Additive Manufacturing as a Means of Gas Sensor Development for Battery Health Monitoring

Abstract

Lithium-ion batteries (LIBs) still need continuous safety monitoring based on their intrinsic properties, as well as due to the increase in their sizes and device requirements. The main causes of fires and explosions in LIBs are heat leakage and the presence of highly inflammable components. Therefore, it is necessary to improve the safety of the batteries by preventing the generation of these gases and/or their early detection with sensors. The improvement of such safety sensors requires new approaches in their manufacturing. There is a growing role for research of nanostructured sensor’s durability in the field of ionizing radiation that also can induce structural changes in the LIB’s component materials, thus contributing to the elucidation of fundamental physicochemical processes; catalytic reactions or inhibitions of the chemical reactions on which the work of the sensors is based. A current method widely used in various fields, Direct Ink Writing (DIW), has been used to manufacture heterostructures of Al₂O₃/CuO and CuO:Fe₂O₃, followed by an additional ALD and thermal annealing step. The detection properties of these 3D-DIW printed heterostructures showed responses to 1,3-dioxolan (DOL), 1,2-dimethoxyethane (DME) vapors, as well as to typically used LIB electrolytes containing LiTFSI and LiNO₃ salts in a mixture of DOL:DME, as well also to LiPF₆ salts in a mixture of ethylene carbonate (EC) and dimethyl carbonate (DMC) at operating temperatures of 200 °C–350 °C with relatively high responses. The combination of the possibility to detect electrolyte vapors used in LIBs and size control by the 3D-DIW printing method makes these heterostructures extremely attractive in controlling the safety of batteries.

1. Introduction

The development of solid-state sensors and sensor arrays with low costs and efficiency is a growing goal of the sensor community. Detecting potential hazards in mixtures or ionizing radiation is a challenging task that requires the determination of specific individual components positively and sensitively. For this purpose, the development of sensor arrays with a wide range of varying materials and performances/possibilities is necessary. Whereas many approaches are based on various synthesis steps, the automatic combination of many complex materials can easily be realized by e.g., additive manufacturing or three-dimensional (3D) printing [1]. A large variety of 3D printed sensors have been developed and manufactured recently in the field of biotechnology e.g., for detection of glucose [2], selected medicament [3], trace elements [4], neurotransmitters [5], nucleic acids [6] and/or proteins [7].

Sharafeldin et al. [1] pointed out that 3D printing is very promising even for the detection of cancer and other diseases, because these complex diagnostic devices could be simply connected to portable devices like smartphones with batteries [1]. Also the fabrication of strain sensors by 3D printing has been demonstrated by Liu et al. [8] using various printing methods, such as Digital Light Processing (DLP) and Direct Ink Writing (DIW) [8]. Han et al. [9] presented an overview of the challenges of current biomedical sensors [9]. The authors hint at some possible limitations, one of which is related to the biocompatibility of printed materials [9]. Another concern is related to their recyclability and reuse on the stability of the signal determination [9]. It is proposed that one of the solutions to improving this problem is the association of dynamic thresholds of Flexiforce Sensor [10]. Another idea is to increase the use of other materials to develop 3D printed sensors based on nanocomposites with optimized characteristics [9].

Not only biotechnology can profit from the rapid developments enabled by the 3D printing of sensors. Another rapidly growing field is the safety monitoring in Lithium-ion batteries (LIBs) [11,12], attributable to highly reactive components inside this type of battery. Regarding this type of battery, safety is a significant concern and it must be monitored carefully and reliably. Battery safety requires sensors for the detection of many different volatile compounds (e.g., C₄H₁₀O₂, C₃H₆O₃, 1,2-dimethoxyethane, dimethyl carbonate, C₄H₈O₃) [13] that could be formed upon battery failure. Especially due to their use in portable electronics, such as computers or smartphones [14,15], or in electric or hybrid vehicles, safety monitoring is even more important and therefore, there is a need of suitable sensors that fit the requirements for the possible application [16]. Further, with the increase in LIB’s performance in terms of energy density and power density, the safety guarantee has not yet been fully addressed [17], thus the main causes of fires and battery explosions being the heat leakage and the presence of inflammable components [15,17,18]. One of the solutions proposed by Chen et al. [17] to secure the batteries against thermal and mechanical harm is the improvement of the outer casing [17]. Another solution is to mount the batteries in the parts of auto vehicles that are least affected during an accident [17] and to prevent the thermal runaway before sensors are indispensable.

For safer batteries related to their heating protection, Chen et al. [18] have developed a class of ultra-fast and thermo-responsive reversible polymer switching (TRPS) material, which consists of the use of graphene-coated, nano-spiked Ni particles on polymer composite films, thus demonstrating good battery characteristics at ambient temperatures and their rapid disconnection under abnormal regimes, such as overheating and short circuiting [18]. The generation of heat and its accumulation inside the batteries is often accompanied by the generation of flammable gas due to various parasitic reactions, therefore it is necessary to improve the safety of the batteries by preventing the generation of these gases. [15,17,19].

