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Boundary-engineering in nanostructures has the potential to dramatically impact the development of materials for high- efficiency conversion of thermal energy directly into electricity. In particular, nanostructuring of semiconductors can lead to strong suppression of heat transport with little degradation of electrical conductivity. Although this combination of material properties is promising for thermoelectric materials, it remains largely unexplored. In this work, we introduce a novel concept, the directional phonon suppression function, to unravel boundary-dominated heat transport in unprecedented detail. Using a combination of density functional theory and the Boltzmann transport equation, we compute this quantity for nanoporous silicon materials. We first compute the thermal conductivity for the case with aligned circular pores, confirming a significant thermal transport degradation with respect to the bulk. Then, by analyzing the information on the directionality of phonon suppression in this system, we identify a new structure of rectangular pores with the same porosity that enables a four-fold decrease in thermal transport with respect to the circular pores. Our results illustrate the utility of the directional phonon suppression function, enabling new avenues for systematic thermal conductivity minimization and potentially accelerating the engineering of next-generation thermoelectric devices.
Understanding heat transport in the presence of nanoscale boundaries is of paramount significance for many applications, including thermoelectrics1,2, thermal rectifiers3 and thermal dissipators4. When the dominant phonon mean free path (MFP) Λ approaches the characteristic length scale Lc of a material, classical phonon size effects lead to a decrease in thermal transport5. This regime is effectively described by the Knudsen number, defined as the ratio Kn=Λ/Lc. For example, first-principles calculations of silicon show that half of the heat is carried by phonons with MFPs larger than one micron6,7, supporting the strong phonon suppression observed in porous materials with microscale pores8. In addition, very low thermal conductivities have been measured in many nanostructures, including nanoporous materials8,9,10,11,12,13,14, nanowires15,16 and thin films17, corroborating the use of such material systems for thermoelectric applications.
The thermoelectric figure-of-merit in semiconductors is defined as ZT=σS2T/κ, where σ is the electrical conductivity, S is the Seebeck coefficient, κ is the lattice thermal conductivity and T the temperature. The numerator of ZT (the “power factor”) is generally maximized at relatively high carrier concentrations, so that the average electron MFP is on the order of a few nanometers18. Consequently, a properly engineered nanostructure can significantly decreases κ with little effect on σ, yielding an increase in ZT. Despite many attempts at minimizing thermal transport in nanostructures, however, thermal transport optimization is still largely unexplored, primarily due to practical experimental limitations and a lack of systematic engineering approaches.
In this work, we address the latter by introducing a novel concept, the directional phonon suppression function S(Λ, Ω), that describes the suppression of phonons with a given MFP Λ and direction within arbitrary geometries. By taking into account phonons travelling both along straight lines and through multiple phonon-boundary scattering events, S(Λ, Ω) turns out to be a powerful tool for tuning thermal transport in complex nanostructures. We employ this approach to optimize thermal transport in Si-based nanoporous materials. We first compute the thermal conductivity, κ, of a material system composed of a circular pores in a square lattice, finding significant heat transport degradation with respect to the bulk. Then, we use the information provided by S(Λ, Ω) to identify a new structure, based on rectangular pores, that exhibits κ as small as 1Wm−1k−1, well below the amorphous silicon limit (1.8Wm−1K−1)19. As our engineering approach can be applied to any combination of material and geometry, it paves the way to high-throughput search of ultra-low thermal conductivity materials.
While the methodology developed in this work is applicable to nanostructures with arbitrary materials and shapes, for the sake of clarity we describe our model specifically in relation to porous Si. The first step for computing heat transport in the presence of nanoscale boundaries is calculation of the thermal conductivity of the corresponding bulk material, which we denote κbulk. With no loss of generality, throughout the text we consider an isotropic bulk MFP distribution of a thermally isotropic material, Kbulk(Λ), which is related to κbulk via
where f(Ω)4π is the angular average (4π)−1∫4πf(Ω)dΩ and is a versor described in terms of the polar angle ϕ and the azimuthal angle θ,
As , Eq. 1 reduces to the well-known formula . The term Kbulk(Λ) is calculated via density functional theory6,7; for Si at room temperature, we obtain κbulk≈155Wm−1k−1, in agreement with previous work20.
