Cheng Chi, Gongze Liu, Meng An, Yufeng Zhang, Dongxing Song, Xin Qi, Chunyu Zhao, Zequn Wang, Yanzheng Du, Zizhen Lin, Yang Lu, He Huang, Yang Li, Chongjia Lin, Weigang Ma, Baoling Huang, Xiaoze Du & Xing Zhang
Nature Communications volume 14, Article number: 306 (2023)
Abstract
The giant thermopower of ionic thermoelectric materials has attracted great attention for waste-heat recovery technologies. However, generating cyclic power by ionic thermoelectric modules remains challenging, since the ions cannot travel across the electrode interface. Here, we reported a reversible bipolar thermopower (+20.2 mV K−1 to −10.2 mV K−1) of the same composite by manipulating the interactions of ions and electrodes. Meanwhile, a promising ionic thermoelectric generator was proposed to achieve cyclic power generation under a constant heat course only by switching the external electrodes that can effectively realize the alternating dominated thermodiffusion of cations and anions. It eliminates the necessity to change the thermal contact between material and heat, nor does it require re-establish the temperature differences, which can favor improving the efficiency of the ionic thermoelectrics. Furthermore, the developed micro-thermal sensors demonstrated high sensitivity and responsivity in light detecting, presenting innovative impacts on exploring next-generation ionic thermoelectric devices.
Introduction
Ionic-conducting polymer composite ionic thermoelectric (i-TE) materials have attracted wide attention as they exhibited high ionic thermopower or Seebeck coefficient1,2,3. Different from electrons and holes in the electrical-conducting thermoelectric (e-TE) materials, the charge carriers of the i-TE materials are free cations and anions. Under a temperature gradient, ions will move across the i-TE material from the hot side to the cold side. Due to the mass transportation difference between cations and anions, they build an internal ionic Seebeck voltage based on the Soret effect4,5. Moreover, the introduced more interactions between ions and polymers significantly enhanced the change in Eastman entropy of polymer composites6,7,8, favoring obtaining a high ionic thermopower or Seebeck coefficient (Si) of ~10 mV K−1, which is about two orders higher than that of semiconductor e-TE materials (~200 μV K−1)9,10,11. Moreover, polymer composites essentially exhibit the advantages of flexibility, low cost, and environment friendly, which are regarded as the most promising candidates for low-grade heat harvesting, thermal sensing, and sustainable energy developments12,13,14,15.
Usually, it is necessary to connect p- and n-type e-TE materials in series to build TE modules to generate continuous electricity and maximum output power in practical applications. Regarding the emerging i-TE materials based on the Soret effect16,17, ions show preferential movement along or against thermal gradients, and the ionic thermoelectric capacitor (i-TEC) was developed to convert heat to electricity5,18,19. However, the i-TEC cells cannot produce a continuous current flow under a constant temperature difference (ΔT). Because they operated in a capacitive mode and ions only accumulated at the interface near electrodes, ions cannot transport across the electrode interface20,21,22. The heat source must be repeatedly established and removed for every charging and discharging cycle to ensure ions move back and forth, which is not convenient in practical applications. Although the i-TE devices periodically contacted the heat and cold source providing another way to convert heat to power, the ionic thermoelectric generators (i-TEGs) still need to detach from the heat sources and take time to re-establish the temperature difference in every cycle, which increases energy consumption and reduce the conversion efficiency. Further efforts are needed to address the limitations of ionic thermoelectric technology applications.
Achieving the ions to move back and forth alternately under a constant heat source is a major milestone to achieve producing cyclic energy by i-TEGs. Generally, the thermopower is an intrinsic property of i-TE material, and the i-TE material usually exhibits only one type of thermopower, either p- or n-type characteristics, which is determined by the charge type of ions that dominates the thermodiffusion process. Some recent work reported that the sign of thermopower could be tuned to the opposite by modifying the internal structure or compositions by doping methods23,24,25, however, the process of tuning the sign of thermopower can only be converted once and is not reversible. Unluckily, the ions of i-TE materials cannot have reciprocating motion behaviors under a constant heat source, up to now, producing continuous energy remains challenging.
