Gas-discharge induced flash sintering of YSZ ceramics at room temperature.

Abstract: This is the first study to conduct the flash sintering of 3 mol% yttria-stabilized zirconia (3YSZ) ceramics at room temperature (25 °C) under a strong electric field, larger than 1 kV/cm. At the standard atmospheric pressure (101 kPa), the probability of successful sintering is approximately half of that at low atmospheric pressure, lower than 80 kPa. The success of the proposed flash sintering process was determined based on the high electric arc performance at different atmospheric pressures ranging from 20 to 100 kPa. The 3YSZ samples achieved a maximum relative density of 99.5% with a grain size of ∼200 nm. The results showed that as the atmospheric pressure decreases, the onset electric field of flash sintering decreases, corresponding to the empirical formula of the flashover voltage. Moreover, flash sintering was found to be triggered by the surface flashover of ceramic samples, and the electric arc on the sample surfaces floated upward before complete flash sintering at overly high pressures, resulting in the failure of flash sintering. This study reveals a new method for the facile preparation of flash-sintered ceramics at room temperature, which will promote the application of flash sintering in the ceramic industry.

Keywords: flash sintering; yttria-stabilized zirconia (YSZ); room temperature; flashover; AC field; low atmospheric pressure

1 Introduction

Flash sintering is a novel field-assisted sintering technique (FAST) discovered by Cologna et al. ^[1] in 2010. During flash sintering, ceramic samples are subjected to a moderate electric field and current flows through ceramics. In this process, ceramics can be densified more rapidly (usually in < 5 min) at furnace temperatures several hundred degrees lower than that utilized during traditional sintering. Various materials such as ionic conductors, semiconductors, and insulators have been successfully prepared by flash sintering or other FASTs ^[2–9]. 

Yttria-stabilized zirconia (YSZ) has a wide range of applications such as electrolytes and barriers ^[10–15]. It is also the most widely studied material in flash sintering research. DC power is more commonly used than AC for the flash sintering of YSZ. Many researchers have attempted to lower the onset temperature of YSZ by increasing the electric field power in both DC and AC flash sintering [16]. Downs and Sglavo ^[17] succeeded in flash sintering cubic 8% mol yttria-stabilized zirconia (8YSZ) at 390 ℃ under a 2.25 kV/cm DC field and a 120 mA current; however, the linear shrinkage of the sintered samples reached only 8.5%. Yadav and Raj ^[18] induced flash sintering on dense 3YSZ and 8YSZ polycrystals at 6.00 kV/cm DC and 180 ℃ furnace temperature (approaching its Debye temperature limit), inducing the strongest electric field ever utilized for this process. Liu et al. ^[19] sintered 8YSZ to 95.3% relative density under an AC field of 2760 V/cm and at 420 ℃. Steil et al. ^[20] sintered 8YSZ pellets to 80% relative density with a 300 V/cm AC field at 800 ℃, while the electric field strength in other AC flash sintering experiments of YSZ is lower than 200 V/cm ^[10,21–27]. Currently, the Debye temperature is still regarded as the lower bound of flash sintering for YSZ ^[28]. Moreover, thus far, there have been no reports on flash sintering of YSZ at room temperature. 

Biesuz et al. ^[29] and Shi et al. ^[30] found a correlation between dielectric breakdown and flash sintering. According to Liu et al. ^[31], the dielectric breakdown under AC can trigger the flash sintering of zinc oxide at room temperature (lower than its Debye temperature of approximately 166.85 ℃), and they reported the highest relative density of sintered zinc oxide of 99% ^[31,32]. These results indicate that flash sintering induced by AC dielectric breakdown is likely to facilitate the formation of dense YSZ ceramic samples at furnace temperature lower than their Debye temperature (the Debye limit temperature of YSZ ceramics ranges from 176.85 to 251.85 ℃) ^[18]. 

Several studies on flash sintering in different gas environments have been reported. Liu et al. ^[33] found that a lower oxygen partial pressure leads to a higher concentration of electrons and oxygen vacancies in YSZ, which will boost its conductivity and reduce its flash sintering onset voltage. Zhang and Luo ^[34] proved that in a reduced atmosphere (Ar + 5% H₂), the flash sintering of zinc oxide can occur at a temperature lower than 120 ℃ in a 1000 V/cm electric field. Therefore, the atmospheric environment is a key parameter in flash sintering. According to Paschen’s law, the dielectric breakdown voltage of an air gap decreases with pressure when the product of gap length and pressure is higher than 0.5 cm·mmHg. The surface breakdown (flashover) voltage of insulators decreases as the atmospheric pressure decreases ^[35–37]. Hence, in flash sintering at low pressure, the lower onset voltage of the flashover possibly facilitates flash sintering. 

