Optimizing the thermoelectric performance of graphene nano-ribbons without degrading the electronic properties

Article metrics


The enhancement of thermoelectric figure of merit ZT requires to either increase the power factor or reduce the phonon conductance, or even both. In graphene, the high phonon thermal conductivity is the main factor limiting the thermoelectric conversion. The common strategy to enhance ZT is therefore to introduce phonon scatterers to suppress the phonon conductance while retaining high electrical conductance and Seebeck coefficient. Although thermoelectric performance is eventually enhanced, all studies based on this strategy show a significant reduction of the electrical conductance. In this study we demonstrate that appropriate sources of disorder, including isotopes and vacancies at lowest electron density positions, can be used as phonon scatterers to reduce the phonon conductance in graphene ribbons without degrading the electrical conductance, particularly in the low-energy region which is the most important range for device operation. By means of atomistic calculations we show that the natural electronic properties of graphene ribbons can be fully preserved while their thermoelectric efficiency is strongly enhanced. For ribbons of width M = 5 dimer lines, room-temperature ZT is enhanced from less than 0.26 to more than 2.5. This study is likely to set the milestones of a new generation of nano-devices with dual electronic/thermoelectric functionalities.


During the last decade, thermoelectricity has been the subject of renewed interest because of its expected contribution to current and future energy issues1, 2. The conversion capacity of a thermoelectric material is reflected by the dimensionless figure of merit ZT, which was first introduced by Ioffe3,4,5. The best materials used to date in practice are compounds of Bismuth and Lead such as Bi2Te3, Bi2Se3, PbTe and their alloys, with a ZT~16. However, due to the slow advances in their efficiency, the toxicity of elements such as Se and Pb and also the limited resources in Tellurium7, 8, the development of these materials in thermoelectricity remains limited.

In 1993, the studies of Hicks and Dresselhaus suggested that nanostructuring materials should offer better thermoelectric performance due to quantization effects9, 10. Following these primary researches, a number of works have been carried out to target high thermoelectric performances in nanoscale-designed materials2, 6, 11. Among those studies, graphene and other 2D nano-materials have shown to be promising candidates for thermoelectric applications owing to their extraordinary electronic properties and especially the high flexibility they offer in tuning electronic and thermal properties, which can lead to large ZT, depending on material and structure design6, 11.

In fact, 2D graphene has naturally poor thermoelectric properties because of its very high thermal conductivity and its gapless characteristic which induces extremely small Seebeck coefficients6, 11,12,13. Interestingly, it has been shown that graphene is one of the most versatile materials in terms of thermoelectric properties that can be tuned from low to very high performance by nanostructuring6. First, graphene nano-ribbons (GNRs) can have higher ZT compared to 2D sheets due to a bandgap opening induced by finite size effects, which results in larger Seebeck coefficients. The first investigation of thermoelectricity in ribbons was proposed by Ouyang and Guo in 200914. They showed that ZT of an armchair ribbon with 15 dimer lines along the width is enhanced compared to that of 2D graphene, though not exceeding 0.1. In a previous study, we pointed out that the maximum value ZT = 0.35 can be obtained for the narrowest armchair ribbon with a width of three dimer lines15.

To explore the thermoelectric properties of graphene with the aim of achieving higher ZT, different strategies based on more sophisticated structures than pristine nanoribbons have been proposed. For instance, mixed structures made of armchair and zigzag sections have been shown to exhibit ZT max ~1 thanks to the mismatch of phonon modes and the resonant tunneling of electrons between the different sections16, 17. In refs 15 and 18, graphene or BN stubs (flakes) were attached onto a graphene ribbon to generate interface phonon scattering. In the case of BN flakes attached to a GNR, ZT = 0.81 was reported for a ribbon of width M = 5 with even ZT = 1.48 in the presence of vacancies15. Vacancy or edge roughness disorder was also proved to be relevant to reduce the thermal conductance and achieve high thermoelectric performance19, 20. Another interesting idea is to introduce nano-pores in the active region. In graphene ribbons with the presence of nano-pores, ZT can be dramatically enhanced up to 5 in some specific configurations21,22,23. Superlattice structures are also common designs to provide electronic transmissions with a step profile, which was proven to be associated with high ZT 22, 24, 25. Chevron-type graphene ribbons including 14C isotope doping were shown to have ZT up to 3.25 at 800 K and about 2 at room temperature thanks to strongly reduced thermal conductance25. Graphene/h-Boron Nitride (G/BN) super-lattices have been also recently proposed to achieve high ZT in straight ribbons7, 26, 27.

Although these strategies eventually yield high figures of merit ZT, we observe that a reduction of the phonon conductance is usually accompanied by a degradation of the electrical conductance which is likely to reduce the electronic performance of devices. Even in the case of Chevron-type ribbons with a fraction of 14C isotopes25, mini-bandgaps are induced by the superlattice structure yielding a lower electrical conductance compared to that of the straight ribbon counterpart.

Since electronic properties of graphene are among its most intriguing and tunable ones28, 29, it is strongly desirable to enhance its thermoelectric performance by decreasing its phonon conductance while keeping the electronic conduction properties unaltered.

