# Thermal Conductivity of a Monolayer of Exfoliated Graphite Nanoplatelets Prepared by Liquid-Liquid Interfacial Self-Assembly

Authors: Jinglei Xiang; Lawrence T. Drzal
Journal: Journal of Nanomaterials
 (2010)

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## Abstract

A monolayer film composed of exfoliated graphite nanoplatelets (xGnPs) was extracted from a chloroform-water interface and supported on a glass substrate. The nanoplatelets are interconnected at the edges without overlapping forming a very densely packed structure with uniform thickness. Micro-Raman spectroscopy with a 50 mW 532 nm laser generating heat at the center of a xGnP sample was used to probe the thermal conductivity of the xGnP monolayer at different power levels. The Raman G peak shift of graphite was used to record the local temperature rise in the monolayer. The cross-sectional area of heat conduction is determined by the thickness of individual nanoplatelets. A UV-Vis spectrometer was used to measure the absorption of light by the monolayer. Depending on the interface density, the thermal conductivities are around 380 W/m K and 290 W/m K for monolayers with average particle size of 10μm and 5 μm, respectively.


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## Body

## 1. Introduction

Exfoliated graphite nanoplatelets (xGnPs) are produced from exfoliating the acid intercalated graphite by rapid thermal treatments. Nanoplatelets of various sizes from 1μm to 10 μm can be obtained through controlled size reduction which includes sonication and ball milling. The thickness of individual platelets is within 5–20 nm depending on the intercalation as well as the exfoliation processes. These nanoplatelets prove very effective in improving the mechanical, electrical, and barrier properties of polymer nanocomposites [1–3]. However, the enhancement in thermal conductivity is lower than expected in nanocomposites mostly due to the large thermal interface resistance between the matrix and the nanofiller [4–7].In this paper, the thermal transport properties of xGnP particles were investigated and the effect of thermal interface resistance on nanoscale heat transfer was discussed. Earlier work has shown that graphene, a one-atom-thick sheet of covalently bonded carbon atoms with sp2 hybridization packed in a honeycomb crystal lattice, supports 2D phonon propagation that gives rise to a remarkably high thermal conductivity in the basal plane of the graphene [8]. It is difficult to use conventional techniques such as 3ω, laser flash, and thermal bridge to measure thermal conductivity of this very delicate system such as single-layer graphene without causing physical damage during sample preparation and handling. Confocal micro-Raman spectroscopy, a nondestructive, optical technique has been successfully used to extract thermal properties of thin films [9, 10]. Balandin et al. successfully measured thermal conductivity of a mechanically cleaved single layer graphene ribbon with Raman spectroscopy that uses the Raman G peak of graphene as a probe for local temperature determination at the laser spot. The measured thermal conductivity of graphene is 4400–5300 W/m K [11].  Similarly with Raman spectroscopy, Faugeras et al. used temperature readout obtained from the intensity ratio of Stokes to anti-Stokes signal to study the thermal properties of a large circular-shaped graphene membrane also obtained from micro-mechanical cleavage and they concluded thermal conductivity to be 600 W/m K [12]. These single layer graphenes were all suspended over a microtrench with their edges connecting to either bulk graphite or gold heat sinks. Recently, Cai et al. reported a CVD grown graphene monolayer suspended or supported over a holey Au/SiN substrate. The thermal conductivity of graphene was measured by monitoring the graphene G peak shift with laser heating. The measured conductivities for suspended and supported graphene are 2500 + 1100/−1050 W/m K and 370 + 650/−320 W/m K, respectively [13]. It was surmised that the huge difference is due to the phonon leakage and scattering at the substrate-graphene interface. More recently, Ghosh et al. investigated the dimensional crossover of thermal transport in few-layer graphene (FLG) using the same technique, they showed that the room temperature thermal conductivity changes from 2800 W/m K to 1300 W/m K as the number of atomic planes in FLG increases from 2 to 4 [14].Despite the numerous literature that focus on the thermal conductivity of graphene and few-layer graphene, there is no report that investigates the thermal conductivity of a monolayer film consisting of individual graphite nanoplatelets (which consists of multiple layers of graphene). Here, a monolayer film of xGnP was extracted from a liquid-liquid interface following the procedures reported by Biswas and Drzal [15] and deposited on a substrate for thermal conductivity measurement by confocal Raman spectroscopy that shed light on the effectiveness of those highly conductive nanoplatelets in heat conduction. In a monolayer, individual nanoplatelet is lying flat on the glass substrate and densely connected to each other resembling a percolated conductive network in a nanocomposite except that the nanoparticles are highly ordered with well-defined contacts instead of a random distribution of particles with uncontrolled contacts. Heat spreads in a 2D plane in the monolayer and the efficiency of heat conduction of such monolayers was studied.