Here, we reported a unique reversible bipolar thermopower characteristic of the same solid-state i-TE materials by manipulating external electrodes. Specifically, the same polymer composite exhibited a p-type thermopower of +20.2 ± 4 mV K−1 and an n-type thermopower of −10.2 ± 0.83 mV K−1 when assembling with different electrodes at 298 K and 70% relative humidity (RH). It is found that the strength of the interfacial interaction and the polarization arrangement of ions differed significantly relating to the different electrode materials. Moreover, we proposed a promising i-TE generator prototype with the bipolar thermopower property, which successfully achieved producing cyclic energy under a constant heat source only by alternately exchanging electrodes. Meanwhile, a developed micro-thermal sensor exhibited high sensitivity when detecting small fluctuations of heat, bringing significant and innovative impacts on the development of next-generation i-TE devices.
Results
Bipolar thermopower property
The developed solid-state i-TE polymer composite material comprised of poly(vinylidene fluoride-co-hexafluoropropylene) (PVDF-HFP), propylene carbonate (PC), and sodium trifluoromethanesulfonimide (NaTFSI), which was abbreviated as PNP and prepared by the solution casting method (details in Supplementary methods). Here, a series of different electrode materials, aligned carbon nanotube (a-CNT), multi-walled CNT (MWCNT), single-walled CNT (SWCNT), and metal electrodes (Au, Pt, and Cu) are selected to serve as test electrodes. For measuring the thermopower, pieces of rectangular PNP films with identical sizes were cut from one matrix and were suspended on these E|E electrodes, which were named the E|PNP|E systems, E = (a-CNT, MWCNT, SWCNT, Au, Pt, and Cu). When starting to apply a series of positive and negative temperature gradients (±ΔT), the initial hot and cold terminals of the PNP were connected to the work and counter electrodes of the voltage meter, respectively, which is used to monitor the voltage variations in real-time (Fig. S1, Supplementary Information). For the Cu|PNP|Cu system (Fig. 1a, top), the sign of the generated voltage between the hot side and cold side (ΔVCu = Vhot−Vcold) is negative in response to a positive ΔT, as shown in Fig. 1b (blue curve). It was implied that the Na+ cations dominated the thermodiffusion process2,24,26, performing a p-type characteristic, as illustrated in Fig. 1c (left). Then, a series of temperature differences (ΔT = ±6 to ±1 K) were applied to the Cu|PNP|Cu systems. The produced thermoelectric voltage differences of p-type Cu|PNP|Cu systems followed a good linear relationship with the temperature differences, as shown in (Figs. 1d and S2a, Supplementary Information). The thermopower or ionic Seebeck coefficient (Si) of i-TE material is defined as Eq. (1)24
Si=−(VH−VC)/(TH−TC)�i=−(�H−�C)/(�H−�C)
(1)
where VH and VC correspond to the voltage of the hot electrode at temperature TH and the cold electrode at temperature TC, respectively. By fitting the slope of the measured data, the calculated thermopower of the p-type Cu|PNP|Cu was 20.2 ± 4 mV K−1 at RH 70%, 298 K (Fig. 1e). To test the stability of the Cu electrode, the X-ray photoelectron spectroscopy (XPS) curves of Cu electrodes before and after measurement are overlapped well (Fig. S3, Supplementary Information) and no new peaks were observed on the used Cu electrodes, representing no chemical reaction on the Cu electrode. And there is no color change on the surface of the used Cu electrode and no obvious decay of the produced thermoelectric voltage of the Cu|PNP|Cu system after 30 cycles test, suggesting high stability of the Cu electrodes with the PNP composite. Moreover, the control experiment by using the noble metal Pt and Au electrodes to measure the thermopower of PNP was carried out. The measured thermopower of Pt|PNP|Pt and Au|PNP|Au are 19.3 ± 3.2 and 21.1 ± 3.8 mV K−1, respectively (Figs. 1d, e and S4, Supplementary Information) under the same test condition, which is consistent with the thermopower of Cu|PNP|Cu system.
