Introduction

Recently, the two-dimensional electron gas (2DEG) at the n-type (LaO)+/(TiO2)0 interface in LaAlO3/SrTiO3 heterostructures (HS) system has attracted considerable attention due to its unique interfacial properties and promising applications in the next-generation nanoelectronics1,2,3,4. The typical explanation for the formation of 2DEG is the so-called “polar catastrophe” mechanism5,6. The LaAlO3 film is formed by alternating charged (LaO)+ and (AlO2)− layers, while the SrTiO3 substrate is considered as stacks of neutral (SrO)0 and (TiO2)0 layers. The n-type (LaO)+/(TiO2)0 interface can be formed by growing LaAlO3 films on the SrTiO3 substrate. Then an electronic reconstruction occurs at the LaAlO3/SrTiO3 interface to compensate the polar discontinuity by migrating electrons from the interfacial polar (LaO)+ layer to the adjacent non-polar (TiO2)0 layers.

Although the LaAlO3/SrTiO3 HS system exhibits a high interfacial carrier density with 3.2 \(\times\) 10−14 cm−2, the electron mobility is low (1 cm2V−1s−1) at room temperature (RT), which limits its application in the photoelectric devices7,8. This phenomenon is originated from that the conduction band bottom of SrTiO3 is composed of highly dispersed \(d_{xy}\) orbitals and the electrons on these orbitals show high mobility at low temperature. While it consists of lowly dispersed \(d_{xz}\)/\(d_{yz}\) orbitals at RT. The multi-band degeneracy leads to the inter-band transition scattering and stronger electron-phonon coupling effect, which reduces the electron mobility. To broaden the application of LaAlO3/SrTiO3 HS system at RT, some approaches are proposed to improve its interfacial electron mobility. For instance, defect engineering9,10, strain engineering11,12, and find other materials to replace the SrTiO3 channel material13,14. Z. Q. Liu et al.9 pesented that the interfacial carrier density of LaAlO3/SrTiO3 HS system at RT increases with the decrease of oxygen partial pressure, and the carrier mobility shows the opposite trend. Ariando et al.12 reported that the electron mobility of interfacial 2DEG in LaAlO3/SrTiO3 HS system is sensitive to the biaxial strain. The biaxial compressive strain decreases the electron mobility and increases the interfaical carrier density. The largest electron mobility is \(<10\) cm2V−1s−1at RT. Zou et al.13 prepared a polar/polar perovskite oxide heterostructure, that is, LaTiO3/KTaO3 HS system with (LaO)+/(TaO2)+ interface, and found that this HS system exhibits high interfacial electron mobility of 21 cm2V−1s−1 at RT, which is higher than that of well-known LaAlO3/SrTiO3 HS system. Therefore, the performance of LaAlO3/SrTiO3 HS system can be effectively regulated by perovskite channel material KTaO3. The search for other channel materials with high electron mobility at RT to further improve the interfacial electron mobility of pervoskite-type HS system has become a research focus.