In this study, an AC power source was used, and we discovered that the relative densities of the 3YSZ samples can be increased to 99% by flash sintering at room temperature for 30 s. The surface flashover phenomenon in the flash sintering process was also discussed.

2 Experimental methods

High-purity 3YSZ powder (> 99%, average grain size 30 nm, Nanjing Mission New Materials Company Limited, Nanjing, China) was blended with a binder through spray-drying granulation. The mixture was uniaxially pressed into dog-bone-shaped samples at 270 MPa, and the sample dimensions are shown in Fig. 1(a). The green bodies of the YSZ samples were then heated in a furnace to 400 ℃ at a heating rate of 2 ℃/min, and maintained at this temperature for 2 h for binder removal through drying. Next, the samples were presintered at 1100 ℃ for 2 h at a heating rate of 2 ℃/min to enhance their strength. Finally, high-temperature GW02 silver paste was painted on both ends of the dog-bone-shaped ceramics to decrease contact resistance with the circuit. Painted samples were baked at 650 ℃ for 10 min for silver consolidation. The samples sintered in this experiment were denoted as S20–S100, as listed in Table 1. 

The flash sintering setup is shown in Fig. 1(b). The 3YSZ samples were placed in a vacuum chamber, and connected to a high-voltage AC test power source (50 Hz, DTW-100/50, Xinyuan Electric Company, China) through 0.5 mm radius platinum wires. The capacity, maximum output voltage, and rated output current of the test power source were 100 kV·A, 50 kV, and 1 A, respectively. This test power supply was typically used in high-voltage engineering applications. A corundum board was placed between the ceramic samples and the bottom of the vacuum chamber for insulation. Our test power source cannot limit the current automatically. High-voltage resistors, whose total resistance varies from 0 to 20 kΩ, were also added into the circuit to limit the current in the experiment. 

Fig. 1 (a) Dimensions of our dog-bone-shaped sample (in mm). (b) Flash sintering experiment setup. 

The pressure inside the vacuum chamber was adjusted to the standard values after connecting the circuit. Because of the use of the air pump, the lowest barometric pressure in the chamber used in this study was 20 kPa. The 50 Hz high-voltage test power supply was turned on to initiate the flash sintering experiment on YSZ. The 50 Hz AC power was controlled manually, and its initial output voltage was ~0.9 kV. The output voltage was increased in small increments until the current surged, which signified the onset of flash sintering. The average rising rate of the voltage was maintained at < 0.4 kV/s to prevent voltage surge from increasing the onset voltage. After the flash sintering process started, the current was maintained for 30 s before the output of the test source was lowered to a minimum and turned off. 

The output voltage and current variations were recorded using an acquisition card with an acquisition rate of 5000 Hz. The voltage, current, electric field, current density, and power density mentioned here were root-mean-square values. The video of the YSZ samples during flash sintering was recorded by a high-speed camera (Phantom V2012). The exposure time of all the images recorded by the high-speed camera shown in Figs. 3–5 was set lower than 100 μs to capture the electric arc whose light emission was extremely strong. This means the light of normal intensity cannot be recorded. The relative densities of all samples were measured by Archimedes drainage. The crystalline structures of the YSZ ceramic samples were determined through X-ray diffraction (XRD) analysis (D8 Advance, Bruker, Germany). Scanning electron microscopy (SEM; SU8010, Hitachi, Japan) was conducted to acquire high-resolution microstructure images of the sample and fracture surfaces. The surfaces of samples S20, S60, and S100 were polished and thermally etched at 1300 ℃ for 30 min before being observed by SEM. 

3 Results and discussion 

3. 1 Variations of electrical parameters during flash sintering

Table 1 summarizes the experimental conditions of typical 3YSZ flash sintering experiments. The onset electric field, flash current density, and relative density are listed with different pressures used in the experiment. The estimated temperatures in the steady state were acquired using black body radiation models ^[38].  Compared with other studies, our estimated temperatures are much higher because of the high steady state power ^{[1,5,19,34,39]}. 

