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Review

Polyoxometalate–Polymer Composites with Distinct Compositions and Structures as High-Performance Solid Electrolytes

by
Takeru Ito
Department of Chemistry, School of Science, Tokai University, Hiratsuka 259-1292, Japan
Inorganics 2025, 13(3), 75; https://doi.org/10.3390/inorganics13030075
Submission received: 14 January 2025 / Revised: 18 February 2025 / Accepted: 3 March 2025 / Published: 5 March 2025
(This article belongs to the Section Inorganic Materials)
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Abstract

:
Solid electrolytes, including polymer electrolytes, are a promising option for improving the performance of environmentally friendly batteries such as rechargeable lithium-ion batteries or fuel cells. Hydrogen–oxygen fuel cells producing only water under power generation are attracting widespread attention, and they need proton conductors as electrolytes. Fluoropolymer electrolytes such as Nafion® have been utilized for hydrogen–oxygen fuel cells below 100 °C; however, they are not applicable over the working temperature. Therefore, other types of polymer electrolytes are demanded for hydrogen–oxygen fuel cells. Polyoxometalate (POM) inorganic clusters are known as proton conductors and are utilized to prepare POM–polymer composites for solid electrolyte application. In such POM–polymer composites, distinct compositions and structures are significant for improving the performance of proton conductivity. Recently, POM–polymer composites with distinct compositions and structures have been synthesized to obtain high proton conductivity. The key factor is to use single-crystalline compounds. Here, several examples are overviewed by classifying them into three categories: (i) single-crystalline POM–polymer composites, (ii) organically modified POM (org-POM) polymers, and (iii) POM hybrid polymers using polymerizable cations. The application of proton-conductive solid electrolytes is focused on.

Graphical Abstract

1. Introduction

Efficient energy conversion and usage are crucial for realizing sustainable societies. The development of environmentally friendly batteries is an urgent issue. As for rechargeable batteries, lithium-ion batteries have already been industrialized [1,2], and the development of sodium-ion batteries as next-generation rechargeable batteries is underway [3,4]. Other environmentally friendly batteries include fuel cells, such as hydrogen–oxygen fuel cells producing only water for power generation [5]. In hydrogen–oxygen fuel cells, hydrogen gas is converted to a proton with the help of a platinum catalyst, and the proton moves in the electrolyte to react with oxygen to produce water. The electrolyte should be a proton conductor, desirably used in the solid state with respect to safety problems [6,7,8,9]. Commercial hydrogen–oxygen fuel cells employ polymer electrolytes [5]. Fluoropolymers with deprotonatable sulfo groups such as Nafion® are typically used in the form of a membrane. These fluoropolymers behave as superior proton conductors only in the presence of water molecules below a working temperature of 100 °C for hydrogen–oxygen fuel cells. The working temperature should be higher, over 100 °C, to prevent poisoning from the platinum catalyst and to improve the reaction efficiency. Additionally, the fluorine contained in the fluoropolymer electrolytes may be harmful to the environment. Therefore, proton-conductive and fluorine-free polymer materials working over 100 °C are required as solid electrolytes for hydrogen–oxygen fuel cells. Although several systems have been reported [10,11,12,13,14,15,16,17], polymer electrolytes exhibiting higher performance are in demand.
For enhancing the conductive properties of polymer materials, conductive polyoxometalate inorganic clusters (POMs) are promising candidates. POMs are molecular oxide anions with distinct structures [18,19,20,21,22,23,24]. POMs contain many transition-metal atoms in the d0 state, and have electrochemical characteristics beneficial to the conductive properties: they behave as electron reservoirs or as reactive components in multi-electron reactions. Their physicochemical properties can be designed and controlled by changing the molecular structures and by converting the counter cations [22,23,24]. Heteropolyacids, POMs with protons as counter cations, are highly proton-dissociative, and well known as “superacids”. Heteropolyacids exhibit proton conductivity in the presence of water vapor [25], but they are hygroscopic and their durability in the presence of water vapor should be improved. Their proton conductivity decreases under heating due to the loss of water molecules, which is a similar disadvantage to that of proton-conductive fluoropolymers. Cation exchange and hybridization with polymer matrices are possible options for the application. Several proton-conductive POM compounds [25,26,27,28,29,30,31,32,33,34,35,36] and composites with polymers [37,38,39,40,41,42,43,44,45,46,47,48,49,50] have been reported to date. The hybridization of POMs with polymer matrices is usually based on simple combination to enhance the proton conductivity at working temperatures over 100 °C. However, precise control of compositions and structures is rather difficult to achieve, which could be a drawback for the emerging high proton conductivity.
Utilizing single-crystalline materials is an effective way to prepare POM–polymer composites with distinct compositions and structures. Single crystals can be ambiguously revealed with respect to their chemical compositions and molecular structures. Synthesizing single-crystalline POM–polymer hybrids leads to the construction of POM–polymer composites having distinct compositions and structures. Another promising method is to use single-crystalline polymerizable POM monomers for the preparation of well-defined POM–polymer composites.
Recent progress in synthetic methodology has enabled the successful preparation of single-crystalline POM–polymer composites and composites using single-crystalline polymerizable POMs. They possess distinct compositions and structures and exhibit high proton conductivity, and they could be candidates as alternatives to the conventional fluoropolymer electrolytes. Such POM–polymer composites can be categorized into three classes (Figure 1): (i) Single-crystalline POM–polymer composites (Figure 1a). POM and polymer matrices that are effective for proton conductivity are hybridized to obtain single crystals. (ii) Organically modified POM (denoted as “org-POM”) anions (Figure 1b). org-POMs with polymerizable groups can be precisely synthesized, and can sometimes be obtained as single crystals. (iii) Single-crystalline POMs hybridized with polymerizable cations (Figure 1c). The combination of POMs and polymerizable cations is variable. These three types of POM–polymer composites are overviewed below regarding the synthetic method, structure, and characteristics of proton conductivity.