BaSnO3 film with Sn 5s orbitals at the bottom of conduction bands has considered as an ideal material for oxide transistor channel material due to its high electron mobility at RT. This is because that the s orbitals are less localized than d orbitals, which results in larger band dispersion and lower electron effective mass. Compared with traditional SrTiO3 films, BaSnO3 film with s orbitals at the conduction band bottoms has extremely high electron mobility at RT, with a value of 150 cm2V−1s−115. Our group have explored the possibility of producing a high-mobility 2DEG in LaGaO3/BaSnO3 HS system using first-principles electronic structure calculations. This HS system presented twice larger electron mobility and enhanced interfacial conductivity compared to the prototype LaAlO3/SrTiO3 HS system16. Kookrin et al.17 combined experimental and theoretical approach to study the different electrical properties of perovskite-type LaInO3/BaSnO3 HS system on MgO and SrTiO3 substrates, which are well explained by the varying deep acceptor densities for the HS system on two different substrates. They also reported that when the thickness of LaScO3 (LaInO3) film is 12 unit cells, the interfacial charge density of HS system at RT is about 2.5 \(\times\) 1013 cm−2, and the electron mobility is about 20-25 cm2V−1s−1, which is obviously higher than that of LaAlO3/SrTiO3 system. Moreover, with the increase of La concentration doped in BaSnO3, the interfacial electron density and mobility of HS system shows an increasing trend18,19. Aggoune et al.20 preliminally explored the formation mechanism of 2DEG and two-dimensional hole gas (2DHG) by regulating the polarity and thickness of LaInO3 film, as well as the interface structure using the first-principles calculation. However, the detailed formation mechanism for 2DEG needs further systematically studied. Particularly, the changes of electrical properties of the BaSnO3-based HS systems deposited on the substrates with different lattice parameters also need further investigation. This lattice mismatch between the HS system and substrate is easy to form growth strain, which is also usually induced by varying experimental preparation parameters and the uneven thermal diffusion during the heating/cooling process caused by the mismatch of thermal expansion coefficient between the HS system and substrate. Previous researchers12,21 have found that this growth strain is generally in the range of – 3% \(\sim\) 3%. For example, Z. Huang et al.12 selected four substrates with different lattice parameters to prepare Nb-SrTiO3 thin film and LaAlO3/SrTiO3 HS system. The lattice mismatch between the HS system and substrate resulted in – 2.98% (LaAlO3), – 0.96% (LSAT), 0 (SrTiO3), and 0.99% (DyScO3) strains, respectively. C. W. Bark et al.21 deposited LaAlO3/SrTiO3 HS system on the substrates with different lattice parameters by pulsed laser deposition, resulting in a biaxial range of – 1.21% (NdGaO3) \(\sim\) 1.59% (GdScO3) in the HS system. Lan Meng et al.22 prepared WS2 film by chemical vapor deposition on SiO2/Si substrate, and then cooled it rapidly. In the process of rapidly cooling, the mismatch of thermal expansion coefficient between WS2 film and substrate led to local stress in WS2 film, but the stress/strain value was not referred to in this paper. Besides growth strain, we can dynamically regulate the force of film/heterostructure by artificially applying strain in the experiments, which is called “extrinsic strain”. Then the range of strain can be artificially regulated according to the ultimate force of the material. For example, B Jalan et al.23 applied different stresses on the epitaxial SrTiO3 thin films by three-point bending, studying the changes of electron mobility of film with the temperature and stress.

Figure 1
figure 1

Calculated total density of states (DOS) for the n-type (LaGaO3)m/BaSnO3 HS models with different LaGaO3 unit cells. (a) m = 2, (b) m = 3, (c) m = 4, (d) m = 5, (e) m = 6 and (f) m = 8. The vertical dashed line indicates the Fermi level at 0 eV in this and each subsequent DOS plot. The insets are the enlarged view of the DOS near fermi level for models.

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In this work, we systematically investigated the (LaGaO3)m/BaSnO3 HS models by means of the first-principles calculations. Firstly, the LaGaO3 film thickness dependence of the formation of 2DEG in the unstrained (LaGaO3)m/BaSnO3 HS model was studied. Next, we explored the influence of biaxial strain in the ab-plane on the critical thickness of LaGaO3 film for forming 2DEG. The electrical properties of LaGaO3/BaSnO3 HS system dependent on the biaxial strain were analyzed from the electron effective mass, interfacial electron density, electron mobility, and electrical conductivity. This work may provide some guidances for adjusting the electrical properties of LaGaO3/BaSnO3 HS system by biaxial strain.

Results

Bulk parent compounds

First, we calculated the lattice parameters and energy band gap of LaGaO3 and BaSnO3 materials in their cubic phase, shown in Table S1 in the supporting information. The calculated lattice constants from GGA+U functional are well consistent with the experimental values (3.939 vs 3.860 Åfor LaGaO3 and 4.186 vs 4.115 Åfor BaSnO3)24,25. In contrast, the calculated energy band gaps from the GGA+U approach are underestimated with respect to the experimental values (3.668 vs 4.4 eV for LaGaO3 and 2.208 vs 3.1 eV for BaSnO3)26,27, which is due to the well-known shortcoming of the GGA functional that cannot give an accurate description for the electron-electron correlation-exchange interaction. However, this underestimation has been determined that it has no influence on our conclusions about the 2DEG at the perovskite-type HS systems because the electronic states that contribute to the formation of DEG can be well reproduced from GGA+U calculations28,29,30. Then our GGA+U approach can well predict the 2DEG-related Sn 5s states as well as the critical thickness of the LaGaO3 for forming the 2DEG in the LaGaO3/BaSnO3 HS system.