In particular, the generation of heat and its accumulation inside the batteries is often accompanied by the generation of inflammable gases, such as CO, H₂, CH₄, C₂H₄, C₂H₆, and C₃H₈ due to various parasitic reactions depending on temperature, electrolysis, electrolytes and the appearance of thermal leakage [13,20]. Therefore, it is necessary to improve the safety of the batteries by preventing the generation of these gases and/or by the implementation of suitable sensors for early hazard detection and rapid disconnection of the battery. Essl et al. [13] investigated, tested, and proposed the use of various gas sensing structures as early detectors of battery deterioration. Here, it is shown that sensing structures based on metal oxide semiconductors (MOX) are the most promising candidates due to their speed of response with high sensitivity, low cost, and their ability to easily connect to the battery management system (BMS) [13]. Following the studies, the authors mention that it is possible to detect battery failures with gas sensors, but through the many different failure mechanisms, ongoing study is still necessary [13].

The recent huge demand towards portable devices with precise sets of properties requires cost-effective materials and new approaches to fabricate devices out of these materials [19]. Based on that, 3D-DIW devices have attracted our consideration, due to their design potentiality as shown already e.g., for new strain sensing [21] or totally electronic components [22]. The progress in gas detecting and in 3D-DIW approaches will initiate larger capabilities to embody e.g., oxides directly onto multisensory or portable devices [23]. Previous reports claim that this 3D-approach will permit the assembly of multiple sensors through DIW for the precise sensing of specific vapors in various atmospheres, especially for battery safety. Thus, the development of a class of 3D-DIW nanomaterial consisting of semiconducting oxide particles, which can detect explosive vapor leakages and indicate on necessity of rapid disconnection battery under abnormal concentrations, such as C₃H₆O₂, C₄H₁₀O₂ vapors, electrolytes containing LiTFSI and LiNO₃ salts in a mixture of DOL:DME, as well as to LiPF₆ salts in a mixture of EC:DMC is highly demanded. Oxide-based nanostructures, especially a combination of p and n-type conductivity (CuO and Fe₂O₃), TiO₂ and Al₂O₃/CuO and CuO:Fe₂O₃, are highly prominent investigated mixtures for gas sensors due to their response, stability, and good sensitivity [19,24,25,26].

This work reports on the use of the 3D-DIW printed nanocrystalline films tested as reliable, accurate, and selective sensors for the test of battery electrolytes vapor at relative concentrations. At this stage our input and aim is to promote battery safety through early leak detection, which we consider of high importance, especially for the electrification of the mobility sector and its large-format lithium ion batteries [13,17]. In the future, a tighter control of the reactions occurring inside the battery by monitoring the electrolyte composition via non-intrusive sensors may be a promising approach to improving the batteries’ lifetime and performance.

In the presented study, two different sensor concepts, both prepared via additive manufacturing, were demonstrated and investigated regarding their applicability for battery safety monitoring by studying their sensing properties in the presence of commonly used battery vapors, electrolytes, and solvents. This work will promote the 3D printing of such sensors for battery safety in premiere, e.g., to place a sensor outside a battery pack, or for it to be integrable into the pouch cell or inside the pouch cell, where it has direct access to the evolving gases in a smart battery device. This study is only to evaluate the additive manufacturing of nanomaterials as a means of gas sensor development to detect evolving gases, thus it is a first step in the sensor design.

2. Materials and Methods

For the preparation of the sensor devices a single-step, 3D-DIW approach reported by Siebert and co-workers [23] in a recent article was used (see Figure 1). The Cu—based stripes/traces prepared by DIW were covered with nanowire arrays with a size of ~25 nm only after thermal annealing (TA) at 425 °C for 3 h in ambient temperature, thus forming CuO/Cu₂O/Cu microparticles (MPs) bridge-lines. In the previous work, printed devices were mainly based on networked MPs stripes which possess a diameter of ~20 µm directly on the substrate, while in this work a subsequent thermal atomic layer deposition (ALD) of Al₂O₃ (20 nm) with a following TA at 600 °C for 3 h. Subsequently, the 3D-DIW Cu MPs-based layer/stripes developed a non-planar CuO/Cu₂O/Cu structure totally covered with a 20 nm thin Al₂O₃ layer by ALD deposition. The samples of net bridging MPs were contacted externally with Au-contacts as reported [23].

