A model has been developed to account for and prevent the anomalies encountered in topographic images of transition metal dichalcogenide monolayers using dynamic atomic force microscopy (dAFM). The height of WS2 monolayers measured using dAFM appeared to be increased or decreased, resulting from the interactions between the tip and the surface. The hydrophilic SiO2 substrate appeared higher than the weakly hydrophilic WS2 when the tip amplitude was low or at a high set point (high force). Large amplitudes and low set points corrected the step height inversion, but did not recover the true step height. Removing water from the sample resulted in an order of magnitude reduced variation in step height, but the WS2 appeared inverted except at low amplitudes and high set points. Our model explains the varying step heights in dAFM of TMDs as a result of varying tip-sample interactions between the sample and substrate, in the presence or absence of capillaries. To eliminate contrast inversion, high amplitudes can be used to reduce the effect of capillary forces. However, when capillaries are not present, low amplitudes and high set points produce images with proper contrast due to tool operation in the repulsive regime on both materials.
Transition metal dichalcogenides (TMDs) are a class of layered materials from which a single layer can be isolated with a thickness less than 1 nm. TMD monolayers have unique optical and electrical properties including high absorption relative to their thickness1, direct band gaps2,3,4, rapid charge separation5, and can even be ferromagnetic6,7,8 or superconducting9,10,11. Due to their thinness, monolayer TMDs interact strongly with their environment; this strong interaction makes characterization of trapped contaminants, surface adsorbed contaminants, water layers, and the TMD-substrate step height necessary to predict and understand device operation12,13,14,15,16. Dynamic atomic force microscopy (dAFM), in which a nanoscopic tip is driven sinusoidally, can measure topography while providing a plethora of additional data channels for characterizing the surface absorbed contaminants. dAFM allows for simultaneous measurement of surface potential17, long range attractive forces18, dispersive and conservative forces19, and performing magnetic20 and electrical measurements17,18. Contact AFM can provide a subset of these measurements, but cannot be used to characterize tip-sample forces in the region of attractive force above the surface where the tip snaps into contact, within 1–3 nm of the sample surface21.
In topographic measurements of TMDs on substrates, the step height from the substrate to the top of the TMD is often assumed to be the same as the bulk interlayer spacing, which can be measured accurately by X-ray diffraction. However, due to possible contaminant layers, incomplete bonding to the substrate, and different forces between the TMD and substrate, the measured step height is not necessarily the same as the bulk interlayer separation. Variation in AFM step heights of TMDs have not been systematically investigated to date; reports in literature include a wide range of measured WS2 thicknesses, 0.6 nm – 0.92 nm22,23, as opposed to the bulk interlayer spacing of 0.67 nm. Even with a perfectly conformal and contaminant-free TMD monolayer on a substrate, the measured thickness can vary and the WS2 can appear lower than the substrate (i.e., an inverted image), a phenomenon known as contrast inversion24,25,26. This is contrary to measuring a monolayer step within the same material, where step height anomalies are not observed27,28, indicating that varying step heights are an artifact of stepping from one material to another. Thin film and nanoparticle topographies from many sample-substrate systems have shown similarly varying height and contrast inversion, including block copolymers, nanoparticles, and self-assembled monolayers on Au and mica24,25,26,29,30,31,32,33. For these other material systems, the measured layer thicknesses and nanoparticle heights have been found to be dependent on tip amplitude and force34. In graphene on SiO2, varying step heights have been attributed to capillary effects35 or to compressed trapped contaminant layers between the graphene and the substrate36. These trapped water layers have been directly observed37,38. It was reported that the effect of capillary forces was minimized by operating AFM in the repulsive regime on both sample and substrate35. The trapped contaminant layers were shown to be compressed to the substrate by the tip force36, which explains why high tip forces produced results closer to the bulk interlayer spacing. Step height, thickness, and topography measurements in AFM of TMD monolayers exhibit many artifacts and features which have not been systematically studied.
Here we report our systematic study on dAFM topography of monolayer TMDs. We show that step height errors are caused primarily by varying surface water layer thicknesses on the less hydrophilic TMD and hydrophilic SiO2. We investigate the effect of tip amplitude and set point on measured step heights of TMDs on SiO2. We use amplitude-phase-distance (APD) data to produce force distance curves which allows for a quantification of the attractive force experienced by the tip when approaching the surface. We demonstrate that the variation in step heights is reduced by an order of magnitude after partial removal of surface water, which decreases the capillary forces experienced by the tip. Finally, we define the tip-sample interactions which result in contrast inversion and prescribe operational settings in terms of appropriate amplitudes and set points which restore proper contrast.