In this article, on the basis of atomistic simulation, we show that by introducing appropriate disorders in armchair GNRs, very high thermoelectric performance can be achieved while fully preserving their natural excellent electronic properties. Indeed, the phonon conductance can be modulated strongly by introducing either 14C isotopes in a 12C lattice or vacancies. Isotopes reveal their effect mainly in the high-frequency region of the phonon spectrum while vacancies impact both the high and low-frequency regions. Additionally, if vacancy positions correspond to the sites of low electron density, the electronic conduction is shown to be unaffected. Combining all these effects, a maximum value of ZT can be tuned from 0.26 to values larger than 2.5 at room temperature for a ribbon width of M = 5 dimer lines.


We study armchair GNRs as sketched in Fig. 1. Figure 1a presents a pristine (without disorder) structure made of carbon 12C and each unit cell contains two chain lines L 1 and L 2 . The active region includes N A unit cells and the length can be calculated as L A  = 3a 0  × N A  − a 0 where a 0  = 0.142 nm is the distance between two nearest-neighbor atoms. The width of the ribbon is characterized by the number of dimer lines M along the y direction. Since each unit cell contains 2 M atoms, the total number of atoms in the active region is 2 M × N A . Figure 1b illustrates the cases in which the active region is either doped by 14C isotopes or/and includes vacancies.

Figure 1

Schematic view of devices made of armchair graphene nano-ribbons. (a) Pristine 12C structure without disorders, the width of ribbons is characterized by the number of dimer lines M, and the active region contains N A unit cells with the length L A . (b) The active region includes a fraction of isotope 14C doping and a vacancy at position m = 6.

In this study, 14C isotopes were considered to appear randomly in the active region. We designed different configurations with distinct disorder positions but with the same density of disorder. Actually, for a given isotope doping density, ten different configurations were considered and eventually the average value for the transmission was taken as \(\langle {T}_{e(p)}\rangle =(\sum _{i=1}^{10}{{T}^{i}}_{e(p)})/10\). Then these averaged transmissions were used for the computation of electronic and thermal conductances. As shown later, the electronic properties remain unchanged by varying positions of scatterers along the device length, so that the notations of all electronic quantities were kept unchanged and without the average symbol 〈〉. The average phonon conductance is noted as 〈K p 〉. Moreover, although the Boltzmann transport equation can describe transport properties of both electrons and phonons, it actually considers the dynamics of particles classically in which all quantum interferences between multiple scattering events are ignored, this formalism is therefore not relevant for considering nano-structures in the presence of defects30. Hence we have chosen the Landauer-Büttiker formalism in combination with tight binding models that can properly include the presence of defects at the atomic level. The details on the Tight-Binding and Force-Constant models used for electrons and phonons, respectively, and on the computational methodology may be found in Supplemental Material.

Isotopes: phonon scatterers transparent to electrons

Since 12C and 14C isotopes have the same electronic configuration and only differ in their mass, their random distribution generates phonon scattering without affecting the electronic properties. Thus the band structure, the electrical conductance and other electronic quantities are the same as those of pristine structures.

In Fig. 2, we display the room temperature electronic and thermoelectric properties of pristine GNRs. Figure 2a shows the contributions of electrons to the different thermoelectric parameters, including the electrical conductance, the Seebeck coefficient and the electron thermal conductance for armchair ribbon of width M = 5. It is worth noting that this ribbon belongs to the group M = 3p + 2 which has been found to be semi-metallic (gapless) in the first nearest-neighbor (1NN) calculations31, 32. Using third nearest-neighbor (3NN) calculation, it is noticeable from the inset that the transmission is equal to zero near the energy E = 0, which actually indicates the presence of a small energy gap in this structure. This result is in agreement with the predictions of ab initio calculations33. Thanks to the existence of a bandgap, the Seebeck coefficient is found to be significant and as high as 0.45 mV.K−1, i.e. higher than the value of 80 µV.K−1 in 2D graphene13.

Figure 2

Electronic and thermoelectric properties of a pristine structure of width M = 5 at room temperature. (a) The electrical conductance, the Seebeck coefficient, the electron thermal conductance and the power factor plotted as functions of chemical potential. The inset reports the transmission spectrum. (b) The electronic and total figure of merit ZT e and ZT. (c) Maximum value of figure of merit ZT max and K p in different ribbons displayed as a function of M. In (a) and (b) the vertical dotted line indicates the position of ZT max .

In Fig. 2a, the power factor P = G e .S 2 is plotted in solid black line. The peak of the power factor is located at the crossing point of the Seebeck coefficient and the electrical conductance that is not the position of the peak of the Seebeck coefficient. The figures of merit ZT and ZT e calculated by including or not, respectively, the lattice thermal conductance K p are displayed in Fig. 2b. Without the phonon contribution, the figure of merit ZT e is much higher and reaches a maximum value of 12.93. However, the full ZT only reaches 0.26. The substantial difference between ZT e and ZT reflects that the conductance K p contributes considerably to the total thermal conductance. Figure 2a shows that K e at ZT max is about 0.039 nW.K−1 whereas K p can take the value of 0.809 nW.K−1 for M = 5, as shown in Fig. 2c. K p is thus about 20.7 times larger than the electron thermal conductance. Hence the phonon conductance is the predominant one and has to be reduced to enhance the thermoelectric performance.