The second set of sensors has been fabricated as stripes/traces by DIW using Cu-Fe, MP of Fe, and Cu particles (purity 99.9%) onto the substrate with a subsequent thermal annealing at 425 °C. The porous bridging nanostructures are made of heterojunctions which are connected via non-planar CuO/Cu₂O/Cu nanowires/MPs and Fe₂O₃/Fe nanospikes/MPs as reported before [19]. Characterization of the nanomaterials was performed in detail as reported in our paper [19]. DIW, as a subdivision of additive manufacturing, alike to 3D-printing, as mentioned in several papers, facilitate the duration and productive creation of modern structures/systems with multiple levels of involvement for advancing technologies [19,27,28,29,30,31]. The fabricated 3D-printed mixed metal oxide nanomaterials arranged in stripes/traces will be shown with respect to battery vapor sensors featuring a flexible design concept, proving this approach to be the most attractive for the near future applications.

For the preparation of the Cu-based stripes/traces set of sensors, copper microparticles of ~20 µm in diameter were sonicated in H₂O, then a powder of polyethylene oxide (M_v~2,000,000, Sigma-Aldrich, St. Louis, MO, USA) was added at 20 °C (see representation Figure 1a). Stripes were printed from MPs prepared as reported in

Table 1. Data for all sample sets preparation [23]. “Reprinted with permission from {Siebert, L.; Lupan, O.; Mirabelli, M.; Ababii, N.; Terasa, M.-I.; Kaps, S.; Cretu, V.; Vahl, A.; Faupel, F.; Adelung, R. 3D-Printed Chemiresistive Sensor Array on Nanowire CuO/Cu₂O/Cu Heterojunction Nets. ACS Appl. Mater. Interfaces 2019, 11, 25508–25515, doi:10.1021/acsami.9b04385}. Copyright {2019} American Chemical Society.”

Sample Set	3D-T	3D-L
Base solution PEO content	6%	6.5%
Trace height	>0.2 mm	0.2 mm
Trace width	>0.6 mm	0.6 mm
Trace orientation	transversal	longitudinal

and discussed in detail previously [23]. The stripes/traces were DIW as a single layer through a custom apparatus (see representation Figure 1b). 3D stripes/traces were printed on the glass substrate in the current work as before (Figure 1b) [23]. Figure 1d shows the digital images of the representative samples after 3D printing and the samples being divided into individual sensors by interdigitating gold contacts.

The fabrication steps of the second set, or Cu-Fe-based sensor devices, is depicted in Figure 2. Initially, the fabrication of the rheological optimal ink was conducted (Figure 2a) based on Cu and Fe microparticles with a 96 vol% of C₂H₅OH, Polyvinyl butyral (PVB) (by Kuraray). The average diameters of the Cu and Fe microparticles were ~20 and ~50 µm, respectively [19]. The mixture ratios of the used ink were 3:1:1 (C₂H₅OH:PVB:metals) by weights and the metals’ MPs were mixed in a 1:1 ratio by weights. The ink was inserted in a 40 cm³ cartridge (Figure 2a) and left overnight before DIW, then loaded into a setup with a tapered nozzle (~0.59 mm) and stripped on the substrate (Figure 2b) [19]. For the next steps, the specimens were dehydrated for 22 h at 20 °C.

The DIW stripes/traces-based sensors were afterwards TA at 425 °C for 3 h and 600 °C for 3 h in an ambient atmosphere, both at a heating rate of 35 °C s⁻¹ (Figure 2c). The temperatures for the TA used in the current work is changed compared to the previous works. The TA at 425 °C led to the formation of nanospikes and nanowires atop the MPs in the samples not covered with Al₂O₃, whereas the TA at 600 °C allowed for oxidation of the ALD treated MPs. Afterwards, gold contacts (~180 nm thick) were sputtered on top through a shadow mask onto each specimen (Figure 2d). The temperatures of the TA used in current and previous works are different.

Transmission electron microscope (TEM) investigation of the Al₂O₃/CuO-3D DIW heterostructures was performed with a FEI Tecnai F-30 G² STwin (Thermo Fischer Scientific, Waltham, MA, USA) operated at 300 kV. Sample material was scraped off of the top of a finished CuO/Al₂O₃ sensor device after thermal annealing and placed on a Cu TEM (Plano GmbH, Wetzlar, Germany) grid in order to investigate the nanostructure of the deposited Al₂O₃ layer. To gain additional insight into the stoichiometry and chemical composition, the Al₂O₃/CuO-3D heterostructures were investigated by X-ray photoelectron spectroscopy (XPS, Omicron Full Lab., Omicron Nano-Technology GmbH, and non-chromatized Al-anode, 240 W, Taunusstein, Germany). Survey spectra were measured with a VSW hemispherical analyser at 100 eV pass energy, and high resolution spectra at 30 eV pass energy. After collecting the spectra, potential charging of the sample was corrected by setting the C-1s line of aliphatic carbon to the reference value of 284.5 eV [32]. For the evaluation the software CasaXPS (version 2.3.16) was used [33].

