Review on texturization effects in thermoelectric oxides

  • Rishi Prasad
  • Shekhar D. BhameEmail author
Open Access
Review Paper


Sustainable energy sources and energy-harvesting technologies have been researched for decades. Thermoelectric conversion is currently one of the primary foci in this area. Thermoelectric research has been concentrated into two parts—(i) strategies to enhance the efficiency of existing thermoelectric materials and (ii) development of new materials with promising thermoelectric parameters. Although such strategies have led to the improvement of thermoelectric non-oxide-based materials, the limitations possessed by them does not allow to be used at high temperatures. Due to the same reason, oxide-based materials have gained much attention. Here, we discuss about the oxide thermoelectric materials in detail and the effect of texturization on their morphology and transport properties. There is a lot of scope available for such class of materials for high-temperature applications.


Thermoelectric review Oxide thermoelectrics Effect of texturization Thermoelectric figure of merit 


Renewable energy has been one of the very widely studied topics since the past few decades due to the rising problem of fulfilling the energy demands. The increasing demand for oil and electricity is a much-known fact that cannot be ignored. On a global average, more than 70% of the energy generated is wasted one way or the other. TE energy harvesting is promising in providing opportunities to harvest the waste heat that is rejected out of the automobile exhausts, chimneys of factories, etc. In this review, we will concentrate only on thermal energy harvesting. Thermoelectric materials can be used as a source for both power generation and cooling devices [1]. Metal-based thermoelectric conversion materials were studied earlier followed by semiconducting materials. Since metallic TE materials are not ideal for high-temperature applications as they are prone to corrosion and hamper the conductivity, oxide-based thermoelectric materials have gained much attention. The world market of thermoelectric generators is 25–50 million$ per year and that for cooling devices is 200–250 million$ per year that attracts a lot of research in this area [2].

Ioffe in the 1930s proposed the idea that semiconductors act as better thermoelectric materials than metals that were previously used [3]. Though Altenkirch (in 1909) was the first to establish a mathematical expression which relates physical properties of thermoelectric materials and the efficiency of simplified thermopile or thermoelectric generators, his equation contained various parameters like electromotive force, thermal, and electrical resistances etc., Ioffe was the first to quantify Z (Thermoelectric figure of merit) by integrating all the variables introduced by Altenkirch into one term as Z [4, 5].

The maximum energy conversion efficiency is given by ƞmax and is defined as:
$$ \eta_{{\max = \frac{{T_{{{\text{hot}}}} - T_{{{\text{cold}}}} }}{{T_{{{\text{hot}}}} }} \frac{M - 1}{{M + \frac{{T_{{{\text{cold}}}} }}{{T_{{{\text{hot}}}} }}}}}} , $$
where M = (1 + ZTavg)1/2, Tavg being the average temperature, Z is the thermoelectric figure of merit, and Thot and Tcold are temperatures of the hot and cold end of the module, respectively [6, 7]. The potential of a thermoelectric material for the application is measured with the help of a term called as the dimensionless thermoelectric figure of merit (ZT) which measures the maximum heat conversion into electricity. ZT is given by:
$$ ZT = \frac{{ S^{2} \sigma }}{{\kappa_{{\text{e}}} + \kappa_{{\text{l}}} + \kappa_{{{\text{bip}}}} }}T, $$
where S (V/K) is the Seebeck coefficient, σ (S/m) is electrical conductivity, and \(\kappa\)e, \(\kappa\)l, and \(\kappa_{{{\text{bip}}}}\) (W/m K) are the electronic, lattice, and bipolar contribution to thermal conductivity due to bipolar effects [8, 9]. The power factor S2σ is optimized in narrow gap semiconductors as a function of carrier concentration (typically ~ 1019–1020 carriers/cm3).
Figure 1 shows the optimization of ZT by tuning the carrier concentration for Bi2Te3 [10]. It was observed that maximum ZT could be obtained on tuning the carrier concentration to be between ~ 1019 to ~ 1020 carriers/cm3.
Fig. 1

Optimization of ZT by tuning the carrier concentration for Bi2Te3. Image adapted with permission from Snyder et al. [10], Springer Nature

Since Wiedemann–Franz law relates electrical and thermal conductivities as directly proportional quantities (\(\kappa\)e = LT σ), the quantities S, σ, and \(\kappa\) for a conventional 3D crystalline system cannot be varied independently to give a high ZT value. Because what is desired is a high Seebeck coefficient, high electrical conductivity, and low thermal conductivity. If electrical conductivity is low for a material, carrier concentration has to be increased. As we increase the carrier concentration, electrical conductivity would increase. This, in turn, would reduce the Seebeck coefficient and increase the electrical contribution to thermal conductivity. The complex relationships of these parameters can be summarized in the Fig. 3 and also in the form of the equation as:
$$ S = \frac{{8\pi K_{{\text{B}}}^{2} }}{{3eh^{2} }}m^{*} T\left( {\frac{\pi }{3n}} \right)^{2/3} , $$
$$ \sigma = ne\mu = \frac{{ne^{2} \tau }}{{m^{*} }}, $$
$$ {\rm K}_{{{\text{tot}}}} = \kappa_{{{\text{lat}}}} + \kappa_{{{\text{ele}}}} + \kappa_{{{\text{bip}}}} = \kappa_{{{\text{lat}}}} + L\sigma T + \kappa_{{{\text{bip}}}} , $$
where KB is a Boltzmann constant, m* is density of states effective mass, h is the Planks constant (6.6260 × 10–34 mkg/s), n being carrier concentration, e is charge of an electron (1.6021 × 10–19 coulombs), µ is carrier mobility, τ is relaxation time, \({\rm K}\)tot, \(\kappa\)lat, \(\kappa\)ele, \(\kappa\)bip being total, lattice, electronic and bipolar contribution to thermal conductivity, and L is Lorentz number (2.44 × 10–8 W Ω/K2) [11, 12]. \(\kappa\)bip is usually observed for relatively narrow band-gap materials, which leads to the decrease of TE efficiency. This effect is the consequence of the diffusion of both electrons and holes in the same direction. The minority conductors get thermally exited through the bandgap leading to the cancellation of net charge in the conduction band. They reduce the Seebeck coefficient as the minority charge carriers contribute significantly. This is generally observed for very narrow bandgap semiconductors (Eg < 0.5 eV) [13, 14]. What is commonly observed is for an ideal metal, they possess high electrical conductivity and low thermal conductivity. Glasses exhibit high thermal conductivity and low electrical conductivity. Since a mixture of these two properties would be optimum for a thermoelectric material, such materials are termed as “phonon glass electron crystal” since it would possess high thermal conductivity like glass and still possess high electrical conductivity like an ordered crystal. It has been reported by Dresselhaus that as the dimension of material decreases and approaches a nanometer scale, it possibly causes differences in the density of states and gives rise to quantum confinement effects allowing new methods to tailor S, σ, and \({\rm K}\) values independently to achieve high ZT [15].
Although there are significant reports of various class of thermoelectric materials exhibiting low thermal conductivity and high electronic conductivity leading to high power factor and ZT, as shown in Fig. 2. Operating them at a high temperature for waste heat conversion is still a concern. A number of concerns such as toxicity, low melting point, high oxidation tendency, and stability at high temperature are yet to be addressed in detail.
Fig. 2

The development of high ZT materials over the year for non-oxide-based systems [adapted with permission from Zhang et al. [11], Elsevier]

Figure 2 shows the development of high ZT materials over the year for non-oxide-based systems adapted from Zhang et al. [11]. The extreme left indicates the state-of-the-art materials, mid-portion indicates the improvement till close to 2010, and the last part shows very high ZT obtained in the recent decade. Few of the newly included materials other than the reference quoted above are PbTe–SrTe, Cu2Se/CNT, PbSe + 2%HgSe, and Na-doped SnS.