Interestingly, when the same PNP film was assembled with a-CNT electrodes (Fig. 1a), the sign of the produced ΔVa-CNT (ΔVa-CNT = Vhot−Vcold) of the a-CNT|PNP|a-CNT system was positive in response to a same positive ΔT (red line, Fig. 1b), which is opposite to the sign of the Cu|PNP|Cu system (blue line, Fig. 1b). Accordingly, the positive ΔVa-CNT suggested that a higher number of TFSI– anions moved to the cold side25, and the TFSI– anions dominated the thermodiffusion process of the a-CNT|PNP|a-CNT system (Fig. 1c, right), exhibiting n-type behavior. Thus, the thermal diffusion sequences of Na+ and TFSI– ions have been reversed when assembling with a-CNT electrodes compared to Cu electrodes. In addition, after introducing a series of positive and negative temperature gradients (ΔT = ± 6 to ±1 K) to the a-CNT|PNP|a-CNT system, the sign of the produced thermal voltage is always opposite to the Cu|PNP|Cu system at every ΔT (Fig. S2b, Supplementary Information). After fitting the slope of the measured thermal voltage ΔVa-CNT with the ΔT (Fig. 1d), the calculated thermopower of n-type a-CNT|PNP|a-CNT systems was −10.2 ± 0.83 mV K−1 (Fig. 1e).
In addition, we also conducted to measure the thermopower of PNP using the SWCNT and MWCNT-based electrodes. They also performed n-type characteristics and the measured thermopower of PNP tested by SWCNTs and MWCNTs are −8.17 ± 1.2 and −5.2 ± 1.35 mV K−1, respectively, (Fig. 1d, e). The digital photos of the a-CNT, MWCNT, and SWCNT films are shown in Fig. S5 (Supplementary Information). Due to their softness and self-adhesive nature, the a-CNT is easy to form tightly contact with the PNP composite compared to thick SWCNT and MWCNT films. Having good contact is of great significance for reducing contact resistance and improving the ionic thermoelectric conversion performance. Meanwhile, the a-CNT bundles are well aligned along the length direction with small entanglements, they exhibited higher conductivity of 3 × 105 S m−1, a lower sheet resistance of 1–1.5 Ω m−2, a stronger mechanical strength of ~120 MPa, low cost and high stability and flexibility compared to common SWCNT and MWCNT-based films, as summarized in Table S1 (Supplementary Information).
Moreover, the thermopowers of the PNP samples at different relative humidity (50% RH–90% RH) were further investigated. The ionic thermopower of the p-type Cu|PNP|Cu system increased from 8.12 mV K−1 (50% RH) to 26.62 mV K−1 (90% RH), (Fig. S6, Supplementary Information). The porous structure of PVDF-HFP and the hydrophilic nature of sodium salt tend to absorb water from the moisture environment and could fill the space in the PVDF-HFP matrix. The absorbed water could help improve the dissociation of the NaTFSI ion pairs by weakening the electrostatic attraction6,27. Further increasing the humidity level may create continuous water percolation paths or ion transport channels, which could reach a saturation state. The magnitude of the ionic thermopower of the n-type a-CNT|PNP|a-CNT sample slightly increased from −8.11 ± 1.5 mV K−1 at 50% RH to −10.2 ± 0.83 at 70% RH, which was caused by water absorption effect as discussed above. Further increasing the humidity level, the thermopower reached a relative saturation value of −9.7 ± 0.86 mV K−1 at 80% RH (Fig. S7, Supplementary Information). Thus, varying the humidity level only contributes to the change in the magnitude of the thermopower of Cu|PNP|Cu and a-CNT|PNP|a-CNT systems, but it does not influence the sign of the p-type characteristic of the Cu|PNP|Cu and the n-type behavior of a-CNT|PNP|a-CNT.
Bipolar thermopower property analysis
Interestingly, the same PNP material with different electrodes performed p- and n-type characteristics by assembling with different external electrode materials. The above findings strongly suggested the electrode materials induce significant disparities in the transportation kinetics of ions near the electrodes. The p-type Cu|PNP|Cu and n-type a-CNT|PNP|a-CNT were selected to further investigate the electrode effect on the thermopower.
Accordingly, we conducted a real-time in-situ Raman method to dynamically characterize the ions thermodiffusion process under a ΔT. Intrinsically, the peak location and the intensity of the Raman spectrum can accurately detect the existence of ions and their concentration28,29. The PNP shows a predominate peak at 742 cm−1, which is donated to the vibrational mode corresponding to the expansion and contraction of the whole TFSI– ions30, whereas no such peak was observed from the mixture of PVDF-HFP and PC molecular, as shown in Fig. S8 (Supplementary Information). Accordingly, the Raman peak located at ~742 cm−1 related to TFSI– anion is selected to investigate the electrode effect on the ion thermodiffusion process of the Cu|PNP|Cu, and a-CNT|PNP|a-CNT system.