The gas-sensing properties measurements were performed continuously through a Keithley2400 source meter using LabView software (from National Instruments), as described in previous works [34,35]. The gas and vapor responses were calculated according to Equation (1), where R_gas and R_air represent the electrical resistances of the samples exposed to gas/vapors and under normal environmental conditions, respectively [36,37]:

$$S_p=\frac{R_{gas}-R_{air}}{R_{air}}\ast 100\%.$$

(1)

For testing the sensing properties of commonly used battery electrolytes, different samples were prepared. The electrolyte labeled as E1 is prepared by dissolving 0.7 M of lithium bis (trifluoromethanesulfonyl)imide (LiTFSI, Sigma-Aldrich, St. Louis, MO, USA) and 0.25 M of lithium nitrate (LiNO₃, Sigma-Aldrich) in 1,3-dioxolane and 1,2-dimethoxyethane (v/v = 1/2) solvents (both Sigma-Aldrich). The electrolyte labeled as LP30 was used as received (Sigma-Aldrich) and is composed of 1M of LiPF₆ in EC:DMC (v/v = 1/1). Further, the pure solvents 1,3-dioxolane and 1,2-dimethoxyethane labeled as C₃H₆O₂ and C₄H₁₀O_2, respectively, were also investigated.

3. Results

3.1. 3D-DIW Chemosensors Based on Semiconducting Oxide Nanostructures on CuO/Cu₂O/Cu Heterojunction Net with Al₂O₃ Coating for Battery Safety Applications

Studied samples were printed from suspensions with 1.5:1.0 Cu:H₂O weight ratios as reported in Table 1 and in our previous paper [23]. Afterwards, samples were thermally annealed and integrated into a sensor structure for further studies.

SEM images (Zeiss Gemini Ultra55 Plus, Oberkochen, Germany) of the prepared Al₂O₃/CuO-3D heterostructures after a second thermal annealing (TA) at 600 °C for 3 h in ambient conditions are presented in Figure 3. At low magnification (Figure 3a), Cu microparticles deposited on the glass substrate can be observed. MPs that were ALD coated with a thin layer of Al₂O₃ and subsequently TA at 600 °C for 3 h show a relatively homogenous surface structure (see Figure 3a). Figure 3b,c show micro agglomerations formed of Al₂O₃/CuO-3D heterostructures with diameters in the range of 12–20 µm from oxidized MPs, which entirely covered the device substrate and appear as a non-planar structure on the DIW stripes/traces. Figure 3d shows the formation of structured and interconnected crystallites of Al₂O₃/CuO on the surface of the oxidized Cu MPs with diameters in the range of 150–600 nm. A similar behavior was also observed for SCS deposited copper oxide layers in our previous papers after TA at 650 °C [37,38].

To determine the lattice parameters for the monoclinic structure and the unit cell volume for CuO, Equation (2) was used [39]:

$$\frac{1}{d^2}=\frac{1}{si{n}^2\beta }\left(\frac{h^2}{a^2}+\frac{k^{2}si{n}^2\beta }{b^2}+\frac{l^2}{c^2}-\frac{2hl cos \beta }{ac}\right).$$

(2)

The structural parameters of the Al₂O₃/CuO-3D heterostructures indicate no significant changes in values in comparison to previous studies [38].

The XRD patterns of the Al₂O₃/CuO-3D-DIW heterostructures are presented in Figure 4 (pattern 1 for as-grown and pattern 2 for TA at 600 °C for 3 h). For the as-grown structure (pattern 1), the presence of CuO, Cu₂O and metallic Cu phases is evidenced. After thermal annealing (pattern 2), all significant reflections are attributed to CuO (pdf #41-0254, Tenorite syn) with the highest intensity for the (−111/002) and (111) reflections at 2θ angles of 35.53° and 38.64°, respectively. Reflections related to the crystalline phases of Al₂O₃ were not detected, strongly indicating an amorphous Al₂O₃ layer. For copper and iron oxide heterostructures fabricated by the 3D printing process, the XRD pattern is presented in Figure S1 (Supplementary Material). From XRD data the presence of CuO and Fe₃O₄ phases, as well as of Cu₂O, Fe₂O₃, metallic Cu, and metallic Fe is evidenced.

In Figure 5a a high angle annular dark field (HAADF) scanning TEM (STEM) (Thermo Fischer Scientific, Waltham, MA, USA) micrograph of the edge of a CuO/Cu₂O microstructure is shown. From HAADF-STEM Z-contrast a core region consisting of heavier elements and a shell/layer region containing lighter elements (or lower mass thickness) becomes visible. By using STEM-EDX mapping of the elemental distribution it is shown that the layer contains aluminum oxide, while the inner region is made up of copper oxide. The homogenous distribution of the O-K signal shows that both areas are oxidized. From high-resolution TEM (HRTEM) micrographs of the edge region shown in Figure 5a, it is revealed that the Al₂O₃ layer is amorphous and has a thickness of ca. 20 nm, cf., example in Figure 5b.