Oxides are considered to be more stable with a high melting point, relatively less toxicity, and cheap. During the initial days of development, thermoelectric community had ignored this class of materials due to the low conductivity of carriers and ionic nature. However, due to the features that possess, they have been investigated since past 2 decades. Their electronic properties can be tuned by manipulating their crystal structures, chemical compositions, and doping concentrations. As thermoelectric oxides exhibit high covalent and ionic character, they tend to show high thermal conductivity. Hence, doping them with suitable elements is necessary. It has been seen that, in solids that show poor thermal conductivity, the phonon mean free path is in the range of interatomic distance. Hence, doping the right element not only alters electronic properties but also alters the thermal properties [16]. A number of oxide-based thermoelectric materials have been reported. A few promising ones to mention are SrTiO3, Ca3Co4O9, NaxCoO2, ZnO, In2O3, and BiCuSeO.

SrTiO 3

Strontium titanium oxide (STO) is an n-type perovskite oxide. They have a cubical crystal structure and belong to the space group of pm\(\overline{3}\)m [17] with a very high melting point of 2353 K. Since they have a very high melting point, it is a potential high-temperature thermoelectric candidate [18].

In Fig. 3, the periwinkle blue sphere indicates Sr atoms, brown indicates Ti atoms, and black sphere indicates oxygen atoms. STO has a wide bandgap of 3.2 eV. STO shows promising Seebeck coefficient, electrical conductivity, carrier mobility, and large effective mass (m* ~ 10mo). The high Seebeck coefficient is attributed to the sixfold degeneracy of 3d-t2g conduction band of Ti [19]. The carrier concentration of STO can be controlled by adequate doping of elements to transform it from insulating to semiconducting with a concentration of ~ 1021 cm−3 [20]. It has been seen that Nb and La doping makes way for STO single crystals as an effective thermoelectric material. Okuda et al. reported very high Seebeck coefficient (2800–3600 µW/Km) and power factor (28–36 µV/(Kcm) for La-substituted STO (Sr1−xLaxTiO3) which was comparable to Bi2Te3 [21]. However, since they show high thermal conductivity (6–12 W/m/K for single-crystalline STO) obtaining a high ZT was limited [22], since then, a lot of studies has been done on reducing the thermal conductivity to enhance ZT. In 2003, Muta et al. tried to understand the effect of rare-earth element doping in the STO crystal. Not much difference in electrical conductivity was seen on varying the substituent rare-earth element. However, in the case of thermal conductivity, the dopant had a strong influence. La and Sm showed a decrease in thermal conductivity as temperature increased. Gd, Dy, and Y doping led to the least thermal conductivity without much dependence on the temperature. This trend was attributed to temperature-independent phonon impurity scattering. The order of thermal conductivity on doping is La > Sm > Gd > Y > Dy with Dy being the element of substitution with least thermal conductivity (~ 2.2 W/m/K) which naturally led to better ZT than the rest as Seebeck coefficient and electrical conductivity was almost the same [23]. Since Nb and La have one of the most structural tolerance for doping in STO and since it possesses highest electrical conductivity, B site substitution with Nb gained much attention [20]. Few other rare-earth substitutions in the STO matrix along with reduced sintering time were reported by Kovalivisky et al. Pr, Nd, and Sm incorporation showed promising electronic conductivity as compared to La, Ce, Gd, Dy, and Y doping. However, small cation elements like Dy and Y gave rise to better Seebeck coefficient. Oxygen-deficient perovskite layers present in Nd-, Sm-, and Dy-doped STO led to phonon scattering leading to ZT as high as 0.42 at 1190–1225 K [24]. Tungsten substitution in the STO was performed by Kovalivisky et al. Tungsten substitution at the B site greatly increased the electrical conductivity without affecting the Seebeck coefficient to a great extent. Tungsten is interesting as it can donate two electrons per W cation and also scatters the phonons due to mass fluctuation in STO. While a ZT of 0.24 was reached at 1300 K by substituting 0.06 portion of W, on codoping W and Nb in STO (Sr0.97Ti0.8Nb0.17W0.03Oδ) resulted in a ZT of 0.28 at 1270 K. Better performance due to Nb codoping was assigned to the phase separation and phonon scattering [25]. Kovalivisky et al. reported the effect of Pr substitution. Results show that Pr leads to an increase in electrical conductivity reducing the Seebeck coefficient. At the same time, thermal conductivity reduction was also observed and maximum reduction in thermal conductivity was found for x = 0.30 in Sr1−xPrxTiO3. However, a ZT of ~ 0.34 at 1173 K was obtained for x = 0.10 [26]. Improvising the electrical conductivity in oxide-based system is crucial and this was addressed by Akin et al. by creating the oxygen vacancies. They could successfully improvise the electrical conductivity by creating A site vacancies in La-doped STO leading to oxygen loss that leads to improvement in electrical conductivity [27]. However, clarity on the influence of such vacancies on thermoelectric properties was further established by Lu et al. They obtained a ZT of 0.4 at 973 K (for x = 0.15 in Sr1−3x/2LaxTiO3−δ) by tuning the A site and oxygen vacancies along with mixed valent Ti3+ and Ti4+ that held responsible for the improvement [28]. Most recently in 2018, Srivastava et al. reported promising ZT of 0.36 (900 K) and 0.38 (1000 K) for Cu and Fe inclusion, respectively, in Sr0.8La0.067Ti0.8Nb0.2O3−δ system. As the resistivity was decreased, an increase in power factor up to 75% was reported. It has to be noted that the reduction of thermal conductivity was most effective in the case of Fe inclusion than the Cu inclusion as Fe acted as a better phonon scattering centre [22]. Electrons confined in quantum wells with dimensionality narrower than de-Broglie wavelength results in 2D electron gas that exhibit exotic electronic properties. 2D electron well enhances Seebeck coefficient for STO as carrier electrons are more localized in STO than in heavy metals as it is an insulator [18]_ENREF_93_ENREF_93. High Seebeck coefficient has been seen for one atom thick STO layers containing 2D electron gas (2DEG). Seebeck coefficient of up to 850 µV/K leading to a ZT2DEG of 2.4 and ZTeff of ~ 0.24 (including the barrier layer) was reported by Ohta et al. [29]. Very recently, Nb-doped SrTiO3/rGO composite was explored. The cationic vacancies, oxygen vacancies due to rGO, and heterointerfaces lead to increased phonon scattering. Mobility of charge carriers dramatically increased due to the cationic vacancies and heterointerfaces. These features lead to a high power factor of ~ 1.98 mW/K2m promising ZT of 0.29 at 1180 K [30]. Tkach et al. in 2018 made use of a unique two-step firing process to obtain bimodal distribution of 20% Nb-doped STO fine particles (particles smaller size ~ 270 nm) with a grain size of ~ 2.3 µm and 59 µm while for the coarse particles (particles with larger size ~ 800 nm) exhibited an average grain size of ~ 8 µm. The lower number of grain boundaries within the large connected grains in fine size STN20 leads to better electrical conductivity (328 S/cm at 970 K). Energy filtering effects in the fine size STN20 further reportedly lead to an increase in Seebeck coefficient with temperature. The power factor of this material obtained was 13.4 µW/Kcm which is comparable with that of state-of-the-art thermoelectric material Bi2Te3 and finally leading to a ZT of 0.36 at 970 K [31]. Meanwhile, a much simpler approach was followed by Ekren et al. where a fixed amount (0.5 wt%) of B2O3 and 0.3 wt% ZrO2 were composited with Sr0.9Nb0.1TiO3 to obtain 1400 S/cm at room temperature and ~ 200 S/cm at 1273 K. A drastic improvement in electrical conductivity was seen on just 0.3 wt% addition of ZrO2. The dislocation density enhancement on addition of ZrO2 that leads to increased oxygen vacancies thereby increasing the carrier concentration (also helps in reduction in thermal conductivity) hold responsible for this improvement. The addition of ZrO2 also lead to the formation of uniform-sized smaller grains leading to barely irregular grain boundaries that lead to carrier mobility improvement. Lowest Seebeck coefficient and highest power factor (~ 1000 µV/m. K2) were obtained for the same composition leading to a ZT of 0.37 at 1015 K [32]. To tune the thermal conductivity, substituting Ca and Ba at the A site has resulted in lowering the same [33, 34]. However, it was reported that these dopants also supresses the power factor, thereby hampering the thermoelectric performance [35]. Though there were other reports of doping STO, addition of secondary phases, and tuning the A and B site vacancies, no further improvement in ZT as reported by Kovalivisky et al. [24] has been seen till date.
Fig. 3

