A common characteristic of borophene polymorphs is the presence of hollow hexagons (HHs) in an otherwise triangular lattice. The vast number of possible HH arrangements underlies the polymorphic nature of borophene, and necessitates direct HH imaging to definitively identify its atomic structure. While borophene has been imaged with scanning tunneling microscopy using conventional metal probes, the convolution of topographic and electronic features hinders unambiguous identification of the atomic lattice. Here, we overcome these limitations by employing CO-functionalized atomic force microscopy to visualize structures corresponding to boron-boron covalent bonds. Additionally, we show that CO-functionalized scanning tunneling microscopy is an equivalent and more accessible technique for HH imaging, confirming the v1/5 and v1/6 borophene models as unifying structures for all observed phases. Using this methodology, a borophene phase diagram is assembled, including a transition from rotationally commensurate to incommensurate phases at high growth temperatures, thus corroborating the chemically discrete nature of borophene.
The recent experimental realization of 2D boron1,2,3,4,5,6,7,8 (i.e., borophene) has spurred broad interest in its unique material attributes such as in-plane anisotropy9, massless Dirac fermions10, and seamless phase intermixing7. The polymorphic nature of borophene2,3, which is rooted in the rich bonding configurations among boron atoms, further distinguishes it from other 2D materials and offers an additional means for tailoring its material properties. However, when combined with the large number of predicted lattice structures for borophene, polymorphism introduces challenges for the unambiguous identification of borophene atomic structures experimentally. For example, while conventional metal-tip scanning tunneling microscopy (STM) has provided atomic-scale characterization of borophene4,5,6,7, the convolution of topographic and electronic structure in the resulting images coupled with Moiré superlattices with the underlying substrate leads to experimental uncertainties that do not provide sufficient differentiation among possible borophene lattices. While comparison of available experimental data with density functional theory calculations and simulated images help exclude some possibilities, sufficient ambiguity remains such that the literature lacks consensus for many observed borophene phases5,11. Consequently, an experimental method for definitively identifying borophene atomic structures is needed in order to establish the fundamental structure–property relationships that underlie emerging borophene applications. Since the first evidence of enhanced scanning probe spatial resolution with pentacene-functionalized tips12, deliberate tip functionalization with CO13, H214,15, Xe16, and CuOx17,18 has been utilized to resolve spatial details down to the subatomic regime. Although the physical mechanisms that lead to this improved spatial resolution is still under debate19, geometric imaging with functionalized tips reveals inter-molecular and intra-molecular chemical bonds, particularly in carbon-based molecular or graphitic systems20,21,22.
In an extension of this methodology, we show here that cryogenic ultrahigh vacuum non-contact CO-functionalized atomic force microscopy (CO-AFM) geometrically resolves features that are consistent with boron-boron covalent bonds. We further demonstrate that CO-functionalized STM (CO-STM)22 resolves borophene HHs and thus provides equivalently unambiguous geometric identification of borophene atomic lattice structures in a manner that is experimentally less demanding. By applying this approach to several borophene phases produced at different growth temperatures, a borophene phase diagram is constructed that includes multiple borophene polymorphs with different rotational alignments on Ag(111). In particular, a transition from rotationally commensurate to rotationally incommensurate borophene phases is observed at high growth temperatures, which suggests that borophene is a chemically discrete two-dimensional material as opposed to a surface reconstruction or alloy with the underlying Ag(111) growth substrate.
Non-rotated borophene phases
Borophene polymorphs are characterized by different arrangements and concentrations of HHs in an otherwise 2D triangular lattice. Figure 1a shows a conventional bare-tip STM image of intermixed v1/5 (colored blue) and v1/6 (colored red) phase borophene grown at a previously established temperature of ~450 °C7. By comparing these borophene structures with the atomic lattice of the Ag(111) growth substrate (Fig. 1b), the horizontal HH row directions of both phases are found to be 30° rotated with respect to the Ag atomic chains (directions a or b in Fig. 1c), consistent with previously proposed structural models4 as shown in Fig. 1c. For v1/5 and v1/6 phase borophene, the HHs are arranged in a staggered and aligned manner, respectively, with the unit cells of the HH lattices indicated by the black arrows. High-resolution STM imaging of v1/5 phase borophene with a bare metal tip (Fig. 1d) reveals a strong brick-wall type Moiré pattern modulating finer features.