## 2. Experimental Details

### 2.1. Materials

Exfoliated graphite nanoplatelets were prepared by exfoliating the acid intercalated natural graphite purchased from Asbury Graphite Mills, Inc, NJ. A microwave exfoliation process developed at MSU produces exfoliated material superior to conventional thermal treatments because of the fast heating rate and high energy density [2]. The volume of exfoliated graphite is over 500 times that of the initial volume occupied by graphite intercalated compounds. The surface area was measured by Brunauer-Emmet-Teller (BET) using N2 adsorption at 77 K. Two kinds of exfoliated nanoplatelets produced from different graphite sources were measured and their surface areas were determined to be 20–40 m2/g and 200–220 m2/g, and are referred to as low surface area (LSA) xGnP and high surface area (HSA) xGnP in later discussion. Chloroform, used for liquid-liquid interface extraction of a monolayer of xGnP was purchased from J. T. Baker and used directly without purification.


### 2.2. Extraction of a Monolayer xGnP at the Liquid-Liquid Interface

A monolayer of densely packed xGnP particles was prepared on the glass substrate following the procedure by Biswas and Drzal [15]. To summarize the process, graphite nanoplatelets were dispersed in chloroform at 0.1 mg/mL. The supernatant of the suspension was obtained by 10 min centrifugation at 5000 rpm. Then water was added to the supernatant solution followed by high power sonication. The xGnP particles then quickly adsorbed at the chloroform-water interface and a monolayer was extracted on a glass slide. The samples were dried in air and then annealed at 250 C for 2 h. The xGnP coated region is 3 cm × 2.5 cm.


### 2.3. UV/Vis Spectrum

The optical transparency of the monolayer coated glass slide was measured by UV-Vis spectrometer (Perkin Elmer Lambda 900). The amount of light transmitted was measured and the light absorbed by the xGnP monolayer was calculated from  transmission  spectrum.


### 2.4. Scanning Electron Microscopy

A JEOL JSM-7500F scanning electron microscope was used to examine the morphology of the monolayer on the glass slide. The sample was not gold coated and the imaging was done at 5 kV at a working distance of 4.5 mm.


### 2.5. Confocal Raman Spectroscopy

A LabRAM ARAMIS laser Raman spectrometer (Horiba Scientific) with a 532 nm 50 mW DPSS laser was used to probe the G band of xGnP particles. To determine the temperature dependence of G peak, an INSTEC (STC 200) heating stage was used to heat the sample and a very low laser power was used to collect the Raman signal to avoid laser-induced heating. Monolayers of both LSA and HSA xGnP were prepared on the microscopic glass slides for subsequent measurements. The laser was focused on the center of the monolayer and a filter that controls different amount of laser coming through the objective lens was used to induce different levels of heating in the samples. A D1, D06, D03, D0 filter was used in each experiment that corresponds to 10%, 25%, 50%, and 100% laser power. Both the x50 and x100 objective lenses were used for each sample measured. The laser spot sizer0 was 0.24 μm and 0.19 μm for the x50 and x100, respectively, which were determined using r0=λ/πNA, where NA is the numerical aperture of 0.9 and 0.75 for the x100 and x50 objectives.


