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Open Access Short Review

Perovskite Oxide Thermoelectric Module - A Way Forward

Abanti Nag *

  1. Materials Science Division, CSIR - National Aerospace Laboratories, Bangalore, India

Correspondence: Abanti Nag

Academic Editor: Wei Wang

Special Issue: Design and Development of Perovskite Materials for Energy Conversion Devices

Received: July 27, 2023 | Accepted: October 07, 2023 | Published: October 11, 2023

Catalysis Research 2023, Volume 3, Issue 4, doi:10.21926/cr.2304024

Recommended citation: Nag A. Perovskite Oxide Thermoelectric Module - A Way Forward. Catalysis Research 2023; 3(4): 024; doi:10.21926/cr.2304024.

© 2023 by the authors. This is an open access article distributed under the conditions of the Creative Commons by Attribution License, which permits unrestricted use, distribution, and reproduction in any medium or format, provided the original work is correctly cited.


In the era of renewable and sustainable energy, perovskite materials remain pioneers as energy harvesting materials, be it thermoelectric waste heat harvesting or photovoltaic solar cell application. Oxide perovskite material is an emerging thermoelectric material in solving energy shortage issues through waste heat recovery. The chemical and structural stabilities, oxidation resistance, and cost-effective and straightforward manufacturing process are a few advantages of the oxide-based thermoelectric materials. The perovskite thermoelectric materials and module thereof does not require any vacuum bagging for operation at high temperature, irrespective of the application environment. Perovskite CaMnO3 displays a high Seebeck coefficient (S~-350 μV/K) due to correlated electron structure and low thermal conductivity (3 W m-1 K-1) but high electrical resistivity simultaneously. The electrical resistivity of CaMnO3 can be tuned by electron doping at the Ca-site and Mn-site. Electron doping by substituting Mn3+ with trivalent rare-earth ions increases the carrier concentration in the CaMnO3 system by partially reducing Mn4+ to Mn3+, improving electrical conductivity without altering the Seebeck coefficient. The dual-doped Ca1-xYbx/2Lux/2MnO3-based n-type perovskite thermoelectric material showed a much higher power factor than undoped CaMnO3 and proved to be an efficient perovskite from the application point of view. The thermoelectric module, in combination with CaMnO3 as an n-type element and Ca3Co4O9 or doped-Ca3Co4O9 as the p-type element, is the most efficient device reported to date. The lab-scale power generation experiment is carried out for 4-element and 36-element modules consisting of perovskite Ca1-xYbx/2Lux/2MnO3 as n-type elements and Ca3Co4O9 as p-type elements. The results showed the challenges of up-scaling the perovskite module for high-temperature waste heat harvesting applications.

Graphical abstract

Click to view original image


Perovskite oxide; thermoelectric module; power harvesting; waste heat

1. Introduction

Thermoelectric, as the word explains, represents the direct conversion of heat energy, waste heat, to electrical energy [1,2,3]. In the present scenario of continuous depletion of natural energy sources and the alarming situation of environmental pollution and global warming, there is a need for alternative sources of eco-friendly energy. Reducing waste heat to electricity is an option, as any industrial process generates lots of heat energy, which eventually goes wasted. Conventional systems for heat energy conversion, such as Rankine engines, involve moving parts that make them bulky and unsuitable for use in remote locations as they require constant maintenance. On the other hand, thermoelectric energy conversion using thermoelectric materials does not involve moving parts and, thereby, zero maintenance [4,5,6]. The word thermoelectric is a generic term for three related effects, viz. Seebeck result denotes voltage built-up in certain materials upon exposure to a temperature gradient, the Peltier effect describes heat absorption or release rate at materials junction on applying electric current, and the Thompson effect denotes a change in heat flux density of a material in a temperature gradient allowing current density to flows [7]. Thermoelectric energy harvesting involves the Seebeck effect, the principle of which was followed in simple devices such as thermocouples. The most prerequisite phenomenon of efficient thermoelectric energy harvesting is the thermoelectric materials used in the machine. A dimensionless quantity called the figure-of-merit (ZT) defines the performance of thermoelectric materials [8,9]. A considerable Seebeck coefficient (α), high electrical conductivity (ρ), and low thermal conductivity (κ) result in maximum ZT according to the following relationship [10].

