Visualizing Uniaxial-strain Manipulation of Antiferromagnetic Domains in Fe1+YTe Using a Spin-polarized Scanning Tunneling Microscope

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Summary

Using uniaxial strain combined with spin-polarized scanning tunneling microscopy, we visualize and manipulate the antiferromagnetic domain structure of Fe1+yTe, the parent compound of iron-based superconductors.

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Kavai, M., Giannakis, I., Leshen, J., Friedman, J., Zajdel, P., Aynajian, P. Visualizing Uniaxial-strain Manipulation of Antiferromagnetic Domains in Fe1+YTe Using a Spin-polarized Scanning Tunneling Microscope. J. Vis. Exp. (145), e59203, doi:10.3791/59203 (2019).

Abstract

The quest to understand correlated electronic systems has pushed the frontiers of experimental measurements toward the development of new experimental techniques and methodologies. Here we use a novel home-built uniaxial-strain device integrated into our variable temperature scanning tunneling microscope that enables us to controllably manipulate in-plane uniaxial strain in samples and probe their electronic response at the atomic scale. Using scanning tunneling microscopy (STM) with spin-polarization techniques, we visualize antiferromagnetic (AFM) domains and their atomic structure in Fe1+yTe samples, the parent compound of iron-based superconductors, and demonstrate how these domains respond to applied uniaxial strain. We observe the bidirectional AFM domains in the unstrained sample, with an average domain size of ~50-150 nm, to transition into a single unidirectional domain under applied uniaxial strain. The findings presented here open a new direction to utilize a valuable tuning parameter in STM, as well as other spectroscopic techniques, both for tuning the electronic properties as for inducing symmetry breaking in quantum material systems.

Introduction

High-temperature superconductivity in cuprates and iron-based superconductors is an intriguing state of quantum matter1,2. A major challenge in understanding superconductivity is the locally intertwined nature of various broken symmetry states, such as electronic nematic and smectic phases (that break rotational and translational symmetries of the electronic states), with superconductivity3,4,5,6,7. Manipulation and deliberate tuning of these broken symmetry states is a key objective toward understanding and controlling superconductivity.

Controlled strain, both uniaxial and biaxial, is a well-established technique to tune the collective electronic states in condensed matter systems8,9,10,11,12,13,14,15,16,17,18,19,20,21,22. This clean tuning, without the introduction of disorder through chemical doping, is commonly used in various kinds of experiments to tune bulk electronic properties23,24,25,26. For example, uniaxial pressure has proved to have an immense effect on superconductivity in Sr2RuO413 and cuprates27 and on the structural, magnetic, and nematic phase transitions of iron-based superconductors10,14,28,29 and was recently demonstrated in tuning the topological states of SmB624. However, the use of strain in surface-sensitive techniques, such as STM and angle-resolved photoemission spectroscopy (ARPES), has been limited to in situ-grown thin films on mismatched substrates26,30. The major challenge with applying strain to single crystals in surface-sensitive experiments is the need to cleave the strained samples in ultrahigh vacuum (UHV). In the last few years, an alternative direction has been to epoxy a thin sample on piezo stacks9,10,18,31 or on plates with different coefficients of thermal expansion19,32. Yet in both cases, the magnitude of the applied strain is quite limited.

Here we demonstrate the use of a novel mechanical uniaxial-strain device that allows researchers to strain a sample (compressive strain) without constraints and simultaneously visualize its surface structure using STM (see Figure 1). As an example, we use single crystals of Fe1+yTe, where y = 0.10, the parent compound of the iron chalcogenide superconductors (y is the excess iron concentration). Below TN = ~60 K, Fe1+yTe transitions from a high-temperature paramagnetic state into a low-temperature antiferromagnetic state with a bicollinear stripe magnetic order26,33,34 (see Figure 3A,B). The magnetic transition is further accompanied by a structural transition from tetragonal to monoclinic26,35. The in-plane AFM order forms detwinned domains with the spin structure pointing along the long b-direction of the orthorhombic structure34. By visualizing the AFM order with spin-polarized STM, we probe the bidirectional domain structure in unstrained Fe1+yTe samples and observe their transition into a single large domain under applied strain (see the schematic in Figure 3C-E). These experiments show the successful surface tuning of the single crystals using the uniaxial-strain device presented here, the cleaving of the sample, and the simultaneous imaging of its surface structure with the scanning tunneling microscope. Figure 1 shows the schematic drawings and pictures of the mechanical strain device.