In Fig. 2c, K p and ZT max are also displayed for other ribbon widths. It can be observed that ZT reduces with increasing ribbon width since the phonon conductance increases. Narrow ribbons should therefore be considered for a higher ZT. Although thinner ribbons with M = 3 or 4 exhibit larger ZT, these ribbons are still difficult to synthesize in practice. The narrowest ribbon ever achieved had a thickness of M = 5 and was successfully synthesized by growing armchair GNRs in ultrahigh vacuum34.

To aim at the highest thermoelectric performance with a possible practical achievement, we hence focus on the case M = 5 in the course of the following discussion, unless otherwise stated.

To enhance ZT, 14C isotopes have been inserted as phonon dopants in the active region in order to generate phonon scattering and suppress K p . To determine the most effective doping density to alter the phonon conductance, we plot the evolution of 〈K p 〉 as a function of the 14C doping percentage in Fig. 3. In Fig. 3a, it can be observed that 〈K p 〉 seems to reach a minimum for a density of about 70%. This apparent imbalance between 12C and 14C densities come from the fact that the leads are made of pure 12C graphene. To understand the effective range of frequency that isotopes affect, we plot the transmitted phonon spectrum in Fig. 3b. The spectrum of transmitted phonon energy is derived from the product of the transmission and the distribution function g p: T p (ω).g p(ω,T). As can be seen in Fig. 3b, all structures with different densities of 14C are significantly impacted in the high frequency range. The 0 to 350 cm−1 frequency range remains weakly changed. For higher doping concentrations (dotted blue and dashed-dotted green lines), isotopes have an increasing influence in the low-frequency range and even completely suppress the vibrational modes of high frequency from 1200 cm−1 to 1600 cm−1 resulting in a decreased phonon conductance. The spectrally selective impact of isotopes on graphene phonon thermal conductance has not been previously highlighted so far35,36,37.

Figure 3

(a) Average phonon conductance as a function of 14C concentration. (b) Phonon energy spectrum versus frequency defining the frequency range impacted by isotopes. Data provided for M = 5, N A  = 30 (L A  = 12.64 nm) nanoribbons.

Now, we analyze the effect of the device length and temperature. In Fig. 4a we plot the phonon conductance 〈K p 〉 as a function of temperature for different device lengths ranging from N A  = 30 (L A  = 12.64 nm) to N A  = 100 (L A  = 42.46 nm), for an isotope density of 70%. Compared to the case of pristine pure 12C ribbon (black solid line), as expected and as already observed in other cases of disorder in GNRs19, increasing the device length in the presence of isotope disorder clearly tends to reduce the thermal conductance. For instance, at T = 300 K, 〈K p 〉 is equal to 0.809 nW.K−1 in the pristine structure but drops to 0.52 nW.K−1 in a disordered device of length L A  = 12.64 nm and even to 0.49 nW.K−1 and 0.44 nW.K−1 for devices of lengths 21.16 nm and 42.46 nm, respectively.

Figure 4

(a) Average phonon conductance as a function of temperature for different device lengths with 70% isotope doping. The solid black corresponds to the pristine structure. The inset reports the distribution function g p(ω,T) at different temperatures. (b) The inverse of the phonon thermal conductivity as a function of 1/L A . Symbols are numerical results and the solid lines are the fitting curves. Data provided for M = 5 nanoribbons.

However, we clearly see also that at low temperature below 100 K the effect of isotope disorder is negligible whatever the device length. This behavior is consistent with the fact that at low temperature the width of the distribution function g p(ω,T) covers only the low-frequency range (see inset of Fig. 4a), and with the previous results (Fig. 3b) showing that the transmission of such low-frequency modes is not impacted by isotope disorder.

To reveal the evolution of the phonon conductance with respect to the increase of the length and also exploit the potential of low phonon conductance in long devices, we consider with more care the length-dependence of 〈K p 〉 under the effect of disorder by introducing Matthiessen’s rule which can be expressed in this context as38

$$\frac{1}{\tau }=\frac{1}{{\tau }_{lattice}}+\frac{1}{{\tau }_{disorders}},$$

where τ is the total relaxation rate, τ lattice and τ disorders are the relaxation rate due to the lattice, i.e. phonon-phonon scattering, and to disorders, respectively. Within the ballistic regime, τ lattice  ≈ ∞ whereas in the presence of disorders \({\tau }_{disorders}\sim {L}_{A}/\Lambda \) where Λ refers to the phonon mean free path. If we assume this mean free path to be independent of length, \(1/\tau \sim 1/{L}_{A}\). It has been shown also that the phonon thermal conductivity \({\sigma }_{p}\sim \tau \) 38, and thus we have \(1/{\sigma }_{p}\sim 1/{L}_{A}\). Since the thermal conductivity is proportional to 〈K p 〉.L A , the quantity 1/(〈K p 〉.L A ) is expected to be a linear function 1/L A . This quantity is plotted in Fig. 4b as a function of 1/L A for different temperatures. The quasi-linear behavior is indeed observed and the results reveals that the conductivity at very long device length converges to a finite value independent on the temperature.