## 2.1. Materials

Exfoliated graphite nanoplatelets were prepared by exfoliating the acid intercalated natural graphite purchased from Asbury Graphite Mills, Inc, NJ. A microwave exfoliation process developed at MSU produces exfoliated material superior to conventional thermal treatments because of the fast heating rate and high energy density [2]. The volume of exfoliated graphite is over 500 times that of the initial volume occupied by graphite intercalated compounds. The surface area was measured by Brunauer-Emmet-Teller (BET) using N2 adsorption at 77 K. Two kinds of exfoliated nanoplatelets produced from different graphite sources were measured and their surface areas were determined to be 20–40 m2/g and 200–220 m2/g, and are referred to as low surface area (LSA) xGnP and high surface area (HSA) xGnP in later discussion. Chloroform, used for liquid-liquid interface extraction of a monolayer of xGnP was purchased from J. T. Baker and used directly without purification.


## 2.2. Extraction of a Monolayer xGnP at the Liquid-Liquid Interface

A monolayer of densely packed xGnP particles was prepared on the glass substrate following the procedure by Biswas and Drzal [15]. To summarize the process, graphite nanoplatelets were dispersed in chloroform at 0.1 mg/mL. The supernatant of the suspension was obtained by 10 min centrifugation at 5000 rpm. Then water was added to the supernatant solution followed by high power sonication. The xGnP particles then quickly adsorbed at the chloroform-water interface and a monolayer was extracted on a glass slide. The samples were dried in air and then annealed at 250 C for 2 h. The xGnP coated region is 3 cm × 2.5 cm.


## 2.3. UV/Vis Spectrum

The optical transparency of the monolayer coated glass slide was measured by UV-Vis spectrometer (Perkin Elmer Lambda 900). The amount of light transmitted was measured and the light absorbed by the xGnP monolayer was calculated from  transmission  spectrum.


## 2.4. Scanning Electron Microscopy

A JEOL JSM-7500F scanning electron microscope was used to examine the morphology of the monolayer on the glass slide. The sample was not gold coated and the imaging was done at 5 kV at a working distance of 4.5 mm.


## 2.5. Confocal Raman Spectroscopy

A LabRAM ARAMIS laser Raman spectrometer (Horiba Scientific) with a 532 nm 50 mW DPSS laser was used to probe the G band of xGnP particles. To determine the temperature dependence of G peak, an INSTEC (STC 200) heating stage was used to heat the sample and a very low laser power was used to collect the Raman signal to avoid laser-induced heating. Monolayers of both LSA and HSA xGnP were prepared on the microscopic glass slides for subsequent measurements. The laser was focused on the center of the monolayer and a filter that controls different amount of laser coming through the objective lens was used to induce different levels of heating in the samples. A D1, D06, D03, D0 filter was used in each experiment that corresponds to 10%, 25%, 50%, and 100% laser power. Both the x50 and x100 objective lenses were used for each sample measured. The laser spot sizer0 was 0.24 μm and 0.19 μm for the x50 and x100, respectively, which were determined using r0=λ/πNA, where NA is the numerical aperture of 0.9 and 0.75 for the x100 and x50 objectives.