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Protocol

NOTE: The U-shaped body is made of 416-grade stainless steel, which is stiff and has a low coefficient of thermal expansion (CTE), ~9.9 μm/(m∙°C), as compared to ~17.3 μm/(m∙°C) for 304-grade stainless steel.

1. Mechanical uniaxial-strain device

  1. Clean the U-shaped device, the micrometer screws (1–72 corresponding to 72 rotations per inch), the Belleville spring disks, and the base plate by sonicating them separately in acetone first and then in isopropanol, for 20 min each, in an ultrasonic bath sonicator. This removes any impurities/particles. This process should be carried out in the hood.
  2. Bake them in an oven for 15–20 min to get rid of any water residue and to degas.
  3. Using a sharp razor blade, while observing under an optical microscope, cut the Fe1+YTe sample to size, namely 1 mm x 2 mm x 0.1 mm.
  4. Assemble the parts together as shown in Figure 1C, first panel. The opening inside the U is 1 mm and can be tuned smaller or large by a pair of micrometer screws located on the sides of the device.

2. Application of the strain

  1. In two separate dishes, mix silver epoxy (H20E) and nonconductive epoxy (H74F) according to the instructions on the epoxy data sheet.
  2. On the U-shaped device, apply a thin layer of silver epoxy (H20E) to create electrical contact, and mount the sample (of a size of 1 mm x 2 mm x ~0.1 mm) with its long axis oriented along the b-axis of the Fe1+yTe sample, on top of the device, across the 1 mm gap, as shown in Figure 1C. In a convection oven, bake the device for 15 min at 120 °C.
  3. Cover the two sides of the sample with nonconductive epoxy so that the sample is firmly supported on the device. Bake for 20 min at 100 °C.
    1. Using an optical microscope, examine the position of the sample from all angles to check for a parallel alignment of the sides of the sample with the gap.
    2. Optionally, place samples within the gap and enforced by H20E and H74F epoxy (Figure 1C).
  4. Under an optical microscope, apply compressive strain by rotating the micrometer screw while observing the surface of the sample.
    NOTE: Here we applied a 50° strain, but this can be modified depending on the amount of strain to be applied to the sample. The pressure is transferred to the sample by a series of Belleville spring disks. There should be no cracks or bending of the sample after the pressure is applied.
  5. Screw the device onto the base plate as shown in Figure 1B.
    1. Apply a thin layer of silver epoxy (H20E) from the base plate onto the U-shaped device to create electrical contact between the sample and the plate. Bake for 15 min at 120 °C. Measure the electrical contact using a multimeter.
    2. Using a thin layer of H74F nonconducting epoxy, glue an aluminum post (the same size as the sample) onto the strained sample, perpendicular to the a-b cleaving plane. Bake the assembled device for 20 min until the epoxy is cured.

3. Transfer of the device to the scanning tunneling microscope head

  1. Transfer the staining device with the sample and the post through the loading dock of the variable-temperature, ultrahigh vacuum scanning tunneling microscope, to the analysis chamber (see Figure 2A).
  2. Using an arm manipulator, knock off the aluminum post in ultrahigh vacuum at room temperature, to expose a freshly cleaved surface.
  3. Immediately transfer the device (with the strained sample) in situ with another set of manipulators to the scanning tunneling microscope chamber and to the microscope head (see Figure 2B), which has been cooled down to 9 K. Carry out all experiments at 9 K.
  4. Allow the sample to cool down overnight before carrying out the next steps.