2. Single-Crystalline POM–Polymer Composites

Conventional POM–polymer composites have been prepared by mixing POM compounds and polymer matrices [37,38,39,40]. Neutral POM compounds can be added to polymers as conductive components [44,45,46,47]. POM anions can also be combined with polymers with a cationic moiety by using electrostatic interactions [48]. Polymer matrices can be constructed by sol–gel reactions with coexisting POM species [49,50]. All these methods enable the facile preparation of POM–polymer composites and have been widely investigated. However, as mentioned above, the precise design and control of chemical compositions and material structures are rather difficult to achieve at a molecular level.
To solve this problem, utilizing single-crystalline materials is a promising option. Recently, simply mixing POMs with polymer matrices led to single-crystalline POM–polymer composites (Figure 2 and Figure 3) [51,52,53,54,55,56,57,58]. The conductive mechanisms have been discussed in detail. In 2016, Tsuboi et al. found that Keggin-type polyoxotungstate ([PW12O40]3– (PW12) and [SiW12O60]4– (SiW12)) formed single-crystalline composites with poly(ethylene glycol) (PEG), which is effective for proton conductivity [51]. In a typical synthesis, a heated aqueous solution containing dodecatungstophosphoric acid (H3PW12O40, H-PW12), PEG, and CsNO3 gave colorless crystals of a POM-PEG composite (Figure 3a). The negative charge of POM was compensated with Cs+ and residual H+. The crystal structure was formed by an inorganic framework consisting of PW12 and Cs+. There were one-dimensional (1D) channels with diameters of ca. 6 Å × 8 Å along the c-axis, plausibly holding PEG and H2O molecules. The atomic positions of the PEG molecules could not be determined solely by single-crystal X-ray diffraction, but their presence was confirmed by elemental analyses and spectroscopic measurements. The POM-PEG composite (Cs-PW12-PEG1000) exhibited a proton conductivity of 1.2 × 10–5 S cm–1 at 170 °C (443 K) under anhydrous (non-humidified) conditions (Figure 3a). Using POMs with a larger molecular size, such as Dawson-type POMs ([α-P2W18O62]6−, P2W18), resulted in a moderate anhydrous proton conductivity of 1.3 × 10–4 S cm–1 at 150 °C (423 K) (CsK-P2W18-PEG400, Figure 3b) [52]. Preyssler-type [Bi(H2O)P5W30O110]12− (BiP5W30) and the PEG system exhibited a proton conductivity of 4.0 × 10–4 S cm–1 at 95 °C (368 K) [53]. Larger POMs seem to enhance the anhydrous proton conductivity due to the enlargement of the spaces between POM anions, which enables effective segmental movement of PEG chains and/or the formation of a hydrogen bonding network.
POM-PEG composites were rather unstable as solid electrolytes under humidified conditions due to solubility problems. Changing the polymer matrix to poly(allylamine) (PAA) drastically enhanced the proton conductivity, since protonated PAA can serve as a cationic species interacting with POM anions to stabilize the crystal structures of POM–polymer composites [53,54,55,56,57]. An inorganic framework constructed from larger Preyssler-type POMs and counter metal cations worked as an effective host for a PAA matrix. The PAA position was not decided by single-crystal X-ray measurements derived from severe disordering. In the [Na(H2O)P5W30O110]14− (NaP5W30) and K+ inorganic framework (K-NaP5W30-PAA5000), a 1D channel structure filled with PAA molecules was formed along the c-axis, and exhibited a high proton conductivity of 1.7 × 10–3 S cm–1 at 65 °C (338 K) under mild humidity (RH 75%) (Figure 3c) [53]. Changing POM species to BiP5W30 enhanced the conductivity to the order of ~10–2 S cm–1 (8.3–9.7 × 10–3 S cm–1) at 95 °C (368 K) under mild humidity (RH 75%) [54]. Furthermore, the introduction of a lanthanide ion (Eu3+) attracting water molecules led to robust composites exhibiting ultrahigh conductivities of 1.0–1.2 × 10–2 S cm–1 at 95 °C (368 K) under humidity (RH 90%) [55]. The combination of a Eu-introduced Preyssler-type POM with poly(vinyl alcohol) (PVA) realized a high proton conductivity of 8.3 × 10–3 S cm–1 at 95 °C (368 K) under mild humidity (RH 75%) [56]. Polar Preyssler-type POMs of [Ca(H2O)P5W30O110]13− (CaP5W30) and [Eu(H2O)P5W30O110]12− (EuP5W30) formed a staggered array in the crystalline lattice, which surprisingly helped the emergence of ultrahigh proton conductivities of 2.8 × 10–2 S cm–1 (CaP5W30 system) and 2.3 × 10–2 S cm–1 (EuP5W30 system) under the same conditions [57]. The combination of Preyssler-type POMs and a PAA matrix is quite promising for solid electrolytes with ultrahigh proton conductivity.

