Study on Lithium-Ion Battery Degradation Caused by Side Reactions in Fast-Charging Process

Introduction

It is recorded that electric vehicles can reduce emissions by about 10–20% and pollution caused by transportation (Onat et al., 2014; Almeida et al., 2019). With the increasing number of electric vehicles, the driving range and the charging speed are getting more and more attentions, which requires continuous improvement of the energy density and the maximum charge/discharge rate of lithium-ion batteries. To meet these requirements, the electrodes of the batteries are tended to get thicker and denser (Zhang et al., 2003a; Chen et al., 2021; Zhou et al., 2021). However, as the thickness and density of the cathodes of the batteries increase, the electrolyte is difficult to fully enter the electrode, increasing the possibility of lithium plating on the anode and the risk of safety (Doyle and Newman, 1995; Zhang et al., 2003b; Ouyang et al., 2015; Waldmann et al., 2018; Tomaszewska et al., 2019). Thermodynamically, under normal conditions, the reaction enthalpy of lithium-ion plating is greater than that of lithium-ion insertion, and it is difficult for lithium plating to occur (Legrand et al., 2014; Gao et al., 2021). However, during the charging process, an induced overpotential is formed due to the shift in equilibrium, which may cause the potential of graphite particles to drop below 0 V, resulting in the lithium plating (Hein and Latz, 2016). The lithium plating is a serious side reaction, which would severely consume the amount of cyclable lithium in the battery. It can also lead to a reduction in battery capacity and an impaired safety of the batteries (Fleischhammer et al., 2015; Yang et al., 2020; Su et al., 2021; Zhang et al., 2022).

Another cause of loss of lithium inventory (LLI) in lithium-ion batteries is the overgrowth of SEI film (Matadi et al., 2017). During the first charge/discharge cycle of a lithium-ion battery, the electrode material reacts with the electrolyte at the solid-liquid phase interface, forming a passivation layer covering the surface of the electrode. The process is called the chemical formation. The passivation layer is the SEI film, which is an interface layer with the characteristics of a solid electrolyte. It is insulated against electrons, but Li⁺ can enter and exit freely. Although the SEI films are formed on both cathode and anode, the SEI film on the cathode has much less influence than that on the anode (Guan et al., 2018). After numerous charge/discharge cycles, the SEI film on the anode surface would gradually increase (Klett et al., 2014), which would consume lithium-ions and cause the battery capacity to gradually decay (Barré et al., 2013; Stiaszny et al., 2014). Usually, the SEI film and lithium plating would affect each other. When the battery is charged at high current rates or the ionic conductivity of the SEI film is significantly reduced at low temperatures, lithium-ions cannot be embedded in the anode in time, and they would accumulate on the SEI film, resulting in lithium plating. The plating of lithium is generally reversible, and the plated lithium would be re-oxidized at about 0.1 V, which is much lower than the potential of delithiation of the anode (Burow et al., 2016). Therefore, the plated lithium would dissolve into recyclable lithium-ions during discharge. However, the two side effects could affect each other. The lithium plating would cause the SEI film damage, forcing the regeneration and increasing of the SEI film (Koleti et al., 2020). In addition, a secondary SEI film can also be formed on the plated lithium surface (Zhao et al., 2019).Due to the uneven deposition of lithium on the surface of the anode, some protrusions will be formed on the surface of the SEI film, making the SEI film uneven (Lewerenz et al., 2017; Wu et al., 2020). With the continuous progress of lithium plating, some protrusions would grow into lithium dendrites, which would penetrate the separator, causing internal short circuits and thermal runaway of lithium batteries. It could seriously affect the safety of lithium-ion batteries (Ecker et al., 2017a). In addition, during the lithium plating process, some of the plated lithium would be fractured and exfoliated. When the plated lithium is completely covered by the SEI film, they would become “dead lithium,” causing irreversible loss of cyclable lithium (Zhao et al., 2019; Zhu et al., 2020; Lin et al., 2021; Zhu et al., 2021; Choi and Park, 2022)。

It can be concluded that the lithium plating and SEI film growth have an impact on the battery performance, influencing cycle ability and safety of lithium-ion batteries. In addition to the LLI phenomenon, the relevant literature also shows that loss of active material (LAM) will also affect the battery performance, which is usually caused by materials mechanical pulverization, metal dissolution, graphite exfoliation and electrolyte decomposition, resulting in the decline of battery capacity (Xie et al., 2021; Ruan et al., 2022).

