundary. To solve equation (11) for eigenvalues, the procedure detailed below was adopted. First of all, following the general particle-in-a-box method, the azimuthal contribution can be separated: 0(r, 0, z) = f(r, z) exp(/&0). The equation for f(r, z) than can be expressed in the usual for cylindrical coordinate system form
3 ft2 1 /1 d / d \ 52 | _ ^ fc2 12
5 2m f(r, z) dr V dr\ dz2/ ' 2mr2 '
7 Since boundary conditions mix radial and axial coordinates, further exact separation is
9 impossible. Moreover, the electron diffraction pattern presented in Figure 2 reveal an
11 amorphous carbon layer which is about 23 nm thick, which results in phonons dispersion near
the MWCNT tip being essentially isotropic. Therefore, high phonon anisotropy, typical for
16 CNTs, is no longer valid for the interface region. To overcome this obstacle, we now employ
18 the first order perturbation theory for the region of the taper angle. In order to do this, ^ (r, z)
20 can be represented as a product f(r, z) = rç(rK(z), where rç(r) has a weak z dependence
due to the boundary conditions for r being dependent on z. In order to find rç (r) in the first
25 approximation, Eq. (12) is first solved in the 0th approximation obtained under the assumption
27 that k = 0 and therefore, d2rç(r)/dz2 = 0. Introducing z dependent boundary conditions
29 would then results in d2rç(r)/dz2 ^ 0. Finally, this derivative is substituted into Eq. (12) to
34 presented below.
38 The starting approximation for rç(r) is naturally /|fc|(An,|fe| r/fl), where /|fc| is the Bessel
find the first approximation to the solution. The individual key steps of this procedure are
function of the first kind with index |fc| and An,|fc| is the nth zero of such a function. After
43 substituting Eq. (10) into this expression, the second derivative of ^(r) is calculated and
45 substituted into (12), resulting in the inhomogeneous equation
52 2 — lKl 2 \ / r \ r«0
53 «n—72--r | /in — I + ■
2 fc2 - |fc| A / r \ rfl0 ( r \ 2—p--r l/|fc| (An,|fc| —I + ^-7|fc| + i (An,|fc| —1
Km J v A",|fe| v
1 52<"(z) _ 2m£ fc2
57 <"(z) dz2 ft2 r2'
10 11 12
20 21 22
Note that all the calculations are performed in the first order regarding k2. While Eq. (13) has multiple terms, it would allow for the separation of variables. Moreover, after the separation of variables, we obtain an inhomogeneous second order differential equation with respect to which allows for an exact solution. While the initial solution may look unwieldy, it can be shown that it remains limited when r ^ 0 at any k, i.e. no singularity was introduced due
to approximation used. After simplification, the boundary condition ^(R) =
in the following form:
JikiUR)
, Xn,\k\X , f, X
+ Ri Jm+i{An,m —
be written
J\k\ n,WRT
A is the modified eigenvalue sought. By substitution, the integrand in Eq. (14) can be presented via dimensionless variable, finally obtaining
J\k\(AR)-—2—Ylk\(An,lk\) I J\k\(u)[(k2-k-u2)J\k\(u)+uj\k\+1(u)]udu = 0. (15)
2An,\k\ I
Here, the integral can be calculated via hypergeometric functions. Denoting the whole second term in Eq. (15) as k2P leads to the first order approximation for the energy eigenvalue:
in our approximati
2mR2{A2n'lkl
J\k\ + l{^n,\k\))
Note that in our approximation, the density of states for the radial component of the wave function scales perfectly with spatial dimensions, i.e. Eq. (15) depends on the MWCNT shape only as well as k. The resulting density of states (obtained as a continuum approximation for the discrete energy spectrum) for a single axial mode is presented in Figure 4.
10 11 12
20 21 22
100 150 200 250
e=E/E„
Figure 4: Dimensionless density of states (DoS) versus dimensionless energy (s = E/E0 ) for a single axial mode. E0 = h2 /(2mR%); dimensionless density of states is the number of possible states per dimensionless energy unit.