Crystal structure of STO simulated using VESTA

Effect of texturization

Quin et al. followed a Reactive Template Grain Growth Method (RTGG) assisted tape casting method whereby a Ruddlesden–Popper-type phase SrO(SrTiO3)n material was synthesised that has a multi-layered structure. They consist of alternating layer of perovskite STO and superlattice layer of SrO stalked along the c-axis. Where they could achieve a Seebeck Coefficient of − 399 µV/k at 1073 K without any dopant as compared to the highest Seebeck coefficient reported by Gd/Sm doped SrO(SrTiO3)n synthesised by conventional solid-state-assisted hot-pressing method (− 350 µV/k at 1073 K) [36]. Such an improvement was achieved by controlling the microstructure and annealing temperature. Promising Seebeck coefficient has been reported for SrTiO3 textured using the RTGG technique by Gao et al. where the texturization induced a low thermal conductivity of 2.1/Wm/K at 1027 K and Seebeck coefficient of ~ 313 to ~ 328 µV/K within the temperature range of 230 K to 1027 K [37]. The reported thermoelectric parameters in all the cases were found to be higher for the textured samples.

Ca 3 Co 4 O 9 (CCO-349)

The challenges of creating novel TE oxides have led to investigating a lot of materials. Layered cobaltates such as Ca3Co4O9 (CCO-349) and NaxCoO2 (NCO- × 12) have been found to be promising candidates for thermoelectricity. One of the major steps in thermoelectric oxide materials was the discovery of NaxCoO2 by Terasaki et al. in 1997. This material possesses a unique conduction mechanism. The charge carriers are transported via the CoO2 layer for p-type conduction and phonon path is mediated through the Na+ layer. They possess a highly anisotropic structure with a Seebeck coefficient of 200 μΩ cm in the plane and 100 μV/K resistivity giving rise to a power factor of 50 μW/(Kcm) which was comparable to that of the traditional material Bi2Te3 with 40 μW/(Kcm) [38]. This anisotropy refers to the in-plane anisotropy caused because of hexagonal lattice distortion by the square RS-type layer, CCO-349 exhibits a larger thermopower meanwhile shows very less resistivity. They have thermal stability to up to 973 K. High carrier concentration and low thermal conductivity make it a good example of electron crystal phonon glass-type material [39]. In the layered cobaltate system, only calcium cobaltate has one cation with different oxidation state. A general representation of this system is [CaCoO]RS [CoO2]. Where RS represents rock salt structure. This represents a misfit structure with a rock salt disordered layer of Ca2CoO3 sandwiched between CdI2 type CoO2 layers stalked along c-axis with [40, 41]. These two layers share the same lattice parameters. a = 4.8270(5) Å, c = 10.8300(2) Å, and β = 98.136(1) Å. Misfit of unit cell along the b-axis changes the lattice parameter b values as b1 = 4.5615(2) Å, b2 = 2.8173(1) Å for Ca2CoO3 and CoO2 layer, respectively [42]. The cobaltates are said to reduce thermal conductivity due to phonon scattering from incoherent boundaries. Thermoelectric properties of CCO-349 (whisker-based single crystals) showed a high ZT of 1.2–2.7 for at 873 K. These results show that there is a lot of potential for such materials in thermoelectric applications [43]. ZT of 0.87 at 973 K was reported by Shikano and Funahashi for single-crystalline (Ca2CoO3)0.7CoO2 misfit oxide [44]. Due to the complexity of the production of single crystals, development of polycrystalline materials is of importance. Polycrystalline material synthesis has also been reported for these materials with various substitutions like Eu [45], Lu [46], Ho, and Ga [47] to give promising ZT values. Bismuth has been considered as one among the most promising dopant. It has shown to increase electrical conductivity and Seebeck coefficient. Bismuth also leads to a reduced thermal conductivity due to the larger size of Bi atoms and also their corresponding mass [48]. Silver is another promising dopant that leads to an increase in electrical conductivity and reduction in thermal conductivity because of the heavy ion. Whereas for Ag that is added as a composite mixture with CCO-349, Ag acts as a connector between the cobaltate grains leading to a decrease in the scattering of charge carriers leading to increasing conductivity at grain boundaries. While doping of Ag+ ions increases the thermopower and charge mobility along with charge concentration, composite decreases thermopower due to metal Ag at grain boundaries. However, a balance between doping and compositing in the same system (Ca2.7Ag0.3Co4O9/Ag-10 wt%) can lead to a promising ZT of 0.5 at 1000 K [49]. Very recently, the highest ZT of 0.74 has been achieved by Saini et al. at 800 K for Tb doped CCO-349 system. This is the highest ZT ever reported for a polycrystalline oxide-based system [50].

Effect of texturization

On following the thermoforging process by Pravel et al. on-calcium cobalt oxide (CCO-349), a decrement in electrical resistivity was seen on increasing the applied pressure during the process which increases grain alignment. This study made way for further exploration of thermoforging and the influence of applied pressure on CCO-349 system [51]. On a comparative study of the effect of sintering technique on the thermoelectric performance, Liu et al. found that SPS leads to higher degree of grain orientation.