3. Organically Modified POM (org-POM) Polymers

Some inorganic POM anions can react with an organic moiety to form covalent bonds between the POM skeleton and the organic moiety, which leads to organically modified POMs (denoted as org-POMs hereafter). Typical examples are shown in Figure 4. The synthetic methodology of org-POMs has dramatically progressed in recent decades and has attracted widespread attention for the bottom-up construction of functional materials [59,60,61,62,63,64,65,66,67,68,69,70]. org-POMs are synthesized by utilizing the reaction between an organic reagent and oxygen atoms of the oxo or hydroxo moiety of a native POM, causing the organic groups to covalently bond to the oxygen atoms of the POM (Figure 4a). In other words, org-POMs are organic moiety-grafted POM anions. Several organic moieties such as polymerizable and/or coordinative groups can be introduced into the native POM skeleton. The introduced moiety can be sequentially extended by several organic reactions such as a click reaction (Figure 4b). The molecular structure of org-POMs can be unambiguously characterized by several spectroscopic methods. Single-crystal X-ray diffraction analysis is also applicable when suitable crystals can be obtained. The native POMs utilized for the synthesis of org-POMs are typically lacunary Keggin- and Dawson-type POMs holding unsaturated oxygens (Figure 4c, left). Vanadium-substituted Dawson-type POMs and Anderson-type POMs with relatively active oxygens in the oxo or hydroxo group (Figure 4c, center and right) are also employed. Detailed syntheses of org-POMs have been comprehensively reviewed [60,65,68].
Several org-POMs with a polymerizable moiety and their derivative polymers have been synthesized since 1992 [71,72,73,74,75,76,77,78,79,80,81,82,83,84,85,86,87,88,89,90]. These polymerizable org-POMs work as monomers, and POM–polymer composites with distinct compositions and structures have been obtained. Single crystals of polymerizable org-POMs have been reported as rare examples [74,75,76]. Moore et al. synthesized an org-POM with a styrylimido moiety by using a Lindqvist POM ([Mo6O19]2–, Mo6) (Figure 5a, org-Mo6-V) [74]. The single crystals were obtained by diffusion of diethylether vapor into an acetonitrile solution as tetrabutylammonium (TBA) salt. This single-crystalline org-POM monomer was successfully copolymerized with 4-methylstyrene (MS) by radical polymerization using 2,2′-azobis(isobutyronitrile) (AIBN). Lu et al. reported org-Mo6 derivatives with iodobenzene or ethynylbenzene moieties [75]. Single crystals of an ethynylbenzene-grafted org-POM were crystallized from the concentrated solution as TBA salt (Figure 5b, org-Mo6-E). Org-Mo6-E was polymerized with an iodobenzene derivative (ID) by the Sonogashira coupling reaction to obtain a π-electron-conjugated polymer. The conjugated polymers synthesized from Org-Mo6-E were processed into thin films, and their application as organic photovoltaic cells was investigated. Similar conjugated polymers derived from single-crystalline org-Mo6 can be prepared by a one-pot synthesis [76].
