Two-Dimensional Large Gap Topological Insulators with Tunable Rashba Spin-Orbit Coupling in Group-IV films

Abstract

The coexistence of nontrivial topology and giant Rashba splitting, however, has rare been observed in two-dimensional (2D) films, limiting severely its potential applications at room temperature. Here, we through first-principles calculations to propose a series of inversion-asymmetric group-IV films, ABZ₂ (A ≠ B = Si, Ge, Sn, Pb; Z = F, Cl, Br), whose stability are confirmed by phonon spectrum calculations. The analyses of electronic structures reveal that they are intrinsic 2D TIs with a bulk gap as large as 0.74 eV, except for GeSiF₂, SnSiCl₂, GeSiCl₂ and GeSiBr₂ monolayers which can transform from normal to topological phases under appropriate tensile strain of 4, 4, 5, and 4%, respectively. The nontrivial topology is identified by Z₂ topological invariant together with helical edge states, as well as the berry curvature of these systems. Another prominent intriguing feature is the giant Rashba spin splitting with a magnitude reaching 0.15 eV, the largest value reported in 2D films so far. The tunability of Rashba SOC and band topology can be realized through achievable compressive/tensile strains (−4 ~ 6%). Also, the BaTe semiconductor is an ideal substrate for growing ABZ₂ films without destroying their nontrivial topology.

Introduction

Topological insulators (TIs) are new states of quantum matter interesting for fundamental condensed matter physics and important for practical applications^1,2,3. In particular, for two-dimensional (2D) TIs, all the scatterings of conducting edge states are completely forbidden, while the surface states of three-dimensional (3D) TIs are not protected against scattering at any angles other than 180°. The helical edge states of nanoribbons made from 2D TIs provide massless relativistic carriers with intrinsic spin-momentum lock and negligible backscattering, ideal for the realization of conducting channels without dissipation in electronic devices^4,5. However, quantum spin Hall (QSH) effect has only been experimentally observed in HgTe/CdTe^6,7 and InAs/GaSb^8,9 quantum wells at very controlled and low temperature. In spite of this successful progress, the experimental realizations of these topological quantum states in 2D films are still challengeable.

Graphene^1,2, the first 2D TI model, supports an unobservable small bulk gap due to its extremely weak spin-orbit coupling (SOC). Afterwards, several candidate materials are proposed to overcome the issue in graphene for the observation of QSH effect. These samples include silicene¹⁰, germanene¹¹, stanene¹², plumbene¹³, bismuth¹⁴, and arsenene¹⁵, in which they exhibit the topology properties alike to grapheme, but their nontrivial bulk gaps are still small. Motivated by the experimental synthesis of hydrogenated germanene (GeH)¹⁶, the chemical functionalization on honeycomb structure, e.g., Bi/Sb/As^17,18,19,20 and Ge/Sn/Pb films^{21,22,23,24,25,26,27}, has been proposed to host QSH effect with enhanced band gaps. For example, Xu et¹² reported that the nontrivial band gap of pristine stanene is merely 0.1 eV, while it is enlarged to 0.3 eV under fully halogenation^{12,23,24,25,26}. More interestingly, the bulk gaps of 2D plumbene films with chemical decoration, PbX (X = H, F, Cl, Br and I) monolayers, have been elevated to a remarkable 1.34 eV¹³ the largest gap of all the reported 2D TIs as we know. All these results provide a great potential for the realization of QSH effect at room temperature in device paradigms for quantum information processing.