A sheet-like grains with 1–2 µm can be seen in both the cases due to the layered structure. However, a massive grain alignment and reduction in pore size can be seen in the case of SPS (Fig. 4b, c). This grain alignment not only leads to greater density of material (90%-SPS as compared to 70%-CS), but also holds responsible for the higher electrical conductivity. The measured electrical conductivity for the CS sample was 34 S/cm at 973 K, whereas SPS sample exhibited an electrical conductivity of 118 S/cm. Although Seebeck coefficient variation was less, the higher difference in electrical conductivity leads to a high-power factor of 3.51 × 10–4 W/m/K2 (SPS) as compared to 1.1551 × 10–4 W/m/K2 (CS). These factors lead to 34.5% increment in ZT of SPS sintered sample as compared to the CS sample [52]. Lin et al. performed a unique combination of SPS and dynamic forging technique leading improved texturization over the just SPS processed sample. It has been seen that this technique allows in lowering the resistivity of the sample without affecting much of Seebeck coefficient. To reduce thermal conductivity, lanthanum was doped in the CCO matrix. La leads to scattering of phonon as it is a heavy mass element leading to mass fluctuation in the matrix. Finally, ZT of 0.26 at 975 K was reported [53]. Neodymium substitution in the CCO matrix along with texturization efforts was done by Parvel et al. in 2007. Their results show that Nd increased the decomposition temperature of CCO. Also, thermoforging led to an increase in electrical conductivity of the sample by 2.5-fold. The decrease in carrier concentration with Nb substitution holds responsible for the improvement in Seebeck coefficient and thermopower [54]. A comparative study of conventional sintering, hot-pressing and spark plasma sintering, their texturization effects, and influence on thermoelectric parameters of CCO-349 were done by Kenfaui et al. The micrographs obtained for these methods revealed that there were a platelet formation and high degree of orientation in the case of the hot-pressed sample. The order of degree of orientation was: HP > SPS > CS. Densification and texturing are found maximum in HP sample, and thus, resistivity is minimum (6.1 mΩ cm at 300 K), and Seebeck coefficient of 550 µW/m/K2 at 850 K in the case of HP which was claimed to be one of the lowest resistivity and highest S reported along the ab plane [55]. Since the synthesized product was only 0.5 mm thick, module making would be a challenge. Hence, they stalked the multi-layers of CCO. Each layer of CCO was hot-pressed and polished. They were stalked together, hot-pressed again, and was cut along ab and c direction. Thermoelectric parameters measured parallel and perpendicular to c-axis show highly anisotropic nature of the sample. Finally, a ZT of 0.16 was realized along the ab plane [56]. To obtain a better power factor, optimizing stress while pressing multi-layers of CCO was later identified. Better power factor (595 µW/m/K2) at higher stress level (30 MPa) was realized by the team at 900 K along the ab plane [57, 58]. The anisotropic resistivity behaviour was also explored later using a modified SPS technique called as SPT. In this technique, a pre-sintered pellet is kept in a die of bigger diameter in the second step for free deformation of pellet resulting in better texturization and platelet formation along the axis perpendicular to the pressing direction [59]. An improvement of 40–60% (170–180 µW/m/K2) in power factor was reported in 2016 as a result of microwave sintering. Microwave sintering resulted in an increase in density as well as the growth of elongated grains. The main reason for the enhancement is assigned to better electrical conductivity due to low porosity and texturing [60]. Strontium-doped CCO349 synthesised by hot-pressing exhibited higher electrical conductivity and lower Seebeck Coefficient. Resistivity close to those sintered by SPS method (6 mΩ cm) was obtained for the hot-pressed Sr-doped (6.5 mΩ cm) sample at 1073 K. Presence of Sr and Ca carbonate impurities on the surface of the sample along with grain alignment and good conductivity between the grains was attributed to be responsible for the improved electrical conductivity. Almost 20% higher PF (1.16 mW/Km at 800 °C) were exhibited by the Sr-doped samples as a result of high chemical pressure effects. Though there was significant improvement in electrical conductivity and power factor, ZT was estimated to be 0.29 at 1073 K due to the high thermal conductivity (4.4 W/K m) [61]. ZT as good as 0.36 at 1073 K were reported for CCO synthesised by calcining the nitrate hydrate precursors followed by cold pressing at 200 MPa and sintering at 1173 K. The porous structure clearly has lead to the reduction in thermal conductivity, which, for a highly dense sample, is a bane [62].
Fig. 4

Scanning electron microscopy of the fracture surface of CS (a) and SPS (b, c) materials

NaxCoO2 (NCO)

Great interest in misfit oxide-based thermoelectric materials was seen after the reporting very high thermopower of ~ 100 μV/K by Terasaki et al. in 1997 for NaxCo2O4 [38]. Since the thermal conductivity exhibited by this lamellar based material was very low, it is considered to be fitting into the PGEC concept [63]. This oxide has a misfit double-layer structure. One layer consists of the CdI2 type-CoO2 ions with edge-shared octahedra and Na ions stalked along c-axis on the other. While CoO2 layer acts as an electron reservoir and is responsible for electronic conductivity and thermopower, the Na+ ion layer acts as an electron donor to the CoO2 layer and also holds responsible for reducing the thermal conductivity. The Na ions are intercalated between the CoO2 layers. The concentration of Na ions can be varied to manipulate the number of conduction electrons on the Co layers [64]. When x = 0, the electrovalency of cobalt is + 3 with 5 electrons occupying the ground state of the t2g band. And when x = 1, the electrovalency of cobalt is + 4 with a fully filled ground state t2g band [65]. They crystallize in the hexagonal structure with a space group of P63/mmc. In these family of oxides, since carrier density does not contribute to the power factor, tuning the same would leave no difference in the power factor. This class of materials was then found to be a promising candidate for high-temperature thermoelectrics as they exhibited good chemical stability and non-toxicity as compared to the other state-of-the-art materials like Bi3Te3 and PbTe [66]. Reports on polycrystalline NaCo2O4 with Cu doping at the Co site prepared by solid-state mixing method following hot pressing exhibited ZT of 0.88 at 573 K for Na(Co1−xCux)2O4 (x = 0.05). Though the thermal conductivity was 30% higher for the hot-pressed sample, a reduction in room temperature electrical resistivity from 2 to 1.1 mΩ cm (for NCO) as a result of hot pressing holds responsible for this improvement [67]. At low temperature, for sodium-deficient system, intercalated water results in superconducting transition. High Seebeck coefficient of ~ 120 µV/K was reported by tailoring the Na (x = 0.15) stoichiometry in NaxCo2O4 [68]. Later on, adding metallic phase of (Ag, Ti, Rh, Pd) into this system was tried to increase the electronic conductivity which was successful (not in the case of Ti) which also led to the Seebeck coefficient improvement and has been reported in [69, 70]. Also, compositing NCO with Ag has led to enhancement of thermoelectric properties as seen in the work by Seetawan et al. A 2% doping at the cobalt site exhibited marginally lower resistivity (66 µΩ cm) over the complete temperature range as compared to the other compositions. A reduction in thermal conductivity was also observed mainly due to the single-phase NCO and due to the Ag presence, while the other compositions exhibited mixed phase. These factors combined to gather with a high power factor of 0.31 mW/m/K at 973 K leading to a ZT of 0.124 at 973 K [71]. It has been seen that out of the transition-metal element addition (Ni, Fe, Mn, and Cu) into the cobalt site, only Ni and Cu were a promising dopant which rules out the possibility of other elements mentioned as an effective dopant for enhanced thermoelectric performance [72, 73, 74]. Addition of Zn has also led to enhancement in thermopower [75]. Krasutskaya et al. recently reported a ZT of 1.57 at 1100 K for x = 0.89 with a low thermal conductivity of 0.829 mW/(mK2) which is one of the highest ZT reported for polycrystalline NCO-based system [76]. By doping Co site with a minute fraction of Fe (Na0.71Co0.95Fe0.05O2) increased thermopower along the ab plane to a greater extent and was reported recently by Richter et al.[77]. Behera et al. reported a low-temperature synthesis by nitrate–citrate combustion method which followed a low heat treatment strategy to obtain a ZT of ~ 0.01 at 780 K for the La0.85Na0.15CoO3-based compound. The thermopower of this compound was found to be promising (~ 374 µV/K at 318 K) due to strong electron correlation and degeneracy of 3d orbitals of Co. However, thermal activation of holes due to Na (induces p-type conductivity) content at higher temperature reduces the thermopower [78].