Figure 1a exhibits the range of observed step heights for single crystalline WS2 monolayers grown on SiO2 (CVD WS2) in phase feedback, based on set point and tip amplitude, the two essential parameters for dAFM. In dAFM operation, as the tip begins to interact with the sample, the tip amplitude is reduced, the resonant frequency can shift, and the phase can increase or decrease from its in-air value. Any of those three variables can be used for feedback when scanning. While the amplitude is not sensitive to the sign of the tip-sample force, the phase will increase with a net positive tip-sample force and the phase will decrease with a net negative tip-sample force29. We chose phase feedback to ensure operation in the repulsive regime. We have defined the oscillation amplitude as the distance the tip travels from the lowest to highest point (Fig. 1b). We have defined the set point as the percent reduction in amplitude when using amplitude for feedback and the angle reduction from 90° when using phase feedback (Fig. 1b). For both feedback modes, high set point means high force. The height is the piezo height which corresponds to the tip-sample distance plus an arbitrary offset. As shown in Fig. 1a, the set point and amplitude can cause an increase or decrease in the apparent thickness, in agreement with other reports34,39. In this work, the AFM images were taken consecutively on the same sample (CVD WS2), with tip amplitudes 121 nm, 145 nm, and 169 nm and the set point at 9°, 18°, and 27° (phase feedback mode; amplitude feedback produced a similar range of results). The tips used were pulled SiO2 fibers with high Q (~1600) and the range of amplitudes used produced results comparable to a range of 20–60 nm for common Si tips. AFM images were corrected for line-by-line offset and parabolic error from the piezo scanner using the “flatten” function of WSxM40. Four of the nine images had negative step heights, i.e., the TMD was imaged as if it was pressed into the substrate below the surface. As can be seen, changing either the set point or the amplitude affected the step height measured on the same sample. We cannot attribute the step height variation or contrast inversion to sample roughness, as the SiO2 substrate roughness was < 0.5 nm RMS and the WS2 roughness was <0.5 nm RMS, excluding bilayer defect regions. For the same experiment with exfoliated materials, large steps (>6 nm) were recorded and no contrast inversion was observed over a wide range of set points and amplitudes which we attribute to contaminants trapped between the TMD and the substrate. High vacuum annealing reduced the observed height of exfoliated samples and caused them to appear inverted under certain amplitudes and set points. We have also worked with graphene but have never observed inversion, only obtaining measured heights greater than the bulk interlayer spacing of 0.34 nm. We also used contact mode AFM, which is less affected by water layers26 and does not produce contrast inversion36. However, in our experiments it also did not result in a consistent, unambiguous measurement for the step height.
Figure 1c examines the transition of the contrast from a negative to positive step height. We generated phase feedback dAFM topographic images of a non-annealed CVD WS2 monolayer at varying amplitudes from 145 nm to 266 nm in intervals of 24 nm (Fig. 1c). A constant set point of 9° was used for all images, chosen as a mid-range value. For each image, twenty step heights were obtained and averaged for the measured step height, while error bars were calculated as the standard deviation. As shown in Fig. 1c, the measured step height of the WS2 was inverted at low tip amplitudes and transitioned to correct contrast at a critical amplitude. Figure 1a shows that this critical amplitude depends on the set point. At the same time, the variability in the measured step height was larger when scanning at the low amplitude of approximately 150 nm.
To reduce the effect of a water layer, we annealed a sample in air at 130 °C for 30 minutes. After annealing, when scanning with a wide range of typical amplitudes (60–362 nm) and set points (9–23°), contrast inversion was observed for all combination of parameters. The correct contrast was restored using low amplitudes (<20 nm) and high set points (>30°), directly contrary to the case before annealing, which indicates that the surface forces between the tip and sample are different before and after annealing. This is summarized in Figure S1, which repeats the experiment in Fig. 1a but for an annealed sample. After annealing, it is shown that low amplitudes exhibit correct contrast. Placing the samples in a low humidity environment did not effectively remove surface water41. In addition, the measured (apparent) step heights for the annealed samples had a smaller variation (<0.5 nm standard deviation), centered higher than the interlayer spacing value of 0.67 nm. We investigated the remaining variation through amplitude-phase-distance (APD) curves.