As illustrated in Fig. 2a, the Cu|PNP|Cu or a-CNT|PNP|a-CNT systems were vertically exposed to the laser source when performed test and the ΔT was applied across PNP samples from the left (hot) to right (cold) side. The digital photos of the Cu|PNP|Cu and a-CNT|PNP|a-CNT systems are shown in Fig. S9a, b (Supplementary Information). The Raman line scans, consisting of ~20 scanning cycles (Fig. S9c, d, Supplementary Information), were performed every 10 s on a fixed location near the hot side interface of PNP/electrode (PCu and Pa-CNT). It is observed that the magnitude of the Raman peak at ~742 cm−1 corresponding to TFSI– ions at Pa-CNT point varied slightly in the first 30 s (Fig. 2b, e). Interestingly, after 30 s, it is clear to find that the amplitude of the peak intensity of TFSI– ions significantly reduced until 160 s, which proves that the concentration of TFSI– ions at the Pa-CNT point decreased. As the TFSI– ions near the interface of the hot side was motivated by heat, these TFSI– ions started departing from the hot side to transport to the cold side. Accordingly, the TFSI– ions diffused away from the hot side toward the cold side and led to a decrease in the concentration of TFSI– ions near the hot interface after a certain period. The intensity of peak at ~742 cm−1 reached a relatively steady state value of ~60% of the initial status. In contrast, for the Cu|PNP|Cu system, the variation of the magnitude of the TFSI– peak intensity at PCu region is very limited (Fig. 2c, e), which is much more weakened than the a-CNT|PNP|a-CNT system. The Raman mapping strongly suggests that the TFSI– ion is more active near the a-CNT electrode than that of the Cu electrode, demonstrating the a-CNT electrode is more favorable for the diffusion of TFSI− ions.
Further, the surface morphology of Cu and a-CNT electrodes was studied by the scanning electron microscope (SEM). It is observed that the Cu electrode has a flat surface morphology, which is quite distinct from the rough surface of the a-CNT electrode in Fig. S10 (Supplementary Information). As known, the rough a-CNT electrode surfaces introduced a larger surface area and much more ions adsorption sites of PNP film compared with that of the flat Cu electrodes31. Accordingly, the molecular dynamics (MD) simulations were further performed to investigate the interfacial absorption behaviors of NaTFSI (C2F6NNaO4S2) with the a-CNT and Cu electrodes at the atomic scale (detail in Supplementary Methods). Fig. S11 (Supplementary Information) showed the top and side view of the MD snapshots of the Na+ cations and TFSI– anions on the Cu and a-CNT electrode surface at 300 K, respectively. The arrangement of TFSI– anions on electrode surfaces were characterized by analyzing the radial distribution functions (RDF) of NTFSI-NTFSI-–NTFSI-NTFSI- on these two electrode surfaces at 300 K, as shown in Fig. 2d. The RDF was defined as the probability of finding a nitrogen atom at a certain distance from another tagged nitrogen atom. The RDF of NTFSI-NTFSI-–NTFSI-NTFSI- on a-CNT electrodes surface exhibits two obvious peaks at 4.7 and 7.3 Å (Fig. 2d), indicating the long-range order of TFSI– anions polarization on the a-CNT surface, which is similar to the crystal-like structures32. By contrast, the two peaks of RDF at 6.1 and 7.6 Å on the Cu electrode surface are not well separated, indicating the TFSI– anions are disorderly arranged near the Cu electrodes33, which is also observed from the simulation of the mapping ions distribution near the electrode (Fig. 2g). The difference in the molecular arrangement of the TFSI– anions are associated with the lattice match between the lattice structure of electrode surfaces and the TFSI– anions, similar to the formation of ice crystal on the graphene oxide34. Moreover, it can be observed that the arrangement of TFSI– anions are highly ordered near the surface of a-CNT electrodes compared with the relative disorder distribution of Na+ ions on the a-CNT electrode surface (Fig. 2g). The ordered arrangement decreased the collision probability of TFSI– anions, enhancing the thermodiffusion priority of TFSI– anions near the a-CNT electrode surface compared to the Na+ ions35,36, which is consistent with the Raman experimental observations.