Different from the equivalent circuit model (ECM) that only describes the output characteristics of lithium-ion batteries, the electrochemical model is based on the laws of physics to describe the real electrochemical behavior inside the battery (Plett, 2015; Schimpe et al., 2018). Currently, electrochemical lithium-ion battery models include microscale models, pseudo three-dimensional models (P3Ds), P2D models and single particle models (SPMs). Among them, the microscale model is complex and computationally expensive, which is not suitable for battery diagnosis. Therefore, most researches on battery state diagnosis based on electrochemical models generally uses SPMs or various reduced-order models (ROMs) to improve computational efficiency (Khalik et al., 2019). These electrochemical models are computationally small and generally have efficient simulation performance; however, they could not well describe the battery behavior under high current rates charge/discharge with severe gradient distribution of internal particles (Xia et al., 2017). In this work, to balance the above two models, a P2D model was proposed, which could truly simulate the electrochemical behavior of the battery within the acceptable calculation scale (Han et al., 2021).

In practice, the control of lithium plating and SEI film growth is very important (Gao and Tang, 2008; Sturm et al., 2019; Li et al., 2021). In this research, a P2D model of LiNi_0.8Co_0.15Al_0.05O₂ ternary lithium-ion battery was built, and the correction of SEI film and lithium plating was added to simulate the internal changes of lithium-ion battery during charge/discharge. In the follow-up experiments, we designed a cyclic charge/discharge experiment, focusing on analyzing the changes of the SEI film and the lithium plating on the anode under high current rate charge/discharge conditions, as well as their contributions to the battery aging at different cycle stages.

Methods and Model

Li-Ion Battery P2D Model and Its Parameters

In this work, the P2D model was modified to simulate aging process of lithium-ion batteries, which was first introduced by Doyle et al. (Yang and Wang, 2018). In the following, the governing equations were briefly reviewed and the schematic diagram of the model was shown in Figure 1 where the electrochemical behaviors of lithium-ions and electrons during discharge were described.

FIGURE 1

FIGURE 1. Schematic diagram of the modified P2D model of lithium-ion batteries.

The model takes into account the transport of charges and species in the active material along the electrode thickness direction (x) and within solid particles (r), and x and r directions describe the coupling of electrochemical reactions on the surface of active material particles via the Butler-Volmer kinetics (Ecker et al., 2017b; Momeni Boroujeni and Birke, 2019).

$j_{In}=a_s{i}_0(\exp \left(\alpha \raisebox{1ex}{$\eta F$}\!\left/ \!\raisebox{-1ex}{$RT$}\right.\right)-\exp (-(1-\alpha )\raisebox{1ex}{$\eta F$}\!\left/ \!\raisebox{-1ex}{$RT$}\right.))$(2.1)

And $i_0$ is concentration-dependent exchange current density

$i_0=kF{c}_e^{\alpha }{(c_{max}-c_s)}^{\alpha }{c}_s^{1-\alpha }$(2.2)

Where $j_{In}$ is the intercalation current density of lithium-ion, $a_s$ is the volume-specific active area, $\alpha$ the symmetry coefficient of the reaction, $\eta$ is the electrochemical overpotential, $k$ the reaction rate constant, $c_e$ is the $L{i}^{+}$ concentration in electrolyte, $c_s$ is the $L{i}^{+}$ concentration in active material, and $c_{max}$ is the maximal $L{i}^{+}$ concentration in active material. Diffusion of lithium-ion in spherical particles is described by Fick’s law in a radial coordinate r:

$\frac{\partial c_s}{\partial t}=\frac{1}{r^2}\frac{\partial }{\partial r}\left(D_s{r}^2\frac{\partial c_s}{\partial r}\right)$(2.3)

Where $D_s$ is the solid-phase diffusion coefficient. Further, initial values $c_{a0}$ and $c_{co}$ are introduced for the solid-phase volume elements of anode and cathode at $t=t_0$. Respectively, in the electrolyte, diffusion and migration are considered as following:

$\epsilon \frac{\partial c_e}{\partial t}=\frac{\partial }{\partial x}\left(D_{e,eff}\frac{\partial c_e}{\partial x}\right)+(1-t_p)\frac{j_{In}\left(x\right)}{F}$(2.4)