Hasegawa and Nomiya et al. employed a mono-lacunary Dawson-type POM ([α2-P2W17O61]10–, P2W17) as a native skeleton to obtain org-POMs in dimethylammonium (DMA) salt forms [86,87,88]. Polymerizable POMs decorated with methacryloyl, acryloyl, and allyl moieties were grown as single crystals (Figure 6). In the case that organosilyl reagents were utilized, two organic moieties were introduced into one Dawson-type P2W17 skeleton (Figure 6a–c) [86,87,88], while one organic moiety was grafted onto one P2W17 skeleton when an organogermyl reagent was used (Figure 6d) [88]. This was due to the larger atomic size of germanium compared to silicon. Two organosilyl units can be replaced by forming a Si–O–Si bond in the lacunary space of one W atom, while only one organogermyl unit can enter the lacunary space. The DMA cation in an org-POM with a methacryloyl moiety (org-PW17-MA, Figure 6a) was exchanged with a proton by using an ion-exchange resin [87]. The resulting acid form of org-PW17-MA was utilized as a monomer to synthesize a copolymer with methyl methacrylate (MMA) by radical polymerization. The acidities of the acid-form org-PW17-MA monomer and hybrid copolymer were evaluated using the Hammett indicators, demonstrating stronger acidity than 95% H2SO4. These acid-form org-PW17-MA derivatives are promising for acid catalysts and proton-conducting materials.
org-POM application to proton conductors is rather in its infancy [89,90,91,92]. Recently, the use of acid-type org-POMs obtained by the ion-exchange reaction as effective proton conductors has been verified [93,94,95,96]. Lu et al. reported the proton conductivity of org-POM polymers prepared from the TBA salt of a vanadium-substituted Dawson-type POM ((TBA)6H3[P2V3W15O62)], TBA-P2V3W15) (Figure 7) [93,94]. The norbornene moiety was covalently bonded to the oxo groups of the substituted vanadium atoms (org-P2V3W15) as a starting material. The TBA salt of org-P2V3W15 was thoroughly characterized, but the single crystals were not obtained, probably due to the steric hindrance of the rather large organic moiety [35]. The org-POM monomer (TBA salt) was successfully polymerized by ring-opening metathesis polymerization. The obtained homopolymer could be copolymerized with norbornene-poly(ethylene oxide) (PEO) derivatives. The TBA cations of the homo- and copolymers were exchanged with protons by an ion-exchange resin, and their proton conductivities were investigated. The prepared copolymers exhibited ultrahigh proton conductivities of 1.11 × 10–1 S cm–1 for a random copolymer and 3.00–3.57 × 10–2 S cm–1 for a block copolymer under humidified conditions (RH 100%) at 80 °C (353 K) [94].
He et al. synthesized an org-POM functionalized by a PEG moiety which enhanced the proton conductivity of Nafion® [95]. A mono-lacunary Keggin-type POM (K8[SiW11O39], K-SiW11) was employed in potassium (K+) salt form as a native skeleton, and two PEG branches were introduced by using an organosilyl reagent, which resulted in the K+ salt of amphiphilic org-SiW11 (Figure 8). Two long PEG moieties might prevent the growth of single crystals [35,97]. The K+ cation of org-SiW11 was exchanged with a proton by an ion-exchange resin. Amphiphilic org-SiW11 in H+ form had high miscibility with Nafion®, and was co-assembled to prepare hybrid thin films. Supramolecular interactions between the amphiphilic org-SiW11 and Nafion® led to stable immobilization of the POM in Nafion®. The proton conductivity of the amphiphilic org-SiW11 (3 wt %)-added Nafion® reached an ultrahigh value of 2.26 × 10–1 S cm–1 under humidified conditions (RH 100%) at 80 °C (353 K). The org-SiW11-added Nafion® showed additional enhancements in tensile strength (12.6 MPa) and fuel cell performance (power density 372 mW cm–2, maximum current density 1.15 A cm–2), which were both superior to those of pristine Nafion®. Fluoroalkyl-functionalized org-SiW11 was further demonstrated to be a supramolecular additive for Nafion® by the same group [96]. The proton conductivity and proton/vanadium selectivity were improved compared to pristine Nafion®, being applicable to fuel cells and vanadium flow batteries.