Table 1 Main parameters of 3YSZ flash sintering experiments 

Figure 2 shows the variations in the electric field, current density, and power density during the flash sintering process of S60, which is similar to those of the remaining samples. The electric field strength is increased gradually, and the current density is maintained at an extremely low level during the incubation stage. A flash sintering event occurs when the electric field exceeds a certain level, during which an abrupt increase in the current density occurs, and the electric field suddenly drops. After the flash event, the electric field stabilizes at a low value, and the current density remains unchanged until the electric power is turned off. The power density of the 3YSZ sample surges to its maximum when flash sintering occurs and gradually decreases to a lower value at the steady rate. Although the variation tendency of the electrical parameters described in Fig. 2 coordinates with the findings of previous flash sintering studies, the visual phenomenon in our flash sintering experiment is very different from that reported in other studies ^[40], as shown in Fig. 3. 

Fig. 2 Electric field, current density, and power density variations during flash sintering of sample S60. 

3. 2 Flash sintering at standard atmosphere pressure 

Two phenomena occur during the flash sintering process at the standard atmospheric pressure, as shown in Figs. 3 and 4. The “0 s” in Figs. 3 and 4 corresponds to the moment when current surge point as Fig. 2 demonstrates. With sample S100-1 (Fig. 3), the arc appeared but no flash sintering occurred. Moreover, with sample S100-2 (Fig. 4), the arc first appeared, then disappeared, and finally flash sintering occurred. When the flash current density reaches 60.0 mA/mm² at 100 kPa, flash sintering fails owing to the floating up of the electric arc, as shown in Fig. 3. After flashover occurs (Fig. 3(b)), the electric arc does not induce global flash sintering, and only floats over the ceramic samples during the entire 30 s process, as demonstrated in Figs. 3(b)–3(d). Therefore, even if ceramic sintering does not appear, the arc-floating phenomenon indicates that an electric arc appears in our flash sintering experiments. 

Fig. 3 Snapshots recorded using a high-speed camera during the flash sintering of S100-1: (a) before flash sintering and at (b) 0 s, (c) 2.16 s, (d) 10.09 s, (e) 20.04 s, and (f) 30.07 s after the onset of current surge at a current density of 60.0 mA/mm².

Figure 4(a) shows the S100-2 green body without sintering, and Figs. 4(b)–4(f) present snapshots captured at 0, 1.78, 5.50, 10.69, 11.30, 13.50, and 17.45 s after the onset of flash sintering at 100 kPa, close to the standard atmosphere pressure. At the beginning of the flash sintering process, as shown in Fig. 4(b), the surface flashover occurs, and an electric arc appears above the sample. Considering that the onset voltage indicated in Fig. 2 is much lower than the breakdown voltage of the air gap, and the arc appears outside the sample, this phenomenon is very likely to be surface flashover rather than air gap breakdown inside the sample. (Surface flashover is a special kind of air gap breakdown. It happens in the air gap very close to the dielectric surface, where the electric field is strongly intensified, so its breakdown voltage is much lower.) Figure 4(b) presents the moment when the current density surges, as shown in Fig. 2. In the first 10 s after the flash onset, the electric arc produced by the flashover floats above the upper surface of the sample, and there is no indication of flash sintering. Then, two glowing areas develop from both ends of the sample (Fig. 4(e)), and connect with each other on the upper part of the sample (Fig. 4(f)). The glowing area covers the entire upper part 13.50 s after the flash onset (Fig. 4(g)), and the electric arc disappears, which indicates that the current starts to completely flow through the upper part of the sample. Finally, the glowing area expands to the entire sample, indicating the start of global flash sintering (Fig. 4(h)). The entire process, from the onset of flashover to global flash sintering (Figs. 4(b)–4(g)), takes more than 15 s at 100 kPa. The total flash sintering time, after Fig. 4(h), is only approximately 12.55 s. 