And the liquid-phase potential ${\varphi }_0$ could be governed as following:

${\varphi }_e=-\frac{\partial }{\partial x}\left({\sigma }_{eff}^e\frac{\partial c_e}{\partial x}\right)+(1-t_p)\frac{j_{In}\left(x\right)}{F}$(2.5)

Where ${\sigma }_{eff}^e$ is the effective electrolyte conductivity, x is a linear coordinate orthogonal to the plain electrode area, and $t_p$ is the transference number. The effective diffusion coefficient is derived from porosity $\epsilon$ and tortuosity $\tau$ as following:

$D_{eff}^e=D_e\frac{\epsilon }{\tau }$(2.6)

Further, to investigate the influence of lithium plating and SEI film growth on cyclic aging of lithium-ion batteries, two correction terms were added into the P2D model (Reniers et al., 2019), where two reactions competes with intercalation reactions during charge. And the current density of the total reaction $j_{tot}$ could be redefined as following:

$j_{tot}=j_{In}+j_{Pl}+j_{SEI}$(2.7)

Where $j_{In}$ is the intercalation current density of lithium-ions into the anode particles, $j_{SEI}$ is the current density of SEI film formation, $j_{Pl}$ current density of lithium plating.

According to the Butler-Volmer kinetics, the intercalation current density of lithium-ions entering the negative electrode particles can be obtained as following.

$j_{In}=\frac{k_{In}\sqrt{c_e{c}_s^{\text{*}}\left(c_s^{max}-c_s^{\text{*}}\right)}}{F}\left(\exp \left(\frac{F-F\alpha }{RT}{\eta }_{In}\right)-\exp \left(-\frac{F\alpha }{RT}{\eta }_{In}\right)\right)$(2.8)

Furthermore, it is assumed that the reaction of the SEI film is irreversible (Müller et al., 2019), and there is no secondary SEI film formed on the lithium plating surface. The current density of SEI film could be defined as following:

$j_{SEI}=-a_s\left(nF{k}_{SEI}{c}_s\right)\exp \left(\frac{nF\alpha }{RT}{\eta }_{SEI}\right)$(2.9)

It is assumed that there is not the dissolution of lithium and the generation of “dead lithium” in the reaction. The expression of lithium plating in the model is similar to that of SEI film growth:

$j_{Pl}=-a_s\left(nF{k}_{Pl}{\mathit{c}}_{\mathit{s}}\right)\exp \left(\frac{nF\alpha }{RT}{\eta }_{Pl}\right)$(2.10)

The solid phase particles and the electrolyte also meet the basic rules of mass conservation and charge conservation. The charge conservation of the solid phase particles could be defined as following:

$\frac{\partial }{\partial x}\left({\sigma }_{eff}\frac{\partial {\Phi }_s}{\partial x}\right)=jF{a}_s$(2.11)

Accordingly, the mass conservation equation of solid phase particles:

$\frac{D_{eff}^s}{r^2}\frac{\partial }{\partial r}\left(r^2\frac{\partial c_s}{\partial r}\right)=\frac{\partial c_s}{\partial t}$(2.12)

The charge conservation equation of electrolyte:

$\frac{2RT(1-t_{+})}{F}\frac{\partial }{\partial x}\left({\kappa }_{eff}\frac{\partial \text{ln}{c}_e}{\partial x}\right)-\frac{\partial }{\partial x}\left({\kappa }_{eff}\frac{\partial {\Phi }_e}{\partial x}\right)=jF{a}_s$(2.13)

And the Mass-conservation equation of electrolyte:

${\epsilon }_s\frac{\partial c_e}{\partial t}=\frac{\partial }{\partial x}\left(D_{eff}^e\frac{\partial c_e}{\partial x}\right)$(2.14)

${\epsilon }_{p,n}\frac{\partial c_e}{\partial t}=\frac{\partial }{\partial x}\left(D_{eff}^e\frac{\partial c_e}{\partial x}\right)+\frac{(1-t_{+})}{F}j$(2.15)

All the above equations build the framework of the battery model, and all spatial derivatives are discretized by finite volume method. The description of all parameters can be found in Table 1.

TABLE 1

TABLE 1. Symbols and descriptions of the P2D model parameters.