Meanwhile, the MD simulation found there is a significant difference in the number densities of both Na+ cations and TFSI– anions on the a-CNT and Cu electrode surfaces. On the a-CNT electrode surface, the peak position at 1.5 Å of the number density of Na+ cations is much smaller than that of the peak at 4.7 Å of TFSI– number density (Fig. S12a, Supplementary Information). By contrast, on the Cu electrode surfaces, the peak position (3.5 Å) of the number density of Na+ ions is larger than that of TFSI– ions (1.6 Å) (Fig. S12b, Supplementary Information). Such an obvious difference in the number density of ions is strongly related to the interaction strengths between electrodes and ions. The smaller peak position implied stronger interfacial interaction between ions and electrodes37. Hereby, it implied that the interfacial interactions between Na+ ions and a-CNT electrodes are stronger than that of TFSI– ions with a-CNT electrodes. To further quantitively study the interaction energy, the density functional theory (DFT) calculations of the interactions between the (a-CNT and Cu) electrodes and the (TFSI– and Na+) ions are performed38,39 (see the “Methods” section and Fig. S13, Supplementary Information). From the DFT calculation results (Fig. 2f), it’s interesting to find that the TFSI– ions formed a stronger interaction with the Cu electrode (0.53 eV) than that interaction with the a-CNT electrode (0.31 eV). In contrast, the Na+ ions formed a stronger interaction with the a-CNT electrode (1.82 eV) than the interaction strength with the Cu electrode (1.30 eV). The stronger interaction between Na+ ions and the a-CNT electrodes could immobilize part of Na+ ions and induce a larger drag force to Na+ cations, impeding the departure process of Na+ ions from a-CNT electrodes. As a result, the a-CNT|PNP|a-CNT exhibits the n-type characteristic.
Further, it is well known the temperature gradient provided the thermally driven force to motivate ions to depart from the hot side. But few reports have investigated the effect of the competition between the thermally driven force and the interfacial interaction induced by the electrode on the transport behaviors of ions. Hereby, a series of temperature differences (ΔT: 0–25 K) were applied to the a-CNT|PNP|a-CNT system to provide various strengths of thermal-driven force. At the original equilibrium status (ΔT = 0 K), the Na+ cations and TFSI– anions were evenly distributed in the material (Fig. 3a, stage I). Once the heating started, the Na+ and TFSI– ions of the a-CNT|PNP|a-CNT system were motivated, and the voltage between the hot and cold side (ΔVa-CNT) was produced correspondingly. As observed in Fig. 3b (stage II), the produced ΔVa-CNT exhibited a positive value, which suggested a higher concentration of TFSI– anions transported to the cold side (Fig. 3a, stage II), representing the n-type behavior of the a-CNT|PNP|a-CNT system. When the ΔT was raised to 6 K, the amplitude of the produced ΔVa-CNT was also increased. The amplitude of the ΔVa-CNT gradually reached a saturated value when the ΔT reached near 12 K.
Surprisingly, the value of ΔVa-CNT dramatically dropped, and the overall ΔVa-CNT almost became neutral when the ΔT reached about 15 K (Fig. 3b, stage III). It implied that the number of effective Na+ cations diffused from the hot side to the cold side is relatively equal to the amount of TFSI– anions, which compromised the ionic Seebeck effect. It is suspected that the larger ΔT greatly strengthened the thermally driven force and enabled more amount of Na+ cations to leave the hot a-CNT electrode, gradually balancing the ΔVa-CNT, as illustrated in Fig. 3a (stage III). Moreover, the ΔVa-CNT was even changed to the negative direction under a large temperature difference (ΔT > 20 K) (Fig. 3c, stage IV). It is inferred that the gradually enhanced thermal-driven force on Na+ ions is larger than the attraction force by the a-CNT electrode. As a result, a greater number of free Na+ cations departed from the hot electrode Na+ cations and dominated the thermodiffusion process (Fig. 3a, stage IV), which transformed from n-type to p-type characteristics of the a-CNT|PNP|a-CNT. Moreover, the thermoelectric voltage ΔVa-CNT always exhibited a negative value during cyclic repeated testing at ΔT = 25 K, confirming the p-type behavior at a higher ΔT.