In an effort to gain higher spatial resolution, imaging of these phases was repeated with CO-AFM. In particular, Figure 1e shows the characteristic inelastic electron tunneling spectra of CO obtained on borophene after decorating the metal tips with a CO molecule (hindered translation and rotation modes at 3.2 meV and 17.6 meV, respectively), confirming successful tip functionalization (Supplementary Fig. 1)23. In contrast to the STM image in Fig. 1d, the constant height CO-AFM image in Fig. 1f geometrically resolves the HH lattice and verifies the proposed v1/5 phase borophene structure, where the HHs are separated by bright ridges at positions expected for boron–boron covalent bonds. In agreement with the experimental image, Figure 1g shows a simulated CO-AFM image24,25 with an overlaid v1/5 phase atomic structure. While the apparent bonding structures of the 6-membered boron rings (i.e., HHs) are clearly resolved, minimal contrast is observed for the triangular boron lattice, where only 3-membered boron rings exist. This limited spatial resolution is reasonable given the fact that 4-membered carbon rings have also not been resolved with CO-AFM26. Nevertheless, resolving the HH lattice is sufficient for determining the structures of borophene polymorphs and thus CO-AFM is a definitive tool for identifying borophene atomic lattice structures3.
In light of the highly demanding nature of non-contact AFM in terms of instrumentation and operation, we further demonstrate that more experimentally accessible CO-STM imaging provides equivalent geometric information in Fig. 1h. Compared to the bare-tip STM image in Fig. 1d, a lattice of staggered protrusions (red arrows) matching the HH lattice are clearly resolved in addition to the less-obvious Moiré pattern. By performing CO-STM imaging in dynamic mode27 (i.e., with an oscillating STM tip), this contrast is further enhanced (Fig. 1i) at milder imaging conditions (Supplementary Fig. 2), which helps improve the stability of the adsorbed CO molecule on the tip apex.
30°-rotated borophene phases
At higher growth temperatures (~500 °C), v1/5 phase borophene dominates7, although another phase with a rectangular lattice also begins to appear (Fig. 2a). This structure was first observed in high-temperature growth and assigned to a buckled triangular lattice5. The 3 Å × 5 Å lattice constants are also indicative of v1/6 phase borophene, which normally grows at lower temperatures4. However, the absence of a linear Moiré pattern typically seen for v1/6 phase borophene suggests that this phase might be the v1/6 sheet on Ag(111) with a different orientation with respect to the underlying Ag(111) lattice as suggested previously28,29. Indeed, instead of being parallel as in the low-temperature v1/6 phase (Fig. 1c), the HH rows in this case are perpendicular to those of a neighboring v1/5 borophene domain in Fig. 2b (yellow arrows). We thus label this phase as v1/6 −30° as schematically shown in Fig. 2c, indicating that the borophene lattice orientation is rotated by 30° on Ag(111) compared to the low-temperature v1/6 phase.
A polycrystalline domain of the v1/6−30° phase with 60° grain boundaries (GBs; yellow arrows) is shown in Fig. 2d. Figure 2e, f are high-resolution STM and CO-AFM images of v1/6−30° phase borophene, respectively, where the aligned HHs are clearly resolved in Fig. 2f with neighboring HHs separated by bright ridges at positions expected for boron–boron covalent bonds. In Fig. 2g, the simulated CO-AFM image with an overlaid atomic structure again agrees well with experimental observations, confirming our structural assignment as v1/6−30°. On the other hand, simulated CO-AFM images of a buckled triangular lattice deviate from the experimental image (Supplementary Fig. 3). Compared to the bare tip STM image, each bright protrusion splits into two protrusions with inequivalent brightness in the CO-STM image in Fig. 2h. A series of bare-tip STM, CO-AFM, and CO-STM images of a 60° GB in v1/6−30° phase borophene is shown in Fig. 2i, j, l, respectively. Based on the apparent bonding positions resolved in Fig. 2j, we propose an atomic structure of the GB seamlessly connecting adjacent grains (Fig. 2k). This proposed structure yields a simulated CO-AFM image (Fig. 2k) that agrees well with experimental observation, further supporting our assignment of the v1/6−30° phase.