Simulation Design and Data Processing

The discharge cut-off voltage of the battery was set to 2.5 V. Then, it was charged with constant current at 1 C. When the voltage reached 4.1 V, it was under constant voltage charging until the charging current was less than C/20. The battery was then discharged with constant current at 1 C until the voltage reached 2.5 V. It should be noted that there was a rest for 10 min after each charge or discharge.

To reduce the computational cost, an aging factor of decay = 100 is introduced in the process of lithium plating and SEI film growth, in 2000- cycle groups. (Abdel- Monem et al., 2017),Therefore, each cycle here is equivalent to 100 cycles. Namely, only 20 cycles need to be calculated for 2000 cycles in practice. The battery information and experimental design can be found in Table 2 and Table 3.

TABLE 2

TABLE 2. Basic parameters of battery.

TABLE 3

TABLE 3. Sets of experiment groups.

SEI film thickness, lithium plating thickness, relative discharge capacity and relative capacity of cyclable lithium are defined for results and discussions, whose calculation formulas are provided as Eqs 2–16 to Eqs 2)–(19. The related parameters are shown in Table 4.

$Dischargecapacity(-)=\frac{t_e-t_s}{1\left[h\right]}$(2.16)

$Lithiuminventory(-)=\frac{L{i}_i-L{i}_c}{L{i}_s}$(2.17)

$Thicknesslithiumplating\left(\text{nm}\right)=\frac{c_{Pl}{M}_{Pl}}{{\rho }_{Pl}}A{s}_{Pl}$(2.18)

$ThicknessSEIfilm\left(\text{nm}\right)=\frac{c_{SEI}{M}_{SEI}}{{\rho }_{SEI}}A{s}_{SEI}$(2.19)

TABLE 4

TABLE 4. Parameters related to evaluation indicators.

Results and Discussion

Figures 2, 3 show the capacity curves of the cell with respect to different temperatures and current rates under long-cycle conditions, respectively. It can be found that as the number of cycles increases, the capacity of the cell decreases continuously. It means that during gradual degradation, the available lithium-ion of the battery is continuously depleted, which directly lead to a continuous decrease of available discharge capacity. At the same time, the significant difference between the discharge capacity decay curve and the cell capacity retention curve indicates that a considerable amount of available lithium-ion is solidified in the battery during the process. In addition, the slope changes of the two curves of indicates changes in the proportion of the non-recoverable part of the solidified lithium-ion. A large slope means a considerable loss of available lithium-ion in a short term. Accordingly, it can be found that the decay rate of the battery in early cycles is significantly faster than that in late cycles, and the capacity retention rate gradually approach a constant value in late cycles. The available discharge capacity curve is sensitive to both low temperatures and high charge rates, while the capacity retention curve is more sensitive to the rate factor than the temperature factor. The retention curve of 4C capacity in Figure 2 even shows a significant inflection point in early cycles. The reasons for these phenomena would be discussed in detail after the reason of available lithium-ion loss was analyzed.

FIGURE 2

FIGURE 2. Influence of temperature on charging capacity and available lithium-ion decrease.

FIGURE 3

FIGURE 3. Influence of charge rate on charging capacity and available lithium-ion decrease.

It was reported that the loss of available lithium-ion was due to the performance degradation caused by SEI growth and lithium plating (Jaguemont et al., 2016; Jiang et al., 2016; Zhao et al., 2018; Han et al., 2021). To clarify the contributions of these decay mechanisms at different stages and their activation thresholds under different working conditions, the thickness of SEI film and lithium plating was further investigated. The results were shown in Figures 4–6.

FIGURE 4

FIGURE 4. Influence of charge rate on SEI film growth at room temperature.

Figure 4 showed the thickness change of SEI film under long-cycle conditions. It showed that the thickness of SEI film was approximately linearly related to the number of cycles. At the same time, the variation trend of the SEI film thickness and the battery capacity decay in middle and later cycles were highly consistent. Therefore, it was speculated that the battery capacity decay in middle and late cycles was mainly caused by SEI generation, while the rapid lithium-ion loss in early cycles was caused by other decay mechanisms. Furthermore, we found that the SEI film formation was insensitive to the charging rate. In Figure 4, there was basically no detectable change of SEI film under the conditions of high charge rates (i.e., 3–5 C). However, under the conditions of medium charge rates (i.e., 1–2 C), the equilibrium thickness of the SEI film was slightly thinner than that under high charging rate conditions. At 2 C, the SEI film thickness at late cycles was even thinner than that at 1 C. This also proved that charge rates was not a sensitive factor for the SEI film growth.