## 3. Results and Discussions

The formation of a stable monolayer of xGnP particles that were closely connected without overlapping was driven by the gain in interfacial energy that enables the nanoplatelets to be adsorbed to the oil-water interface [16–18]. Since these graphite nanosheets are highly hydrophobic on their basal planes while the oxygen functional groups on the edges render them hydrophilic, it is expected that a meniscus will be generated around the particles and “like” menisci overlap to generate large attractive capillary force to form a close packed structure at the liquid-liquid interface [18, 19]. While the magnitude of this lateral capillary force is negligible for spherical particles with diameter less than 10 μm [20], Bowden et al. showed that, for planar shaped particles at the liquid-liquid interface, the lateral capillary force is quite significant even for particles with thicknesses of few nanometers [18]. Depending on the starting material and intercalation and exfoliation conditions, the average thickness of individual nanoplatelets may vary which will be reflected in the optical transparency measurement.Figures1(a) and 1(b) shows the SEM images of the two glass substrates coated with LSA and HSA xGnP monolayers. From SEM micrographs, individual nanoplatelets come into contact with each other at the edges (indicated by arrows in the figures) so well that there is no noticeable gap left between them thanks to the regular geometry of the platelet edges. In some portions of the glass substrate, gaps can be observed between nanoplatelets, but every single one is connected to the adjacent particle without overlapping for both LSA and HSA monolayers which proves the strong edge interaction among nanoplatelets. With multiple inspection of different parts of the monolayers, it is concluded that the LSA monolayer has an average particle size of around 5–10 μm. In the HSA monolayer, however, more gaps exist among individual platelets and the average size of the nanoplatelet is within 1–5 μm. It is obvious from the SEM images that the interface density in the HSA monolayer is higher than the LSA monolayer.(a) SEM image of a LSA xGnP monolayer film supported on a glass substrate. (b) SEM image of a HSA xGnP monolayer film supported on a glass substrate.
(a)(b)


### 3.1. Optical Transmission and Absorption of xGnP Monolayers

The optical transparency of those monolayers was determined by scanning a blank glass slide and a xGnP coated slide to eliminate the effect of reflective loss from the slides. Since the reflection of the graphite nanosheets is negligibly small [21], it is not accounted for in this calculation. The amount of light absorbed was calculated by subtracting the light transmitted through the glass slide: A(absorption)=1-T(transmission). Figure 2 shows the percentage transmission of light for both the LSA and HSA monolayers from 350 nm to 1000 nm. The optical transparency for the LSA and HSA monolayer is 20.5% and 49.6%, respectively, at 532 nm. The absorption is then calculated to be 79.5% and 50.4% for the LSA and HSA monolayers. The fact that the HSA xGnP went through better intercalation and exfoliation contributes to the production of much thinner nanoplatelets, which boosts the optical transparency. The thickness of the individual HSA xGnP and LSA xGnP were previously measured to be around 10 nm and 20 nm, respectively, by AFM [15].Figure 2
Percent transmission of light for LSA and HSA monolayers scanning from 350 nm to 1000 nm. Inset is the photo of LSA and HSA coated monolayers supported on glass substrates.


### 3.2. Confocal Micro-Raman Spectroscopy Analysis

The laser-induced heating of the graphite nanoplatelets causes a red shift of the G band because of bond softening. The G band shift is believed to be linearly dependent on the temperature of the sample [22]. A heating stage that heats individual graphite nanoplatelets at a very low laser power  was used to obtain a temperature calibration profile. Two measurements were taken at each temperature up to 473K. The slope of the temperature dependence of G peak was determined to be −0.021 cm−1/K shown in Figure 3.  However, in the monolayer samples, heat absorbed by the graphite nanoplatelets propagates to the edge of the nanoplatelet and the large thermal interface resistance is expected to scatter the phonons (lattice vibrations). This is in stark contrast to constructing a graphite or Au heat sink around an individual nanoplatelets. A phonon being transported along the monolayer encounters numerous interfaces that reduce the heat conduction efficiency. It is necessary to focus the laser on the center of the monolayer to ensure that heat spreads uniformly in a circular geometry. In fact, if the laser beam was focused on the edge of the sample, the local temperature will increase much higher due to the presence of a boundary that impedes heat dissipation. During the experiment, the edges of the monolayer sample was kept at ambient temperature at around 300 K, additional heat sinks were not used because of the huge surface area of the monolayer compared with the laser spot size. The Raman G-peak shift was collected at different laser power levels (i.e., 100%, 50%, 25% and 10%) with the selection of a proper filter. Figures 4(a) and 4(b) show the G-peak shift at different power levels for both the LSA and HSA monolayers. The presence of oxygen functional groups on the edges of xGnP are likely to alter the carbon bonding from sp2 to sp3 type, and this gives rise to a D band in the Raman signal (1350 cm−1). Due to the difference in the size of the nanoplatelets in LSA and HSA monolayer, the HSA sample has more edge areas exposed to the laser and this provides a possible explanation to a higher D band observed in HSA samples.Figure 3
Raman G band shift of xGnP with temperature and linear curve fitting.(a) Raman G peak shift of the LSA monolayer at different laser power levels. (b) Raman G peak shift of the HSA monolayer using different laser power levels.
(a)(b)