All these results strongly suggest that to further reduce the phonon conductance by degrading the phonon transmission in the low-frequency range, another scattering mechanism should be added to that induced by isotope disorder. We will see in the next section that vacancies appropriately positioned in the ribbon can be the appropriate scatterers in this respect.

Introduction of 3i vacancies

Since isotopes cannot significantly suppress the phonon transmission at low frequencies, we investigate here the effect of vacancies for further reduction of the phonon conductance. We assume that vacancies can be controlled experimentally using focused electron beam techniques39, 40. To minimize the effect of vacancies on the natural electronic performance, we first examine carefully the charge distribution over lattice sites.

It has been shown that the electronic properties of armchair GNRs vary for different groups of number of dimer lines M. We display in Fig. 5a the electron density at each site of lines L 1 and L 2 in a unit cell of pristine ribbons. The values M = 12, 13, 14 characterizes the three GNR width of groups M = 3p, 3p + 1 and 3p + 2, respectively, where p is an integer number. From one edge to the center of a ribbon, the panels of Fig. 5a show that the charge at position m = 3i is the lowest compared to other ones. For groups 3p and 3p + 1, the ratio between highest and lowest charge is about 10 and 24, which means that the charge at positions 3i contributes to about 10% and 5%, respectively, to the total charge. Interestingly, this ratio is about 2.1 × 103 for the group M = 3p + 2. Our investigation reveals that in this group the charge at positions 3i only contributes about 0.05% of the total charge. This observation suggests that vacancies should be localized at position m = 3i from the edges to minimize their effect on the electronic properties. More specifically, vacancies appearing at positions 3i in the structures M = 3p + 2 should not change at all the electronic properties due to extremely low charge at these lattice sites.

Figure 5

(a) Spatial distribution of the electron density in pristine ribbons of width M = 12 (group 3p), M = 13 (group 3p + 1) and M = 14 (group 3p + 2), charge is minimal at positions m = 3i from one edge, especially in the group 3p + 2. (b) Pictures of the effect of vacancies on the electrical conductance at different positions for 3 groups of ribbon widths.

To verify the change of the electronic properties in the presence of vacancies, we have investigated all possible cases and summarized them in a picture displayed in Fig. 5b. Since positions m = 3i + 1 and 3i + 2 have high charge localization, any vacancies at these positions will cause a dramatic change in the electrical conductance, e.g., a strong reduction of G e in the full range of energies as indicated in both panels of Fig. 5b. For the cases of vacancies at positions m = 3i, ribbons belonging to groups M = 3p and 3p + 1 still exhibit a smaller electrical conductance compared to that of the pristine structure as seen in the left panel of Fig. 5b.

Interestingly, ribbons of group M = 3p + 2 with vacancies at positions m = 3i fully preserve their electrical conductance in low-energy region, which is the most relevant range for device operation. Due to the resulting unchanged electrical conductance, the Seebeck coefficient and the power factor, the thermoelectric performance also remains unaltered with the appearance of 3i vacancies. To support the validity of these predictions from tight binding calculation in the presence of vacancies, we carried out first principles calculations of some typical cases, including the lattice relaxation effects due to vacancies. The most important results can be found in Supplemental Material.

To consider the effect of 3i vacancies on phonon transport, we only consider a 2% random vacancy density in a 3i line. Since each dimer line in the active region contains 2 × N A atoms, 2% 3i vacancies/line results in only 0.04 × N A 3i vacancies/line. Hence, for the structure having N A  = 50 unit cells (21.16 nm), only 2 vacancies were introduced. This small density of vacancies should thus not significantly distort the structure.

In Fig. 6a, the average phonon conductance of four structures is plotted as a function of temperature for the sake of comparison: the solid black line corresponds to the pristine structure, whereas the dashed, dotted and dashed-dotted lines refer to isotopes (70%) only, vacancies in line 3 (2%) only and to the combination of the two effects, respectively. Vacancies lead to a stronger reduction of the phonon conductance compared to the case of the sole isotope doping. Moreover, vacancies reveal their effect in the low-temperature range. This result is reflected by the phonon spectrum shown in Fig. 6b. The effect of vacancies is observed even at low frequencies (dotted blue line) in comparison to the case of isotope doping (dashed red line). Combining the two effects, the phonon conductance is further reduced (dash-dotted green line). The phonon spectra in Fig. 6b suggests that in the presence of vacancies, increasing the length of devices tends to suppress the transmission of phonon modes in the full range of frequencies. A very low phonon conductance is thus expected in long devices including both isotope disorder and vacancies.

Figure 6

(a) Average phonon conductance of four devices: pristine (solid black), with 70% isotope only (dashed red), 2% 3i vacancies only (dotted blue) and for both types of disorder (dashed-dotted green). (b) Spectrum functions of different disordered structures. Data provided for M = 5 nanoribbons.