Rashba SOC, on the other hand, generally leads to spin-polarized band dispersion curves with in-plane opposite helical spin texture²⁸. This feature originates from structural inversion-symmetry breaking at the surface/interface system, allowing the control of spin direction through an electric field²⁹. As compared with inversion-symmetric TIs, these systems are called 2D inversion-asymmetric TIs (IASTIs), which are more promising due to their perfect performance in realizing new topological phenomena, such as crystalline-surface dependent topological electronic states³⁰, pyroelectricity³¹, natural topological p-n junctions³² and so on. In conventional semiconductor materials^33,34,35,36, Rashba SOC can only be tuned in a relatively limited range under electric field since it is generally rather weak, so it would be one of the important reasons to interpret the great attention the Datta-Das spin FET³⁷, which still has not been realized in experiments. Recently, Arguilla et al.³⁸ synthesize 2D honeycomb Ge_1−xSn_xH_1−x (OH)_x film from the topochemical deintercalation of CaGe_2–2xSn_2x. In comparison with inversion-symmetric systems^{15,16,17,18,19,20,21,22,23,24,25,26,27,28,29,30,31}, the introduction of tin breaks the inversion-symmetry of 2D germanene, which may induce a significant large Rashba SOC. Motived by above suppose, we attempt to extend and advance the group-IV 2D films to realize giant Rashba SOC accompanied with nontrivial topology, which may our proposal achievable experimentally accessible.

In present work, we report on the electronic and topological properties of a series of 2D IASTIs in group-IV binary films, which are called as ABZ₂ monolayers, where A and B belong to group-IV elements (Si, Ge, Sn, Pb), as well as Z is the decorated halogen atoms (F, Cl, and Br), as illustrated in Fig. 1 (a). We find that most of these group-IV binary films are demonstrated as 2D IASTIs possess sizeable band gaps, reaching a maximum value of 0.74 eV for PbSnCl₂, which exceed the thermal energy at room temperature. Though GeSiF₂, SnSiCl₂, GeSiCl₂ and GeSiBr₂ monolayers are normal insulators (NI), they can transform 2D TI phases under tensile strain of 4, 4, 5, 4%, respectively. The nontrivial quantum states are identified by Z₂ topological invariant together with helical edge states induced by SOC, as well as berry curvature of these systems. The most prominent feature in these systems is the giant Rashba splitting energy, for example, a value of 0.15 eV for PbSiCl₂, which is the largest value reported in 2D films so far. Furthermore, a favorable tunability of Rashba SOC and nontrivial topology can be obtained through achievable compressive/tensile strains (−4 ~ 6%). We also find that the Te (111)-terminated surface in semiconductor BaTe is an ideal substrate for experimental realization of these monolayers, without destroying their nontrivial topology. The coexistence of giant Rashba SOC and band topology in these films may bring rich spin-related phenomena in 2D IASTIs, which offers a special contribution to nanoelectronics and spintronics.

Figure 1

(a) Top view and side view of 2D PbSiCl₂ monolayer. (b) 2D Brillouin zones with specific symmetry points. (c) Total energies of ABCl₂ monolayers as a function of lattice constant a, respectively.

Calculated methods and details

All calculations are carried out using the plane wave basis Vienna ab initio simulation pack (VASP) code^39,40 implementing density functional theory (DFT). The projector-augmented wave (PAW) method⁴¹ is used to describe electron-ion potential. The exchange-correlation potential is approximated by generalized gradient approximation (GGA) in the Perdew-Burke-Ernzerhof (PBE)⁴² form. Considering the possible underestimation of GGA method, the Heyd-Scuseria -Ernzerhof (HSE06) hybrid functional is employed to check the band topology⁴³. We use an energy cutoff of 450 eV and maximum residual force less than 0.001 eV/Å. Periodic boundary conditions are employed to simulate these 2D systems, and the Brillouin zone is sampled by using a 17 × 17 × 1 Gamma-centered Monkhorst-Pack grid. Moreover, SOC is taken into account in terms of the second-variational procedure. The phonon dispersion calculations are carried out by employing the PHONOPY code⁴⁴ through the density-functional perturbation theory (DFPT) approach.