The calculation of the total density of states takes into account the axial contribution; a typical result is shown in Figure 5. The parameters used are directly related to the MWCNT shown in Figure 3 and are discussed further below.
10 11 12
20 21 22
10 20 30
Energy (zJ)
Figure 5: Total modified density of states (DoS) for the MWCNT presented in Figure 3.
Note that while the single mode density of states is mostly linear with some variations, the total density of states shows the expected close to quadratic shape.
3.4. Experimental verification
In order to validate our theoretical results, extensive experimental and theoretical considerations presented in [27] were used. The experimental results together with the heat conductance model allows for the estimation of the interface thermal resistance between MWCNT enhanced SThM tip and various materials. Timofeeva et al. [27] found the value of the interface thermal resistance between MWCNT enhanced SThM tip and aluminum to be 5x10-9 K m2 W-1 and between the same MWCNT enhanced SThM tip and 3 nm thick graphene flake to around 10-8 K m2 W-1. This value is noticeably higher than those found in ,36] for bulk graphene-metal interface, which illustrates influence of MWCNT etry on its properties. Interestingly Ref. [36] points out that phonon transport is indeed
3 predominant at the interface, thus supporting our model. TEM images and the associated
5 diffraction patterns displayed in Figure 2 A show the 23 nm thick amorphous carbon layer
mentioned above and the transition from ordered structure with sp2 hybridization (region I) to
10 amorphous carbon (region IV). That means that the first 23 nm of the MWCNT from the tip
12 are, in fact, amorphous, most likely the result of the structural modification induced by the
14 cutting the MWCNT with a focused ion beam (heat load) during the SThM tip fabrication.
17 This observation fully justifies the isotropic phonon model presented above.
21 To estimate speed of sound in MWCNT an average density 1300 kg m and elastic modulus
23 63 GPa, were used the data of Ref. [40,41]. This results in ^ « 7 x 103 m/s. For the
25 aluminum substrate, the speed of sound was assumed to be 5*103 m/s. The base of the
28 MWCNT appears to be larger than the tip apex. However, during the experiment, the contact
30 pressure is high enough to ensure that the contact area on sample matches the MWCNT tip
32 apex. After performing the steps outlined in the theoretical model, the final result for the
34 interface thermal resistance was 2.2* 10-9 K m W-1, which is close to the experimental results
39 After repeating the same procedure, the interface thermal resistance was found to be around
-9 2 -1
41 4.2*10 K m2 W This value is about 2 times lower than the experiment data for MWCNT-
43 graphene interface resistance. This difference is most probably explained by an imperfect
45 contact in theMLperimental setup. On the other hand, the value obtained for MWCNT-
48 graphene is significantly higher than the thermal resistance between diamond-diamond
50 (~7.3*10-9 K m2 W-1) and MgO-diamond (~7.5*10-9 K m2 W-1) reported in the literature [43].
52 This is attributable to the lower density of states in both MWCNT and graphene compared to
54 that of bulk 3D materials, even though their acoustic properties are similar [44]. A summary
above. For the graphene substrate, the speed of sound to be 2.1* 104 m/s was considered [42].
of th of th
of the results presented above are given in Table I.
10 11 12
20 21 22
Table I: Interface thermal resistance values for MWCNT-Al andMWCNT-graphene
Interface MWCNT-Al MWCNT- Graphene
K m2 W-1 K m2 W-1
Theory 2.2x10-9 4.2x10-9
Experiment [27] 5.0x10-y 1.0x10-9 (
The model proposed above relies on several assumptions which simplifies the calculation and remove the unknown phenomenological parameters. The deviations observed between experiment and theory may also be explained by the inherent assumptions of the model. For instance, the model predictions should be in better agreement with low temperatures experimental results which are not available. Likewise, an accurate estimation of temperature behavior at the interface at in the bulk material, as well as a realistic phonon dispersion and density of states will also lead to a higher degree of agreement between experiment and theory. Finally, the effects of the probe-sample interface may include few monolayers of water that would be present even if only one of the contacting surfaces is hydrophilic.
