Lead-free SnTe-based compounds as advanced thermoelectrics
Graphical abstract
This review firstly outline the basic physical and chemical properties, and subsequently summarize the research progress of SnTe from carrier concentration optimization, band engineering and phonon transport regulations.
Introduction
Thermoelectric (TE) materials can be used to convert temperature gradient into electric power, and present an advanced technology for energy harvesting [[1], [2], [3], [4]]. There has been a long history of Radioisotope Thermoelectric Generators (RTGs) powering the spacecraft launched by NASA since 1930s [5]. TEs are now actively considered for a wide variety of new applications, such as the conversion of automobile exhaust heat into electricity [[6], [7], [8], [9], [10]]. The effectiveness of a TE material is evaluated by the dimensionless figure of merit ZT = S2σT/κ = S2σT/(κlat+κele), where S is the Seebeck coefficient, σ is the electrical conductivity, T is the absolute temperature, and κ is the thermal conductivity that comprises two major components: the electrical contribution κele = LσT (L is the Lorenz number) and the lattice contribution κlat [11,12]. Usually, the term S2σ is called as power factor which reflects the electrical properties of TE materials. An ideal TE material requires high σ like in metals, large S like in insulators, and low κ like in glasses [[13], [14], [15]]. The strong interdependence of these physical parameters makes it quite challenging to increase ZT of a given material in a large freedom [12,16,17].
Thanks to the development of new concepts relating to size effects and band structure engineering, we have witnessed the rapid advance of TE materials and the explosive growth of TE community over the past three decades [10,[18], [19], [20], [21], [22], [23], [24], [25], [26]]. The best ZT, which had staggered around unity for half a century before 1990s, was steadily improved to ∼1.5 in 2000s and is further promoted to well above 2 as recently demonstrated in PbTe system [[27], [28], [29], [30]]. However, due to the concern on the perceived toxicity of Pb, there has been a growing interest of developing high performance lead-free TE materials to replace PbTe [[31], [32], [33]]. The typical examples include skutterudites, half-Heusler alloys, tin or copper chalcogenides, magnesium silicide, etc. [29,[34], [35], [36], [37], [38], [39], [40], [41], [42], [43], [44], [45], [46], [47]] Among these materials, SnTe holds the greatest promise because it resembles PbTe in many aspects [32,48,49].
The exploration of SnTe as a potential TE material can be traced back to 1960s when its anomalous electron transport behavior (two valence bands character) was identified [50,51]. Some explorative doping studies were also performed with the aim to optimize the TE performance of SnTe [[52], [53], [54], [55], [56], [57], [58]]. However, the ZT (far below unity) of SnTe was still much lower than that of PbTe at that time because of its very low Seebeck coefficient and over high thermal conductivity originating from the intrinsically large volume of tin vacancies [32,59]. Therefore, for a long time, the progress of SnTe had a slow pace until very recently when the band structure engineering [29,48,[60], [61], [62], [63], [64], [65], [66], [67]] and nanostructuring stratagems [29,62,[68], [69], [70], [71], [72]] were applied to this old but intriguing system. As a consequence, a competitive maximum ZT of 1.4–1.8 at 900 K has been achieved in optimized SnTe, making it a robust material for middle temperature TE power generation when lead-free materials are required [[73], [74], [75], [76], [77], [78], [79]].
Several nice review articles have been published recently highlighting the rapid progress of SnTe-based thermoelectric materials [31,59,[80], [81], [82]]. We hereby aim at providing a comprehensive and timely overview on the historical researches and recent developments of SnTe TE materials in an attempt to understand its basic structural chemistry and physical properties, and to guide its further development. Unlike the pervious articles, we expound electronic structure feature of SnTe in the way of describing the connection between PbTe and SnTe, and discuss the influence on hole concentration dependent Seebeck coefficient. Moreover, the intrinsic lattice thermal conductivity has also been analyzed from the perspective of lattice dynamics and resonance bonds by comparing with InSb. Generally, we organize this review as follows. First, we summarize the crystal, electronic structures and lattice dynamics of SnTe. Then, the effective technologies that successfully enhanced the TE performance of SnTe are discussed in detail. Future possible directions for further enhancing ZT of SnTe are proposed at the end of this review.
Section snippets
Crystal and electronic structure
SnTe crystalizes in the rocksalt structure (Fmm group) [52,83] under normal pressures at T > 300 K with a lattice parameter of ∼6.31 Å. The SnTe structure is formed by two inter-penetrating face-centered-cubic lattices. Sn and Te atoms are connected by bonds with mixed ionic and covalent character. Each atom is octahedrally coordinated by six nearest neighbors of the other type, Fig. 1(a). Both the conduction band minimum (CBM) and valence band maximum (VBM) of SnTe locate at the L points of
Lattice dynamics and resonant bonding
Though crystallizing in simple and highly symmetric rocksalt structure, pristine SnTe features low κlat (note: its total thermal conductivity κ is high because of the large contribution from the free holes) [20,93,94]. This becomes particularly obvious when compared with InSb, a compound adjacent to SnTe in the Periodic Table, Fig. 2(a). The lower κlat of SnTe in comparison with InSb was ascribed to their difference in crystal structure. Rocksalt structured SnTe has octahedral bonding while the
Phase diagram of SnTe
Fig. 3(a) shows the phase diagram of Sn–Te system, where a maximum value in the liquidus is present at 50.4 at.% Te, corresponding to the highest congruent melting point of 1079 K [83]. SnTe can stabilize above room temperature only when Sn is deficient and the widest range of homogeneity appears approximately at 946 K (50.1–50.9 at.% Te) [97]. The calculated defect formation energies for SnTe are shown in Fig. 3(b). Undoubtedly, tin vacancies are most easily prone to forming no matter Sn is
Carrier concentration optimization
Suppressing the over high hole population of SnTe is the prerequisite for its thermoelectric performance optimization [58,[99], [100], [101]]. The simplest strategy is to compensate cationic vacancies by adding extra Sn in its nominal starting composition [102]. For instance, Tan et al. [20] found that by use of 3 mol.% excess Sn, at room temperature, the hole density of SnTe is significantly reduced from 2.2 × 1020cm−3 to a value as low as 5.0 × 1019cm−3. Some halogens (iodine) and group VA
Phonon transport regulations
In addition to electronic bands engineering, phonon transport regulations are equally important for thermoelectric performance optimization. The lattice thermal conductivity can be approximately expressed as: κlat = CVlυ/3, where CV is heat capacity, l is the phonon mean free path and υ is the velocity of phonon group [150,151]. In most solids, CV is almost invariant above Debye temperature (exceptions are seen in some liquid-like thermoelectrics with highly mobile ions, though). Therefore, κlat
Conclusion and prospect
As an environment friendly compound, SnTe has received increasing attention in the past several years. A lot of efforts have been made to engineer its intriguing two-valence-band electronic structures with aim to improve its electrical transport properties. In the meantime, many advanced technologies have been applied to mitigate phonon transport of SnTe, including vacancy/interstitial defects scattering, dislocations scattering and lattice softening. The combination of these efforts
Credit author statement
Yu Zhang: Preparation, Writing-Original Draf; Jinchang Sun: Commentary; Jing Shuai: Critical review; Xinfeng Tang: Critical review; Gangjian Tan: Critical review, Revision, Visualization presentation, Writing – review & editing.
Declaration of competing interest
The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
Acknowledgements
We would like to acknowledge the financial support from the National Natural Science Foundation of China (Grant No. 11804261) and National Key Research and Development Program of China (Grant No. 2019YFA0704900).
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