Results and Discussion

Figure 1(a) displays the honeycomb lattice of ABCl₂ (A ≠ B = Si, Ge, Sn, Pb) monolayers, accompanied with its Brillouin zone in Fig. 1(b). All these configurations are iso-structural to inversion-symmetric Ge/Sn/Pb monolayers with C_3v symmetry^{19,20,21,22,23,24,25}, but the A and B sublattices are occupied with different group-IV atoms, resulting in inversion-symmetry breaking. To verify the geometric stability of these structures, the total energies ABCl₂ monolayers with respect to lattice constant a are illustrated in Fig. 1(c), where a is varied to identify structural ground state. Interestingly, the double-well energy variation curves occur in all cases, namely, the high-buckled (HB) and low-buckled (LB) states, respectively. In HB structure, the vertical layer distance lies in the range of 3.58 − 5.15 Å, while the distance in LB state is smaller within 1.42−2.51 Å, as listed in Table 1. The LB structure here, however, is more stable by at least 1.04 eV per unit cell than HB structure, different form the cases of III-Bi films, where the HB structure is the ground state. Thus, we only focus on stable LB chlorinated monolayers in the following. Furthermore, the energetically structural stability is evaluated by the formation energy expressed as

Table 1 Calculated equilibrium lattice parameters a(Å), the buckled height h(Å), band Gaps E_g(eV), band Gaps with SOC E_g (eV), the band gap located at Γ point E_Γ(eV), gap at Γ with SOC E_Γ-SOC(eV) and topological Invariants (Z₂) for six films.

Where E(ABCl₂) and E(AB) are the total energies of chlorinated and pristine AB monolayers, respectively, while μ(Cl) is the chemical potential of chlorination atoms. As listed in Table 1, the calculated formation energies are in the range of −2.284 ~ −3.146 eV per atom, indicating no phase separation emerges in these systems. For practical application as a nanodevice, the 2D films should be chemically inert and environmentally friendly. Thus, the phonon spectrum dispersions are calculated and plotted in Fig. 2, which demonstrates that all ABCl₂ monolayers are dynamically stable since all the vibrational models are real in the whole Brillouin zone.

Figure 2

Phonon band dispersions denote the PbSnCl_2, PbGeCl_2, PbSiCl_2, SnGeCl_2, SnSiCl₂ and GeSiCl₂ films.

The band structures of ABCl₂ monolayers are shown in Fig. 3, with the orbital-projected components displayed in Fig. S1 in the Supplementary Information. In the absence of SOC, the PbSnCl₂, PbGeCl₂ PbSiCl₂ and SnGeCl₂ monolayers show gapless semiconductor feature with valence band maximum (VBM) and conduction band minimum (CBM) degenerated at the Γ point. The Fermi level locates exactly at the degenerated point with a zero density of states. Notably, the slopes of the valence band and conduction band in such a touching point show the parabolic dispersion, instead of a linear one, as illustrated by a 3D band structure for PbSnCl₂ monolayer (Fig. 4 (a)). This scenario for the electronic properties is quite similar to Ge/Sn/Pb monolayers^{21,22,23,24,25,26,27}. Upon including SOC, the band structures produce a transition from semimetal to semiconductor, as the degenerated states at the touching point separate from each other, see Figs 3(a–d) and 4(b). As observed in previously reported Bi/Sb/As^17,18,19,20, the SOC-induced band-gap opening at the Fermi level is a strong indication of the existence of topologically nontrivial phases. Furthermore, from Si to Pb atom, the band gap opening gradually increases (Table 1), since the SOC effect gets stronger due to increasing atomic numbers of heavier atoms. Here we label this SOC-induced band gap at the Γ point as E_Γ-soc, to be distinguished from whole gap (E_g-soc), as listed in Table 1. To eliminate the possible underestimation of the band gap, we employ additional HSE06³⁷ to confirm the existence of band inversion for all these systems. As expected, the values of E_Γ are enhanced to 0.74, 0.49, 0.41 and 0.23 eV, respectively, for PbSnCl₂, PbGeCl₂, PbSiCl₂ and SnGeCl₂ monolayers.