Effect of texturization

The hydrothermal method was reported by Zhang et al. for the synthesis of NCO so as to develop materials with oriented growth which would add on to the texturing effects leading to improvements in thermoelectric performance. A strong anisotropic behaviour was exhibited by the HT sample as the grain boundary density was different along in-plane and out-of-plane direction. However, the CSS sample failed to exhibit such a behaviour as a result of higher grain size and lower degree of grain alignment. Hence, in-plane electrical conductivity and Seebeck coefficient was much higher (Fig. 5a) along the complete temperature range as compared to the out-of-plane direction resulting in a drastic improvement in power factor of ~ 0.43 from ~ 0.08 mW/m K2 at 993 K (Fig. 5b). Due to the high orientation degree of NCO-based materials, the grain boundary density is more along the out-of-plane direction. As a result of grain boundary scattering due to the high grain density, thermal conductivity decreases (also leads to reduction in electrical conductivity) (Fig. 5c). However, NCO prepared by HT and cut along the in-plane direction exhibits maximum ZT of 0.064 at 923 K (Fig. 5d) due to the high power factor and low thermal conductivity (~ 5.2 W/mK at 923 K) [79]. The transport properties of layered cobaltates are highly anisotropic due to the layered structure. Hence, texturization finds potential in the improvement of their properties as it would lead to a higher degree of grain alignment, thereby increasing the electrical conductivity.
Fig. 5

Electrical conductivity (a), Seebeck coefficient (a), power factor (b), thermal conductivity (c), and thermoelectric figure of merit (d) variations with respect to temperature for the NCO-based material under two pressing directions


ZnO is an n-type wide band-gap semiconductor having bandgap of 3.37 eV, and has been used extensively for various applications such as UV-light emitters, solar cells, flat panel display, light-emitting devices, piezoelectric transducers, brake linings, cosmetics, dental cements, lubricants, paints, phosphors, and other products due to its low cost, abundance, non-toxicity, and thermal/chemical stability [80, 81, 82]. Wurtzite structure is the most common structure exhibited by ZnO with a space group of P63mc. However, zinc blend structure with a space group of Fm3m is also seen under pressure. A typical wurtzite crystal structure is shown in Fig. 6. Here, the brown sphere indicates zinc atom and blue indicates an oxygen atom.
Fig. 6

Crystal structure of wurtzite-type ZnO simulated with VESTA

Elements such as Aluminium, Indium, Gallium, etc. are doped in the ZnO matrix to optimise the wide bandgap of ZnO for applications in the field of solar cells, thermoelectric, and optoelectronic applications [83, 84, 85]. A high carrier concentration (> 1020 cm−3) is exhibited by the group III elements which makes them ideal dopants. Out of the group III elements, Al has been identified to be the most abundant and also is a shallow donor making it one of the most suitable dopants to increase the n-type character [80]. ZnO exhibits a harmonically vibrating lattice as a result of the ionic and covalent nature leading to high thermal conductivity (~ 40 W/m/K1). M. Ohtaki in 1996 identified ZnO to be a potential thermoelectric material exhibiting a PF of 8–15 × 10–4 W/m K2 for aluminium-doped zinc oxide and leading to ZT of 0.3 at 1273 K. Though they possess high thermal conductivity due to the ionic character of ZnO, due to higher carrier mobility and carrier concentration, the electrical conductivity shot up without much decrement in thermopower [86]. Observation of enhancement in thermopower of Al-doped ZnO-based systems was reported by Ohtaki as a result of phonon scattering by the nanovoids—leading to suppressed thermal conductivity [87] to give a ZT of 0.55 to 0.57 at 1273 K, thermionic effects due to the nanovoids and suspected carrier energy filtering by the nanovoids to deliver a ZT of up to 0.6 at 1250 K [88]. Later, dually doped ZnO (Ga, Al) set a benchmark by exhibiting a ZT of 0.65 at 1247 K where Ga acted as the scattering centres to reduce thermal conductivity, whereas Al acted as an agent to increase the carrier mobility which increases the electrical conductivity [89]. More recently, Jood reported a ZT of ~ 0.44 for 1000 k that reached thermal conductivity of ~ 2 W/mK. However, further improvements are necessary to obtain better ZT values [90]. Very recently, Zhakharchuk et al. reported a slightly improved ZT of close to 0.12 for Zn0.994Al0.003Zr0.003O at 1200 K. While new scattering interfaces and suppression of thermal conductivity were due to zirconia, enhancement of electrical transport properties mainly led to this enhancement [91]. Recently, Cd1−xZnxO were explored and was seen to exhibit one of the highest ZT of 0.52 at 1000 K for any n-type oxide-based material with 1% doping. The phonon scattering from multiple scale scattering sources such as point defects, grain boundary, ZnO nanoprecipitates, and micropores leads to very low thermal conductivity and can be attributed to as the main reason for the high ZT reported [92]. Further optimisation of dopant and size of nanoparticle could also lead way for better ZT [93]. Lately, Al and Zr codoping have been found to be a promising combination in the ZnO matrix which would suppress the thermal conductivity and boost electrical conductivity. Zn0.997Al0.002Zr0.005O showed a ZT of 0.12 at 1173 K. This mixed combination was seen to exhibit the lowest thermal conductivity and better ZT than the individual-doping compositions [94]. Dy doping has been tried in the ZnO matrix by Anju et al. Since Dy possess higher ionic radii and since they produce localised magnetic moment due to unpaired electron, it can effectively act as the phonon scatterer and lead to reduction in thermal conductivity. On the addition of 1% Dy atoms, thermal conductivity was reduced to up to 2 W/mK at 900 K. Also, since Dy leads to remarkable increase in electrical conductivity, i.e., up to 1000 times as compared to pristine ZnO at 373 K. These factors lead to an improved ZT of 0.11 at 923 K [95].

Effect of texturization

The thermoelectric properties exhibited by pure and doped zinc oxide are discussed above. However, it is known that texturization could lead to an improvement in the thermoelectric parameters. Han et al. synthesised aluminium-doped ZnO by various methods to obtain rods, platelets, and nanoparticles. SPS technique was used for sintering and induce texturing in the sample (Fig. 7). The relation between various morphologies on the thermoelectric parameters after texturing was then explored [96].
Fig. 7

Illustration of the consolidation process for a rods, b platelets, and c particles which were cut parallel and perpendicular to the pressing direction for measurements

It was seen that the rods exhibited maximum electrical conductivity (Fig. 8a) and carrier mobility (Fig. 8b). One of the reasons for this improvement is the aligning of rods along the perpendicular direction leading to a reduction in number of grain boundary, thereby reducing the scattering of charge carriers, hence proving that microstructure and morphology plays an important role. The parallelly cut rods and platelets exhibited least thermal conductivity which again is a proof of anisotropic behaviour (Fig. 8c). Parallelly cut samples exhibit maximum grain boundaries leading to maximum phonon scattering. However, nanoparticles exhibit the least thermal conductivity due to impurity scattering and grain boundary scattering. Though nanoparticles exhibit poor electrical conductivity, carrier mobility, and carrier concentration as compared to the other morphologies, since they exhibit the least thermal conductivity, and the ZT exhibited by nanoparticles is maximum (ZT = 0.30 at 1223 K) (Fig. 8d) [96].
Fig. 8

Electrical conductivity (a), carrier mobility (b), thermal conductivity (c), and thermoelectric figure of merit (d) of Zn1−xAlxO (x = 0.02) measured for samples cut parallel and perpendicular to pressing direction