To explore the combined effect of isotopes and vacancies in long devices, we have also plotted in Fig. 7a the inverse of the average phonon thermal conductivity versus the inverse of the device length. The numerical results were obtained for devices with length from N A  = 50 (L A  = 21.16 nm) to N A  = 1400 (L A  = 596.26 nm). The open symbol curves are numerical data while the solid lines are fitting curves. It can be seen that as in the case involving only isotope doping in Fig. 4b, we again observe a convergence here, however the numerical curves are not strictly linear. Actually, this non-linear behavior can be understood from the fact that the phonon mean free path Λ may be not constant but length-dependent due to a competition between boundary scattering at side and axial boundaries. A change in length can cause a distortion in the total scattering and thus affect Λ. The mean free path is almost constant when the device is long enough because of the dominant side scattering.

Figure 7

(a) The inverse of the thermal conductivity as a function of 1/L A . (b) Average phonon conductance as a function of the active length L A . In the both panels, symbols are numerical results and the solid lines are fitting/analytical results. In Figure (b), the filled symbols are additional numerical results for comparison with results predicted by solid lines. Data provided for M = 5 nanoribbons.

Since longer devices lead to lower thermal conductivity (and thus lower conductance), a higher thermoelectric performance is expected in long devices. To calculate ZT, we need to specify 〈K p 〉 in those long devices. The computation of Green’s functions in long devices is very expensive so employing a fitting function is convenient to predict results in very long devices. We found that the fitting results are better with a quadratic fitting in the form of \(1/({K}_{p}{L}_{A})={p}_{1}/{{L}_{A}}^{2}+{p}_{2}/{L}_{A}+{p}_{3}\). The quadratic term can be considered as a correction due to the length-dependence of the phonon mean free path, p 2 reflects the reduction rate of the phonon conductivity over the device length and it is actually the phonon thermal resistance and p 3 is obviously the inverse of the conductivity in infinitely-long devices. The set of fitting parameters {p 1, p 2, p 3} for 100 K, 300 K, 400 K and 800 K are given in Table S2 (see in the Supplementary material). We also applied a similar fitting for the results in Fig. 4b and the parameters are shown in Table S1. An analytical expression for the phonon conductance can subsequently be retrieved with \(\langle {K}_{p}\rangle ={L}_{A}/({p}_{1}+{p}_{2}.{L}_{A}+{p}_{3}.{{L}_{A}}^{2})\). The numerical (open symbols) and analytical (solid) results of the phonon conductance are plotted in Fig. 7b. The analytical results with the fitting parameters agree well with the numerical results. The analytical results and their extrapolation show that the phonon conductance is continually reduced and tends to saturate in very long devices.

Enhancement of figure of merit ZT

In the presence of only 2% vacancies at positions 3i, all electronic properties of M = 5 ribbons remain unchanged, i.e. the same as in Fig. 2a. With the reduction of the phonon conductance due to both isotopes and vacancies as discussed above, the figure of merit is likely to be enhanced.

In Fig. 8a we show ZT at 300 K as a function of the chemical energy µ for the device of length L A  = 212.86 nm for two cases (1) with 70% of isotopes and (2) with 70% of isotopes and 2% of additional 3i vacancies. With only isotope doping, ZT reaches a maximum value of 0.61 at either µ = −0.23 eV or 0.03 eV. In the presence of additional vacancies, ZT is pushed strongly up to 1.52. The two peaks of ZT are now located at µ = −0.22 eV and 0.02 eV. In these devices, the combined effect of both isotopes and vacancies thus leads to a ZT about 2.5 times larger than the one in the case of isotope disorder only.

Figure 8

(a) Figure of merit ZT as a function of chemical energy demonstrated for an isotope doped device of length 212.86 nm with and without additional vacancies 3i. (b) ZT max as a function of the device length, except for the black lines corresponding to isotopes only, other curves refer to of the combined effects of 70% isotope doping plus 2% 3i vacancies, the symbols are numerical data and the solid lines are the fitting curves. Data provided for M = 5 nanoribbons.

In Fig. 8b, open symbols correspond to numerical results while solid lines refer to ZT resulting from the analytical formula of 〈K p 〉. Except for the cases of isotope doping only (open triangles and solid black lines), other results are shown for the cases when the two types of disorder are applied simultaneously. As observed from the black and green lines, the total effect is always larger than the effect of the sole isotope doping for a given length.

The additional effect of vacancies is also length-dependent, i.e. ZT max substantially increases with the increase of the device length L A . The behavior at different temperatures is however different, i.e. the slope of the curves is larger when temperature varies from 100 K to 400 K. At 100 K, ZT max increases by 0.43 from 0.41 at L A  = 21.16 nm to 0.84 at L A  = 298.06 nm. In this range of lengths, at 300 K and 400 K, ZT max increases by 1.12 (from 0.66 to 1.78) and 1.25 (from 0.76 to 2.01), respectively. However the slope drops for T = 800 K since ZT slowly increases from 0.48 for L A  = 21.16 nm to 0.56 for L A  = 85.06 nm and reaches 0.69 at 298.06 nm and then saturates. At L A  = 596.3 nm and T = 400 K, ZT max reaches a value of about 2.5 and the analytical results using the fitting form of 〈K p 〉 predict that ZT max  ≥ 3 can be reached in longer devices if phonon-phonon scattering can still be neglected.

It is worth to note that ZT max at temperature T = 800 K is smaller than that at lower temperatures. This is a surprise since 〈K p 〉 is almost not dependent on temperature in very long devices as seen in Fig. 7b. It means that at higher temperatures, higher ZT are expected because ZT is proportional to T. Actually, this result can be understood if we pay attention to a quantity that is less important at lower temperatures in the total thermal conductance, which is the electron thermal conductance K e .