2DEG in the n-type LaGaO3/BaSnO3 HS system

The calculated total density of states (DOS) for the n-type (LaGaO3)m/BaSnO3 HS system with different LaGaO3 unit cells (m=2, 3, 4, 5, 6 and 8) are shown in Fig. 1, where the vertical dotted line at 0 eV represents the fermi level. At m=2 and 3, the fermi level of (LaGaO3)m/BaSnO3 HS system is on the top of the valence bands, and the HS system shows insulating characteristics. The band gap of HS system decreases with the increase of LaGaO3 film thickness. While at m=4, 5, 6 and 8, the band gap disappears and all the HS models exhibit metallic properties. With the increase of LaGaO3 film thickness, the metallic states near the fermi level increase. These results indicate that the critical thickness of insulator-to-metal transition is 4 unit cells for LaGaO3 film in the n-type LaGaO3/BaSnO3 HS system, which is similar to the case of well-known n-type LaAlO3/SrTiO3 HS model31.

Figure 2
figure 2

Calculated layer-resolved partial DOS for the n-type (LaGaO3)2/BaSnO3 HS model along with the charge density projected on bands forming the 2DEG.

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Figure 3
figure 3

Calculated layer-resolved partial DOS for the n-type (LaGaO3)3/BaSnO3 HS model along with the charge density projected on bands forming the 2DEG. The isovalue of 1.1\(\times\) 10−4 e/bohr3 is used to produce the charge density plots.

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To further understand the origin and charge transfer of metallic electronic states in the n-type (LaGaO3)m/BaSnO3 HS system, We calculated the layer-resolved partial DOS for n-type (LaGaO3)m/BaSnO3 HS system at m=2, 4 and 8, as shown in Figs. 2, S1 in the supporting information and Fig. 3, respectively. To directly observe the contribution of each layer to the metallic states, we calculated the charge density projected on metallic bands for each model. For the convenience of discussion, the first and second layers of SnO2 are defined as IF-I and IF-II, respectively. For the (LaGaO3)2/BaSnO3 HS system in Fig. 2, the layer-resolved partial DOS and the charge density show that the fermi level does not cross the conduction bands and valence bands. Then there are no metallic states exist in the IF-I and IF-II layers, and the HS system shows insulating characteristic. These phenomena can be clearly seen in the enlarged view of IF-I and IF-II layers in Fig. 2b. Since the polarization strength of LaGaO3 film in (LaGaO3)2/BaSnO3 HS system is strong enough to make the electrons transfer from the (LaO)+ layer to (GaO2)− layer, neutralizing the holes in (GaO2)− layer. Then there exist no holes on the surface and no electrons at the interface. The polar discontinuity in the n-type (LaO)+/(SnO2)0 interface is offset by strong polarization in LaGaO3 film, which is similar to the LaAlO3/SrTiO3 HS system31.

For the (LaGaO3)8/BaSnO3 HS system in Fig. 3, the fermi level passes through the valence bands of the surface (GaO2)− layer, showing p-type conducting states. While the interface indicates n-type conducting states from the interfacial (SnO2)0 layer. Then the overlap of these states make the (LaGaO3)8/BaSnO3 HS system show metallic property in Fig. 1. The O2p states of (LaO)+ and (GaO2)− layers significantly shift toward higher energy with the layers move from the interfacial (LaO)+ layer to the surface (GaO2)−layer, presenting the electrostatic potential in the LaGaO3 film. This is because that the LaGaO3 film in the (LaGaO3)8/BaSnO3 HS model exhibits a weaker polarization than that in the (LaGaO3)2/BaSnO3 HS model, which is not enough to offset the polarity discontinuity between LaGaO3 and BaSnO3. Thus, there exist p-type conducting states from O 2p orbitals on the LaGaO3 surface. In short, the (LaGaO3)8/BaSnO3 HS system present metallic properties with the p-type conducting states from O 2p orbitals on the surface and the n-type conducting states from Sn 5s orbitals at the interface.