Figures 5, 6 showed the growth of lithium plating with the increasing number of cycles under the same long-cycle conditions. As the process of lithium plating would quickly reach equilibrium in early cycles under all working conditions, which could also be proved by Je’s group (Zhang et al., 2021).Figures 5, 6 only displayed early cycles of the process of lithium plating formation. Basically, the lithium plating was very obvious in early cycles, and the thickness tended to stabilize rapidly as the number of cycles increases, suggesting that the formation of lithium plating was responsible for the rapid decline of battery performance in early cycles. Furthermore, it was found that there was an obvious threshold in terms of charge rate for the lithium plating. As shown in Figure 5, at 25°C, under medium charge rates, the process of lithium plating could not occur; while under high charge rates, it became more and more obvious with the increase of charge rate. The equilibrium thickness of lithium plating had a monotonically positive correlation with charge rate. Figure 6 showed that low temperature would significantly aggravate the lithium plating. These results basically explained the rapid performance degradation at early cycles. The increase of charge rate and SOC would also aggravate lithium plating, resulting in stronger degradation. Meanwhile, according to automotive standards, a capacity retention rate of 80% usually indicates end-of-life (EOL), i.e., SOH = 80%. The increase in charge rate and the decrease in temperature would actually shift the EOL to lower cycle numbers and thus shorten the lifetime of the battery (shown in Figures 1, 2). The result is consistent with other researches, which reported that the cycle life was about 90–140 cycles at the low temperatures (Fan and Tan, 2006), while at higher temperature (i.e., 45°C), the cycle life was more than 2000 cycles (Abdel- Monem et al., 2017). Generally, lithium plating can lead to serious performance degradation, and at high charge rates and low temperatures, the contribution of lithium plating is significantly higher than that of SEI film growth.

FIGURE 5

FIGURE 5. Influence of charge rate on lithium plating thickness at room temperature.

FIGURE 6

FIGURE 6. Influence of temperature on lithium plating thickness charged under 3C.

Variation regularity of lithium plating thickness with different charge rates and different temperatures was shown in Figure 7. Under high charge rates (i.e., 3–4 C), compared with the normal temperature of 25°C, the thickness of lithium plating was significantly higher than that at low temperatures, which was consistent with existing researches. And the trend was shown in Figure 6 (Waldmann et al., 2014; Yang et al., 2018). However, at 45°C, the thickness of lithium plating tended to increase. Therefore, lithium plating differs from other degradation processes in terms of temperature dependence. Danzer and Mehrense reported the same findings (Fan and Tan, 2006; Waldmann et al., 2014), considering it was caused by low-temperature charging, high current and high state of charge (SOC). They also found that poor capacity balance would lead to metal lithium plating at a relatively high temperature. In addition to capacity loss and impedance rise, the lithium plating can also cause an internal short circuit in the battery, resulting with a serious safety hazard (Waldmann et al., 2014; Tippmann et al., 2014). Zhang’s study (Chandrasekaran, 2014) showed that during low-temperature charging, the intercalation of lithium-ion in graphite particles and the lithium plating on the particle surface competed with each other, while high charge rate currents led to limited charge transfer at the particle/SEI interface. However, some researchers (Waldmann et al., 2018) believed that low temperature would reduce the ionic conductivity of SEI film, resulting in the inability of lithium-ions to quickly enter the anode, thereby accumulating on the surface of the SEI film to form metallized deposits. This explains the reason for the sudden and sharp thickening of the lithium plating caused by the high charge rate charging at low temperatures, as shown by the 0°C curve in Figure 6. The rapid decrease in lithium-ion mobility and the increase of the carrier concentration in the anode region jointly limited the transport process of lithium-ion. To verify above speculation, the specific growth process of lithium plating in a single cycle was further studied in Figure 8. It was found that at 0°C, the lithium plating induced by high charge rates (i.e., 3–5 C) was significantly intensified as the charge rates increased. And, lithium plating only occurred at high SOC conditions. This was consistent with Danzer’s findings (Fan and Tan, 2006). When the graphite potential decreased below 0 V with respect to Li/Li⁺, lithium plating would occur. If the diffusion of lithium-ion in the graphite particles was too slow, the particle surface would be saturated with lithium-ions, resulting in lithium plating (Klett et al., 2014).