In Fig. 9, we compare the electron and phonon conductances of the device of length L A  = 596.26 nm for a set of different temperatures. As can be seen, the electron thermal conductance K e (at ZT max ) increases exponentially with the increase of temperature, i.e., K e is about 0.0116 nW.K−1 at 100 K, but at 300 K it contributes up to 0.0261 nW.K−1 into the total thermal conductance. This value even jumps up to 0.503 nW.K−1 at 800 K. Although K e at ZT max for T < 800 K is still smaller than K p of the pristine structures, it shows that in the structure with isotopes and vacancies, due to the dramatical reduction of 〈K p 〉, K e becomes larger than 〈K p 〉 at high temperatures, i.e., K e is predominant over 〈K p 〉 for T ≥ 450 K. At 800 K, K e is much larger than 〈K p 〉 and becomes the leading term therefore reducing the thermoelectric performance. These results suggest that the device performance are optimal in the medium range of temperature 300 to 400 K, in which K e remains smaller than 〈K p 〉.

Figure 9

Comparison between the phonon and electron thermal conductances at positions of ZT max for different temperatures. Data provided for M = 5 and N A  = 1400 (L A  = 596.26 nm) nanoribbons.

Since structures including isotope disorder and 3i vacancies yield a drastic drop of the phonon conductance, we try now to explore this effect for larger ribbon widths, which are more accessible in practice. In Fig. 10 we show results of ZT max for a ribbon of width M = 11 dimer lines. The open symbols and solid lines are the numerical results and the results using 〈K p 〉 fitting for the system of 50% doping 14C and 5% vacancies m = 6. Since in the ribbon M = 11, the bandgap is smaller than in the ribbon M = 5, the device reaches the best performance at lower temperature, that is around 300 K instead of 400 K as observed in the case M = 5. For this device, ZT max reaches about 0.68 for the length of 170.3 nm at 300 K. ZT > 1 can be achieved for the devices of length >500 nm. Actually, ZT > 1 can be obtained even in short devices if we introduce more vacancies in other lines 3i. The filled triangular purple point is the result obtained for the device of length 170.3 nm when we have introduced 5% vacancies also in line m = 3 and m = 9 together with vacancies in line m = 6. The resulting figure of merit ZT is about 1.07 at room temperature and would be higher for longer devices.

Figure 10

ZT max as a function of the device length for the case of a larger ribbon with M = 11. The open symbols and solid lines are numerical data and fitting curves for the case of 50% isotope doping and 5% vacancies in the m = 6 line. The filled symbol is the numerical results of the device with 50% isotope doping and 5% vacancies in lines m = 3, 6, 9.


We have introduced a new concept yielding the enhancement of the thermoelectric figure of merit via thermal conductance reduction without degrading the electronic performance. We firstly showed that isotope disorder strongly suppress transmission of high frequency phonons. We then established a picture showing the effect of vacancy positions on the electronic properties. It came out that in position 3i in armchair nanoribbons of width M = 3p + 2, vacancies do not alter the electrical conductance and the Seebeck coefficient while yielding a strong reduction in the transport of low frequency phonons.

The ribbons of width M = 5 in the presence of both isotope disorder and 3i vacancies have shown a dramatic improvement of figure of merit with a maximum value of ZT larger than 2.5 in long devices of lengths larger than 600 nm. Interestingly, these devices manifest their best performance in the medium temperature range from 300 K to 400 K.

We also demonstrated that larger ribbons of width M = 11 can achieve ZT > 1 thanks to isotope and vacancy engineering. These results can motivate the development of a new generation of nanodevices with dual thermoelectric/electronic functionalities.


In this work we employed a Tight Binding (TB) model up to the third nearest neighbor (3NN) interactions including overlap matrices for electron study33, 41. A Force Constant (FC) model involving up to the four nearest neighbor interactions was also used to investigate phonon properties42. Green’s functions formalism43 was applied for transport examinations of both electrons and phonons. Thermoelectric quantities were calculated by Landauer-Onsager’s approach44. The detail can be found in the Supplementary material.


  1. 1.

    Zheng, X. F., Liu, C. X., Yan, Y. Y. & Wang, Q. A review of thermoelectrics research - Recent developments and potentials for sustainable and renewable energy applications. Renew. Sustain. Energy Rev. 32, 486–503, doi:10.1016/j.rser.2013.12.053 (2014).

  2. 2.

    Heremans, J. P., Dresselhaus, M. S., Bell, L. E. & Morelli, D. T. When thermoelectrics reached the nanoscale. Nat. Nanotechnol. 8, 471–473, doi:10.1038/nnano.2013.129 (2013).

  3. 3.

    A F Ioffe. Energetic basis of thermoelectrical cells from semiconductors. Acad. Sci. USSR, Moscow (in Russia) (1950).

  4. 4.

    Goupil, C. Thermodynamics of Thermoelectricity. Intechopen.Com 275–292 (2011).

  5. 5.

    Zlatic, V. & Hewson, A. New materials for thermoelectric applications: theory and experiment. (Springer, 2011).