Figure 4
figure 4

(a) Calculated interfacial charge carrier density (n) and (b) Polarization strength (P) in LaGaO3 (LaAlO3) film for the n-type LaGaO3/BaSnO3 (LaAlO3/SrTiO3) HS system as a function of LaGaO3 (LaAlO3) unit cells. The inset is the locally enlarged view of interfacial charge carrier density for LaGaO3/BaSnO3 HS system.

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To clearly present the transition from the insulating characteristic to the metallic property of LaGaO3/BaSnO3 HS system, we also calculated the layer-resolved partial DOS for the n-type (LaGaO3)4/BaSnO3 HS model along with the charge density projected on bands forming the 2DEG, shown in Fig. S1 in the supporting information. All the characteristics of (LaGaO3)4/BaSnO3 HS model are consistent with that of (LaGaO3)8/BaSnO3 HS system, except that the surface and interface metallic states are less. To quantify the change of interfacial electron concentration of the (LaGaO3)m/BaSnO3 HS system with the LaGaO3 film thickness, we also calculated their interfacial electron concentration by integrating the partial DOS of the Sn 5s orbitals near the fermi level from the interfacial IF-I and IF-II (SnO2)0 layer divided by the interfacial area, shown in Fig. 4a. As a comparison, the interfacial carrier concentration of (LaAlO3)m/SrTiO3 HS system are also calculated in Fig. 4a, which is about 2−6\(\times\)1013 cm−2 at \(m\ge 5\). For (LaGaO3)m/BaSnO3 HS system, at \(m\le 3\), the interfacial electron concentration is zero; at \(m\ge 4\), as m increases, the interfacial electron concentration increases. Similar to LaAlO3/SrTiO3 HS system, a sudden increase of interfacial electron concentration in LaGaO3/BaSnO3 HS system occur from m=4 to m=5. But he values of electron concentration are on the order of 1012 cm−3, which is about an order of magnitude smaller than that in the corresponding (LaAlO3)m/SrTiO3 HS system. This is because that the Sn 5s orbitals are more dispersive and poorly localized for electrons than the Ti 3d orbitals. This phenomenon is unfavorable to the practical application of 2DEG. Therefore, we indicate that the localization of interfacial electrons for the BaSnO3-based HS system can be improved by doping the elements who have d orbitals. This method has already been used to modify the electrical properties of BaSnO3 film. For example, Bing Li etal.32 prepared Nb doped BaSnO3 films by pulsed laser deposition, showing that the BaNb0.05Sn0.95O3 film simultaneously has a high electron mobility of 19.65 cm2V−1s−1and electron density of 6.59 \(\times\)1020 cm−3, which is beneficial to its application in optoelectronic devices.

To analyze the change of interfacial 2DEG for LaGaO3/BaSnO3 HS system with different LaGaO3 film thickness, the average polarization strength in the LaGaO3 film was calculated by the following equation33,34:

$$\begin{aligned} P=\frac{e}{\Omega }\sum _{i=1}^N Z_i^*\cdot \delta _{z_i} \end{aligned}$$
(1)

where \(\Omega\) is the total volume of the LaGaO3 film, N is the total number of atoms in the unit cell, Zi* is the Born effective charge of each atom, and \(\delta _{z_i}\) is the relative displacement of the ith atom in the HS system. The relative displacement \(\delta _{z_i}\) of La(Ga) atoms with respect to the oxygen atom in the same LaO and GaO2 layers is calculated as \(\delta _{z_{La/Ga}} = z_{La/Ga} - z_O\). Our calculated Born effective charge Zi* for La and Ga atoms are 4.03 and 3.34, respectively.