Theoretically, the APD curves can be used to compensate for step height measurement errors24,26,42. This is accomplished by finding the height difference between points of equal phase on the two different materials. We found that, even with annealing, the variation in single point APD curves taken on different parts of a sample was on the same order as the step height (0.67 nm). Without annealing, the variation was an order of magnitude higher, 3–6 nm. Thus, single point APD curves cannot be used in this case to compensate for the differences in tip-sample forces between the WS2 on SiO2 and bare SiO2. We expect that a pristine WS2 on SiO2 sample could have step heights corrected through APD curves, as in other material systems which had tip-sample forces dominated by van der Waals forces24,26,42.
To investigate the effect of the surface water layer on tip-sample interactions, the APD curves on both WS2 and SiO2 were compared before and after annealing the samples in air at 130 °C for 30 minutes (Fig. 2). The effect of water adsorbed on the surface can be clearly seen in the APD curves. The WS2 samples were CVD WS2 monolayer triangles of side length 5–50 nm on SiO2 that had been stored in an Ar environment. We used dynamic APD curves to enable investigation of the tip-sample forces near the sample surface which are inaccessible to the static mode due to tip snap-in. The phase, amplitude, and piezo height were recorded as the tip approached the sample from a non-interacting region (e.g., over 100 nm from the surface). It should be noted that the variations were not due to tip damage; tip damage was minimized by minimizing the approach distance. In these measurements, the retract curves were not used as the tip-sample forces were obscured by additional effects31. The experiment was repeated several times on different days with different WS2 samples. A key observation was that lower tip amplitudes resulted in larger tip-sample interactions in the attractive region (phase >90°) on the APD curves. The data shown are with tip amplitudes ~13 nm, a relatively low value and near the minimum that the tool could be run due to noise in the piezoelectric oscillation sensors. The tip resonance frequency was observed to shift by ~1 Hz from the frequency with free amplitude while in contact. If there was a large shift in the resonance frequency from the original locked in value, the results would be invalid as the amplitude reduction and phase shift would be a mixed effect from tip-sample forces and a frequency shift. Force distance curves and the dissipation coefficient were interpreted from the method of Payam et al.43. The data plotted against piezo height are shown in Fig. 2, with the piezo height shifted to make H = 0 the peak of the phase in the attractive region. The true sample surface is necessarily between the onset of the attractive region, on approach, and the transition to the repulsive regime. The peak of phase is taken as an approximation of the location of the sample surface to allow curves to be compared properly. Additionally, the phase was shifted to be 90° in air, as expected from a damped driven spring in resonance. The raw phase was measured by convolving the driving phase with the tip phase and therefore was 0° in air.
When starting to interact with the sample, the phase initially increased and the amplitude decreased; phase >90° means that the net tip-sample interaction is attractive and phase <90° means the net interaction is repulsive44. While the phase is sensitive to the sign of the tip-sample forces, the amplitude is always reduced, a fundamental property which arises in damped driven spring systems29. In Fig. 2, differences between the samples with and without annealing are apparent. Annealing reduced the amount of the phase increase in the attractive region by approximately 3x, which implies weaker attractive tip-sample forces in annealed samples. Without annealing the sample, the amplitude reduced rapidly and almost the entire amplitude reduction occurred in the attractive region. With annealing, however, the phase increase was smaller and the amplitude reduction was slower, implying smaller attractive forces. In the annealed sample, the amplitude showed a horizontal region (bistability) at the transition from the attractive to the repulsive regime, as is commonly observed35,44,45. After the bistability, the amplitude had a further reduction. We attribute this observation to the existence of water layers on the WS2 and SiO2 surfaces; this resulted in an attractive force due to surface tension which dominated the tip-sample interactions. Pure van der Waals forces would result in a phase increase equal to or less than observed in the annealed samples. On the annealed sample, the attractive region was wider than on the non-annealed sample. When comparing the width and structure of the attractive region on many trials, it was clear that the phase curve in the attractive region was defined by a short range interaction (<3 nm) and a long range interaction, extending from 1 nm to 6 nm from H = 0. On non-annealed samples, some appeared with only a short range interaction which was about 3 times higher than any phase shift on annealed samples, and some had only the long range component which peaked at up to 70% the height of the short range component. We attribute this to capillaries forming at two length scales, depending on local sample conditions for capillary attachment. On annealed samples, only the long range component appeared and was broadened, extending from 1 nm to 8 nm from H = 0. This implies that the stronger, shorter range forces (attributed to capillaries) were mediated by surface contaminants which were removed through annealing. The broadened attractive region on annealed samples was attributed to a net attractive force when initially in contact, not to longer range forces. In the retract curves (not shown), there was no attractive region on annealed samples and a strong attractive region on non-annealed samples, evidence of effective water removal through annealing. Retract curves were not analyzed closely as they are affected by adhesion, piezo hysteresis, and other effects.