### 3.3. Calculation of the Thermal Conductivity of  xGnP Monolayers

The temperature rise at the center of the monolayer caused by the Gaussian-shaped laser heating is proportional to the absorbed laser power and inversely proportional to the efficiency of heat conduction. The volumetric laser heating isqv=q0/t  exp(-r2/r02) with r0 being the laser spot size, r being the radial position measured from the center of the laser beam. Here, q0 is the absorbed laser power per unit area at the laser spot and t is the thickness of monolayer which is the same as the thickness of an individual nanoplatelets. The glass substrate (κ=1 W/m K) interacts with the phonons and causes phonon leakage which reduces the thermal conductivity. The temperature distribution of the supported monolayer can be obtained by the steady state form of the heat diffusion equation in cylindrical coordinate following Cai’s approach [13]:
(1)1rddr(rdTdr)-gκt(T-Ta)+qvκ=0,
where g is the interfacial thermal conductance per unit area between the monolayer and the substrate as well as the air molecules. κ is the thermal conductivity of the monolayer, Ta is the ambient temperature. From the Gaussian-shaped laser heating, the total absorbed power by the monolayer Q is
(2)Q=t∫qv2πrdr=q0πr02.
Let θ=T-Ta and z=(g/κt)1/2r, (1) can be converted to a nonhomogeneous Bessel’s equation:
(3)∂2θ∂z2+1z∂θ∂z-θ=-q0gexp⁡⁡(-z2z02).
The solution to the above equation is
(4)θ(z)=C1I0(z)+C2K0(z)+θp(z),
where I0(z) and K0(z) are the zero-order modified Bessel functions of the first and second kind. The particular solution θp(z) can be obtained using the variation of parameters method and is found to depend on q0/g [23]. The temperature rise in the monolayer measured by Raman laser is
(5)θm=∫0∞θ(z)exp⁡⁡(-z2/z02)zdz∫0∞exp⁡⁡(-z2/z02)zdz.The measured thermal resistance defined asR=θm/Q can be calculated from (2) and (5). Given the temperature dependence of Raman G peak, the temperature rise θm and absorbed power Q is found to be linearly related as is shown in Figures 5(a) and 5(b) and the slope of which yields RLSA equal to 1.12×104 K/W and 1.61×104 K/W, respectively, for the LSA monolayer with x50 and x100 objectives. Similarly, RHSA equals 2.31×104 K/W and 3.54×104 K/W for the HSA monolayer with x50 and x100 objectives. The ratio of the two R values is found to be dependent only on g/κ. With one of the R values measured with either objective, g2/κ can be further obtained. After a curve fitting procedure for g/κ and g2/κ, it is found that g≈50 MW/m2K and κLSA≈380 W/m K for the LSA monolayer while g≈30 MW/m2K and κHSA≈290 W/m K for the HSA monolayer. Due to the difference in xGnP size, the HSA monolayer has a higher interface density than the LSA monolayer which might cause the reduction in overall efficiency of heat conduction due to strong phonon scattering at the particle interfaces.(a) Local temperature of an individual xGnP at the center of a LSA monolayer versus the absorbed laser power with x50 and x100 objectives. The solid lines represent the linear curve fittings. (b) Local temperature of an individual xGnP at the center of a HSA monolayer versus the absorbed laser power with x50 and x100 objectives. The solid lines represent the linear curve fittings.
(a)(b)