To investigate the crystal structure of the sample selected area electron diffraction (SAED), patterns are taken from a larger sample area including the area shown in Figure 5a. The SAED pattern in Figure 5c is characteristic for a polycrystalline sample, which is in agreement with both Figure 5a,b where the inner CuO region appears non-homogenous in HAADF-STEM Z-contrast, as well as in the HRTEM phase contrast. By looking at the rotational average of the SAED pattern in Figure 5c, reflections assigned to monoclinic CuO and Cu₂O are identified. This is in agreement with previous findings for CuO nanostructures prepared in a similar way [40]. The presence of Cu₂O in contrast to the XRD analysis can be attributed to an assumed smaller crystallite size of Cu₂O after annealing, which might be below the detection threshold of coherently scattering domains by XRD. From the homogenous distribution of the Al₂O₃ layer seen in Figure 5a and the intact layer observed in Figure 5b, Al₂O₃ particle formation, as well as diffusion into the CuO, can be ruled out. This is supported by the fact that no crystallization of the Al₂O₃ has occurred for the given annealing temperatures (Figure 5c). In Figure S2 (Supplementary Material) a TEM investigation of copper and iron oxide nanostructures without deposition of an alumina layer are shown. The formation of crystalline CuO and Fe₃O₄ nanowires is demonstrated. Iron oxide nanowires appear to be formed with slightly smaller diameters than the CuO nanowires.

In Figure 6 the Raman spectrum of the Al₂O₃/CuO-3D heterostructures at room temperature, enfolded by 75 and 1000 cm⁻¹, is shown. From Figure 6, the mode peaks depicted at 273 cm⁻¹, 327 cm⁻¹, and 610 cm⁻¹ were designated to the CuO [38]. As in the case of the XRD and SAED measurements, no crystalline Al₂O₃ phase was detected, which again confirms its amorphous state as demonstrated by TEM on AlO_x. For the CuO structures, the zone-center optical-phonon modes are presented in Equation (3) [41]:

$$Г=A_g+2B_g+4A_u+5B_u.$$

(3)

Thus, there are nine optical modes, where 3 modes ($A_g+2B_g$) are Raman active [41,42] and 3$A_u+3B_u$ are infrared active [38,43].

Compositional images taken by energy dispersive X-ray spectrometry (EDX) (Zeiss Gemini Ultra55 Plus, Oberkochen, Germany) elemental mappings of the Al₂O₃/CuO-3D heterostructures after TA at 600 °C for 3 h are presented in Figure 7. Based on the EDX studies, a Cu content of 43.08 at%, an O content of 52.72 at%, and an Al content of 4.21 at% in Al₂O₃/CuO-3D samples was detected, see Figure S3 (Supplementary Material). In addition, Figure S3 (Supplementary Material) shows the EDX spectrum of the Al₂O₃/CuO-3D heterostructures, where peaks of Cu, O, and Al can be distinguished. The estimated [Cu]:[O]:[Al] ratio by EDX analysis (see Figure S3, Supplementary Material) indicates the formation of Al₂O₃/CuO DIW stripes/traces. Uniform distribution of Cu, O and Al elements is observed in the investigated areas. Such results were also confirmed by EDX line scans taken along three micro particles of CuO covered with a thin layer of Al₂O₃, which are shown in Figure S4 (Supplementary Material), respectively.

The XPS investigation of the Al₂O₃/CuO-3D heterostructures with thermal annealing (TA) at 600 °C for 3 h indicates the presence of O, C and Al, which can be detected in the XPS overall spectrum, as depicted in Figure 8a. The signal corresponding to C stems from surface contaminations by atmospheric carbon. The signal corresponding to Al is attributed to the Al₂O₃/CuO-3D heterostructures. The O-1s is mainly related to Al₂O₃, although small contributions from atmospheric contaminations may also be contributing. [33]. A closer look at the high-resolution spectrum of the Al-2p signal, presented in Figure 8b, reveals that the main peak of the Al-2p line is located around 73.5 eV. The Al-2p_3/2 and Al-2p_1/2 lines are not resolved. The peak position around 73.5 eV agrees well with Al³⁺ in Al₂O₃, which is always present between 73.7 eV and 74.8 eV [32,44]. No Cu 2p lines are visible in the region between 920 and 950 eV. This indicates that the Cu concentration in the topmost 5–10 nm is below the XPS detection limit of approximately 0.1%. It appears that the CuO is completely covered with Al₂O₃.