\[ ZT=\frac{\alpha^{2}\sigma}{\kappa}T \tag{1} \]

Now all the physical parameters defining ZT of thermoelectric material are functions of the charge carrier concentration of the materials; while electrical and thermal conductivity increases with charge carrier concentration, the Seebeck coefficient decreases. It is reported that to achieve maximum figure-of-merit, the optimal carrier concentration of the materials should be 1018-1021 cm-3, which falls under the category of heavily doped semiconductors [11,12]. As Seebeck coefficient and thermal conductivity are temperature-dependent parameters, different materials have performance peaks at optimal temperature window, e.g., Bi-Te-based materials show ZT of 0.8-1.1 around 200°C [13,14], Pb-Te-based alloys realize ZT of 1.2 between 200-600°C [15,16,17,18,19,20] and Si-Ge based alloys reach ZT of 0.5-0.9 above 600°C [21,22,23]. Other intermetallic alloys, such as skutterudites, clathrates, and Heusler alloys, are also reported to show ZT values up to 1 [24,25]. However, the aforesaid intermetallic alloys are primarily toxic and non-abundant, unstable in the open atmosphere, and thereby impact the cost and the durability of the thermoelectric module fabricated using intermetallic alloys. Unlike intermetallic alloys, transition metal oxide-based thermoelectric materials are more appropriate for high-temperature applications due to their inertness in chemical and oxidative environments [26,27,28,29]. However, metal oxides are considered inefficient entrants for thermoelectric applications because of high vibrational frequencies (high k) and low carrier mobility (high r) arising from highly polarized metal-oxygen ionic bonds with narrow orbital overlap and high bond energy. Only recently, the single crystal of NaxCoO2 has been reported with ZT close to unity, indicating oxide materials can be competitive with intermetallic alloys [30].

Waste heat recovery through thermoelectric materials requires the fabrication of a thermoelectric module device [31]. A thermoelectric module consists of n- and p-type materials in which electrons and holes participate in the conduction mechanism. Figure 1 shows the schematic of the thermoelectric module. Unlike traditional intermetallic alloys in which one material can be tuned to deliver both n- and p-type conduction, the conduction of metal oxides is uni-polar and arises mainly from an intrinsic defect. The n- and p-type elements are serially connected to flow electrically and vertically the heat from the hot zone to the cold zone to exhibit the conversion of heat energy to electricity in a thermoelectric module. The Seebeck voltage of individual legs gets added up, leading to the current flow through an external load resistance. The performance of the thermoelectric module depends on the hot (TH) and cold (TC) side temperatures it experiences, the temperature gradient (ΔT), and the ZT of the materials. Thus, the efficiency (η) of the thermoelectric module to convert heat (Q) into electrical power (P) can be represented as [10]:

\[ \eta=\frac{\Delta T}{T_{H}}\times\frac{\sqrt{1+Z_{m}T}-1}{\sqrt{1+Z_{m}T}+{}^{T_{C}}\big/_{T_{H}}} \tag{2} \]

where, ΔT = TH - TC and Zm is the figure-of-merit of the module

\[ Z_{m}=\frac{\bigl(S_{n}-S_{p}\bigr)}{\bigl(\rho_{n}+\rho_{p}\bigr)\bigl(\kappa_{n}+\kappa_{p}\bigr)} \tag{3} \]

Click to view original image

Figure 1 Single module configuration.