In porous materials, the volume removal has a degrading effect on heat flow. Furthermore, if the characteristic length Lc of the structure is comparable with the MFPs of heat-carrying phonons, size effects take place and the thermal conductivity is further suppressed. In order to compute the “effective” thermal conductivity κ (which is now a scalar) of an array of aligned pores, we identify a square unit-cell with size L containing a single pore, which is chosen to be circular, and apply a difference of temperature ΔT along , as shown in Fig. 1(a). Periodic boundary conditions are applied at the boundary of the unit cell. We consider the unit cell sizes L=10nm and L=50nm, keeping the diameter of the pore fixed so that the porosity of the material is ϕ=0.25. Assuming the heat flux, J(r), is known, we use Fourier’s law, i.e.,
where is an average along the surface of the hot contact and is normal to this surface. We note that the thermal conductivity is now a scalar. For structures in which phonon-size effects are negligible, heat transport can be modelled by the heat diffusion equation, described by the heat flux J(r)=−κbulkTL(r), where TL(r) is the spatially dependent lattice temperature, computed by the continuity equation ·J(r)=0. Using Eq. 3, we obtain the general expression for the thermal conductivity reduction,
For porous materials with low porosity, macroscopic heat reduction is predicted by the Maxwell-Garnett theory which provides the formula κ/κbulk=(1−ϕ)/(1+ϕ)≈93Wm−1k−121, in excellent agreement with our finite-volume solver of diffusive heat conduction.
In aligned porous materials, the characteristic length Lc is roughly the pore-pore distance22, which in our cases is much shorter than the MFP of most of the dominant phonons in Si6, giving rise to significant phonon size effects. In order to take into account these effects, we employ the recently developed MFP-Boltzmann Transport Equation (MFP-BTE)23,
where T(r, Λ, Ω) is the effective temperature of phonons with MFP Λ and direction and TL(r) is the effective lattice temperature, given by
The weights A(Λ′) ensure energy conservation and are expressed as
Similarly to ref. 24, the walls of the pores are assumed to scatter phonons diffusively. Further details about the computational approach are reported in the Methods section.
where S(Λ, Ω) is the “directional phonon suppression function”, given by
The directional phonon suppression function S(Λ, Ω) is central to our work and describes the MFP dependence and directionality of phonon suppression caused by the boundaries. Once S(Λ, Ω) is known, the thermal conductivity in the nanostructure is given by
The physical meaning of S(Λ, Ω) can be better understood if we apply an angular average to both sides of Eq. 10, which gives
where we used . The term S(Λ, Ω)4π is also given by
which is the conventional MFP-dependent suppression function. This quantity, also called “boundary scattering”, is proven to be effective in MFP-reconstruction experiments and for understanding heat transport regime25,26,27. We note that the variable Λ is the bulk MFP; any result of this work can be translated in terms of the MFP in the nanostructure, Λnano, by means of the transformation Λnano=Λ S(Λ, Ω)4π.
In the following section, we derive the diffusive and ballistic limits of S(Λ, Ω) and connect the findings with the heat transport regimes of S(Λ, Ω)4π. For short MFPs, T(r, Λ, Ω) can be expanded up to first-order spherical harmonics as ref. 28
which is a modified heat diffusion equation that takes into account interactions among phonons with different MFPs. After combining Eqs 11, 12, 13, 14, 15, 16, we obtain the diffusive limit of S(Λ, Ω),
In Eq. 17, the second term represents the fact that the medium is non-gray. In fact, under the gray-medium approximation, where the lattice temperature is TL(r, Λ)=T(r, Λ, Ω)4π, this term vanishes. In this case, phonons are solved independently, leading to a MFP-dependent lattice temperature. For simplicity and with no loss in generality, we now derive the expression of S(Λ→0, Ω) for our nanoporous system within the gray approximation. Under these assumptions, Eq. 16 becomes the Laplacian equation 2TL(r)=0, i.e., the standard Fourier’s law29. By assuming a constant heat flux along the hot contact, the gradient of the lattice temperature is simply and Eq. 11 then becomes
where we used . The Cartesian representation of S(Λ→0, Ω), represented by the surface , is plotted in Fig. 2(a). We note two lobes, oriented along and , consistently with the fact that both the direction of the applied temperature gradient and the normal of the cold contact are aligned with . This symmetry can be also seen by the polar representation
which, when applied to Eq. 17, becomes , as shown in Fig. 2(b). The diffusive limit of S(Λ, Ω)4π within the gray approximation can be obtained by simply performing an angular average of the polar suppression function, i.e.
which is the value obtained by Fourier’s law, as shown in Fig. 1(b). However, by using the general expression for non-gray media from Eq. 14, we obtain a lower value for very small MFPs with a peak around 30nm. This result suggests that the trend obtained by the full MFP-BTE is due to the interaction among phonons with different MFPs. Specifically, the discrepancy in S(Λ, Ω)4π for low-MFP phonons between the gray and the non-gray models arises from the fact that diffusive phonons in Eq. 5 tend to thermalize to an effective temperature (plotted in Fig. 1(c)) that also depends on ballistic phonons.