In 2 O 3 based ceramics

Homologous In2O3–ZnO-based system has been widely studied for their thermoelectric performance as they possess excellent structural and chemical stability even at higher temperature [97]. They are indexed by rhombohedral symmetry. Homologous (ZnO)k.In2O3 belong to the space group of R3m for odd values of k and P63/mmc for even values of k [98]. Particularly, the wide bandgap exhibited by these compounds leads to better thermoelectric parameters as they would resist the thermal excitation of electrons at higher temperature [99]. They exhibit a layered structure with alternating layers of edge-sharing In–O octahedral layers and In–Zn–O layers arrange in a zigzag manner [100]. The n-type conductivity exhibited by this compound is dominant through hexagonal lattice than across the ab plane as the main in-plane conducting path is In–O layer and In–Zn–O being the out-of-plane conducting path [97, 99]. Local charge deficiencies in the crystal are created as a consequence of Zn vacancies created as they are the preferential site for incorporation of In3+ ions. Their ordering further leads to (ZnO)k.In2O3 (IZO)-type phases [101]. It was identified by Ohta et al. in 1996 that such series could be potential thermoelectric material. They reported that ZT would increase with increase in the concentration of ZnO (i.e., k = 3, 5, 7 and 9 with maximum ZT at k = 9). ZT values of 0.11 at 900 K have been reported by Bernik et al. for k = 5 as a consequence of sintering, pre-reacted mixture, and raw mixture in 1:1 ratio leading to lower thermal conductivity [102].

The representation of the crystal structure of In2O3, ZnO, and (ZnO)5In2O3 is given in Fig. 9. The brown sphere indicates Zn atoms, light blue indicates oxygen atoms, and the periwinkle blue indicates In atom. The introduction of point defects in In2O3 results in a glass-like thermal conductivity. The lattice thermal conductivity could be reduced by 60% and extraordinary low lattice thermal conductivity of 1.2 W/mK at 973 K was also reported. However, point defect engineering by co-doping Zn and Ce in the In2O3 system (In2−2xZnxCexO3) leads to a much better thermoelectric parameter (ZT = 0.44 for x = 0.12). Various other elements were doped in ZnO for thermoelectric applications such as Ca, In, Ni, Nb, Dy, Yb, Y, and Gd which have led to a decrease in thermal conductivity. It was identified that Dy, Yb, and Gd are the most suitable dopants, since they possess higher mean atomic mass leading to a low heat capacity which is directly related to thermal conductivity. Kosir et al. studied this system for varying k values of 5, 11, and 18. It was identified that total thermal conductivity was minimum for least k value. Similarly, promising electrical conductivity was seen in the case of k = 5, while 11 and 18 exhibited less electrical conductivity. The reason for this trend was attributed to the InZn planar defect density. Higher the defect density, lower was the thermal conductivity and better electrical conductivity. It was also seen that sintering the composite at 1773 K (ZT ~ 0.125) resulted in a better ZT than for the material sintered at 1573 K (ZT ~ 0.11) at 973 K [103]. Later, in the same year, they reported that the addition of Al into homologous IZO with k = 5 results in a slight increment in ZT. However, the improvement was very little (ZT ~ 0.13) which was for the composition with x = 0.01 in (ZnO)k(In1−xAlx)O and k = 5 which was because of the increment in carrier mobility due to Al and reduction in thermal conductivity [104].
Fig. 9

Schematic representation of crystal structure for parent oxides (In2O3, ZnO) and (ZnO)5In2O3

Berardan et al. later explored the potential of Germanium doped In2O3 (In2−xGexO3) as a thermoelectric material. It was observed that a decrease of fivefold in resistivity of the sample was seen on the addition of just x = 0.002 of Ge in the In2O3 matrix. The resistivity of the sample further decreased on addition of more Ge which resulted in a decrease in resistivity from ~ 25 mΩ cm to ~ 1.5 mΩ cm at x = 0.015 measured at 1000 K. It was also pointed out that Ge addition selectively reduces thermal conductivity (3–0.6 W/mK) without affecting charge carrier mobility altogether giving rise to a ZT of 0.45 at 1273 K [105]. Since In is a rare element, reducing the In content is of importance. Bhame et al. were successful in reducing the indium content and still obtain thermoelectric parameters comparable to the doped In2O3 system. The fluorite-type structure of Ga3−xIn5+xSn2O16 resulted in interesting thermoelectric performance [106]. Zhou et al. observed that in the In–Sn–O system, a lower density of the final sample reduces electrical conductivity. However, reactive sintering with gallium addition seemed to overcome this by densifying the sample further. It resulted in an increase in density to up to 90% of bulk density. Ga2In6Sn2O16 and SnO2 secondary phases were seen as a result of reactive sintering of the precursors. However, a large number of localized grain boundaries among secondary phases result in grain growth and increase the density. Though thermal conductivity increases with Ga addition, finally with a minute addition of Ga, ZT of ~ 0.23 was reported at 1000 K [107]. Combe et al. reported a ZT of 0.3 at 1000 K for the Ge doped In2O3 system. They pointed out a decrease in thermal conductivity at high temperature after the solubility limit of Ge in the In2O3 system (less than 0.5 at%). The decrease in thermal conductivity was attributed to the homogeneously distributed insulating secondary phases of In2Ge2O7 observed after the solubility limit. Though electrical resistivity increased after the solubility limit, the total effect contributed to an enhanced ZT [108].

Effect of texturization

Among the homologous IZO series, k = 5 resulted in maximum ZT and has been mentioned already. Texturization efforts were made on this composition to obtain ZT of 0.18 at 1027 K. The textured samples were obtained by Tani et al. with the help of RTGG method (Fig. 10). A high degree of anisotropy was seen in the electrical conductivity measurements. The samples cut perpendicular to the casting direction (c plane) exhibited less conductivity as compared to the sample cut parallel showing the effect of misalignment distribution of grains. Greater number of grain boundaries is seen in the case of perpendicularly cut sample, whereas long grains and fewer grain boundaries in parallelly cut samples lead to higher electrical conductivity. However, a huge difference between the textured (~ 2 W/mK) and non-textured (~ 5 W/mK) sample is shown in the case of thermal conductivity due to the high density exhibited by them regardless of the direction in which the sample is cut [98].
Fig. 10

The methodology followed for the synthesis of textured IZO (a). b SEM of the parallelly cut, c perpendicularly cut sample processed by RTGG method, and d reference sample

Isobe et al. synthesised Y-doped IZO5 (((ZnO)5 In0.97Y0.03)2O3) by RTGG method to obtain textured samples. SEM images revealed longer grains and grain orientation for the perpendicularly cut sample as compared to the parallel one. Although the sintered specimens exhibited less density, the electrical conductivity was seen to be greater for the textured samples. Textured samples exhibited half the thermal conductivity exhibited by the non-textured specimens. The thermal conductivity exhibited by Y-doped non-textured (impurity scattering) specimen was also exhibited by the textured undoped samples (scattering due to pores). However, combining both the effects textured Y-doped IZO samples exhibited the maximum ZT of 0.33 at 1073 K. Such a ZT was possible due to the samples retaining high electrical conductivity in spite of low density [109].

Kaga et al. reported a ZT of 0.31 for textured Ca-doped IZO as compared to the non-textured sample that showed a ZT of 0.23 at 1053 K. RTGG technique was followed for texturization. RTGG method introduces bigger grains and higher degree of alignment than the reference sample. Electrical conductivity measurements show that there was a certain degree of anisotropy present in the sample. Samples cut parallel to ab-axis exhibited better electronic conductivity. Though at temperatures close to room temperature, the thermal conductivity is less for c-plane measurements, at high-temperature both exhibited almost similar thermal conductivity leading to ZT of 0.31 [110].