The gas-sensing performances of the synthesized structures were measured in the presence of two, typically used battery electrolytes (E1 and LP30) and two individual solvents (C₃H₆O₂ and C₄H₁₀O₂) to simulate their probable response during leakage of an LIB. The results can be seen in Figure 9a. Here, the gas response was determined from Equation (1) and the electrical conductivity indicated p-type conductivity behavior of the investigated DIW stripes/traces [36,45].

Figure 9a shows the gas response to different commonly used battery electrolytes and their solvents with a concentration of 100 ppm at various operating temperatures of the synthesized, 3D printed Al₂O₃/CuO heterostructures. From Figure 9a it can be found that at low operating temperatures of 200 °C and 250 °C, the Al₂O₃/CuO-3D samples are more selective to the C₃H₆O₂ vapor with responses of approximately 11% and 13%, respectively. At operating temperatures higher than 300 °C and 350 °C, the samples are more selective to the C₄H₁₀O₂ vapor with the response’s values of approximately 16% and 16%, respectively. Based on the investigations of Essl et al. [13] the temperatures at which the leaked gases and vapors begin to appear in a real battery system is from ~120 to 140 °C and increasing temperatures can reach the thermal runway (TR), which means that our heterostructures can be used for Lithium-ion battery technology applications. Figure 9b shows the I/V-characteristics at different operating temperatures of 3D printed Al₂O₃/CuO heterostructures. From Figure 9b it can be seen that the samples have a non-linear I-V characteristic.

Figure 10 shows the real dynamic responses of the 3D-DIW Al₂O₃/CuO heterostructures exposed to 100 ppm of C₃H₆O₂ (Figure 10a) and C₄H₁₀O₂ (Figure 10b) in air. From Figure 10a the response to C₃H₆O₂ is approximately 11% at an operating temperature of 200 °C with response and recovery/decay times of τ_r = 19.2 s and τ_d > 25 s, respectively. From Figure 10b the response to C₃H₆O₂ is approximately 16% at operating temperatures of 300 °C and 350 °C with response and recovery/decay times of τ_r = 14.1 s and τ_d > 15 s, and τ_r = 16 s and τ_d > 15 s, respectively.

3.2. Characteristics of Semiconducting Oxide Nanostructures by Direct Ink Writing of Metal Microparticles and Their Potential Application as Battery Safety Sensors

Copper and Iron microparticles are used in that study because these metals form oxide nanowires and nanoflakes of CuO and Fe₂O₃, respectively. CuO is found to be a p-type semiconductor and Fe₂O₃ is an n-type semiconductor. These two may form p-n-junctions with space charge regions that are very sensitive towards changes in the electronic configuration of the individual constituents. On a more general note, this approach demonstrates the faculties that are enabled by utilizing 3D printing or additive manufacturing as a means of gas sensor development for battery health monitoring. By integrating more than one particle type into one sensor the capabilities of quick and simple sensor integration are demonstrated for 3D printing or additive manufacturing.

Figure 11a shows the response of the 3D printed copper and iron oxide heterostructures to the previously used samples with a concentration of 100 ppm at different operating temperatures. From Figure 11a it can be seen that at a low operating temperature of 250 °C, the samples are more selective to the C₃H₆O₂ vapor with responses of approximately 28%. At operating temperatures higher than 350 °C, the samples are more selective to the vapor formed by the decomposition of the E1 electrolyte with the response value of approximately 46%. Figure 11b shows current-voltage characteristics for 3D printed copper and iron oxide heterostructures at different OPT. Experiments were conducted on several devices which all demonstrate the same behavior and exhibit ohmic contact behavior, thus the detection process can be assumed to be unaffected.

Figure 12 shows the real dynamic response curves of the 3D-DIW copper and iron oxide heterostructures exposed to 100 ppm of C₃H₆O₂ (Figure 12a) and E1 (Figure 12b) in air. From Figure 12a the response to the C₃H₆O₂ is approximately 28% at an operating temperature of 250 °C with response and recovery/decay times of τ_r = 9.4 s and τ_d = 21.8 s, respectively. From Figure 12b the response to the E1 vapor is approximately 46% at an operating temperature of 350 °C with response and recovery/decay times of τ_r = 6.7 s and τ_d > 15 s, respectively.

The proposed detection mechanism of the Al₂O₃/CuO-3D and 3D printed copper and iron oxide heterostructures is based on physico-chemical reactions on the surface of the heterostructures, which take place at different operating temperatures, is still under debate. As mentioned by Essl et al. [13] in the range of temperatures of ~120–140 °C, the first failures of the battery cells take place, such as electrolyte vaporization, heat generation, dangerous emissions of vent gases, the composition of toxic vent gases, and the emission of particles. At even higher temperatures thermal runway (TR) takes place [13].