We now investigate the ballistic limit of S(Λ, Ω). For large MFPs, boundary scattering becomes predominant and S(Λ, Ω) starts to depend strongly on the geometry of the material. In this regime, Eq. 5 becomes5
which recovers the well-known behaviour S(Λ→∞, Ω)Λ−1 for the ballistic regime5. We note that in this case, the directional suppression function is simply the ratio between the MFP distribution in the nanostructure and that in the bulk, i.e. Knano(Λ→∞, Ω)=S(Λ→∞, Ω)Kbulk(Λ), and so applies to S(Λ, Ω)4π. As shown in Fig. 2(c), S(Λ, Ω) is pronounced for ϕ=0 and ϕ=π, whereas it rapidly vanishes for other polar angles. This trend can be explained in terms of the view factor, a geometric parameter that quantifies the possibility of having a direct path between the hot and cold contacts30. In porous materials with square pore lattices, most of the heat travels through the spaces between the pores, perpendicular to the applied temperature gradient. The relative contribution of such paths is the view factor. Figure 2(d) superimposes S(Λ, Ω) and the material geometry to better elucidate the relationship between the boundary arrangements and phonon suppression. We also note four sub-lobes corresponding to phonons travelling along directions at 45 degrees with respect to the applied temperature gradient, constituting another set of direct paths. For all the other directions, S(Λ, Ω) describes Multiple Phonon-Boundary (MPB) scattering. In our case, heat transport arising from MPB is negligible, with most of the heat carried by phonons travelling through direct paths.
Using the insights from above, we identify a new nanopore geometry with the same porosity as the circular nanopore case, that has improved properties. This new geometry consists of rectangular pores in a staggered configuration, as shown in Fig. 3(a). The periodicity is larger than the previous case because of the fixed-porosity requirement. From the flux lines plotted in Fig. 3(b), we note that direct paths are absent; thus, phonons scatter multiple times before reaching the cold contact. For low Kns, S(Λ, Ω) is similar to that of the case with circular pores, with the size of the lobes determined by the porosity function f(ϕ) of the new configuration. Interestingly, for high Kns, S(Λ, Ω) has six preferred directions, as shown in Fig. 3(d). The amplitudes of these peaks are significantly smaller than those in Fig. 2(d). Remarkably, the computed κ are 4Wm−1k−1 and 1Wm−1k−1 for L=50nm and L=10nm, respectively, almost five times smaller than their counterparts with circular pores. We note that, for the case with L=10nm, κ is smaller than that of amorphous silicon19. Finally, as this very low thermal conductivity is obtained with no change in the porosity, the transport of electrons, which travel diffusively, will not be significantly suppressed. As a result, the configuration with staggered rectangular pores has promise as a high-ZT material.
In summary, we have introduced the directional phonon suppression function, a novel concept that captures the essence of size effects in unprecedented detail. Guided by this new quantity, we have identified a porous structure, based on rectangular pores arranged in a staggered configuration, with ultra-low thermal conductivity and relatively low porosity. Our work furthers the general understanding of boundary-dominated heat transport. In addition, as our approach is suitable for any combinations of material and geometry, this work provides practical guidance for the development of novel, high-efficiency thermoelectric materials.
The cumulative thermal conductivity requires the calculation of the three-phonon scattering time. These calculations were performed with a 32×32×32 grid in reciprocal space and a 4×4×4 supercell. Force constants calculations were performed with a 5×5×5 supercell. The isotope disorder scattering is included in the calculation. Phonon-related calculations were carried out using ShengBTE20. Density functional theory calculations were performed with Quantum Espresso31. Using a projected augmented wave (PAW) pseudopotential32, with a plane-wave cut-off of 320meV, and a 11×11×11 k-point mesh. Phonon size effects were calculated using an in-house code. The spatial domain was discretized using the finite-volume method solved over an unstructured grid with approximately 6000 elements. The solid angle was discretized into 48 polar and 12 azimuthal angles. The material was assumed to be infinite along the z-direction. The MFP distribution, assumed to be isotropic, was discretized into 30 MFPs.
How to cite this article: Romano, G. and Kolpak, A. M. Directional Phonon Suppression Function as a Tool for the Identification of Ultra-Low Thermal Conductivity Materials. Sci. Rep. 7, 44379; doi: 10.1038/srep44379 (2017).
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Research supported as part of the Solid-State Solar-Thermal Energy Conversion Center (S3TEC), an Energy Frontier Research Center funded by the US Department of Energy (DOE), Office of Science, Basic Energy Sciences (BES), under Award DESC0001.
The authors declare no competing financial interests.
Author Contributions G.R. performed all calculations. G.R. and A.M.K. analyzed and interpreted the data and prepared the manuscript.