BiCuSeO is an interesting class of mixed anionic compounds made of oxide-based chalcogenide atoms. The oxide and chalcogenide atoms are indirectly bonded through the cationic atoms. This leads to an alternating insulating and conducting fluorite-like layers of oxide (Bi2O2)2+and chalcogen (Cu2Se2)2−, respectively, along the c-axis. This naturally leads to better carrier mobility along with the a, b planes than along the c plane resulting in anisotropy. These features make them a suitable thermoelectric material and were first reported in 2010 with Sr doping [11, 111, 112]. They usually crystallize in the tetragonal system with a = b = 3.9273 and c = 8.9293 as unit cell dimensions and belongs to the space group of P4/nmm. The figure shows the crystal structure of BiCuSeO exhibiting a tetrahedral symmetry [113].

Figure 11 represents the BiCuSeO crystal structure. The orange sphere represents a Cu atom, blue sphere represents Se atom, periwinkle blue sphere represents the Bi atom, and black sphere represents the oxygen atoms. At room temperature, their carrier concentration is reported to be 1018 cm−3 and carrier mobility is 22/cm2/V/s [114]. A huge leap in the electrical conductivity for this class of material was achieved in 2010 when Sr was doped with BiCuSeO. The electrical conductivity increased from 470 S/m to 4.8 × 104 S/m at 293 K on Sr substitution at the Bi site by a proportion of just 0.15 at%. This drastic increase was assigned to be responsible due to the carriers that are induced in the (Bi2O2)2+ layer that acts as the charge reservoir by partially substituting Bi3+ with Sr2+ and transferring it to the conducting (Cu2Se2)2− layer. As the thermal conductivity of this material is by default very low (~ 0.65 W/mK at 873 K) along with increased electrical conductivity and Seebeck coefficient (~ 225 µV/K) leads to a ZT of 0.76 at 873 K [115]. Very soon on realizing the potential of oxychalcogenides, especially BiCuSeO, Ca doping at the Bi site resulted in a reduction of thermal conductivity and improved power factor as a result of improvised electrical conductivity as compared to the undoped sample. The replacement of Bi with Ca lead to an increase in the hole concentration hence transferring charge carriers from charge reservoir (Bi2O2)2+ layer to the conducting (Cu2Se2)2− layer. The overall ZT for Bi0.0925Ca0.075CuSeO is reported to be 0.9 at 923 K [116]. However, in 2014, Pei et al. reported the highest ZT of all times till the date for undoped BCSO exhibiting a ZT of 1.4 at 923 K. Such a huge leap from the previously reported ZT for pristine sample (0.70 at 773 K as in [117]) was mainly because of the improvement of power factor (Fig. 12c) due to modulation doping strategy (MD). MD strategy has been used to increase the carrier mobility. They could improve mobility by twofold without deteriorating the carrier concentration. This leads to a high electrical conductivity without and resulted in a very high PF of 10 µW/cm/K2 at 923 K. However, MD had no much influence on the Seebeck coefficient. These factors along with a decrease in Klat (~ 0.25 W/mK) lead to ZT of 1.4 at 923 K (Fig. 12f) [118].
Fig. 11

Crystal structure of BiCuSeO generated using VASP

Fig. 12

The electrical conductivity (a), seebeck coefficient (b), power factor (c), thermal conductivity (d, e), and thermoelectric figure of merit (f) of modulation doped BCSO

Previous reports show that single-element doping has led to the improvement in either electrical conductivity or thermal conductivity. An improvement in both has been observed, but very moderate. To combine both the effects, i.e., reduction in thermal conductivity and increase in electrical conductivity, Liu et al. carried out dual-doping technique, whereby Pb acted as agent for the improvement in electrical conductivity, whereas Ca played the role to reduce thermal conductivity. Since Pb has a delocalised 6 s orbital that has a lone pair of electrons and due to an increased effective mass, Seebeck coefficient and electrical conductivity improve better than any other elemental doping. On the other hand, Ca induces both mass fluctuation (difference in mass), size, and strain field fluctuation (difference in interatomic coupling force) leading to minimum thermal conductivity. Though the solubility limit of Pb is 6–7%, higher amount of Pb exhibited formation of nanoprecipitates which lead to reduction in lattice thermal conductivity. Though the pristine BCSO are known to exhibit high Seebeck coefficient, upon dual doping, it decreases to 175 µV/K at 873 K which three times is lower. Thus, the improvement in electrical conductivity coupled with a moderate Seebeck coefficient gives rise to a promising power factor of 1.0 × 10–3/Wm/K2 for x = 0.06 as compared to 2.2 × 10–4/Wm/K2 at 873 K. The formation of Bi-rich nanoinclusions and CaO2 contributes to phonon scattering leading to a reduction in lattice thermal conductivity from ~ 3.8 to ~ 2.9 W/mK at 873 K. All the factors combined together lead to a high ZT of ~ 1.5 at 873 K [119].

ZT as good as 1.09 was reported in 2016 by Das et al. for the pristine sample of BaCuSeO. However, the high ZT was attributed to a reduction in thermal conductivity 0.19 W/mK at 773 K due to all length scale phonon scattering by micrometre-sized grains, point defects, naturally layered structure, and oxygen vacancies [120]. Replacing Sb at the Bi site and Te in Se site by a proportion of 8 mol% (Bi0.92Sb0.08CuSe0.92Te0.08) remarkably increased the ZT to 1.19 at 873 K. This increase in ZT was due to the increase in band covalency and increase in carrier concentration due to Sb/Te co-doping. Another reason was attributed to the smaller grain size due to long hours (16 h) of ball milling and Cu vacancies created which lead to an increase in hole concentration eventually leading to better electrical conductivity. Sb/Te co-doping was also responsible for the reduction in thermal conductivity as it leads to mass fluctuation and strain field fluctuation by the point defects and nanostructurization [121].

Effect of texturization

Since BCSO is a highly anisotropic material, texturizing these materials would lead to an improvement in the transport properties with respect to the direction of measurement. Hot forging is a method adopted for inducing the texturization in samples. Hot forging leads to higher order of grain alignment which was seen in BCSO with Ba doping. Preferential orientation of grains was seen to get shifted from (102) to (003) direction. It was seen that as the number of hot forging steps increases, the orientation along (003) became more prominent. While the non-textured (0 T) samples exhibited least anisotropy during the transport property measurements, the textured samples exhibited maximum anisotropy (increased with number of hot forging steps). Since the grains arrange themselves in the form of platelets along the a- and b-axis, i.e., perpendicular to pressing direction evident from the SEM, z-Euler images and inverse pole figures, as shown in Fig. 13. The inverse pole figures especially highlight the high grain orientation along the c-axis for 3 T⊥ sample as compared to 0 T⊥. The grain boundary density decreases in this direction leading to increase in both electrical conductivity and thermal conductivity.
Fig. 13

The microstructure (a, e, h, k), grain size distribution (b, f, i, l), z-Euler images (c, g, j, m) of 0, 1, 2, and 3 T⊥ samples, respectively, and the inverse pole figures (d, n) for 0 and 3 T⊥ samples

However, along the parallel cut direction, since the grain boundary density is greater, it leads to a decrease in transport properties. Electrical conductivity increases from 450 to 700 S/cm at room temperature for three times hot forged sample that was cut perpendicular direction. While Hall effect showed not much variation in carrier concentration, so the improvement in electrical conductivity was attributed to an increase in carrier mobility (2/cm/V/s for 0 T⊥ and 4/cm/V/s for 3 T⊥). The transport property improvement along the ⊥ cut samples was attributed to the higher grain alignment as confirmed from the XRD. While the Seebeck coefficient was seen to be independent of any such grain orientation resulting in close to 187 µV/K at 923 K for all the samples, power factor for the 3 T⊥ sample was the highest (8 µW/cm/K2 AT 923 K). Though thermal conductivity would increase with hot forging, the ratio of electrical to thermal conductivity was the highest for 3 T⊥ resulting in a high ZT of ~ 1.4 at 923 K [112].