Therefore, the increased temperature gradient corresponds to the increased available heat for conversion following the Carnot efficiency. The literature has reported that a ZT ~ 1 is required for sufficient energy conversion (10%). To compete with the conventional heat pump, ZT ~ 3 is needed. As a rule of thumb, a thermocouple fabricated from thermoelectric materials with an average ZT of 1.5 would have an efficiency of 20% when operated at a temperature gradient of 500 K [8].

Thermoelectric can become competitive for small applications requiring less than 100 W because it is simple, compact, inexpensive, and easily scalable [32,33]. There is an enormous demand for power harvesting at high temperatures to enable remote sensing technologies. Standalone wireless sensor systems operating at a high temperature require power supplies that can provide adequate power (at a level of 300-500 mW) for operation at a temperature of 500°C in an oxidizing environment. These systems do not exist presently. Therefore, this milestone is a stepping-stone towards developing higher power (1 W) systems with an ambient heat sink. This article summarizes an overview of recent progress on peroxide-based thermoelectric modules with an inclination towards the application in natural environments. An example module has been fabricated and tested to understand the future of perovskite-based thermoelectric modules.

2. Perovskite Oxide Thermoelectric Materials as n-Type Elements

Perovskite-oxides [34] is described by the general formula ABO3, where 'A' can be rare earth, alkaline earth, alkali, and other large ions such as Pb2+ and Bi3+ and 'B' ions can be 3d, 4d, and 5d transitional metal ions. The perovskite SrTiO3 and CaMnO3 are the most promising n-type thermoelectric oxides.

Stoichiometric SrTiO3 is isotropic cubic perovskite in which the 3d t2g orbital of TiO6 octahedron lies in the conduction band. The stoichiometric SrTiO3 exhibits an insulating character with a band gap of 3.2 eV due to the d0 configuration of Ti4+. The semiconductor behavior of SrTiO3 is experienced by doping at A and B-site as follows, where Ln and M represent the rare earth ions and transition metal ions, respectively [35]:


\[ Ln_{2}O_{3}+2BO_{2}\rightarrow2Ln_{A}+2B_{B}^{x}+2e^{'}+6O_{O}^{x}+\frac{1}{2}O_{2}\uparrow \tag{4} \]


\[ 2AO+M_{2}O_{5}\rightarrow2M_{B}+2A_{A}^{x}+2e^{'}+6O_{0}^{x}+\frac{1}{2}O_{2}\uparrow \tag{5} \]

Electron doping shifts the Fermi energy from the forbidden band to the conduction band, making the system conductive through polaron formation. A-site substitution by La and B-site substitution by Nb are widely studied for SrTiO3. A ZT of 0.27 at 1073 K is reported by Ohta et al. for La-doped SrTiO3 single crystal [36]. The power factor of La-doped SrTiO3 (28-36 mW cm-1 K-1) is comparable to Bi2Te3; however, the high thermal conductivity of 9-12 W m-1 K-1 causes a low figure-of-merit in the system. Wang et al. reported suppression of thermal conductivity in mesoporous silica (MS)-SrNb0.15Ti0.85O3 composites and Nb-doped SrTiO3 with yttria (Y2O3) stabilized zirconia (YSZ) nano-precipitates through the formation of thermally insulating second phase at grain boundaries [37]. The ZT values achieved were 0.165 and 0.2 at 900 K, respectively. Similarly, a high ZT of 0.33 at 900 K was reported for Nb-doped polycrystalline SrTiO3 coated with surface-modified nano-sized titania (TiO2) [38]. Park et al. carried out chemical colloidal synthesis accompanied by the SPS process to develop La-doped SrTiO3 with nano-grain that resulted in a ZT of 0.37 at 973 K [39]. Dehkordi et al. adopted a solid-state reaction and SPS technique to prepare Sr0.85Pr0.15TiO3, resulting in a ZT of 0.35 [40]. Dy and La co-doped SrTiO3 (La0.08Dy0.12Sr0.8TiO3) with nano-sized second phases lowered the thermal conductivity to 2.3 W m K1 at 1074 K and showed ZT of 0.36 at 1048 K [41]. Zhang et al. reported a ZT of 0.40 in Nb-doped SrTiO3, where oxygen vacancies are responsible for high electrical conductivity and low ZT [42]. However, the stability of the SrTiO3-based compound is a concern due to the oxidation of TI to Ti4+ above 700 K in air, which results in insulating behavior [43].