4. Carrying out the STM experiments

  1. Prepare the Pt-Ir tips prior to each experiment by field emission on a Cu (111) surface that has been treated with several rounds of sputtering and annealing.
  2. Using the voltage applied to the piezoelectric materials in the microscope by an external controller, move the sample stage to align with the tip, then follow by approaching the sample.
  3. Once the tip is a few Å away from the sample and the tunneling current is registered on the oscilloscope, take topographs at different setpoint biases and setpoint currents.
    NOTE: The scanning tunneling microscope is controlled by manufacturer-provided controller and software. For the operation of the microscope, please refer to the user manual/tutorials (http://www.rhk-tech.com/support/tutorials/).

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Representative Results

STM topographs were measured in constant current mode with a setpoint bias of -12 meV applied to the sample and a setpoint current of -1.5 nA collected on the tip. Pt-Ir tips were used in all experiments. To achieve spin-polarized STM, the scanning tunneling microscope tip has to be coated with magnetic atoms, which can be quite challenging. In this case of studying Fe1+yTe, the sample itself provides a simple means of achieving this. The excess irons (y in Fe1+yTe) are weakly bound on the cleaved surface. Scanning the tip at a low bias and with a high enough current exceeding a few nanoamperes brings the tip in close proximity to these Fe atoms and a few of those atoms can be picked up by the tip36. The other method that yields a spin-polarized tip is by the rapid decrease of the sample-tip separation until contact is made (on the location of excess iron concentration) as measured by a saturation current. During the process, the excess irons bond onto the tip. The successful preparation of a spin-polarized tip is revealed by the magnetic contrast in the topography, whose periodicity is twice that of the lattice constant of top tellurium atoms. This additional modulation is the antiferromagnetic order in the sample, as discussed further below.

Figure 4A shows a 10 nm atomic-resolution topographical image on an unstrained Fe1+yTe single crystal with a nonmagnetic scanning tunneling microscope tip. The atomic structure seen corresponds to the Te atoms, which are exposed after cleaving the sample (see Figure 3A). The Fourier transform (FT) of the topography shows four sharp peaks at the corners of the image along the a- and b-directions, labeled qTea and qTeb, that correspond to the atomic Bragg peaks. The central broad peak in the FT corresponds to long-wavelength inhomogeneity, which is not relevant for the current study. Figure 4C shows another topograph of the same size as in Figure 4A, obtained with a magnetic tip. Unidirectional stripes with a periodicity of twice that of the lattice along the a-axis are observed. The FT of the topograph seen in Figure 4D shows, in addition to the Bragg peaks, a new pair of satellite peaks at QAFM1, corresponding to half the Bragg peak momenta and, therefore, twice the real space wavelength. The new structure corresponds to the AFM stripe order of the Fe atoms just below the surface.

On this unstrained sample, it is not difficult to observe twin domain boundaries where the crystal structure with the long b-axis and the accompanying AFM stripe order rotate 90°. Figure 4E shows a 25 nm spin-polarized topograph of an AFM twin domain boundary. The FT of the image now shows two pairs of AFM order (highlighted by green and yellow circles). Each magnetic domain contributes to only one pair of the QAFM peaks in the FT. To visualize this clearly, we Fourier-filtered each pair of AFM peaks and inversed FT back to real space. The results are shown in Figure 4G,H highlighting the two unidirectional stripe domains.

Thus, we studied the domain structure and boundaries on the surface on a large scale. Figure 5A, Figure 6A, and Figure 7A display large-scale topographs on three different unstrained samples spanning a total region of slightly over 0.75 µm x 0.75 µm. Several smaller zoomed-in topographs are also shown to highlight the stripe structure. The topographs are taken with a high spatial resolution (1024 x 1024 pixels per 0.25 µm2) to allow the Fourier filtering and inverse Fourier transform analysis on the large scale. The corresponding domain structures and boundaries are displayed in Figure 5B, Figure 6C, and Figure 7H. Overall, several alternating stripe domains are observed covering the overall equal areas, as expected for these unstrained samples. It is important to note that on this large scale the surface is overall atomically flat, yet a few different structural irregularities, such as line defects (Figure 5A) and atomic steps (Figure 7A), can be observed. The stripe domains are not affected by these irregularities.