Other oxides

In addition to the oxide-based systems discussed above, there are also a few other materials that are researched upon. One class of them is the double perovskites. Double perovskites are an interesting class of materials that exhibit half-metallic ground state in which conduction electrons are fully spin-polarized. The potential of such double perovskite-based materials for thermoelectric application is highlighted by Roy et al. and high Seebeck coefficient (290 µV/K at 1124 K) for material like Sr2TiFeO6 has been reported [122]. ZT of 0.29 at 1223 K was later reported by the team for p-type BaxSr2−xTiCoO6 (x = 0.2). This material exhibited glass-like behaviour. Thermal conductivity was reported to be within 0.01 to 0.55 W/mK which is very low as compared to the state-of-the-art materials existing in the market. The low thermal conductivity, however, was attributed to the phonon scattering in the crystal due to multiple cations, the transition from relaxor to the glassy state after Burns temperature and shorter grain size [123]. Increasing Ba composition to x = 0.25 showed a very high Seebeck coefficient of ~ 800 µV/K at 1123 K at the cost of compromising electricidal conductivity. However, the author suggests that aliovalent substitution could tune the electrical conductivity of such materials [124]. The promising power factor of ~ 35 µW/mK2 at 1100 K was reported for a composition of n-type Ba0.1Sr1.9Fe0.5Mo0.5O6. While thermal conductivity is taken care by the grain size and cationic phonon scattering centres, metallic electrical conductivity is shown due to the combination of Sr2TiFeO6 and Sr2TiMoO6. On adding Ba alongside increases the Seebeck coefficient at the cost of electrical conductivity leading to such high-power factor values [125]. Pseudobrookites (Fe2TiO5) have been known for their high Seebeck coefficient of -100 to – 370 µV/K within the range of 286–1000 K and low thermal conductivity (1–1.5 W/mK within the temperature range of 673–1000 K) [126]. Efforts have been done to improvise their electrical conductivity to obtain a promising ZT. Improvement in the electrical conductivity, thermal conductivity deuteration, and power factor was reported by et al. recently as a result of optimizing the percentage of Ti content in Fe2−xTi1+xO5. An improvised ZT of 0.014 at 1000 K was obtained at x = 0.25 leading to a few microcracks which reduce the thermal conductivity without affecting the electrical conductivity to a great extent as in the case of x = 0.5 [127]. Since oxides, in general, show high resistivity, oxygen deficiencies were created using vacuum sintering in a helium atmosphere to improve the electrical conductivity of Ni-doped SnO2. Power factor as good as 20.195 µV/K at 950 K was obtained for 3at% doped SnO2 revealing the high-temperature performance potential of this material [128].

On a summary, the following graph depicts the different promising thermoelectric oxides reported over the years.

The development of thermoelectric n and p-type oxides is given in Fig. 14. The various oxides labelled in Fig. 14 are–In–Sn–O [129], (Ca, Bi)MnO3 [130], (Ca,In)MnO3 [131], (Zn, Al)O [86], (Zn, Al)O nanovoid [88, 132], (Zn, Al, Ga)O [89], (Ca, Eu)3Co4O9 [45], (Ca, Ho)3Co4O9 [133], (Ca, Lu)3Co4O9 [46], CaMn1−xNbxO [134], Ca3(Co, Ga)4O9 [47], (Ca, Ag)3Co4O9/Ag [49], (Ca, Ag, Lu)3Co4O9 [58], Na(Co,Cu)2O4 [67], Na(Co,Zn)2O4 [135], NaCo2O4 [136], Bi2Sr2Co2Oy [137], (Sr,Dy)TiO3 [23], Ca(Mn,Nb)O [134], (In,Zn,Ge)O [138], (Zn,Al)O [90], PPP/(Zn.Ni)O [139], (Zn.In)O [140], TiC0.1O0.9@TiOy-TiO2 [141], In(Zn,Sn)O [142], BiCu0.90SeO [143], (Bi,Sr)CuSeO [117], (Bi,Ba)CuSeO [112], (Bi,Na)CuSeO [144], (Bi,Pb)CuSeO [144], (Bi,Ba)CuSeO [112], (Bi,Pb)CuSeO [145], Modulation BiCuSeO [118], (Bi,Ba)CuSeO [146], and (Bi,Ca,Pb)CuSeO [119].
Fig. 14

Representation of the development of thermoelectric oxides over the years

The following table highlights the overall effect of texturization on thermoelectric parameters of various materials as discussed above:

It can be seen from the table that texturization has played a vital role in improving the thermoelectric parameters. However, further studies combining methodologies such as nanostructurisation, modulation doping, and texturization could lead to further improvements. It is clear that ZnO-based materials lack attention and improvements could be made by doping and texturing, since they can be used for high-temperature applications (Table 1).
Table 1

A comparison of effect of texturization on thermoelectric parameters for the promising oxide-based materials (*%change in PF)


Measuring temperature (K)

Before texturization

After texturization

% Change


σ, S/cm

|S|, µV/K

PF, µW/cm/K2

Κ, /Wm/K


σ, S/cm

|S|, µV/K

PF, µW/cm/K2

Κ, /Wm/K















[36, 148]

































− 68.1

[90, 96]




























* resembles % change in PF which is mentioned at the top of table


The effect of nanostructurisation and texturization of thermoelectric ceramics and their credibility for the improvement of figure of merit is discussed. The most typical thermoelectric materials and their heat-recovery range are summarized. Thermoelectric parameters can be tuned by texturization using various methods such as reactive template grain growth method, hot press, spark plasma sintering, hotforging, etc. The representation in Fig. 15 makes it clear that more studies on ZnO, In2O3 Ca3Co4O9 and other oxide-based systems have to be done in the future as they are promising for mid to high-temperature heat-recovery applications. Figure 15 is a representation of various thermoelectric materials classified based on the heat-recovery range (adapted from [147] with modification). The times ahead are expected to see a very robust alternative to the existing alloy-based thermoelectric modules based on oxide materials. A lot of work is already going on in developing the thermoelectric modules using non-metallic materials. Certainly, the progress in nanostructuring and techniques to sinter the powders without significantly affecting the nanostructure will impact the performance of newly developed thermoelectric materials.
Fig. 15

Thermoelectric materials classified based on environmental friendliness and heat-recovery range [adapted and

modified from Ohtaki et al. [147]]



The authors would like to acknowledge the Department of Science & Technology-Science & Engineering Research Board (DST-SERB) for the funds received under the Grant number: SERB/F/3112/2014-15. R. Prasad would like to acknowledge Symbiosis International (Deemed University) for the award of Senior Research Fellowship.


This study was funded by Department of Science & Technology–Science & Engineering Research Board (DST-SERB), India (Grant Number: SERB/F/3112/2014-15).

Compliance with ethical standards

Conflict of interest

The authors declare that we have no conflict of interest.


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Authors and Affiliations

  1. 1.Symbiosis International (Deemed University)Symbiosis Institute of TechnologyPuneIndia

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