On the other hand, CaMnO3 is an orthorhombic perovskite-type structure that shows G-type anti-ferromagnetism and giant magnetoresistance. CaMnO3 displays a high Seebeck coefficient (S~-350 mV/K) due to correlated electron structure and low thermal conductivity (3 W m-1 K-1) but high electrical resistivity simultaneously [44,45,46]. Mn4+ (3d3) in MnO6 octahedron (t2g3eg0) with negligible Jahn-Teller distortion primarily exhibits insulating character due to its eg0 state. Mn 3d states and O p states are accountable for electrical conductivity in the system. Electron doping at Ca-site and Mn-site increases the carrier concentration in the CaMnO3 system by partially reducing Mn4+ to Mn3+, improving electrical conductivity by a few orders of magnitude. Moreover, oxygen vacancies can also reduce Mn4+ to Mn3+, occupying eg0 state partially occupied. Electron-lattice interaction in the system creates a small polaron responsible for polaron hopping conduction for CaMnO3. Further, formations of Mn3+ introduce Jahn-Teller distortion in the design, thereby reducing the thermal conductivity. The electron doping is experienced at Ca-site by rare-earth ions and Bi3+ and Mn-site Nb5+, Ta5+, Mo6+, W6+, etc [47,48,49,50,51]. Yb-doped CaMnO3 shows a ZT of 0.16 at 1000 K, the highest among rare-earth doped CaMnO3 [52]. Kabir et al. reported ZT of 0.25 at 973 K in Bi-doped CaMnO3, where incorporating Bi improves electrical conductivity with marginal reduction of the Seebeck coefficient [53]. The highest ZT value reported for A-site doping is for dual-doped Ca0.96Dy0.02Yb0.02MnO3 with a ZT of 0.27 [54]. Among the B-site doped CaMnO3, W-doped CaMn0.96W0.04O3 exhibit ZT of 0.25 at 1225 K [55]. However, the highest ZT reported in the n-type CaMnO3 system so far is Nb-doped CaMn0.98Nb0.02O3 with a ZT of 0.3 [56].

Double perovskite-based oxide (A2B'B "O6) materials caught attention recently as thermoelectric (TE) materials due to their environment-friendly nature, high-temperature stability, better oxidation resistance, and lower processing cost compared to conventional chalcogenides and intermetallics with Ba2CoNiO6 results in a ZT around 0.8 at room temperature [57,58,59,60,61].

3. p-Type Element Ca3Co4O9

Ca3Co4O9 is "misfit layered” cobalt oxide with a modulated layered structure. The structure of Ca3Co4O9 ([Ca2CoO3]RS[CoO2]1.62) consists of a single CdI2 type CoO2 layer having CoO6 octahedra interleaved with rock-salt- (RS-) type [Ca2CoO3] layers [62]. The rock-salt layer controls the lattice thermal conductivity i.e., the in-plane thermal conductivity reduces with increasing rock-salt layers, keeping the electronic properties of the CoO2 block unperturbed [63,64]. The thermoelectric properties of misfit-layered oxide single crystals showed the most significant ZT = 1.2-2.7 for Ca3Co4O9 at 873 K, and ZT ≥ 1.1 for Bi2Sr2Co2O9 at 1000 K [65,66]. However, the strong anisotropy in the thermoelectric parameters and the non-uniform crystal growth prevent the performance of the bulk compositions, resulting in a maximum ZT of 0.5 [67,68,69,70].