Despite this, the model illustrates a realistic approximation which leads to relatively good fit between theoretical and experimental data. The current model deals only with one type of heat carriers, i.e., acoustic phonons, that is nevertheless appropriate for the CNT or graphene like materials where these are dominating thermal conductance. In addition, the model does not appear to strongly depend on the particular material composition of the probe. This suggests that more conventional materials such as Si3N4 can, in principle, be considered under the same framework, by virtue of their similar/comparable geometry. However, the overall thermal conductivity of the probe tips plays a significant performance role in the ensitivity and resolution of the SThM probe.
10 11 12
20 21 22
The model can be further improved to more involved theoretical constructions - if specific experiments can be designed to remove a few of the assumptions made, which is beyond the scope of this paper. Nevertheless, considering a different type of heat carriers, e.g. electrons or optical phonons, will mostly requires adjusting the density of states in the sample, since the heat carrier should obey the same Schrodinger equation in the MWCNT. In turn, accounting for several distinct heat independent carriers should be relatively straightforward, because the heat conductance is additive as long as carrier densities are low enough so that it does not result in an active carrier interaction. However, accounting for several distinct interacting heat carriers is more challenging. While the exact details depend heavily on the nature of the carriers, the perturbation technique might be used to approximate the equivalent Kapitza resistance.
From a theoretical standpoint, surface phonons might provide an interesting type of heat carrier. The surface density of states is normally much lower than that of the bulk, and the mean fee path of the carrier is also lower. Hence, the different behavior in the density of states from surface to bulk suggests a dissimilar dependence of thermal resistance on the probe geometry, i.e. for extremely thin probes (several nm), the contribution of surface phonons is likely to be significant.
4. Conclusion
We have developed a theoretical model capable of predicting, with a good approximation, the value of thermal resistance of the interface between a MWCNT and a specimen under study. The model accounts for the dimensions, geometrical shape of the MWCNT and the sample as well as the properties of the phonons. The model proposed is based on fundamental quantum rties of heat carriers in confined in MWCNT as well as universal thermodynamic
3 considerations, which makes it a realistic approximation although the model can be enh
5 further if combined iteratively with a systematic set of complex experiments.
10 Experimental validation of the model is challenging because of the difficulty
11 12 13
anced anced
y to measure y to measure
than with MWCNT, the probe is enhanced with a solid semiconductor nanorod [45], the
12 accurately SThM interface thermal resistance values. The actual contact area between the
14 apex of the MWCNT tip and the sample is somewhat hard to measure accurately. However,
17 the results predicted by the model are in fairly good agreement with published experimental
19 data. This is illustrated by the interfacial thermal resistance values for bulk 3D aluminum and
21 2D graphene flake samples. For instance, the values predicted by the model, approximately
23 2x10-9 and 4x10-9 K m2 W-1 for MWCNT-Al and MWCNT-graphene, interfaces,
25 respectively, are of the same order of magnitude as the equivalent experimental data. If rather
30 model can also apply with an adjusted set of material parameters. However, it is important to
32 note that the deviations between theory and experiment are essentially due to the boundary
34 conditions applied to achieve a simplified model. In particular, building in the model, realistic
39 of which require extensive experimental data both at room and low temperature) will yield a
41 higher agreement between theory and experiment.
46 5. Acknowledgments
48 We acknowledge the support from the EPSRC grants EP/G015570/1 and EP/G017301/1,
50 EPSRC-NSF grant EP/G06556X/1 and EU FP7 grants: FUNPROB (GA-269169),
55 We thank the Royal Academy of Engineering/LeverHulme Trust for the award of a Senior
57 ^^^^fcResearch Fellowship to DAZ.
estimates of the phonon dispersion and density of states, interfacial temperature behavior (all
NanoEmbrace (GA-316751), GRENADA (GA-246073) and QUANTIHEAT (GA-604668).
10 11 12
20 21 22
[8] [9]
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