4. POM Hybrid Polymers Utilizing Polymerizable Cations

The counter cation of POM compounds can be changed to control the physicochemical properties, such as the thermal stability and miscibility to hydrophilic or hydrophobic solvents [22,23,24]. Functional counter cations expand the possibilities of POM compounds. Introducing a polymerizable moiety into the counter cations of POM anions will lead to the preparation of another class of POM–polymer composites. Li et al. synthesized a polymerizable surfactant, dodecyl(11-methacryloyloxyundecyl)dimethylammonium (DMDA), and used it to wrap an emissive europium-containing POM ([EuW10O36]9–, EuW10) (Figure 9) [98]. The amphiphilic DMDA-wrapped EuW10 was soluble in conventional organic solvents and reacted with methyl methacrylate (MMA) by radical polymerization. The obtained copolymer of DMDA-wrapped EuW10 and MMA was an excellently transparent polymer composite, exhibiting characteristic emission derived from EuW10. The emission properties were retained after polymerization reactions.
To explore the possibilities of POMs with polymerizable cations as solid electrolytes, we designed polymerizable ionic liquid cations (Figure 10a) [99,100,101,102,103,104]. The cations consist of imidazolium ionic liquid decorated with a methacryloyl group (denoted as MAIm). The ionic liquid contributes to the emergence of conductivity [15,16], and the properties of MAIm can be controlled by changing the substituent of the imidazolium moiety. MAIm with a methyl group (MAImC1) can be hybridized with Keggin-type POMs (PW12 and SiW12) to obtain single crystals of hybrid monomers (MAImC1-PW12 and MAImC1-SiW12) (Figure 11). MAImC1-PW12 and MAImC1-SiW12 are polymerizable by radical polymerization, resulting in hybrid homopolymers [99,100]. Additionally, MAImC1-PW12 and MAImC1-SiW12 can be polymerized with butyl methacrylate (BMA) and a polymerizable ionic liquid with a long alkyl chain (MAImC8-Br). Copolymerization with MAImC8-Br enhanced the proton conductivity with humidity (RH 95%) at 40 °C (313 K), reaching 5.7 × 10–4 S cm–1 for MAImC1-PW12 and 2.7 × 10–3 S cm–1 for MAImC1-SiW12 (Figure 11).
The polymerizable MAImC1 cation can be crystallized with other Keggin-type POMs ([H2W12O40]6– (H2W12) and [PMo12O40]3– (PMo12)) with different negative charges or constituent atoms [101]. In both hybrid crystals, all counter cations were replaced by MAImC1 located in the vicinity of H2W12 and PMo12, which may have caused charge transfer under photoexcitation. The yellow-green MAImC1-PMo12 crystal contained a small amount of dark blue-colored reduced species in most non-reduced yellow PMo12 anions, indicating a weak charge-transfer salt.
The MAImC1 cation formed single crystals with isopolyoxometalates such as [Mo8O26]4– (Mo8) and [V10O28]6– (V10) accompanied by several metal cations. The hybrid crystal of Mo8 was revealed to contain Na+ to form MAImC1-Na-Mo8 as a polymerizable monomer [102]. The introduction of monovalent metal cations into POM–organic crystals has been reported [105,106]. The Na+ cation can be exchanged with Ag+ and K+ to obtain MAImC1-Ag-Mo8 and MAImC1-K-Mo8. MAImC1-Na-Mo8 was polymerized by the radical polymerization reaction, and its conductivity with humidity (RH 95%) at 90 °C (363 K) was 5.1 × 10–5 S cm–1. As for the V10 anion, single crystals with MAImC1 were obtained solely under the coexistence of Ca2+ and Mg2+ as compounds of MAImC1-Ca-V10 and MAImC1-Mg-V10 (Figure 12) [103]. The reason that MAImC1-Ca-V10 and MAImC1-Mg-V10 were selectively obtained was not clear, but the introduction of divalent cations into POM–organic hybrid crystals is rare. The proton conductivities with humidity (RH 95%) at 80 °C (353 K) were a moderate value of 3.0 × 10–4 S cm–1 for MAImC1-Ca-V10 and a high value of 3.3 × 10–3 S cm–1 for MAImC1-Mg-V10. Such metal-cation-containing materials are promising for ionic conductors.
In MAIm cations, imidazolium substitutents can be designed. A deprotonatable MAImH cation was derived from MAIm without a methyl group. Amphiphilic MAImC8 was obtained by introducing an octyl chain. Crystallization of POMs with these MAImH and MAImC8 cations was reported to be rather difficult, but Mo8 and SiW12 were successfully crystallized [104]. Hybrid crystals with MAImH (MAImH-Mo8 and MAImH-SiW12) contain dissociative protons, which could be beneficial to proton conductivity. MAImC8 hybrid crystals (MAImC8-Mo8 and MAImC8-SiW12) exhibited anisotropic layered or tunneling packing of POM anions in the crystal lattice derived from van der Waals interactions of the alkyl chain (Figure 13). Such anisotropic POM packing would be effective for the emergence of conductivity.