Thus, based on the sensor data of the Al₂O₃/CuO-3D heterostructures, the operating temperatures at which the highest response for the C₄H₁₀O₂ vapors was obtained is 300 °C and 350 °C, and knowing from the literature that at temperatures higher than 150 °C on the copper oxide surface adsorbed oxygen species, thus generating voids according to Equation (4) [23,46]:

$$\frac{1}{2}{\mathrm{O}}_2\left(\mathrm{gas}\right)\stackrel{150℃}{\leftrightarrow }{\mathrm{O}}^{-}\left(\mathrm{ads}\right)+{\mathrm{h}}^{+}.$$

(4)

According to SEM images (Figure 3d) it is observed that on the surface of Cu MPs interconnected structures of Al₂O₃/CuO-3D are formed. This formation increases the surface/volume ratio, which is beneficial for sensory applications. Thus, when the C₄H₁₀O₂ vapor is introduced into the test chamber, it will interact with the oxygen species adsorbed on the surface, generating carbon dioxide and water molecules and as a result, will increase the electrical resistance of the heterostructure. In the case of the 3D printed copper and iron oxide heterostructure, the detection mechanism for acetone vapor is described in the previous work [19], and is similar in this case only as to the E1 vapors.

4. New Perspectives

Nanostructured materials and applications are used in a large variety of domains, including radiative environments. The application of nanotechnologies for the nuclear/ionizing radiation field has been demonstrated from the 1970s to the 1980s [47]; however, the prefix “nano-” has not been used in materials with these configurations [48]. Among the applications, we note the method of increasing the efficiency of nuclear fuel combustion by nanoadditives, or hardening the steel by adding 0.5% by mass of Yttrium Oxide NPs, or 0.37% by mass of F₂O₃ nanoparticles. In some materials of the nuclear industry, it is observed that the irradiation of the formation of new ordered, nanostructured phases resulted contrary to the expectations of improving the mechanical properties. The usefulness of nanomaterials has also been demonstrated in the manufacturing of radiation protection clothing with a four times higher radiation absorption efficiency [49].

Nanotechnologies and semiconductor physics are some of the most promising areas of research and applications. Nanocrystals from semiconductors display size-dependent optical and electronic characteristics. Such nanomaterials with crystalline structures bridge the gap among small molecules and large crystals, demonstrating discrete electronic transitions reminiscent of isolated atoms and molecules, in addition to enabling the use of the useful unknown earlier performances of crystalline materials. Moving on to nanodimensions, we create absolutely new conditions for transport effects with respective consequences.

When switching to nanodimensions in semiconductor heterostructures, the increase of energy barriers can be useful in limiting the movement of load carriers, thus, in nanodimensional conditions, this opens new perspectives for highlighting the importance of quantum effects and their applicability. The transition to nanodimensions essentially changes the properties of material—for example, the forbidden band in quantum dots depends on the size of the quantum dots. For these reasons, obtaining different consecutive nanoconfigurations of one and the same material allows us to speak of a completely new material, although it has the same chemical formula and manifests itself with radically different (physical, chemical, optical…) properties from the three-dimensional macroscopic material. We conclude again that nanostructures open new horizons in materials science and nanoelectronics.

Our interest in various research on semiconductor nanostructures in ionizing radiation fields is driven by our expectations regarding: technological applications, which can induce structural changes of irradiated environments, thus contributing to the elucidation of fundamental physico-chemical processes; catalytic reactions or inhibitions of chemical reactions and other technological processes; reliability of nanostructured semiconductor materials in ionizing radiation fields; devices for securing the control of radioactive and nuclear materials (custom control); devices for radiation protection control; and making new protective materials.

We know the wide use of robots in ionizing radiation environments (nuclear power plants, nuclear waste facilities, deep space exploration, etc.). Thus, the impact of radiation on critical components of robots, such as LIBs (its electrolyte materials), is an urgent issue. For these reasons, we are again interested in the durability of sensors that monitor the work of LIBs.

Nanostructured media allow us to measure ionizing radiation with greater accuracy than do single crystals, because we have greater experimental control over the parameters governing the detector: the size and shape of NPs, compared to a single crystal, in which the presence of defects and impurities will decrease sensor performance. Therefore, nanostructured materials can be designed as materials for the next generation of ionizing radiation detection. The adaptation of this depends on overcoming the expected difficulties associated with the use of a composite material, consisting of countless interfaces at which information can be lost.

If we talk about perspectives in medicine, the radiation protection effects of NPs, such as ZnO, carbon, characterized by strong antioxidant properties, have an important role in protecting cells against DNA damage induced by ionizing radiation. The excellent biocompatibility of some metal oxides, ZnO NPs are among the most popular oxide, NPs in biological applications due to their excellent biocompatibility, economic, and low toxicity [50].