  6. 6.

    Dollfus, P., Nguyen, V. H. & Saint-Martin, J. Thermoelectric effects in graphene nanostructures. J. Phys. Condens. Matter 27, 133204, doi:10.1088/0953-8984/27/13/133204 (2015).

  7. 7.

    Algharagholy, L. A. et al. Tuning thermoelectric properties of graphene/boron nitride heterostructures. Nanotechnology 26, 475401, doi:10.1088/0957-4484/26/47/475401 (2015).

  8. 8.

    Guo, Y. et al. Flexible and thermostable thermoelectric devices based on large-area and porous all-graphene films. Carbon N. Y. 107, 146–153, doi:10.1016/j.carbon.2016.05.063 (2016).

  9. 9.

    Hicks, L. D. & Dresselhaus, M. S. Effect of quantum-well structures on the thermoelectric figure of merit. Phys. Rev. B 47, 12727–12731, doi:10.1103/PhysRevB.47.12727 (1993).

  10. 10.

    Hicks, L. D. & Dresselhaus, M. S. Thermoelectric figure of merit of a one-dimensional conductor. Phys. Rev. B 47, 16631–16634, doi:10.1103/PhysRevB.47.16631 (1993).

  11. 11.

    Bonaccorso, F. et al. 2D materials. Graphene, related two-dimensional crystals, and hybrid systems for energy conversion and storage. Science (80-.). 347, 1246501 (2015).

  12. 12.

    Balandin, A. A. et al. Superior thermal conductivity of single-layer graphene. Nano Lett. 8, 902–907, doi:10.1021/nl0731872 (2008).

  13. 13.

    Zuev, Y. M., Chang, W. & Kim, P. Thermoelectric and magnetothermoelectric transport measurements of graphene. Phys. Rev. Lett. 102, 96807, doi:10.1103/PhysRevLett.102.096807 (2009).

  14. 14.

    Ouyang, Y. & Guo, J. A theoretical study on thermoelectric properties of graphene nanoribbons. Appl. Phys. Lett. 94, 263107, doi:10.1063/1.3171933 (2009).

  15. 15.

    Tran, V.-T., Saint-Martin, J. & Dollfus, P. High thermoelectric performance in graphene nanoribbons by graphene/BN interface engineering. Nanotechnology 26, 495202, doi:10.1088/0957-4484/26/49/495202 (2015).

  16. 16.

    Mazzamuto, F. et al. Enhanced thermoelectric properties in graphene nanoribbons by resonant tunneling of electrons. Phys. Rev. B 83, 235426, doi:10.1103/PhysRevB.83.235426 (2011).

  17. 17.

    Li, K. M., Xie, Z. X., Su, K. L., Luo, W. H. & Zhang, Y. Ballistic thermoelectric properties in double-bend graphene nanoribbons. Phys. Lett. Sect. A Gen. At. Solid State Phys 378, 1383–1387 (2014).

  18. 18.

    Xie, Z. X. et al. Enhancement of thermoelectric properties in graphene nanoribbons modulated with stub structures. Appl. Phys. Lett. 100, 10–14 (2012).

  19. 19.

    Sevinçli, H. & Cuniberti, G. Enhanced thermoelectric figure of merit in edge-disordered zigzag graphene nanoribbons. Phys. Rev. B 81, 113401, doi:10.1103/PhysRevB.81.113401 (2010).

  20. 20.

    Mazzamuto, F., Saint-Martin, J., Nguyen, V. H., Chassat, C. & Dollfus, P. Thermoelectric performance of disordered and nanostructured graphene ribbons using Green’s function method. J. Comput. Electron. 11, 67–77, doi:10.1007/s10825-012-0392-0 (2012).

  21. 21.

    Chang, P. H. & Nikolić, B. K. Edge currents and nanopore arrays in zigzag and chiral graphene nanoribbons as a route toward high-ZT thermoelectrics. Phys. Rev. B - Condens. Matter Mater. Phys. 86, 1–5, doi:10.1103/PhysRevB.86.041406 (2012).

  22. 22.

    Yan, Y., Liang, Q. F., Zhao, H., Wu, C. Q. & Li, B. Thermoelectric properties of one-dimensional graphene antidot arrays. Phys. Lett. Sect. A Gen. At. Solid State Phys. 376, 2425–2429 (2012).

  23. 23.

    Hossain, M. S., Al-Dirini, F., Hossain, F. M. & Skafidas, E. High performance graphene nano-ribbon thermoelectric devices by incorporation and dimensional tuning of nanopores. Scientific Reports 5, 11297, doi:10.1038/srep11297 (2015).

  24. 24.

    Mahan, G. D. & Sofo, J. O. The best thermoelectric. Proc. Natl. Acad. Sci. USA 93, 7436–7439, doi:10.1073/pnas.93.15.7436 (1996).

  25. 25.

    Sevinçli, H., Sevik, C., Caın, T. & Cuniberti, G. A bottom-up route to enhance thermoelectric figures of merit in graphene nanoribbons. Sci. Rep. 3, 1228, doi:10.1038/srep01228 (2013).

  26. 26.