4. Perovskite Oxide-Based Thermoelectric Module

Perovskite CaMnO3 is one the most widely explored n-type thermoelectric materials, and several researchers have investigated the power generation capabilities of CaMnO3-based modules. Several groups have reported CaMnO3-based oxide thermoelectric modules where doped and un-doped CaMnO3 were used as n-type elements. Table 1 summarizes the perovskite CaMnO3-based thermoelectric module reported in the literature based on power output [71,72,73,74,75,76,77,78,79,80,81,82]. The thermoelectric module, in combination with CaMnO3 as an n-type element and Ca3Co4O9 or doped-Ca3Co4O9 as the p-type element, is the most efficient device reported to date. We have established that dual-doped Ca1-xLux/2Ybx/2MnO3 is one of the efficient n-type elements in the perovskite CaMnO3 series. Similarly, Ca3Co4O9 without any doping stands for efficient p-type material.

Table 1 The perovskite CaMnO3-based thermoelectric module based on power output as reported in the literature.

5. Development of Materials

The powder sample of dual-doped n-Ca1-xLux/2Ybx/2MnO3 and p-Ca3Co4O9 were prepared by the sol-gel methodology. The n-Ca1-xLux/2Ybx/2MnO3 powder samples were pressed in rectangular blocks and sintered at 1200°C for 5 h. Conversely, p-Ca3Co4O9 powders were sintered through a hot-press technique at 1098 K and a pressure 25 MPa. The n and p-type rectangular blocks were diced into 3 mm × 3 mm × 5 mm cuboids to fabricate the thermoelectric module.

6. Fabrication of Thermoelectric Module

4-elements and 36-element thermoelectric modules were fabricated to study heat to electrical energy conversion in the lab level. The n-Ca0.99Lu0.005Yb0.005MnO3 and p-Ca3Co4O9 elements were sandwiched alternately between insulating alumina plates of thickness 6 mm. The n and p connections were built between protecting alumina plates with silver plates and silver paint. One side of the alumina plate acted as a hot end, and the other side was the cold end. The hot end was attached to the heat source, and the output voltage was recorded from the cold end. The heat sink can be attached to the cold end. However, the lab scale experiment was carried out on a standalone module without attaching any heat sink.

7. Thermoelectric Power Generation [8]

The Seebeck, Peltier, Thompson, and Joule effects are the four basic physical phenomena governing thermoelectric generator operation. Mathematically, the energy flow through a unit volume under steady-state conditions is expressed as follows:

\[ TJ\frac{dS}{dx}+\tau J\frac{dT}{dx}-\rho J^{2}-\frac{d}{dx}\left(\kappa\frac{dT}{dx}\right)=0 \tag{6} \]

where T = Temperature, J = electrical current density, S = Seebeck coefficient, τ = Thompson coefficient, ρ = electrical resistivity, and κ = thermal conductivity of the materials. Considering the negligible Thompson effect (as explained in Ref. 8, Chapter 2), the heat flow at the hot side is (where I is the current flow) can be represented as:

\[ \begin{aligned} Q_{h}& =\left[S_{TEG}T_{H}I+K_{TEG}(T_{H}-T_{C})-\frac{1}{2}I^{2}R_{TEG}\right] \\ &=\left[\left(S_{p}+S_{n}\right)T_{H}I+\left(K_{p}+K_{n}\right)(T_{H}-T_{C})-\frac{1}{2}I^{2}\Big(R_{p}+R_{n}+R_{contact}\Big)\right] \end{aligned} \tag{7} \]

Similarly, the heat flow from the cold side can be represented as:

\[ \begin{aligned} Q_{c}& =\left[S_{TEG}T_{H}I+K_{TEG}(T_{H}-T_{C})+\frac{1}{2}I^{2}R_{TEG}\right] \\ &=\left[\left(S_{p}+S_{n}\right)T_{H}I+\left(K_{p}+K_{n}\right)(T_{H}-T_{C})+\frac{1}{2}I^{2}\big(R_{p}+R_{n}+R_{contact}\big)\right] \end{aligned} \tag{8} \]

The resistance of the module (RTEG) is collected form of the resistance of n-element (Rn), p-element (Rp), and the contact resistance (Rcontact).