As established previously, intermixing of v1/5 and v1/6 phase borophene takes place when the two phases have rotationally aligned HH rows7. Therefore, it is reasonable to expect that v1/5−30° phase borophene (schematically shown in Fig. 3a) would intermix with the v1/6−30° phase at appropriate growth conditions. Indeed, at a higher growth temperature (~550 °C), an undulated structure appears as shown in the bare-tip STM image in Fig. 3b, which has previously been referred to as the striped phase5 and suggested to be induced by an undulating Ag surface reconstruction under a v1/6−30° sheet28. However, based on the CO-STM image in Fig. 3c, we conclude that this phase adopts the v1/5 borophene structure as evidenced by the staggered arrangement of protrusions (yellow circles) representing the HH lattice. Furthermore, instead of the brick-wall type Moiré pattern observed for the low-temperature v1/5 phase, the apparent larger-scale undulation results from a ~4% larger inter-HH spacing along the HH rows than the interatomic spacing of the underlying Ag, which is reproduced qualitatively in Fig. 3d by rotating v1/5 phase borophene by 30° on Ag(111). The coexistence of this structure with v1/6−30° phase borophene with parallel HH rows and a seamless phase boundary is shown in the CO-STM image in Fig. 3e, confirming a rotation angle of 30° and thus the identity of this phase as v1/5−30°. Since phase intermixing results from line defects in each phase adopting the structure of the other phase7, we identify various v1/5−30° line defects in v1/6−30° phase borophene with different widths as shown in the top row of Fig. 3f–i (CO-STM images). The yellow circles denote the staggered HH pattern in the v1/5−30° regions, while the corresponding structures are displayed in the bottom row. Additional CO-STM and CO-AFM images of intermixed v1/6−30° and v1/5−30° phase borophene are provided in Supplementary Fig. 4.
Rotationally incommensurate borophene phases
All of the borophene phases discussed thus far (i.e., v1/6, v1/5, v1/6−30°, and v1/5−30°) are reasonably characterized as being rotationally commensurate with the underlying growth substrate since the HH rows are aligned along high symmetry directions of the Ag(111) surface. In contrast, at similar conditions where phase intermixing is observed for v1/6−30° and v1/5−30° borophene, another new structure is observed as shown in the derivative image of the bare-tip STM topography in Fig. 4a. As seen in the zoomed-in inset images, the borophene domain on the left is v1/5 phase borophene with a characteristic brick-wall type Moiré pattern (orange square), whereas the domain on the right shows a distorted brick-wall type Moiré pattern (green square). The CO-STM image of this new domain structure is provided in Fig. 4b and reveals a HH lattice with staggered protrusions (red arrows) that are indicative of a v1/5 borophene sheet. However, due to the ~36° angle (instead of 30° angle for v1/5) between the directions of the HH rows and the Ag atomic chains (vertical direction, Fig. 4a), this borophene sheet is denoted as v1/5−6°. Rotationally incommensurate v1/5 borophene sheets are generally depicted in Fig. 4c as v1/5-α, where α is the rotation angle by which the sheet deviates from the v1/5 phase. In Fig. 4d, a CO-AFM image of the v1/5−6° phase with an overlaid atomic structure confirms the assignment as a v1/5 sheet.