The calculated polarization strength in the LaGaO3 film of n-type (LaGaO3)m/BaSnO3 HS system with different LaGaO3 thickness are shown in Fig. 4b. As the LaGaO3 film thickness increases from 2 to 8, the average polarization strength in the LaGaO3 film decreases from 52.59 \(\mu\)C\(\cdot\) cm−2 to 34.52 \(\mu\)C\(\cdot\) cm−2 , indicating that the electrostatic force drives the electron from (LaO)+ layer to (GaO2)− layer is weaken, leading to the increase of interfacial electron density. Combined with the total DOS diagram in Fig. 1, it can be concluded that the critical polarization strength of insulator-to-metal transition for LaGaO3/BaSnO3 HS system is 43.50 \(\mu\)C\(\cdot\) cm−2 (polarization strength at m=4), which is lower than that of LaAlO3/SrTiO3 HS system with the value of 50.03 \(\mu\)C\(\cdot\) cm−2 .

2DEG in the strained LaGaO3/BaSnO3 HS system

Based on the discussions above, we know that the critical thickness of insulator-to-metal transition for the unstrained (LaGaO3)m/BaSnO3 HS system is 4 unit cells. The formation of 2DEG at the interface is strongly related to the distortion of LaGaO3 film. To study the changes of interfacial electronic states induced by this distortion, we calculated the total DOS of (LaGaO3)m/BaSnO3 (m=2, 3, 4, and 5) HS models with different biaxial strains of −3%, −2%, 2%, and 3%, as shown in Fig. 5. The “\(+\)” and “−” signs indicate tensile and compressive strains, respectively. Our calculated total DOS shows that all the (LaGaO3)2/BaSnO3 HS models with − 3%, − 2%, 0, 2%, and 3% strains show semiconducting characteristics (first row in Fig. 5). While the (LaGaO3)3/BaSnO3 HS model with − 3%, − 2%, and 0 strains and the (LaGaO3)4/BaSnO3 HS model with −3% strain also show a similar semiconducting behavior. With the strain from −3% to 3%, the band gap of (LaGaO3)4/BaSnO3 HS model decreases and vanishes. A small number of states present at the fermi level for the models with 0, 2% and 3% strains, thus exhibiting weak metallicity. All the (LaGaO3)5/BaSnO3 HS models exhibit metallic properties and more states arise near the fermi level with the strain from compressive to tensile. In short, we can obtain the following conclusions: (1) For the unstrained (LaGaO3)5/BaSnO3 HS system, 4 unit cells of LaGaO3 is the minimum critical thickness to obtain a 2DEG; (2) For the −3%-biaxially-strained HS system, a critical thickness of 5 unit cells of LaGaO3 is required, while 3 unit cells are the minimum requirement to form a 2DEG for the 3%-biaxially-strained HS system. These results present biaxial strains on the BaSnO3 substrate has a significant impact on the critical thickness of LaGaO3 film for forming 2DEG.

Figure 5
figure 5

Calculated total DOS for the n-type (LaGaO3)m/BaSnO3 (m =2, 3, 4, and 5) HS models with different strains. (a) − 3%, (b) − 2%, (c) 0%, (d) 2% and (e) 3%. The insets are the enlarged view of the DOS near fermi level for models.

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To exhibit the distribution of 2DEG for the n-type (LaGaO3)m/BaSnO3 HS models with various biaxial strains, we further plotted the partial density states of Sn 5s orbitals in IF-I and IF-II layers for (LaGaO3)4/BaSnO3 HS system with the biaxial strains of − 3%, 0, and 3% in Fig. S2 in the supporting information. The fermi level of the (LaGaO3)4/BaSnO3 HS system with −3% strain does not cross the Sn 5s orbitals, exhibiting an insulating property. But for the unstrained and 3%-strained (LaGaO3)4/BaSnO3 HS models, the fermi level crosses the Sn 5s orbitals, showing an metallic property. Moreover, the 3%-strained (LaGaO3)4/BaSnO3 HS system has a higher concentration of electronic states near the fermi level compared to the unstrained HS system.

Figure 6
figure 6

Calculated average polarization strength (P) in the LaGaO3 film for n-type (LaGaO3)4/BaSnO3 HS models with different biaxial strains.