In analyzing the role of nanostructured semiconductor oxides, there is no doubt in the presence of ZnO as a sensor for a wide range of gases or toxins. ZnO (intrinsically or doped with impurities, is a semiconductor with a high band gap (Eg = 3.37 eV), characterized by a lower impact of nuclear radiation compared to Si, GaAs, and GaN. The scintillator synthesis on glass substrates indicates that it can be a promising material system for the detection of alpha radiation. The evaluation was performed at different sources of alpha radiation demonstrating a high sensitivity and reproduction of the results from 5% (high alpha radiation activities) to 20% (very low alpha radiation activities) [51].

Another eloquent example refers to X-ray sensitive ZnO nanofilms for medical radiodiagnosis. The experimental data indicated that the zinc oxide device possesses some increase in its sensitivity to the ionizing radiation as the X-ray effective energy decreases, unlike other types of semiconductor electronic devices frequently used as an X-ray detector [52]. It should be noted that ZnO sensors also have a dual application, such as the application of UV sensors as a scintillator for X-ray detection [53]. In combination with the metal contacts in Au and Ag, the ZnO sensors improve the substance of their luminescence parameters [54].

A new use of NPs from oxides of different elements, such as Al₂O₃, SiO₂, Sc₂O₃, TiO₂, V₂O₅, Cr₂O₃, MnO₂, Fe₃O₄, CoO, NiO, CuO, ZnO, ZrO₂, MoO₃, Nd₂O₃, Sm₂O₃, Eu₂O₃, Gd₂O₃, Er₂O₃ and HfO₂ are studied as radiosensitizing perspectives. The results inspire optimism for the use in radiotherapy and radiodiagnosis [55]. The role of nanostructures in the detection of various gases, or ionizing radiation, is expected to be developed especially in p-n structures, CMOS, various strip detectors, AC coupled strip detectors, double strip detectors, pixel detectors, hybrid pixel detectors, various drift detectors, different SSD, and other bi/three nanodimensional structures.

5. Conclusions

This work reports the response of the 3D printed Al₂O₃/CuO, as well as copper and iron oxide heterostructures, to various vapors of battery electrolytes and typically used solvents with a concentration of 100 ppm at different operating temperatures. For Al₂O₃/CuO-3D heterostructures, the detection of the C₃H₆O₂ vapors with a response of approximately 11% at an operating temperature of 200 °C was realized, with response and recovery/decay times of τ_r = 19.2 s and τ_d > 25 s, respectively. However, at operating temperatures higher than 300 °C and 350 °C, the higher response is to C₄H₁₀O₂ with a gas response value of approximately 16% showing response and recovery/decay times of τ_r = 14.1 s and τ_d > 15 s, and τ_r = 16 s and τ_d > 15 s, respectively. For the 3D printed copper and iron oxide heterostructures, it was found that at a low operating temperature of 250 °C, the samples showed the highest response to the C₃H₆O₂ vapor with responses of approximately 28%. However, at operating temperatures higher than 350 °C, the samples are more selective to the vapors formed by the degradation of the E1 electrolyte with a response value of approximately 46%. As a continuation of our research, different metal and semiconductor oxides are characterized by various techniques, demonstrating unique electrical, structural, and optical properties, which allow their use in various detection devices. A promising area of nanostructured sensors is gas or vapor detection. TEM, as well as SEM investigations, confirmed the formation of a homogenous, 20 nm thick Al₂O₃ layer atop the CuO microstructures via ALD. The formation of this heterojunction alters the gas response compared to the CuO/Fe₂O₃ system and thus allows to tailor the sensors to its intended application. The processes involved in detecting gases with metal/semiconductor oxides are complex and require a fundamental understanding of the physico-chemical interactions between gas molecules and the surface. There is no doubt that nanostructured oxides will play a significant role in the upward development of gas sensors based on them with improved detection performances. Their electrochemical, optical, and radiative detection properties have a significant impact on monitoring the environment, health, and sustainability of the operation of various devices based on (electro-) chemical reactions. The surfaces of metal and semiconductor oxides have been recommended as the performance basis for functionalization and biofunctionalization, demonstrating high stability, sensitivity, and selectivity to a variety of molecules needed to be identified/controlled. The technological realization of the nanodimensions of the sensors based on oxides ensures a large contact surface that determines increased sensitivity and resolution. Electronic, optical properties, and selectivity of sensitivity to harmful components can be managed by technological doping, the formation of nanocomposites, and heat or radiative treatments. Regarding place to mounted or 3D printed such sensors for battery safety, is not only possible or imaginable to place a sensor outside a battery pack, but it might also be integrable into the pouch cell or inside the pouch cell, where it has direct access to the evolving gases. However, since this study is only to evaluate if such a sensor is detecting and at which time it is detecting evolving gases, it is a first step in the sensor design. By checking the sensor properties, the second step of our perspective paper is how to integrate it into a smart battery device. Presented results and perspectives clearly indicate a possibility to develop chemosensors based on semiconducting oxide nanostructures for battery safety applications and ionizing radiation by a DIW approach.