When taking topographical images (2D AFM images) of WS2 on SiO2, several channels were recorded simultaneously including the amplitude, phase, and height. In the 2D image taken with phase feedback, we observed the amplitude was reduced on WS2 compared to SiO2 alone at any set point. Using phase feedback ensured that we were in the repulsive regime as the phase is sensitive to the sign of the force. In the absence of dissipative forces, the amplitude should be linear with the sine of the phase46,47, but Fig. 2 shows that in our samples the amplitude -sin (phase) relationship was not first order and varied between samples. When recording using phase for feedback, the phase should be held at zero through the entire map, though it can deviate at steps due to a time lag from the feedback loop. Considering the shape of APH curves, which are constrained to decay over a specific height range equal to the free amplitude, the consistently lower amplitude on WS2 could be due to either a wider attractive region on WS2 or a greater amplitude reduction in the attractive region on WS2; we observed the latter in both the annealed and non-annealed cases. If this trend of amplitude reduction were in the contact region it could be attributed to the softness of WS2 or to compressing the layer, but instead it occurred in the attractive region. Thus the amplitude reduction on WS2 implies a stronger attraction between the tip and WS2 than SiO2, whether annealed or not.
To produce FD curves, the height was converted to the tip-sample distance, D. In this case, the distance is defined as the minimum distance between the tip and the sample, D = H-A + offset, where H is the height, A is the amplitude, and the offset is to make D = 0 at the sample surface. In practice, D = 0 is set to the location of the peak of the phase in the attractive region. When plotted against D, there was a clear difference between samples from annealed and non-annealed samples (Fig. 3). When in full contact and without long range interactions, the amplitude should reduce concomitantly with the height (dA/dH = 1). In that case, the amplitude and phase curves should be a vertical line at D = 0. In the case of weak long range interactions, such as van der Waals forces, the slope of the amplitude reduction (dA/dH) near to but smaller or greater than 1, which produces nearly vertical but oscillating curves as shown in Fig. 3 for the annealed cases, both WS2 on SiO2 and nearby bare SiO2. For non-annealed samples, we observed dramatic amplitude reduction (dA/dH > 1), which results in an inverted, non-monotonic curve when amplitude and phase are plotted against D, and as a loop on the PD graph (non-annealed samples in Fig. 3). When D is not monotonic, the FD curves cannot be produced from the theory43. For non-annealed samples, the data goes to negative D before the attractive region starts, since D = 0 was set to be the peak of the attractive region, which means that FD curves could not be produced for non-annealed samples for the entire region of tip-sample interaction. For WS2, the attractive region appeared wider when plotted against D, an artifact of more rapid amplitude reduction (higher dA/dH).
Figure 4 illustrates the main features of the expected force-distance (FD) curves on top and the non-conservative dissipation factor on bottom, constructed by referring to the model in Payam et al.43. The model converts dynamic APD curves to an FD curve and dissipation curve. The inverted slope on the APD curves means that the FD curves cannot be calculated from the integral equations, for the data presented in this paper. This is because the equation for the FD curve integrates the APD curves from d to infinity, which is not well defined when d is not monotonic. In the model, there are three terms in both the models for the force and for dissipation:
where d is the minimum tip-sample distance, k is the spring constant, x is the ordinate in the amplitude (A) and phase (φ) data, Q is the tip quality factor, and ω and ω 0 are the driving and tip resonant frequencies. α is a factor approximately equal to 1/8. By analysis of the terms, for both equations 1 and 3, the second term is smaller than the third term by a factor of . With amplitudes of at least 8 nm in all data taken, the second term can be ignored with a maximum of ~1% error introduced. As derivatives and integrals produce terms of the same order because dA/dH ≈ 1, to within a factor of 5, the ratio of Term 3 to Term 1 can be estimated as proportional to A 0. This was observed in data which was integrable (not shown) – Term 1 dominated for free amplitudes less than about 20 nm, and Term 3 dominated for amplitudes larger than that, with a rapid transition between the two. Thus, in the data presented with an amplitude of 13 nm, Term 1 should dominate and the following discussion applies to Term 1. Another difference between Term 1 and Term 3 is that Term 3 is necessarily local due to the factor in the integral which picks out terms where x ≈ d, while Term 1 depends on the entire data from d to infinity.