Clearly, the ions-electrode interfacial interaction and the thermally driven force significantly interfered with the thermodiffusion of Na+ cations and TFSI– anions. As shown in Fig. 3d, when the thermally driven force is lower than the ion–electrode interaction, the transportation of Na+ cations will be restricted by the a-CNT electrodes and the a-CNT|PNP|a-CNT system performing n-type behavior. With the continued increasing ΔT, the thermally driven force was gradually enhanced. When the thermally driven force is stronger at a large ΔT, the restricted cations will depart from the hot side and diffuse to the cold side and the number of cations departing from the hot side could increase correspondingly. Until the amount of Na+ cations moving to the cold end exceeds the number of TFSI– anions, the Na+ cations finally rule the thermodiffusion process, making the a-CNT|PNP|a-CNT system back to p-type. In this paradigm, adjusting the external electrode materials can effectively obtain a reversible bipolar thermopower to be capable of proceeding in either of two signs, which is significant to design advanced i-TE cells that generate cyclic energy under a constant heat source.
Additionally, the influence of asymmetric electrodes on the thermopower was further investigated. The PNP film was suspended on one a-CNT electrode and one Cu electrode as shown in Fig. S14 (Supplementary Information), which was donated as the a-CNT|PNP|Cu. The same PNP sample was used throughout the whole test, and the hot and cold sides were fixed to connect the work and counter electrodes of the voltage meter, respectively. Heating Cu side or a-CNT side, the positive sign of the ionic thermal voltages ΔVCu-CNT (VCu−Va–CNT) or ΔVCNT-Cu (Va-CNT−VCu) were produced, and the magnitudes of generated voltage increased with enlarging the ΔT (regions I and II, Fig. S15, Supplementary Information), suggesting the TFSI– ions dominated the thermodiffusion process (Fig. S16, Supplementary Information) and demonstrated n-type behaviors. Interestingly, once transferring the PNP from the hybrid Cu|a-CNT electrode to the symmetric Cu|Cu electrodes, it generated a negative sign of ionic thermal voltage ΔVCu-Cu (VCu−VCu) between the hot side and cold side in the region III (Fig. S15, Supplementary Information), behaving as p-type characteristic. In the following test (region IV, Fig. S15, Supplementary Information), this PNP film was transferred back to the a-CNT|Cu electrode and it performed n-type behavior again. Besides, it showed a high degree of reproducibility in response to the temperature differences after the cyclic test. The measured thermopower of the a-CNT|PNP|Cu system reached about −4.8 mV K−1 (Fig. S17, Supplementary Information), which is around half of the a-CNT|PNP|a-CNT system. It may inspect that half part of the delocalized Na+ cations at the Cu/PNP interface of the a-CNT|PNP|Cu system neutralized the thermoelectric voltage during the thermodiffusion process, compared to the a-CNT|PNP|a-CNT system. Clearly, this asymmetric electrode further confirmed that the manipulation of different electrode materials could lead to bipolar thermopower of the same i-TE PNP materials.
Prototypes of i-TE generators and thermal sensors
The previously reported i-TE supercapacitors5,18,26 always require controlling the heat on and off process to push the back-and-forth movement of ions since the ions only accumulated at the electrode interface, which cannot achieve cyclic power generation under a constant heat source. To address such issues, we demonstrated a promising i-TE generator with an interesting reversible bipolar thermopower property that produces cyclic energy under a constant heat course that only requires switching the external electrodes. The i-TEG consists of 10 pairs of Cu electrodes and a-CNT electrodes which were connected in series to improve the output power, as illustrated in Figs. 4a and S18a (Supplementary Information). In brief, the mechanism is explained as followed. Firstly, the 10 pairs of the patterned Cu|Cu electrodes were tightly pressed to contact with the 10 pieces of PNP films from above (Fig. S18b, Supplementary Information). After inducing a temperature difference across 10 pieces of PNP films, taking the data in the first cycle in Fig. 4c as an example, it generated a negative thermal voltage (Vi) with Cu|Cu electrodes until reached a relatively stable value after heating as more amount of Na+ cations moved to the cold side (Fig. 4b-I). Next, the i-TEG was connected to a load to output power to the external circuit and the voltage Vi dropped to near zero, which was caused by the accumulation of electrons and holes of the electrodes to balance Vi (Fig. 4b-II). Then removing the Cu|Cu electrodes while keeping heating constant, the 10 pairs of the patterned a-CNT|a-CNT electrodes were switched to contact with the 10 pieces of PNP films (Fig. S18c, Supplementary Information) and the external resistor was disconnected simultaneously. It is clear to observe the i-TEG produced an opposite sign of thermal voltage (Fig. 4c). Because using a-CNT electrodes makes the PNP behave the n-type characteristic and the TFSI– anions dominated the thermodiffusion process (Fig. 4b-III). The last step was to connect the external resistor to the i-TEG again to produce the power to the external load (Fig. 4b-IV). Furthermore, after repeatedly alternatively switching the electrodes, the produced thermal voltage of the fabricated i-TEG demonstrated high repeatability after 20 cycles (Fig. 4c). Importantly, the proposed i-TEG achieves generating cyclic power under a constant heat source without the need to turn on/off the heat source or join/separate materials from the heat source. Interestingly, there is no necessity to change the thermal contact between the material and heat source and therefore the temperature difference does not need to be re-established, providing a significant innovative impact for expanding the practical applications.