Figure 3: The calculated band structures without and with SOC.

The black lines correspond to band structures without SOC, the red lines correspond to band structures with SOC.

Figure 4

(a) and (b) show 3D band structure of 2D PbSnCl₂ monolayer. (a) PbSnCl₂ monolayer without SOC. (b) PbSnCl₂ film with SOC. Orbitals-resolved band structures without and with SOC for (c) and (d) PbSnCl₂ monolayer.

To confirm the nontrivial topological nature, we introduce the evolution of Wannier Center of Charges (WCCs)⁴⁵ to calculate Z₂ topological invariant due to inversion-symmetry breaking. The Wannier functions (WFs) related with lattice vector R can be written as:

Here, a WCCs can be defined as the mean value of , where the is the position operator and is the state corresponding to a WF in the cell with R = 0. Then we can obtained

Assuming that with S = I or II, where summation in α represents the occupied states and A is the Berry connection. So we have the format of Z₂ invariant:

The Z₂ invariant can be obtained by counting the even or odd number of crossings of any arbitrary horizontal reference line. Taking PbSnCl₂ monolayer as an example, we present the evolution lines of WCCs in Fig. 5(a). One can see that the WCCs evolution curves cross any arbitrary reference lines odd times, yielding Z₂ = 1.

Figure 5

(a) The evolution lines of WFC for PbSnCl₂ monolayer. (b) The energy bands was calculated around the Fermi level by the method of DFT and Wannier. (c) Total (left panel) and (d) spin (right panel) edge density of states for PbSnCl₂. In the spin edge plot, blue/red lines denote the spin up/down polarization.

The most important character of 2D TIs is the appearance of helical edge states with spin-polarization protected by TRS. Here we compute the edge Green’s functions using the ab initio TB model. The ab initio TB model is constructed by downfolding the bulk bands obtained by DFT calculations, using the recursive method in terms of maximally localized Wannier functions (MLWFs)⁴⁶. Figure 4(c) and (d) show the orbital-decomposed band structures, in which the red and blue circles represent group-IV s and p_x,y states, respectively, and the symbol size is proportional to the orbital weight. Obviously, the bulk energy bands near the Fermi level are predominantly from p_x,y orbitals, thus the MLWFs are derived from atomic p-like orbitals. In this case, the TB bulk bands perfectly reproduce the DFT bands around the Fermi level up to ± 1.0 eV, as illustrated in Fig. 5(b). Figure 5(c) displays the local density of states (LDOS) of the calculated edge states. Indeed, all the edge bands for PbSnCl₂ monolayer connect completely the conduction and valence bands and span 2D bulk gap, yielding a 1D gapless edge states, in good agreement with the Z₂ invariant. By identifying spin-up and spin-down contributions in edge spectral function, the counter-propagating edge states exhibit opposite spin-polarization (Fig. 5(d)), which benefit from their robustness against nonmagnetic scattering.

For GeSiCl₂ and SnSiCl₂ monolayers, on the other hand, they exhibit semiconductor feature with direct band gap of 0.285 and 0.265 eV in the absence of SOC, as shown in Fig. 3(e) and (f). As we know that external strain is an effective avenue to tune the band gap, this may introduce a band inversion by SOC. To simulate strain effects on the electronic structures, we employ the external strain to these systems which is defined as ε = (a-a₀)/a₀, where a and a₀ are lattice constants with and without strains, respectively. In Fig. 6 we present the band structures with respect to external strains of GeSiCl₂ as an example, where the red and blue colors represent s and p_x,y states, respectively. One can see that the band structure of GeSiCl₂ is sensitive to the lattice expansion. Without SOC, the CBM (s) and VBM (p_x,y) move toward each other, leading to a reduction of band gap. The band gap closes at the Γ point when ε = 5%, as illustrated in Fig. 6(c), suggesting semi-metallic character at the Fermi level. When the tensile strains are beyond 5%, the p_x,y orbitals shifted above s orbital, see Fig. 6(d). As a consequence, the opposite spatial shift of VBM and CBM decreases the band gap, which is essential to topological phase transitions. With increasing biaxial strain, the energy difference (E_s-p) between the s and p_x,y orbitals at the Γ point near the Fermi level increase monotonically, but the system remains the semi-metallic feature. When SOC is included, a sizable band gap opens, see Fig. 6(e–h). Similar results are also found in SnSiCl₂ monolayer in Fig. 7, but its critical point of elastic strain is 4%, smaller than GeSiCl₂ monolayer. Such an SOC-induced band gap reopening usually corresponds to a NI - TI transition, as illustrated in Fig. 8.