## 3.1. Optical Transmission and Absorption of xGnP Monolayers

The optical transparency of those monolayers was determined by scanning a blank glass slide and a xGnP coated slide to eliminate the effect of reflective loss from the slides. Since the reflection of the graphite nanosheets is negligibly small [21], it is not accounted for in this calculation. The amount of light absorbed was calculated by subtracting the light transmitted through the glass slide: A(absorption)=1-T(transmission). Figure 2 shows the percentage transmission of light for both the LSA and HSA monolayers from 350 nm to 1000 nm. The optical transparency for the LSA and HSA monolayer is 20.5% and 49.6%, respectively, at 532 nm. The absorption is then calculated to be 79.5% and 50.4% for the LSA and HSA monolayers. The fact that the HSA xGnP went through better intercalation and exfoliation contributes to the production of much thinner nanoplatelets, which boosts the optical transparency. The thickness of the individual HSA xGnP and LSA xGnP were previously measured to be around 10 nm and 20 nm, respectively, by AFM [15].Figure 2
Percent transmission of light for LSA and HSA monolayers scanning from 350 nm to 1000 nm. Inset is the photo of LSA and HSA coated monolayers supported on glass substrates.


## 3.2. Confocal Micro-Raman Spectroscopy Analysis

The laser-induced heating of the graphite nanoplatelets causes a red shift of the G band because of bond softening. The G band shift is believed to be linearly dependent on the temperature of the sample [22]. A heating stage that heats individual graphite nanoplatelets at a very low laser power  was used to obtain a temperature calibration profile. Two measurements were taken at each temperature up to 473K. The slope of the temperature dependence of G peak was determined to be −0.021 cm−1/K shown in Figure 3.  However, in the monolayer samples, heat absorbed by the graphite nanoplatelets propagates to the edge of the nanoplatelet and the large thermal interface resistance is expected to scatter the phonons (lattice vibrations). This is in stark contrast to constructing a graphite or Au heat sink around an individual nanoplatelets. A phonon being transported along the monolayer encounters numerous interfaces that reduce the heat conduction efficiency. It is necessary to focus the laser on the center of the monolayer to ensure that heat spreads uniformly in a circular geometry. In fact, if the laser beam was focused on the edge of the sample, the local temperature will increase much higher due to the presence of a boundary that impedes heat dissipation. During the experiment, the edges of the monolayer sample was kept at ambient temperature at around 300 K, additional heat sinks were not used because of the huge surface area of the monolayer compared with the laser spot size. The Raman G-peak shift was collected at different laser power levels (i.e., 100%, 50%, 25% and 10%) with the selection of a proper filter. Figures 4(a) and 4(b) show the G-peak shift at different power levels for both the LSA and HSA monolayers. The presence of oxygen functional groups on the edges of xGnP are likely to alter the carbon bonding from sp2 to sp3 type, and this gives rise to a D band in the Raman signal (1350 cm−1). Due to the difference in the size of the nanoplatelets in LSA and HSA monolayer, the HSA sample has more edge areas exposed to the laser and this provides a possible explanation to a higher D band observed in HSA samples.Figure 3
Raman G band shift of xGnP with temperature and linear curve fitting.(a) Raman G peak shift of the LSA monolayer at different laser power levels. (b) Raman G peak shift of the HSA monolayer using different laser power levels.
(a)(b)