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To further understand the change of electronic states at the interface, the polarization strength of (LaGaO3)4/BaSnO3 HS system with the biaxial strain from − 3 to 3% is calculated, as shown in Fig. 6. The average polarization strength of (LaGaO3)4/BaSnO3 HS system decreases with the biaxial strains from − 3 to 3%. In Fig. 4, we know that the critical polarization strength of unstrained LaGaO3/BaSnO3 HS system is 43.50 \(\mu\)C\(\cdot\) cm−2 corresponding to the values of HS system with 4-unit-cells thickness of LaGaO3 film. The average polarization strength of compressively-strained (LaGaO3)4/BaSnO3 HS system is larger than that of the unstrained HS system. The electrostatic force prevent electron transfer from (LaO)+ layer to (GaO2)− layer is strengthen, resulting in insulating behavior for the compressively-strained (LaGaO3)4/BaSnO3 HS system. On the opposite, the average polarization strength of tensilely-strained HS system is smaller than that of the unstrained HS system. Then the electrostatic force present the electron from (LaO)+ layer to (GaO2)− layer is weaken, thus the (LaGaO3)4/BaSnO3 HS system under biaxial tensile strain present a metallic property. Overall, the polarization strength of (LaGaO3)4/BaSnO3 HS system is strongly influenced by the biaxial strain, which determining the critical thickness of insulator-to-metal transition.

Next, we calculated the electronic band structures for the strained (LaGaO3)4/BaSnO3 HS system along the path M-\(\Gamma\)-X of the interfacial Brillouin zone compared to the unstrained model, shown in Fig. S3 in the supporting information. Some electronic states reside below the fermi level for the unstrained and tensilely-strained (LaGaO3)4/BaSnO3 HS system, indicating metallic properties. While the compressively-strained HS system exhibit an insulating property. Further, we calculated the electron effective mass (m+/m0) for the minimum conduction bands along the \(\Gamma\)-X and \(\Gamma\)-M directions, in which \(m_0\) is the electron effective mass for free electron. The electron effective mass m+ was calculated using the parabolic approximation by the following formula35:

$$\begin{aligned} \frac{1}{m^*} = \frac{1}{\hbar ^2} \frac{\partial ^2E_{CB}}{\partial \kappa ^2} \end{aligned}$$
(2)

where \(\hbar\) is the reduced plank constant, \(\kappa\) is the corresponding wave vector of the conduction bands, and ECB is the energy of the minimum conduction band. For the unstrained (LaGaO3)4/BaSnO3 HS system, the calculated electron effective mass is 0.24m0, which is in good agreement with that of BaSnO3 bulk36. As the biaxial strain changes from −3% to 3%, the electron effective mass decreases from 0.27m0 to 0.18m0. That is, the biaxial compressive strains harm the electron migration characteristic, and the tensile strains play the opposite role. What’s more, we calculated the charge carrier density by integrating the layer-resolved partial DOSs for the conducting states below the fermi level from the interfacial IF-I and IF-II (SnO2)0 layer, see Fig. 7a. The HS systems with biaxial strains from −3 to 3% exhibit an increasing charge density from 0 to 4.49\(\times\)1012cm−2, which provides evidence that the biaxial compressive strain suppresses the production of 2DEG, and the biaxial tensile strain promotes the formation of 2DEG at the interface.

Figure 7
figure 7

(a) The electron effective mass (m+/m0) and interfacial electron density (n), (b) The normalized electron mobility (\(\mu\)/\(\mu _0\)) and normalized electrical conductivity (\(\sigma\)/\(\sigma _0\)) for the (LaGaO3)4/BaSnO3 HS model under different biaxial strains.

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Besides the interfacial charge density, the electron mobility is also an important factor in determining the interfacial conductivity of the 2DEG. We calculated the normalized electron mobility ( \(\mu\)/ \(\mu _0\)) and normalized electrical conductivity ( \(\sigma\)/ \(\sigma _0\)) for (LaGaO3)4/BaSnO3 HS system under different biaxial strains, see Fig. 7b. \(\mu _0\) and \(\sigma _0\) refer to the electron mobility and electrical conductivity of the unstrained (LaGaO3)4/BaSnO3 HS system, respectively. The following two Eqs. (3) and (4) were used37:

$$\begin{aligned} \mu= & {} e<\tau >/m^* \end{aligned}$$
(3)
$$\begin{aligned} \sigma= & {} ne\mu \end{aligned}$$
(4)