5. Summary and Outlook

Polyoxometalate–polymer (POM–polymer) composites with distinct compositions and structures have recently been synthesized as single-crystalline forms or by utilizing single-crystalline starting materials. These materials exhibit promising high proton conductivities of 10–3–10–1 S cm–1 as high-performance solid electrolytes for fuel cell batteries. Such POM–polymer composites can be categorized into three classes. Firstly, single-crystalline POM–polymer composites have been synthesized by combining POM compounds and polymer matrices such as polyethylene glycol (PEG) or polyallylamine (PAA). These POM–polymer composites have been obtained as single crystals. Secondly, organically modified POMs (org-POMs) have been employed as inorganic–organic hybrid monomers. Organic synthesis methods enable the flexible and precise design of org-POM monomers at a molecular level, which leads to the creation of various types of POM–polymer composites. Finally, inorganic–organic hybrid monomers consisting of POMs and polymerizable cations have been obtained as single crystals and utilized to prepare POM–polymer composites.
These POM–polymer composites can be obtained as single crystals. This is a great advantage when designing and controlling a material’s composition, structure, and properties. However, the examples have been rare series of materials. Such POM–polymer composites hold flexible polymer matrices or long alkyl chains, which makes it difficult to obtain and analyze single crystals [35]. For POM–polymer composites using POMs without organic modification, the types of POM anion and counter cation can generally be selected, while POM–polymer composites utilizing org-POMs can be tailored in terms of their organic moiety. org-POM systems are quite promising and widely applied to many systems, from electrochemical to biological usage [59,60,61,62,63,64,65,66,67,68,69,70,107,108,109,110,111]. The native POM skeletons for org-POMs are rather limited, but the variety of POM skeletons is expanding. The search for appropriate combinations of POMs and organic components should be explored to obtain single crystals. A simpler and more effective methodology needs to be discovered in the future.
The POM–polymer composites overviewed here are under development; however, they are promising materials for the application of solid electrolytes for fuel cells. The relationship between the proton conductivity and material structures should be clarified to produce functional materials. The POM–polymer composites mentioned above are promising materials since they possess distinct compositions and structures at a molecular level. The proton conductivity of POM–polymer composites can be clearly associated with the material composition and structure. The revealed results can be effectively fed back to the development of synthetic strategies and to the molecular design of components for POM–polymer composites. The values of proton conductivity are now close to practical use for the solid electrolytes of fuel cell batteries. The next strategy for these POM–polymer composites will be to improve their durability in the presence of moisture and temperature and to investigate material processability.