Figure 6: The GeSiCl₂ energy band structures as a function of strain,the blue points shows s orbit composition and the red points shows p_x,y orbit composition.

(a,b,c) and (d) show GeSiCl₂ film without SOC,(e,f,g) and (h) show GeSiCl₂ film without SOC.

Figure 7

The evolution of atomic s and p_x,y orbital without SOC and with SOC of (a–d) and (e–h) SnSiCl₂ monolayer.

Figure 8

Variation of band inversion strength (BIS) for ABF_2, ABCl₂ and ABBr₂ (A ≠ B = Si, Ge, Sn, Pb) systems with respect to external strain.

To gain a physical understanding of QSH effect, we analyze the orbital contribution around the Fermi level for GeSiCl₂ monolayer. Figure 9 presents the band evolution at the Γ point, in which the energy levels near the Fermi level are mainly composed of s and p_x,y orbitals from group-IV elements. The chemical bonding between Si-Ge atoms makes it split into the bonding and antibonding states, i.e., s^± and p_x,y^±, respectively. At ground state in Fig. 9(a), the bands near the Fermi level are contributed by the p_x,y⁺ and s⁻, with the s⁻ being above p_x,y⁺, indicating a normal band order. When considering the external tensile strains, as illustrated in Fig. 9(b), the enlarged lattice constant weakens the interactions between A and B sublattices, decreasing the splitting between the bonding and antibonding states, which lowers s⁻ and raises p_x,y⁺ level accordingly. Thus, depending on the strength of interatomic coupling, the band gap of GeSiCl₂ can be continuously reduced, with the band order being reversed at critical point (ε = 5%), making it a 2D TI with Z₂ = 1. In another words, the level crossing leads to a parity exchange between occupied and unoccupied bands, inducing a NI-TI phase transition. While for PbSnCl₂, PbGeCl₂ PbSiCl₂ and SnGeCl₂ monolayers, the lattice constant (See Fig. 1(c) and Table 1) is enlarged significantly at equilibrium state, equal to strain-induced GeSiCl₂, thus they are native 2D TIs without any strain. Herein, we must point out that, although the s-p_x,y band inversion is caused mainly by the strength of interatomic coupling, the SOC is still indispensable because it makes the p_x,y⁺ orbital split into p⁺_x+iy,↑& p⁺_x-iy,↓ and p⁺_x-iy,↑& p⁺_x+iy,↓, opening a larger band gap. In previous works, the topological feature mainly originates from p_z states such as graphene and silicene^1,2,3, but here the band topology is attributed to the contribution of p_x,y orbitals on group-IV elements, thus their band gap is enhanced significantly.

Figure 9

The evolution of atomic s and p_x,y orbital without SOC and with SOC of (a) and (b) GeSiCl₂. The horizontal red dashed lines indicate the Fermi level.