To evaluate the shape of the FD curve, we first assume that the tip is driven on resonance which means X = 0 far from the sample surface. The sign of X depends on the phase only, with φ > 90 corresponding to cos(φ) < 0 and thus X < 0. In the attractive region, with φ > 90, the FD curve will show negative values, an attractive force. When φ < 90, then X > 0, and as the phase reduces to zero the term X goes to infinity. Term 1 depends on the integral of X from d to infinity, which means the resulting curve should have an initial attractive region which is quickly dominated by the repulsive force as the phase drops to zero in the repulsive region. The result of applying this analysis to the APD data in Fig. 3 is shown in Fig. 4a (top). In non-annealed samples, the attractive region is narrower, centered closer to D = 0, and the repulsive regime should quickly dominate. This is contrasted to the non-annealed samples which exhibit wide attractive regimes where most of the amplitude reduction occurs, producing much more negative values of X over a wide range of D values, which when integrated produce a wide and deep region of attractive force which is not as rapidly dominated in the repulsive regime, resulting in a smaller slope of the FD curve in that region. Based on the height and width of the attractive regimes, the strength of the attraction was comparable on both materials. If it were possible to construct FD curves from the non-annealed data, they would exhibit approximately 3 times stronger attractive forces since the phase change was 3 times higher in the attractive regime on non-annealed samples.
An assumed and drawn non-conservative energy dissipation factor, similar to the coefficient of dz/dt in a damped-driven spring model, is plotted against tip sample distance in Fig. 4b. To evaluate the shape of the dissipation coefficient curve, we again assume the tip is driven on resonance, which means Y = 0 far from the sample surface (where φ = 90 and A = A0). An interesting case to consider is when A/A0 = sin(φ) as the tip approaches, the condition for zero dissipation46. This agrees with the model, as Y = 0 for all d under that condition. Unlike the FD curve, where the sign depends only on φ, the sign of the dissipation depends on the relative values of sin(φ) and A/A0. If sin(φ) > A/A0, then Y is positive. Considering Term 1, Y is integrated from d to infinity which, if Y is consistently positive, produces a monotonically decreasing function. The derivative would be negative. Thus, the condition for negative dissipation is a rapid decrease in amplitude, so that sin(φ) > A/A0. This is observed throughout the entire attractive region for non-annealed samples, for both WS2 and SiO2. This is also observed at the beginning of tip-sample interaction for annealed samples. The dissipation is proportional to the derivative, so as the APD curves flatten out when in deep contact the dissipation returns to zero. These features are illustrated in Fig. 4b, which takes into account the relative width and height of the attractive regions and the relative values of sin(φ) and A/A0 in each case to produce heuristic curves.
In both annealed and non-annealed samples, the energy dissipation was negative when the tip was slightly above the substrate (not touching the substrate), implying that energy was being given to the tip. This is explained by the existence of attractive forces which pulled the tip in near the lower extent of its travel, but were reduced on the return trip, resulting in a net addition of energy to the oscillating tip. When the tip was in weak contact, energy was dissipated consistent with the model of forming and breaking capillaries with each transit. When in full contact, the energy dissipation was near zero which is expected when the interaction is dominated by the tip-sample repulsion, a conservative force48. For the non-annealed samples, the energy addition in the attractive regime should have been approximately 3 times higher than the annealed samples due to the 3 times higher phase increase in the attractive region. When water was present, there was a large variation in the range and strength of the forces between the tip and WS2 and the tip and SiO2. However, on annealed samples the variation in APD curves, and thus the variation between successive trials’ FD curves and dissipation coefficient was reduced. This was consistent with our observation that the variation in step height was reduced by an order of magnitude in the annealed samples.