Funding

This research was funded in part by JSPS KAKENHI (grant number JP21K05232), Research and Study Project of Tokai University Research Organization, and Izumi Science and Technology Foundation.

Acknowledgments

The author acknowledges the following researchers of Tokai University for their kind collaboration: Shinichi Koguchi, Kaito Sasaki, Masashi Higuchi, Yosuke Okamura, Naoki Shinyashiki, and Yu Nagase.

Conflicts of Interest

The author declares no conflicts of interest. The funders had no role in the design of the study; in the collection, analyses, or interpretation of data; in the writing of the manuscript; or in the decision to publish the results.

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Inorganics 13 00075 g001
Figure 1. POM–polymer composites with distinct compositions and structures as high-performance solid electrolytes: (a) single-crystalline POM–polymer composites; (b) organically modified POM (org-POM) polymers; (c) POM hybrid polymers using polymerizable cations.
Figure 1. POM–polymer composites with distinct compositions and structures as high-performance solid electrolytes: (a) single-crystalline POM–polymer composites; (b) organically modified POM (org-POM) polymers; (c) POM hybrid polymers using polymerizable cations.
Inorganics 13 00075 g001
Inorganics 13 00075 g002
Figure 2. Chemical components utilized for the synthesis of single-crystalline POM–polymer composites: (a) POM anions; (b) polymer matrices. PEG: poly(ethylene glycol); PAA: poly(allylamine); PVA: poly(vinyl alcohol).
Figure 2. Chemical components utilized for the synthesis of single-crystalline POM–polymer composites: (a) POM anions; (b) polymer matrices. PEG: poly(ethylene glycol); PAA: poly(allylamine); PVA: poly(vinyl alcohol).
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Figure 3. Single-crystalline POM–polymer composites. The number of polymer components represents the average molecular weight. One-dimensional channels are indicated by dashed circles. The POM–polymer ratios in the composite are indicated in the figure: (a) Keggin-type POM/PEG system; (b) Dawson-type POM/PEG system; (c) Preyssler-type POM/PAA system. The color of Preyssler-type POMs is changed for clarity.
Figure 3. Single-crystalline POM–polymer composites. The number of polymer components represents the average molecular weight. One-dimensional channels are indicated by dashed circles. The POM–polymer ratios in the composite are indicated in the figure: (a) Keggin-type POM/PEG system; (b) Dawson-type POM/PEG system; (c) Preyssler-type POM/PAA system. The color of Preyssler-type POMs is changed for clarity.
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Figure 4. Organically modified POMs (org-POMs): (a) typical synthetic strategy for grafting an organic moiety to a POM anion; (b) typical extension method for grafted organic moieties; (c) examples of POM skeletons used for the synthesis of org-POMs.
Figure 4. Organically modified POMs (org-POMs): (a) typical synthetic strategy for grafting an organic moiety to a POM anion; (b) typical extension method for grafted organic moieties; (c) examples of POM skeletons used for the synthesis of org-POMs.
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Inorganics 13 00075 g005
Figure 5. POM–polymer composites synthesized from single-crystalline polymerizable org-Mo6 anions. Polymerizable groups are indicated by red ellipsoids. The org-POM/comonomer ratios in the copolymer are indicated in the figure: (a) org-Mo6 with a styryl moiety (org-Mo6-V); (b) org-Mo6 with ethynylbenzene moieties (org-Mo6-E).
Figure 5. POM–polymer composites synthesized from single-crystalline polymerizable org-Mo6 anions. Polymerizable groups are indicated by red ellipsoids. The org-POM/comonomer ratios in the copolymer are indicated in the figure: (a) org-Mo6 with a styryl moiety (org-Mo6-V); (b) org-Mo6 with ethynylbenzene moieties (org-Mo6-E).
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Inorganics 13 00075 g006
Figure 6. Single-crystalline org-POMs derived from a lacunary Dawson-type POM (P2W17). Polymerizable groups are indicated by red ellipsoids: (a) org-POM synthesized by an organosilyl reagent with a methacryloyl moiety (org-P2W17-MA) and POM–polymer composites. The org-P2W17-MA/comonomer ratio in the copolymer is indicated in the figure. (b) org-POM synthesized by an organosilyl reagent with an acryloyl moiety. (c) org-POM synthesized by an organosilyl reagent with an allyl moiety. (d) org-POM synthesized by an organogermyl reagent with an allyl moiety.