To further explore the application of ionic thermoelectrics, a micro-solid-state ionic thermoelectric sensor was proposed to detect light-induced temperature fluctuation, which is an essential part of the electronic skin network, thermal management, health monitoring, and other fields40. This micro i-TE sensor with a feature size of 200–300 μm (Fig. 4d) was fabricated by sandwiching the PNP film (i-TE layer) by a bottom electrode layer and a top metal/CNT electrode layer through the micro-electro-mechanical system (MEMS) technologies, which the fabrication process flow was shown in Fig. S19 and Supplementary Methods (Supplementary Information). Briefly, the working mechanism is to utilize the ionic thermoelectric to detect heat difference generated by the light, as illustrated in Fig. S20, (Supplementary Information). The i-TE sensor was initially exposed to an incandescent lamp for enough time and the produced voltages reached an equilibrium status. Once the light was blocked by hand, where the distance from the sensor is about B1, it can be clearly observed the voltage signal was immediately changed (Fig. 4e). After removing the hand, the voltage quickly came back to its original status. Interestingly, when the hand moved closer to the i-TE sensor with distances of B2 and B3, more amount of light was covered. Thus, it generated a larger ΔT between the top and bottom sides of the i-TE sensor. Accordingly, a much stronger voltage variation signal was observed (Fig. 4e and Supplementary Movie 1), demonstrating high sensitivity for detecting heat. The above results demonstrated that the promising capability for ions and electrode interactions can be used as an effective way of exploring unique properties and designing advanced ionic thermoelectric devices for energy generation and sensing.
Discussion
This work reported a reversible bipolar thermopower behavior of the same i-TE PNP material by adjusting ion-electrode interactions and exhibited giant p-type (+20.2 mV K−1) and n-type (−10.2 mV K−1) thermopowers, respectively. The a-CNT formed stronger interactions with Na+ ions and produced more impedance force to Na+ cations, enabling TFSI– anions to govern the thermodiffusion process of the a-CNT|PNP|a-CNT system, performing n-type behavior. Moreover, the developed i-TEG successfully produced cyclic energy under a constant heat condition by utilizing the bipolar thermopower property, which is significant for expanding the applications of ionic thermoelectrics in the real world. In addition, the fabricated sensors performed high thermal sensibility and fast responsivity using the developed i-TE materials. This work provides significantly innovative impacts on exploring next-generation ionic thermoelectric materials and devices.
Methods
DFT details of interfacial interactions of ions with Cu and CNT electrodes
Density functional theory (DFT) calculations of the interactions between the electrodes (CNT and Cu) and the ions (TFSI– and Na+) are performed by using the Vienna ab initio Simulation Package (VASP) code38,39, where the exchange-correlation effects are treated by the generalized gradient approximation (GGA) in the Perdew–Burke–Ernzerhof (PBE) parametrization41. A vacuum layer >30 Å is set on the electrode surfaces. The TFSI– and Na+ ions are separately put on the electrode surface and the structures are optimized. To embody the electronic states of ions, the total valence electronic numbers are set to be Nall-1 for the models with Na+ ion and Nall+1 with TFSI– ion, where Nall indicates the total of intrinsic valence electronic numbers as shown in Fig. S13 (Supplementary Information). In the geometry optimization, cutoff energy of 500 eV, energy convergence of 10−5 eV, and force convergence of 10−4 eV/Å are set. The total energy is recorded as Etot,ads Then, ions moved far away from the electrode by 15 Å, which is enough to exclude the interactions between electrodes and ions, and the total energy is recorded as Etot,far Lastly, adsorption energy, Ead, can be calculated by Ead = Etot, far−Etot, ads A higher Ead means a stronger interaction between electrodes and ions.
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