The arc-floating performances in S100-1 and S100-2 are different; thus, the later sintering behavior in both samples is affected. Obviously, there are two current paths during the whole sintering process, one in the arc and the other in the sample. Most of the currents flow through the electric arc when surface flashover happens. After a period of time, as the electric arc heats the upper part of the 3YSZ ceramics, the conductivity of the upper part of the 3YSZ ceramics increases, making more currents flow through the upper part. With larger current, the temperature of the upper part of the sample will be further boosted, improving its conductivity and leading to more current flowing through it. Under the impact of this positive feedback loop, partial flash sintering occurs, and more currents flow through the upper part of the 3YSZ samples, with currents of the electric arc decreasing gradually. Finally, currents of the electric arc descend to zero, and the arc disappears, and the only current path was through the sample, as shown in Figs. 4(f) and 4(g). This indicates that, to successfully conduct flash sintering, the arc should be short-circuited by the current passing through the ceramic sample. Furthermore, the arc holding time in S100-2 was different from that in a previous study on ZnO ceramic sintering (< 1 s) ^[31], and it was more than 10 s in S100-1 at standard pressure.

Fig. 4 Snapshots recorded using a high-speed camera during the flash sintering of S100-2: (a) before flash sintering and at (b) 0 s, (c) 1.78 s, (d) 5.50 s, (e) 10.69 s, (f) 11.30 s, (g) 13.50 s, and (h) 17.45 s after the onset of flash sintering, with a current density of 49.8 mA/mm².

Therefore, we can conclude that flash sintering at 100 kPa is triggered by the surface flashover. When the voltage reaches a certain level and the flashover occurs, the electric arc, whose temperature is very high, will dramatically increase the temperature of the upper surface of the 3YSZ samples. Higher temperatures will lead to larger conductivity, and higher conductivity will induce larger current, which will further increase the temperatures. This positive cycle can induce partial flash sintering on the upper part of the ceramic samples. Then, partial flash sintering continues this positive cycle, creates a current pathway in the upper part of samples, and short-circuits the electric arc, making all the currents flow through ceramic samples. Finally, the partial flash sintering expands to the entire sample, and the current flows through the whole sample, inducing complete flash sintering of the 3YSZ samples. Ceramic samples are densified by the current flowing through them. According to the predictions of thermal radiation model ^[38], the ceramic samples reach more than 1500 ℃ in less than 20 s under the heating effect of current inside them. Therefore, the Joule heating as well as the ultrafast heating effect definitely contributes to the densification of the 3YSZ ceramic samples ^[41]. 

Anyway, despite the similarities of densification mechanisms, the onset mechanism of flash sintering proved in our study is very different from those previously reported such as those based on thermal runaway, Frenkel-pair nucleation, and electrochemical effects under DC voltage, in which the current flowing through the interior of the ceramic samples triggers flash sintering ^[38,42–44]. 

3. 3 Flash sintering under a low pressure of 60 kPa

Arc floating is very problematic during 3YSZ flash sintering at pressures of 100 kPa. This is because if the current density when arc appearing is high, the effective sintering time is decreased, which can even lead to the failure of the flash sintering experiment. To address this problem and reduce the onset electric field, we conducted flash sintering experiments at low atmospheric pressures of 80, 60, 40, and 20 kPa. The snapshots captured during flash sintering experiments of S60, which were conducted at 60 kPa, are shown in Fig. 5. The “0 s” in Fig. 5 also corresponds to the moment when current surge as Fig. 2 demonstrates. The flash sintering processes of S20, S40, S60, and S80 are similar to that of S100-2, indicating that a similar onset mechanism. Therefore, it is reasonable to say that the flash sintering in our research is induced by the surface flashover of the 3YSZ samples. 

In addition, there are still some differences between flash sintering at standard atmospheric pressure and low pressure. Based on the flash sintering process of S100-1 (Fig. 4) and S60 (Fig. 5), we find that with similar flash current densities of ~60 mA/mm², flash sintering fails owing to the arc-floating issue at 100 kPa, but succeeds at 60 kPa. During the flash sintering of S100-2 (current density of 49.8 mA/mm²) at 100 kPa, the time for arc floating was more than 10 s, and the global sintering duration was only 12.55 s. However, in S60 (current density of 58.9 mA/mm²), the arc-floating time is less than 2 s, and the complete flash sintering exceeds 27 s. Therefore, by inhibiting the electric arc floating, conducting flash sintering at a low pressure can not only prevent flash sintering failure when the flash current density is high, but also decrease the transition time between the surface flashover and global flash sintering. Thus, roomtemperature flash sintering of 3YSZ at a low atmospheric pressure is possible.

Fig. 5 Snapshots recorded using a high-speed camera during the flash sintering of S60: (a) before flash sintering and at (b) 0 s, (c) 0.95 s, (d) 1.70 s, (e) 2.43 s, (f) 2.90 s, and (g) 15.20 s after the onset of flash sintering at a current density of 58.9 mA/mm².