Figure 6. Single-crystalline org-POMs derived from a lacunary Dawson-type POM (P2W17). Polymerizable groups are indicated by red ellipsoids: (a) org-POM synthesized by an organosilyl reagent with a methacryloyl moiety (org-P2W17-MA) and POM–polymer composites. The org-P2W17-MA/comonomer ratio in the copolymer is indicated in the figure. (b) org-POM synthesized by an organosilyl reagent with an acryloyl moiety. (c) org-POM synthesized by an organosilyl reagent with an allyl moiety. (d) org-POM synthesized by an organogermyl reagent with an allyl moiety.
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Figure 7. Synthetic procedure of org-P2V3W15 anion and proton-conductive POM–polymer composite. The proton conductivity of the POM–polymer composite is indicated.
Figure 7. Synthetic procedure of org-P2V3W15 anion and proton-conductive POM–polymer composite. The proton conductivity of the POM–polymer composite is indicated.
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Figure 8. Synthetic procedure of amphiphilic org-SiW11 anion and proton-conductive POM–polymer composites. The proton conductivity of the POM–polymer composite is indicated.
Figure 8. Synthetic procedure of amphiphilic org-SiW11 anion and proton-conductive POM–polymer composites. The proton conductivity of the POM–polymer composite is indicated.
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Figure 9. Synthetic procedure of inorganic–organic hybrid monomer and polymer utilizing photoluminescent EuW10 and polymerizable DMDA cation. The DMDA-EuW10/MMA ratio in the copolymer is indicated in the figure.
Figure 9. Synthetic procedure of inorganic–organic hybrid monomer and polymer utilizing photoluminescent EuW10 and polymerizable DMDA cation. The DMDA-EuW10/MMA ratio in the copolymer is indicated in the figure.
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Figure 10. Molecular structures of (a) polymerizable ionic liquids, and (b) POM anions crystallized with polymerizable ionic liquids.
Figure 10. Molecular structures of (a) polymerizable ionic liquids, and (b) POM anions crystallized with polymerizable ionic liquids.
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Inorganics 13 00075 g011
Figure 11. Synthetic procedure of single-crystalline monomer and proton-conductive hybrid polymers utilizing polymerizable MAImC1 cation and SiW12.
Figure 11. Synthetic procedure of single-crystalline monomer and proton-conductive hybrid polymers utilizing polymerizable MAImC1 cation and SiW12.
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Inorganics 13 00075 g012
Figure 12. Proton-conductive hybrid crystals synthesized by using polymerizable MAImC1 cation and V10.
Figure 12. Proton-conductive hybrid crystals synthesized by using polymerizable MAImC1 cation and V10.
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Inorganics 13 00075 g013
Figure 13. Inorganic–organic hybrid crystals of POMs derived from polymerizable MAImC8 cation with amphiphilic moiety.
Figure 13. Inorganic–organic hybrid crystals of POMs derived from polymerizable MAImC8 cation with amphiphilic moiety.
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Ito, T. Polyoxometalate–Polymer Composites with Distinct Compositions and Structures as High-Performance Solid Electrolytes. Inorganics 2025, 13, 75. https://doi.org/10.3390/inorganics13030075

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Ito T. Polyoxometalate–Polymer Composites with Distinct Compositions and Structures as High-Performance Solid Electrolytes. Inorganics. 2025; 13(3):75. https://doi.org/10.3390/inorganics13030075

Chicago/Turabian Style

Ito, Takeru. 2025. "Polyoxometalate–Polymer Composites with Distinct Compositions and Structures as High-Performance Solid Electrolytes" Inorganics 13, no. 3: 75. https://doi.org/10.3390/inorganics13030075

APA Style

Ito, T. (2025). Polyoxometalate–Polymer Composites with Distinct Compositions and Structures as High-Performance Solid Electrolytes. Inorganics, 13(3), 75. https://doi.org/10.3390/inorganics13030075

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