Together, the power produced by the module (PTEG) can be represented as:

\[ P_{TEG}=Q_{H}-Q_{C}=S_{TEG}(T_{H}-T_{C})I-I^{2}R_{TEG} \tag{9} \]

A voltage of the module:

\[ V_{TEG}=S_{TEG}(T_{H}-T_{C})-IR_{TEG} \tag{10} \]

8. Power Output Analyses of Fabricated 4-Elements TE Module

The lab-scale testing was initially undertaken on the fabricated 4-element TE module. A hot plate was used for this purpose. The hot side of the module was kept on a hot plate, and the temperature of the hot-plate was raised to 773 K with a uniform heating rate. Open-circuit voltage was measured on the module's cold side during the heating-up process. To measure the output voltage, the Pt-lead wires were attached to the module's cold side. The output voltage was recorded by a digital multimeter-data acquisition system in the open air without any coolant to understand the module's performance in standalone conditions. The four-probe Delta mode technique measured the module resistance, including internal and contact resistance. The voltage terminals were attached to the same position behind the current airports to measure the resistance. Figure 2 shows the power generation properties of the 4-element module. The I-V characteristics showed a maximum intercept at 0.212 V with the hot-side temperature (TH) of 773 K at open air (Figure 2a). The P-V plot showed that the full power achieved was 11 mW (Figure 2b). Figures 2c and 2d show the variation of open circuit voltage, closed circuit voltage (I = 20 mA), and powder output with varying temperatures. The power obtained under a closed circuit is 4 mW at 500°C.

Click to view original image

Figure 2 Calculated (a) module voltage and (b) module power output of fabricated 4-element thermoelectric module under various hot-source temperatures. (c) Open circuit voltage and output voltage calculated at 20 mA current flow and (d) power output with temperature variation.

9. Power Output Analyses of Fabricated 36-Elements TE Module

To understand how scaling up affects the power generation characteristics of the thermoelectric module, the 36-elements module was fabricated similarly with each element dimension of 3 mm × 3 mm × 5 mm. The module was tested under the same conditions as of 4-elements module. Figure 3 shows the power generation properties of a 36-elements module with hot-side temperatures up to 500°C. The I-V plot conducted a maximum intercept at 0.85 Volt with a hot-side temperature (TH) of 500°C where the other side has been experiencing the open-air atmosphere (Figure 3a). The P-V characteristics showed that the maximum power obtained under this condition is up to 18 mW (Figure 3b). Figures 3c and 3d showed the variation of open circuit voltage, closed circuit voltage (I = 20 mA), and powder output with varying temperatures. The power obtained under a closed circuit is 13 mW at 500°C.

Click to view original image

Figure 3 Calculated (a) module voltage and (b) module power output of fabricated 4-element thermoelectric module under various hot-source temperatures. (c) Open circuit voltage and output voltage calculated at 20 mA current flow and (d) power output with temperature variation.

10. Challenges and Future Directions

There were a lot of challenges on thermoelectric modules that need to be addressed for efficient transformation of heat to electricity. The significant advantage is that the figure-of-merit of thermoelectric materials gets halved in the module figure-of-merit due to parasitic losses such as thermal and electrical resistance at the contact points and thermal losses from the side of the thermoelectric elements. Therefore, the fabrication of the module to reduce the heat losses on the one hand and overcome the contact resistance on the other are the daunting tasks to achieve the maximum performance from the thermoelectric module. Thus, the materials development to obtain high ZT alone cannot solve the practical problem of applying thermoelectric materials. Engineering thermoelectric modules with nominal heat loss and contact resistance is one of the aspects of futuristic device technology.


The author thanks Council of Scientific and Industrial Research and National Aerospace Laboratories for financial support.

Author Contributions

The author did all the research work of this study.

Competing Interests

The author has declared that no competing interests exist.


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