In addition to α = 6°, other rotationally incommensurate phases such as v1/5−9° and v1/5−22° phase borophene have been observed (Supplementary Fig. 5). As an example, the CO-STM image in Fig. 4e resolves the HH lattice of v1/5−22° phase borophene with periodically self-assembled v1/6−22° line defects in the middle, as evidenced by the staggered and aligned HH patterns indicated by the yellow circles, respectively. Equivalently, the self-assembled periodic line defects can be categorized as v4/21−22° phase borophene (another example is shown in Supplementary Fig. 5) in a manner analogous to previously reported periodic intermixed phases for non-rotated borophene growth (i.e., α = 0°)7. Combining all of the observations discussed above and established previously, a phase diagram for borophene growth with respect to temperature is summarized in Fig. 4f, where each phase is represented by an oval. The overall trend is that borophene growth transitions from rotationally commensurate phases to rotationally incommensurate phases at high temperatures. Significantly, the existence of rotationally incommensurate phases provides corroborating evidence that borophene layers are chemically discrete from the underlying Ag surface8. It should be further noted that the range of observed borophene phases show similar electronic properties (Supplementary Fig. 6) with no measurable differences in lattice constants.
In summary, we have utilized CO-functionalized scanning probe microscopy to geometrically image and determine the atomic lattice structures of various borophene polymorphs. In addition to CO-AFM, we establish CO-STM as an alternative and comparatively more accessible technique for unambiguously determining borophene atomic structures. Using these methods, we assigned structure models for several phases of borophene in addition to resolving features consistent with boron–boron covalent bonds. In all cases, the borophene phases are found to consist of v1/5 and/or v1/6 domains, although the orientation of these domains with respect to the underlying Ag(111) substrate transitions from rotationally commensurate to rotationally incommensurate at the highest growth temperatures. The resulting phase diagram explains all observations of borophene to date with the newest rotationally incommensurate phases providing strong evidence that borophene is a chemically discrete two-dimensional material as opposed to a surface reconstruction or alloy with the underlying Ag(111) growth substrate. This conclusion is further supported by the recent synthesis of borophene on Cu(111)30. The ability of CO-AFM and CO-STM to resolve the complicated phase diagram for borophene polymorphs suggests that CO-functionalized probes can be similarly employed for the unambiguous determination of atomic structures for other emerging synthetic 2D materials and their heterostructures31.
Borophene growth is described in detail in an earlier report7. Briefly, a solid boron rod (ESPI metals, 99.9999% purity) is evaporated onto Ag(111) films (~600 nm thick) on mica (Princeton Scientific Corp.) in an ultrahigh vacuum preparation chamber (~1 × 10−10 mbar) with an electron-beam evaporator (FOCUS) for a duration of ~30 min to achieve submonolayer coverage. The clean Ag(111) surface for borophene growth is prepared by repeated 30 min Ar ion sputtering at 1 × 10−5 mbar followed by 30 min annealing at 550 °C.
Scanning probe microscopy and tip-functionalization
Low temperature STM/STS and non-contact AFM characterization is performed on a Scienta Omicron LT STM (~2 × 10−11 mbar) at ~4 K interfaced with Nanonis (SPECS) control electronics using qPlus AFM sensors (mounted W tips from Scienta Omicron). Tip functionalization is achieved by leaking CO molecules into the STM chamber (1 × 10−7 mbar for 40 s) and picking up individual CO molecules by ramping the sample bias down to −2 mV and the tunneling current up to 1 nA. For AFM measurements, an oscillation amplitude of 1–2 Å is used. AFM image simulation is based on the method developed by Hapala and coworkers24,25. A lock-in amplifier (SRS model SR850) is used for STS measurements with 2 mVRMS amplitude and ~0.8 kHz modulation frequency. Gwyddion software is used for image processing.
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The experimental work was supported by the Office of Naval Research (ONR N00014-17-1-2993) and the National Science Foundation Materials Research Science and Engineering Center (NSF DMR-1720139). The computational modeling was supported by the US DOE Office of Science (DOE DE-SC0012547). X.L. further acknowledges support from a Ryan Fellowship that is administered through the Northwestern University International Institute for Nanotechnology. The authors kindly thank Ruslan Temirov for valuable discussions.