Furthermore, to clearly show the QSH effect in these systems and confirm its nontrivial topology, we also calculate the intrinsic spin Hall conductivity of PbSnCl₂ monolayer. Using the Kubo formula^47,48, the spin Hall conductivity tensor is expressed as,

Here the spin Berry curvature is given by

where n is the band index, ψ_n,k is the eigenstate, v_y is the velocity operator, and j_x is the spin current operator defined as (s_zv_x + v_xs_z)/2. Also, a factor of 2e/ћ in σ^SH is multiplied to convert its unit into the conventional electron conductivity e²/h. Figure 10(a) displays the k-resolved spin Berry curvature at the Fermi level. One can clearly see the positive peak of Ω^SH(k) around the Γ point, which is consistent with its band topology. The spin Hall conductance via its chemical potential shows a nearly quantized value 2e²/h of conductance within the energy window of the SOC gap ranging from about − 0.2 eV to the Fermi energy, demonstrating that the QSH effect could be easily observed experimentally at room temperature.

Figure 10

(a) The k-resolved spin Berry curvature at the Fermi level of PbSnCl₂ monolayer. (b) The Rashba splitting energy E_R and the momentum offset k_R of PbSiCl₂ monolayer. (c) Spin texture in the highest valence bands for PbSnCl₂ monolayer. Arrows refer to the in-plane orientation of spin, and the color background denotes the z component of the spin. (d) The energy band for ABF_2, ABBr₂ (A≠B = Si, Ge, Sn, Pb) systems.

The most prominent feature in inversion-asymmetric systems is the existence of giant Rashba SOC in valence band edge rather than Dresselhaus splitting⁴⁹. These can be confirmed by the spin texture of Rashba spin splitting in Fig. 10(c), in which the spins of the electronic states are oppositely aligned within the k_x and k_y plane, and are normal to the wave vector k. Here, we magnify the Rashba splitting energy E_R and the momentum offset k_R in Fig. 10(b), which corresponds to the splitting of the VBM along momentum direction at the Γ point, indicated by the rectangular box in Fig. 3(c). According to the linear Rashba model of the 2D systems, the dispersion of Rashba splitting can be expressed as with k = (k_x, k_y), where the m^* is effective mass and is the Rashba constant. Thus we can obtain a giant Rashba parameter eV/Å than the well-known oxide interface LaAlO₃/SrTiO₃ (0.01–0.05 eV/Å)^50,51,52, quantum well InGaAs/InAlAs (0.07 eV/Å)⁵³ and Au (111) surface⁵⁴. These great Rashba splitting energy E_R and momentum offset k_R are desired for stabilizing spin and achieving a significant phase offset for different spin channels.

It is noteworthy that strain engineering can not only tune the topological phase, but also change the Rashba spin splitting significantly in these monolayers. In Fig. 11, we present three parameters (E_R, k_R, α_R) under different biaxial strains by solid triangles for PbSiCl₂ as an example. These three parameters decrease monotonically with the increasing lattice constants, demonstrating that a compressive/tensile strain can enhance/decrease the Rashba SOC strength. For example, the Rashba splitting can reach up to 0.182 eV under −4% strain. Thus, by biaxial strain engineering, we can enhance or reduce the SOC strength according to the experimental demands. The Rashba spin splitting of energy bands obtained here provides a chance for spintronic device applications without magnetic field, for instance, spin field-effect transistor (FET).

Figure 11

Present four parameters (E_R, k_R, α_R, E_g) of PbSiCl₂ monolayer under different biaxial strains by solid triangles.