Figure 6 shows the onset electric field variation at different pressures. Frywell et al. ^[37] reported that the relationship between the flashover voltage and atmospheric pressure can be determined by Eq. (1): 

where P₀ is the standard atmospheric pressure (kPa), U₀ is the flashover voltage at the standard atmospheric pressure (V), n is the influence index of the pressure, P is the atmospheric pressure (kPa), and U_f is the predicted flashover voltage at pressure P. If the sample geometry remains unchanged, this function can be written as

E_f =  aPⁿ (2) 

where E_f is the flashover electric field, and a is a constant. Adopting Eq. (2) as a fitting function, the fitting result is achieved as that shown in Fig. 6. The adjusted R-square value of 0.9718 is higher than 0.95, proving that the relation between the onset field and the barometric pressure can be expressed by this equation. As shown in Fig. 6, the onset electric field of flash sintering would increase as the experimental atmosphere pressure increased. According to the previous research on the flashover of electrical insulators, the n value lies in the range of 0.2–0.9 ^[45], and our n value is 0.7693, indicating that in our experiment, the influence of pressure on the flashover voltage is relatively strong. 

Fig. 6 Average onset electric field as a function of atmospheric pressure. 

3. 4 Short-time flash sintering 

To further confirm that flash sintering is induced by the electric arc of the surface flashover, an additional test was conducted. The experimental conditions (resistor value and atmospheric pressure) were the same as those used for the flash sintering of S60. After flash sintering, the power source was turned to a minimum and switched off immediately (in less than 2 s). The relative density of this sample only reaches 70.0%. The fractured surfaces of the sample sintered using this process were observed by SEM, as shown in Fig. 7. It can be seen that near the upper surface, on which flashover occurs, the microstructure was dense with only a few pores, and the grain sizes were larger. In the central part of this sample, a loose microstructure and pores and small grains were visible, indicating that the sintering was incomplete. The lower surface of the sample appeared to be the same as the green body of YSZ ceramics, and no obvious sintering was observed. These images show a different sintering process: The YSZ sample was sintered from the upper surface near the arc, then spread to the center, and finally to the lower surface. Therefore, the flash sintering process starts from the surface whereon flashover occurs, which confirms the proposed surface flashover mechanism. 

3. 5 Explanation of electrical arc floating 

S100-1 was the only sample for which flash sintering failed. If the atmospheric pressure decreases to 80 kPa similar to that for S80, a strong arc-floating phenomenon 

Fig. 7 SEM images of the fractured surfaces of 3YSZ sample sintered for less than 2 s. 

that leads to flash sintering failure will not occur; thus, higher atmospheric pressure promotes arc floating, as discussed below. The electric arc tends to move upward under the impact of thermal buoyancy ^[46]. The thermal buoyancy of the electric arc (Fb, in N) can be expressed by Eq. (3): 

F_b = ρπr_a²L

where ρ is the density of the ambient atmosphere (kg/mm³), r_a is the radius of the electric arc (m), and L is the length of the electric arc (m), which remains constant in our study. The variations in r_a can be expressed as ^[47]:

where P is the pressure of the ambient atmosphere (kPa), P₀ is the standard atmospheric pressure (kPa), and I_m is the maximum current of the electric arc (A). The 0.86π denominator has a unit of A/m². The density of the ambient atmosphere (ρ) can be determined by Eq. (5): 

where ρ₀ is the density of the ambient atmosphere at the standard atmospheric pressure (kg/mm³), and T is the temperature of the ambient atmosphere (K). Substituting Eqs. (3) and (4) into Eq. (1), we obtain the expression of thermal buoyancy per unit length as a function of ambient pressure and flash current: 

According to Eq. (6), thermal buoyancy per unit of the electric arc increases when the flash current increases or when the experiments are conducted at high pressure, which inhibits both the electric arc from floating higher up and high-energy particles produced by discharge from reaching the upper surface of the samples. Thus, the thermal effects of the electric arc on the 3YSZ samples are weakened, lowering the temperature of the 3YSZ upper surface and inhibiting the development of partial flash sintering. 

In addition, a higher atmospheric pressure leads to a higher oxygen partial pressure. Increased oxygen partial pressure can clearly reduce the conductivity of the 3YSZ samples ^[33], thereby hindering flash sintering. Heat convection intensifies at high pressure ^[48]. This will also suppress flash sintering by diluting the high-temperature particles produced by the electric arc, thereby decreasing the temperature of 3YSZ. 