The variation between the measured height of WS2 on SiO2 and bare SiO2 in an AFM image can be explained by the variation in their hydrophilicities (Fig. 5). While SiO2 is hydrophilic, with contact angle (CA) of 10–50° depending on sample preparation with a predominantly polar component, TMD surfaces have been shown to be entirely dispersive, not polar, and weakly hydrophilic (CA 70–90°)49. Aging in air over a week increases the CA on CVD-grown WS2 from 70° to 83° due to carbon contamination50. It is known that water layers form on surfaces in low to high RH environments, with thicker layers forming in higher RH and on more hydrophilic surfaces. These water layers have been directly observed and quantified using force inversion from APD curves51,52. Capillary necks in AFM are a well-known phenomenon53,54. Capillaries have been directly observed in environmental SEM55. There was a clear difference in the nature of the tip-sample forces between WS2 and SiO2 when water was present, visible in the APD curves in Fig. 3, which accounts for the large variation in measured step height. When defining the set point, the perceived location of the sample surface is established, which results in incorrect measurement of step heights with varying tip-sample interactions. In amplitude feedback mode, the larger capillaries on the hydrophilic SiO2 result in stronger tip-sample interactions and greater amplitude reduction than on WS2. Thus, when water is present on the surface, the feedback loop approaches the tip closer on WS2 to reach the same set point, causing the WS2 to appear lower than the SiO2. To counteract this, the tip amplitude is increased and the set point lowered. This high tip amplitude results in lower relative amplitude reduction from the capillary forces, which we observed both in APD curves and in step measurements (Fig. 1a), in agreement with findings for other material systems45. The argument is similar for the phase feedback. Phase feedback only responds to phase dropping below 90°, and therefore, unlike amplitude mode, the tip approached through into the repulsive regime. With a greater width of the attractive region on WS2 in the PH curve, the TMD appears lower than the SiO2. This is remedied by increasing the amplitude and lowering the set point in order to reduce the relative magnitude of the capillary forces. This effect was observed when taking APD curves at varying amplitudes; the phase increases before contact (indicative of capillary forces) were reduced in height at higher amplitudes.
On annealed samples, the WS2 appeared inset for typical tip amplitudes and set points, which was corrected by using small amplitudes and larger set points, the opposite tool settings required when thick water layers were present. When a sample is annealed, there could still be water on the tip and water would reabsorb on the sample at a speed dependent on the surface’s hydrophilicity and the relative humidity41. Smaller capillaries can still form between the SiO2 and the tip on annealed samples, while having a harder time forming between the weakly hydrophilic WS2 and the tip. These strong tip-sample forces in the case of SiO2 cause the feedback loop not to approach as far on SiO2 to reach the same set point. This results in the SiO2 surface being measured higher than it is physically and the WS2 appearing inset. A low tip amplitude and high set point pushes the operation well into the repulsive regime, reducing the relative effect of capillaries and restoring the proper contrast between WS2 and SiO2. The step height variation was predominantly due to variations in hydrophilicity between samples. This can be corrected by using higher set points to operate further into the repulsive regime where capillary forces are not dominant. This effectively shifts on the PH curve to a region of lower variation between materials. Thus, different tool settings are required to prevent contrast inversion on non-annealed and annealed samples. When capillaries are present, high amplitudes and low set points reduce the effect of the capillaries on the tip, as seen in APH data as smaller angles in the attractive region at higher amplitudes. When capillaries are not present, low amplitudes and high set points ensure operation in the repulsive regime on both substrates, where repulsive forces dominate the tip-sample interactions.
The differences between annealed and non-annealed samples were more pronounced on WS2 than on SiO2, because WS2 is less hydrophilic than SiO2. Therefore, the WS2 does not re-wet as quickly in air after annealing. In addition, the bistability region was clearer on the annealed sample, shown on Fig. 3. The bistability results from a sudden transition from large net attractive force to a large net repulsive force, which we marked as an ad-hoc sample surface. The lack of a bistability on non-annealed samples was the result of total amplitude reduction within the attractive regime. The thick capillaries formed on non-annealed samples caused a net attractive force well into the region of tip-sample physical contact. On non-annealed WS2, the region of negative D was wider than on the non-annealed SiO2. This was a result of more rapid amplitude reduction in the attractive region on the WS2, (dA/dH > 1 causes D < 0), showing greater capillary effects on WS2 than SiO2 before annealing.