    Yang, K. et al. Enhanced thermoelectric properties in hybrid graphene/boron nitride nanoribbons. Phys. Rev. B - Condens. Matter Mater. Phys. 86, 1–8, doi:10.1103/PhysRevB.86.045425 (2012).

  27. 27.

    Vishkayi, S. I., Tagani, M. B. & Soleimani, H. R. Enhancement of thermoelectric efficiency by embedding hexagonal boron-nitride cells in zigzag graphene nanoribbons. J. Phys. D. Appl. Phys. 48, 235304, doi:10.1088/0022-3727/48/23/235304 (2015).

  28. 28.

    Tran, V. T., Saint-Martin, J. & Dollfus, P. Large on/off current ratio in hybrid graphene/BN nanoribbons by transverse electric field-induced control of bandgap. Appl. Phys. Lett. 105, 73114, doi:10.1088/0957-4484/26/49/495202 (2014).

  29. 29.

    Marmolejo-Tejada, J. M. & Velasco-Medina, J. Review on graphene nanoribbon devices for logic applications. Microelectronics J. 48, 18–38, doi:10.1103/PhysRevLett.117.176602 (2016).

  30. 30.

    Torres, L. E. F. F., Roche, S. & Charlier, J. C. Introduction to Graphene-Based Nanomaterials: From Electronic Structure to Quantum Transport. (Cambridge University Press, 2014).

  31. 31.

    Nakada, K., Fujita, M., Dresselhaus, G. & Dresselhaus, M. Edge state in graphene ribbons: Nanometer size effect and edge shape dependence. Phys. Rev. B. Condens. Matter 54, 17954–17961, doi:10.1103/PhysRevB.54.17954 (1996).

  32. 32.

    Son, Y. W., Cohen, M. L. & Louie, S. G. Energy gaps in graphene nanoribbons. Phys. Rev. Lett. 97, 216803, doi:10.1103/PhysRevLett.97.216803 (2006).

  33. 33.

    Cresti, A. et al. Charge transport in disordered graphene-based low dimensional materials. Nano Res. 1, 361–394, doi:10.1007/s12274-008-8043-2 (2008).

  34. 34.

    Kimouche, A. et al. Ultra-narrow metallic armchair graphene nanoribbons. Nat. Commun. 6, 10177, doi:10.1038/ncomms10177 (2015).

  35. 35.

    Jiang, J.-W. et al. Isotopic effects on the thermal conductivity of graphene nanoribbons: localization mechanism. Arxiv:1007.5358V1 54314, 9–13 (2010).

  36. 36.

    Hu, J., Schiffli, S., Vallabhaneni, A., Ruan, X. & Chen, Y. P. Tuning the thermal conductivity of graphene nanoribbons by edge passivation and isotope engineering: A molecular dynamics study. Appl. Phys. Lett. 97, 1–4, doi:10.1021/nl403773f (2010).

  37. 37.

    Scuracchio, P., Dobry, A., Costamagna, S. & Peeters, F. M. Tuning the polarized quantum phonon transmission in graphene nanoribbons. Nanotechnology 26, 305401, doi:10.1088/0957-4484/26/30/305401 (2015).

  38. 38.

    Bera, C. et al. Thermoelectric properties of nanostructured Si(1−x)Ge(x) and potential for further improvement. J. Appl. Phys. 108, 124306 (2010).

  39. 39.

    Rodriguez-Manzo, J. A. & Banhart, F. Creation of individual vacancies in carbon nanotubes by using an electron beam of 1 A^0 diameter. Nano Lett. 9, 2285–2289, doi:10.1021/nl900463u (2009).

  40. 40.

    Robertson, A. W. et al. Spatial control of defect creation in graphene at the nanoscale. Nat. Commun. 3, 1144, doi:10.1038/ncomms2141 (2012).

  41. 41.

    Reich, S., Maultzsch, J., Thomsen, C. & Ordejón, P. Tight-binding description of graphene. Phys. Rev. B 66, 1–5, doi:10.1103/PhysRevB.66.035412 (2002).

  42. 42.

    Wirtz, L. & Rubio, A. The phonon dispersion of graphite revisited. Solid State Commun. 131, 141–152, doi:10.1016/j.ssc.2004.04.042 (2004).

  43. 43.

    Lewenkopf, C. H. & Mucciolo, E. R. The recursive Green’s function method for graphene. J. Comput. Electron. 12, 203–231, doi:10.1007/s10825-013-0458-7 (2013).

  44. 44.

    D’Agosta, R. Towards a dynamical approach to the calculation of the figure of merit of thermoelectric nanoscale devices. Phys. Chem. Chem. Phys. 15, 1758–1765, doi:10.1039/c2cp42594g (2013).

Download references


This work was supported by the TRANSFLEXTEG EU thermoelectric project.

Author information

V.-T.T. designed the structures and performed the calculations. V.-T.T., J.S.-M., P.D., and S.V. discussed the results and wrote the manuscript. All authors approved the manuscript.

Correspondence to Van-Truong Tran or Sebastian Volz.

Ethics declarations

Competing Interests

The authors declare that they have no competing interests.

Additional information

Publisher's note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Electronic supplementary material

Rights and permissions

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Commons license and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/.

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Further reading


By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.