## 3.3. Calculation of the Thermal Conductivity of  xGnP Monolayers

The temperature rise at the center of the monolayer caused by the Gaussian-shaped laser heating is proportional to the absorbed laser power and inversely proportional to the efficiency of heat conduction. The volumetric laser heating isqv=q0/t  exp(-r2/r02) with r0 being the laser spot size, r being the radial position measured from the center of the laser beam. Here, q0 is the absorbed laser power per unit area at the laser spot and t is the thickness of monolayer which is the same as the thickness of an individual nanoplatelets. The glass substrate (κ=1 W/m K) interacts with the phonons and causes phonon leakage which reduces the thermal conductivity. The temperature distribution of the supported monolayer can be obtained by the steady state form of the heat diffusion equation in cylindrical coordinate following Cai’s approach [13]:
(1)1rddr(rdTdr)-gκt(T-Ta)+qvκ=0,
where g is the interfacial thermal conductance per unit area between the monolayer and the substrate as well as the air molecules. κ is the thermal conductivity of the monolayer, Ta is the ambient temperature. From the Gaussian-shaped laser heating, the total absorbed power by the monolayer Q is
(2)Q=t∫qv2πrdr=q0πr02.
Let θ=T-Ta and z=(g/κt)1/2r, (1) can be converted to a nonhomogeneous Bessel’s equation:
(3)∂2θ∂z2+1z∂θ∂z-θ=-q0gexp⁡⁡(-z2z02).
The solution to the above equation is
(4)θ(z)=C1I0(z)+C2K0(z)+θp(z),
where I0(z) and K0(z) are the zero-order modified Bessel functions of the first and second kind. The particular solution θp(z) can be obtained using the variation of parameters method and is found to depend on q0/g [23]. The temperature rise in the monolayer measured by Raman laser is
(5)θm=∫0∞θ(z)exp⁡⁡(-z2/z02)zdz∫0∞exp⁡⁡(-z2/z02)zdz.The measured thermal resistance defined asR=θm/Q can be calculated from (2) and (5). Given the temperature dependence of Raman G peak, the temperature rise θm and absorbed power Q is found to be linearly related as is shown in Figures 5(a) and 5(b) and the slope of which yields RLSA equal to 1.12×104 K/W and 1.61×104 K/W, respectively, for the LSA monolayer with x50 and x100 objectives. Similarly, RHSA equals 2.31×104 K/W and 3.54×104 K/W for the HSA monolayer with x50 and x100 objectives. The ratio of the two R values is found to be dependent only on g/κ. With one of the R values measured with either objective, g2/κ can be further obtained. After a curve fitting procedure for g/κ and g2/κ, it is found that g≈50 MW/m2K and κLSA≈380 W/m K for the LSA monolayer while g≈30 MW/m2K and κHSA≈290 W/m K for the HSA monolayer. Due to the difference in xGnP size, the HSA monolayer has a higher interface density than the LSA monolayer which might cause the reduction in overall efficiency of heat conduction due to strong phonon scattering at the particle interfaces.(a) Local temperature of an individual xGnP at the center of a LSA monolayer versus the absorbed laser power with x50 and x100 objectives. The solid lines represent the linear curve fittings. (b) Local temperature of an individual xGnP at the center of a HSA monolayer versus the absorbed laser power with x50 and x100 objectives. The solid lines represent the linear curve fittings.
(a)(b)


## 4. Conclusions

A densely packed monolayer of xGnP was successfully extracted from a chloroform-water interface driven by interfacial energy minimization and attractive capillary interactions. Confocal micro-Raman spectroscopy was used as a heater and a thermometer to probe the heat conduction efficiency of monolayers made from xGnP of different sizes and thicknesses. The presence of interfaces in the monolayers significantly reduces the thermal conductivity in this assembly of graphene nanoplatelets by almost an order of magnitude lower than the highest reported value for an individual nanoplatelets measured by the same technique. However, the in-plane thermal conductivities of both monolayers are still high with negligible cross plane conduction making it a promising candidate for applications that require fast 2D heat dissipation.



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*Source: 481753-2010-12-05.xml*