where e, \(<\tau >\), \(m^*\) , n, \(\mu\), and \(\sigma\) are the elementary charge, average scattering time, electron effective mass, interfacial electron density, electron mobility, and electrical conductivity, respectively. The scattering time \(\tau\) is determined by all the scattering events, i.e. impurity scattering, electron-phonon scattering and electron-electron scattering. The inverse of \(\tau\) can be described as the sum of rates associated with all the scattering mechanisms according to Matthiessen’s rule38. It has been extremely challenging to calculate the scattering time \(\tau\) due to the complicated scattering mechanisms. One common and simplified approach is to treat \(\tau\) as a constant, which has been validated in prior studies35,39,40 and used in this work. The electron mobility and the electrical conductivity of (LaGaO3)4/BaSnO3 HS system with different biaxial strains are presented in Fig. 7b. As the biaxial strain changes from −3 to 3%, the value of \(\mu\)/\(\mu _0\) and \(\sigma\)/\(\sigma _0\) increases. Compared to the unstrained HS system, the \(\mu\)/\(\mu _0\) and \(\sigma\)/\(\sigma _0\) for compressively-strained (LaGaO3)4/BaSnO3 HS system show lower, while for tensilely-strained HS system present higher.

Discussion

In conclusion, the insulator-to-metal transition critical thickness and electrical properties of unstrained and strained LaGaO3/BaSnO3 HS slab systems are studied using density functional theory calculations. The results show that a critical thickness of 4 unit cells for LaGaO3 film is required for forming 2DEG in the unstrained LaGaO3/BaSnO3 HS system, while the critical thickness of LaGaO3 film increases up to 5 unit cells in – 3%-biaxially-strained HS system and decreases to 3 unit cells in 3%-biaxially-strained HS system. These results are originated from that the biaxial strain along ab plane on the BaSnO3 substrate can significantly affects the polarization strength in the LaGaO3 film. We also find that the biaxial tensile strain can considerably increase the interfacial charge carrier density, electron mobility and electrical conductivity, while the biaxial compressive strain shows the opposite effect. In short, the interfacial electrical properties of 2DEG in LaGaO3/BaSnO3 HS system can be optimized by applying a tensile strain on the BaSnO3 substrate along the ab-plane.

Methods

In this work, all the density functional theory (DFT)41 calculations were carried out using the Vienna Ab initio Simulation Package (VASP)42,43. The projector augmented-wave (PAW) potentials were applied for electron-ion interactions44. The generalized gradient approximation (GGA) parameterized by Perdew-Burke-Ernzerhof (PBE) with the on-site Coulomb interaction approach (GGA+U) was employed for the exchange-correlation functional45. Since the electronic properties of perovskite oxides are sensitive to the U value of transition metal ions. An empirical U value of 7.5 eV was used to describe La 4f orbitals. A cutoff energy of 450 eV was used for the plane-wave basis set, and k-space grids of 10\(\times\)10\(\times\)1 within the monkhorst-pack scheme46 were employed to converge the total energy. The electronic self-consistency calculation was assumed for a total energy convergence of less than 10−5 eV. All the atomic position were optimized until the interatomic forces smaller than 0.03 eV Å−1.

BaSnO3 crystallizes in a cubic phase with a space number of 211 (Pm\(\bar{3}\)m) at RT47, while LaGaO3 exhibits an orthogonal perovskite structure. A symmetric sandwich-type structural model, (LaGaO3)m/(BaSnO3)12.5/(LaGaO3)m, was built to model the n-type (LaO)+/(SnO2)0 interface by adding different thickness of LaGaO3 film on the SnO2-terminated BaSnO3 with the thickness of 12.5 unit cells. A vacuum layer of 20 Å was added on the GaO2-terminated LaGaO3 films to avoid the dipole-dipole interaction between the periodic slabs. To model the epitaxial growth process, all the ions were fully relaxed with fixed lattice parameters along the ab plane. The value of m was set from 2 to 8 to figure out the formation mechanism of 2DEG at the interface. The lattice parameter was changed to simulate various strains from – 3 to 3%, at intervals of 1% in the ab plane.