Finally, we must point out that that the chlorination in group-IV monolayers is not the only way to achieve QSH effect, the same results can be obtained by decorating the surface with other halogens, such as F and Br atoms. As evidenced in Fig. S2 in the supplementary information, the double-well energy curve still exists, with the LB structure being a ground state. The corresponding band structures of ABF₂ and ABBr₂ monolayers with and without SOC are further plotted in Fig. 12. Most of halogenated ABX₂ monolayers are similar to chlorinated ones with a topological invariant Z₂ = 1, except for GeSiF₂ and GeSiBr₂ with Z₂ = 0. However, they can transform into QSH insulators under external strain of 4%, as illustrated in Fig. 8(a) and (c). In addition, Fig. 8 presents the calculated band gaps at equilibrium states, accompanied with the lattice parameters listed in Tables SI and II. Interestingly, the nontrivial band gaps can reach as large as 0.11–0.63 eV (Fig. 10(d)), which is comparable or larger than stanene (0.1 eV)¹² or bismuth (0.2 eV)¹⁴. Such large nontrivial band gaps are capable of stabilizing the boundary current against the influence of thermally activated bulk carriers, and thus are beneficial for high-temperature applications.

Figure 12: The blue points shows s orbit composition and the red points shows p_x,y orbit composition.

(a–f) show ABF₂(A ≠ B = Si, Ge, Sn, Pb) films without SOC, (g–l) show ABF₂(A ≠ B = Si, Ge, Sn, Pb) films with SOC.

Experimentally, choosing a suitable substrate is a key factor in device application, since a free-standing film must be eventually deposited or grown on a substrate. Considering the small lattice constant mismatch between PbSnCl₂ and semiconductor BaTe⁵⁵, we select Te-terminated (111) surface of semiconductor BaTe to support PbSnCl₂ monolayer, as illustrated in Fig. 13. In the equilibrium state, the bottom (top) Sn atoms in PbSnCl₂ are located at top (hcp) sites of the substrate, while the top Pb atoms are located at hcp sites, see Fig. 13(a) and (b). On this Te-terminated surface, Sn atoms bind preferably on top of Te atoms by forming chemical bonds, so the p_z orbital of group-IV atoms and dangling bond of the substrate are both fully passivated. Figure 13(c–f) present the band structures with and without SOC, respectively. One can see that a few bands appear within the bulk gap of substrate around the Fermi level, which is mostly contributed by group-IV atoms according to wave-function analysis. By projecting Bloch wave functions onto atomic orbitals of PnSnCl₂, Bloch states contributed by the s orbital of group-IV atoms are visualize by red dots. These states shift to valence bands around the Γ point, suggesting a clear s-p band order. This SOC-induced band gap is topologically nontrivial as explained by the band inversion, thus it is a robust 2D TI on Te-terminated substrate of BaTe semiconductor.

Figure 13

Top view (a) and side view (b) of the schematic illustration of epitaxial growth PbSnCl₂ on Te(111)-terminated BaTe surface, as well as the band structure without SOC (c,d) and with SOC (e,f) for PbSnCl₂ monolayer.

Conclusions

In summary, by means of first-principles calculations, we predict a series of inversion-asymmetric group-IV monolayers, ABZ₂ (A≠B = Si, Ge, Sn, Pb; Z = F, Cl, Br), allows for the simultaneous presence of topological order and Rashba SOC. The phonon spectrum calculations reveal that they are dynamically stable. The analyses of electronic structures reveal that most of these monolayers are native 2D TIs with a bulk gap as large as 0.74 eV, while GeSiF₂, SnSiCl₂, GeSiCl₂ and GeSiBr₂ can transform from normal to topological phases under tensile strain of 4, 4, 5 and 4%, respectively. The nontrivial topology is identified by Z₂ topological invariant together with helical edge states, as well as the berry curvature of these systems. The most intriguing feature is their giant Rashba spin splitting with a magnitude reaching 0.15 eV for PbSiCl₂, the largest value reported in 2D films so far. A large tunability of Rashba SOC and band topology can be realized through achievable compressive/tensile strains (−4 ~ 6%). In addition, the Te(111)-terminated surface in semiconductor BaTe is predicted to be an ideal substrate for experimental realization of these systems, without destroying their nontrivial topology. Considering their simple crystal structure as well as large nontrivial band gap and giant Rashba splitting energy in these monolayers, these findings present a platform to explore 2D inversion-asymmetric TIs for room-temperature device applications.