FIGURE 7

FIGURE 7. Influence of charge rate on lithium plating thickness at different temperatures.

FIGURE 8

FIGURE 8. Relationship of lithium plating thickness and cell SOC charged under high charge rate at 0°C.

In summary, the emergence of lithium plating was essentially due to the limited large-scale transport of lithium-ion. When the lithium plating conditions were met, the lithium platting phenomenon would occur in early cycles and reach the plating-dissolution equilibrium after several cycles. Low temperature and high charge rate conditions would aggravate the lithium plating. And, high charge rate charging would lead to insufficient SEI film conduction capability, resulting in lithium-ion accumulation on the top of the SEI film.

To quantify the contributions of lithium plating and SEI film growth to the active lithium-ion loss in the battery under working conditions, we investigated the contributions of lithium platting and SEI film growth to the decayed capacity at different charge rates and temperatures (shown in Figure 9). For the same reason to Figures 5, 6, only early cycles were displayed in the figures. It showed that although both lithium plating and SEI film growth would consume available lithium-ion, the consumption by the formation of SEI film was almost negligible under low temperature conditions, and lithium plating was almost the only decay mechanism under this condition, which is consistent with Danzer’s research (Fan and Tan, 2006). And then, it was found that when the temperature and current reached the lithium plating conditions, the process of lithium plating would occur rapidly and consume a large amount of available lithium-ion. As shown in Figure 9A, the high charge rates at 0 °C could even led to a loss of nearly 10% of the available capacity in the short term. It could also be noticed that after certain cycles, the thickness of lithium plating would reach dynamic equilibrium without causing further loss of available lithium-ion, which was consistent with the results represented by Monroe (Zinth et al., 2014; Somerville et al., 2016). In the meanwhile, the lithium-ion loss caused by SEI film formation increased linearly with the number of cycles, which had no significant relationship with the current. And, the continuous accumulation became the dominant factor in middle and late cycles. To sum up, the unreasonable use of the battery (e.g., low temperatures and high charge rates) could lead to the formation of lithium plating at early cycles, causing serious capacity loss and significantly accelerating the aging of the battery. However, the influence of lithium plating was limited to early cycles, as it was rapidly achieved under the combined effect of the reaction potential and the diffusion rate. In middle and late cycles, the continuous available lithium consumption caused by SEI film formation and the withdrawal of the lithium plating mechanism, making it the main cause of lithium loss at this stage. As the capacity decay rate caused by which was approximately linear and was not sensitive to the charge rate, a good battery temperature control system could effectively suppress the battery aging at this stage. At the same time, since the lithium loss caused by lithium plating would reach the maximum only under both low temperature and high charge rates, well-controlled battery temperature could effectively offset the negative effect of fast charging on battery capacity.

FIGURE 9

FIGURE 9. Contributions of lithium plating and SEI film growth charged under different charge rates at different temperatures.

Conclusion

In this study, the corrections of SEI film and lithium plating were added to the P2D model of the battery, and a series of battery cycle aging simulation experiments were carried out using the corrected P2D model, aiming to analyze the contributions of SEI film and lithium plating on battery aging under high charge rate conditions. Through the simulation experiments, it was found that under the high charge rate conditions, the battery capacity attenuation in the early cycles were mainly caused by lithium plating; in middle and late cycles, the thickness of lithium plating tended to be stable, and the capacity attenuation at this stage was caused by the growth of SEI film. At the same time, it was also found that the lithium plating was significantly intensified at low temperature and high charge rates charging conditions. Thus, a good cell temperature control would have a significant inhibitory effect on lithium plating and SEI film, which could partially offset the negative impact of fast charging on battery capacity. This research would provide theoretical support for the improvement of charging and discharging strategies for lithium-ion batteries.

Data Availability Statement

The original contributions presented in the study are included in the article/Supplementary Material, further inquiries can be directed to the corresponding author.

Author Contributions

ZG:Conceptualization, Writing—Original Draft HX:Software, Visualization HY:Investigation, Validation BM:Data Curation XL:Supervision SC:Supervision Methodology, Writing—Review and Editing.

Funding

This work is supported by the Science and Technology Development Project of Jilin province (20200501012GX) and National Natural Science Foundation of China (No. 52102470).

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Publisher’s Note

All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors and the reviewers. Any product that may be evaluated in this article, or claim that may be made by its manufacturer, is not guaranteed or endorsed by the publisher.

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