We have shown that varying tip-surface interactions are the cause of step height measurement errors on TMDs, and contrast inversion in topographic images can be corrected by appropriate set point and tip amplitude: namely high amplitudes when capillaries are present and low amplitudes with high set points on annealed samples. We have found that water layers are the primary cause, with other forces resulting in errors an order of magnitude smaller. Due to the wettability difference between SiO2 and WS2, when water is present in the system, it is not possible to measure the step height with suitable accuracy (+/− 0.05 nm) without fully characterizing the tip-sample forces and finding the true sample surface. High vacuum annealing32 or scanning in liquid would alter the step height by removing potential contaminants, which would only allow one to find the step from pristine SiO2 to pristine WS2. Topographic measurements of TMD samples that have undergone processing (i.e., CVD growth or layer transfer) should include and characterize contaminants through APD and FD curves, because they will contain the contaminant layers. When water is present on the sample surface, high amplitudes and low set points correct contrast inversion due to reduced capillary forces, causing the WS2 to appear higher than the SiO2. When water has been removed from the sample surface, low amplitudes and high set points produce images with correct contrast. This is due to low amplitudes and high set points operating well into the repulsive regime, where the relative effect of capillaries is reduced. Exfoliated samples appeared higher than CVD grown samples, up to 8 nm, due to contaminant layers and unattached edges of the crystal lifted off the substrate. After high vacuum annealing to remove possible contaminants, the step heights were reduced to a similar range as CVD grown samples, including exhibiting contrast inversion, and the same analysis described above applies for CVD grown samples. dAFM’s sensitivity to surface chemistry and long range van der Waals forces, though occluding the topographic measurement, can be a boon to understanding the surface’s state in different environments. As a future work, we propose high sensitivity force volume measurements (taking APD curves in an array and performing force inversion) to elucidate the step height and contaminant layers in processed, real world TMD monolayers.
WS2 monolayer samples were grown through chemical vapor deposition at 900 °C from solid sources (WO3 and S) on silicon substrates. They were confirmed to be monolayers through PL mapping. When not being measured, the WS2 samples were stored in Ar gas in an acrylic box with silica desiccant to prevent oxidation.
Samples were imaged in tapping mode using the Nanonics Imaging model MV-2000 AFM and in contact mode using the Nanonics Imaging model MV-1000. In order to convert the amplitude from volts to nanometers, the tip amplitude and piezo height was recorded in a separate tip approach and retract mapping on sapphire in contact mode. Sapphire was used because the hard surface would not deform during the tip’s contact with the surface. When in full contact the tip-amplitude response should be linear, assuming Hook’s law for the tip deflection. Then using a linear regression of the amplitude over the height, the slopes were found for the approach and retract curves, which agreed as expected. Taking the absolute value and the average of each slope, the conversion factor between volts and nanometers was found to be 0.008004 V/nm.
The conversion from piezo voltage to nm was obtained from imaging a standard sample, and was also assumed to be linear. The true tip-sample distance is obtained by shifting the height to be h = 0 at the sample surface, seen from the approach-retract curve, and adding the tip deflection, which is taken to be negative for downwards deflection. The tip’s spring constant was taken from the manufacturer’s estimate. Errors in spring constant only affect the magnitude of forces measured and do not affect the conclusions drawn from the features.
APD curves were taken using the Nanonics MV2000 and MV1000. In the data set presented in this paper, 10 trials were taken for each sample, interspersing tests on WS2 on SiO2 and bare SiO2, respectfully to prevent systematic errors due to tip degradation, before and after annealing. The APD experiments were performed with both low-Q silicon tips in a beam bounce setup and using a high-Q pulled fiber tip using piezo sensors to detect the tip amplitude and phase. Both experiments produced qualitatively similar results (only the high-Q results are shown in this work). Parameters were typically k = 3–9 N/m, Q = 1400, f = 33 kHz, and the in-air amplitude was A0 = 13 nm for the APD data shown. The tip was driven on resonance at constant frequency.
The datasets generated during and/or analyzed during the current study are available from the corresponding author on reasonable request.
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This work was supported in part by National Science Foundation award (ECCS-1104870) and the Defense University Research Instrumentation Program (FA9550-11-1-0272). This work was also partially carried out at the Micro Device Laboratory funded with support from Contract No. W15QKN-05-D-0011. We thank Shichen Fu for providing CVD-grown MoS2 monolayers.
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