3. 6 Structure and morphology of samples

The XRD spectra of the samples are shown in Fig. 8. According to Fig. 8(a), the powder of the 3YSZ samples consists of a tetragonal phase and a monoclinic phase. After pre-sintering at 1100 ℃ for 2 h, the monoclinic phase was removed from the green bodies of 3YSZ, and only the tetragonal phase remained. The YSZ phase transitions between monoclinic and tetragonal and between tetragonal and cubic are all martensitic transformations. Although the martensitic phase transformation is reversible, the hysteresis effect induces a higher monoclinic to tetragonal transition temperature than tetragonal to monoclinic transition temperature ^[49]. According to Andrievskaya et al. ^[50] and Xie and Xue ^[51], the martensitic transformation temperature of 3YSZ is approximately 600 ℃ for the monoclinic to tetragonal transition and lower than −196.15 ℃ for the tetragonal to monoclinic transition. Thus, the monoclinic phase of 3YSZ becomes tetragonal during pre-sintering at 1100 ℃, and remains tetragonal when cooled to room temperature. 

Figures 8(c)–8(e) also show that the flash-sintered samples only contain the tetragonal phase and not the monoclinic phase. To determine whether a cubic phase exists in the sintered 3YSZ samples, the XRD spectrum of S60, which has the maximum steady-state temperature, measured by slow scanning between 72° and 75°, is shown in the inset of Fig. 8(d). No obvious peak was observed between the two peaks of the tetragonal phase, indicating very low content of the cubic phase. Thus, it is reasonable to state that the 3YSZ samples with a pure tetragonal phase are obtained after flash sintering, and negligible monoclinic or cubic phase is involved. 

Fig. 8 XRD spectra of (a) 3YSZ powder, (b) 1100 ℃ pre-sintered green body, (c) sample S40, (d) sample S60, and (e) sample S80. 

Figure 9(a) shows the surfaces of the green body before pre-sintering, and Figs. 9(b)–9(f) show the microstructures of the polished and thermally etched surfaces of the flash-sintered samples (thermal etching at 1300 ℃ for 30 min). All SEM images were captured at the center of the polished surfaces of the samples, and the magnification factor was 45,000. For a certain sample, the microstructures on the polished surface upon thermal etching were essentially the same at different locations. Nearly no pores are observed in Figs. 9(b)–9(f) because their relative densities are higher than 97%. According to Figs. 9(b)–9(f), the average grain sizes of the flash-sintered samples are approximately 180 nm, which is only six times the average grain size of the initial powder with an average grain size of 30 nm. Therefore, the grains only undergo moderate growth during the pre-sintering and flash sintering processes. Meanwhile, Figs. 9(b)–9(f) show that some grains merge with each other, and their grain boundaries appear dimmer, indicating that the grains are still growing although the samples are fully densified when flash sintering stops. 

Fig. 9 SEM images of (a) green bodies before pre-sintering and polished surfaces of (b) S20, (c) S40, (d) S60, (e) S80, and (f) S100-2. 

Figure 10 shows the polished and thermally etched cross-sections of S20, S60, and S100-2. The interior of the sintered 3YSZ is fully compacted by grains, and there is no obvious structural difference among the 3YSZ samples sintered at different pressures. Nearly no pores are observed in Fig. 10 for relative densities of > 97%, and the average grain sizes are < 200 nm, which is similar to that of the polished surfaces in Fig. 9. 

Fig. 10 SEM images of the cross-sections of polished (a) S20, (b) S60, and (c) S100-2. 

4 Conclusions

In this study, by conducting room-temperature flash sintering at a low pressure, we successfully sintered high-density 3YSZ. It is likely that the surface flashover leads to room-temperature flash sintering, and the onset electric field strength decreases with decreasing air pressure. Additional research should be conducted to further explore the optimal technological parameters of YSZ flash sintering, and find other ceramics whose flash sintering can be induced at room temperature. Nevertheless, our results expand the application scope of flash sintering. However, 80 kPa is not a very low atmospheric pressure, and it can be reached in many plateau cities such as Kunming, where electric power is abundant. Therefore, considering the availability of plentiful electric power sources and suitable atmospheric pressure in such areas, energy-efficient full-electric sintering of YSZ could be achieved in the future. 

Reference: Omitted