From here, we moved on to the strained sample. Figure 8 shows a large-scale topograph, spanning a total region of ~1.75 µm x 0.75 µm, which is more than twice the total area spanned in the unstrained samples shown in Figure 5, Figure 6, and Figure 7. In stark contrast, the FT for each topograph shows only one pair of AFM peaks indicating only a single domain on this strained sample. This can further be visualized by the Fourier-filtered iFT analysis confirming the single stripe domain over the entire area. Once again, the unidirectional stripe order is not to be affected by the different surface irregularities in this strained sample.

Figure 1
Figure 1: Strain device. (A) Schematic of the strain device. The U-shaped device has two micrometer screws for the (1) compression and (2) expansion of the device's gap area. The sample can be confined inside the gap as shown in figure panels A and C or on top of the gap as shown in figure panels A and B. A combination of H20E and H74F epoxies are applied to the sample and cured at 100 °C. Once the epoxy on the sample is cured, a post of about the same surface area as that of the sample is epoxied onto the sample's surface using H74F. (B) The actual setup of the strain device, with a top view, front view, and a zoom-in of the sample. The device is screwed to a sample holder that slides into the microscope head. A contact is created by using conductive epoxy from the device to the sample plate. The transfer of pressure is enabled using a screw and a series of Belleville spring disks. The last panel of B shows the strain device set up, ready to be moved into the UHV analysis chamber. (C) An alternative method is to have a sample inside the gap of the strain device. In the two middle panels of C, a second unstrained sample is epoxied on the device for reference. Please click here to view a larger version of this figure.

Figure 2
Figure 2: Scanning tunneling microscope setup. (A) The scanning tunneling microscope setup. The microscope is placed in an acoustic chamber, which is shielded from radio-frequency (RF) noise. (B) The microscope head with a bare sample holder. The Pt/Ir tip is visible. The sample stage can be moved by a set of piezo actuators so that the sample is right above the tip. (C) The microscope head is placed inside two radiation shields. Please click here to view a larger version of this figure.

Figure 3
Figure 3: Fe1+yTe crystal structure. (A) The crystal structure of FeTe with the top layer showing the tellurium atoms. The red dotted lines outline the three unit cells. (B) A real-space schematic illustration of the atomic unit cell (red solid line) and magnetic structure (black solid line) of FeTe. The magnetic wavevector λafm is twice the atomic distance between Te-Te atoms. The arrows on the Fe atoms indicate the spin orientations. (C) Schematic diagram illustrating the AFM twin domains that form when cooling, through the structural transition from tetragonal to monoclinic at ~60 to 70 K, with an equal population of the two domains. (D) The response of the detwinning process, when an appreciable amount of strain is applied along the b-axis (black arrows) with one domain enhanced (red) and the other domain diminished (blue). (E) A complete detwinned domain, which leaves only one single domain. (F-H) The FT of the real space in panels C-E. The QAFM1 peaks correspond to the red real-space domains, and the QAFM2 peaks correspond to the blue domains. The lattice Bragg peaks are denoted as black dots at the corners of the image. Please click here to view a larger version of this figure.

Figure 4
Figure 4: Unidirectional modulation from unstrained Fe1+yTe. (A) A 10 nm x 10 nm topograph of the atomic lattice structure of Fe1+yTe with no magnetic contrast. (B) The FT of panel A, showing the Bragg peaks at the corners of the images (black circles). (C) A 10 nm x 10 nm topograph of the magnetic structure of Fe1+yTe, measured using a spin-polarized tip. The unidirectional stripes across the a-axis correspond to peaks appearing at QAFM1 = qTea/2 in the FT, as shown in panel D. (E) A 25 nm x 25 nm topographical image across a twin domain boundary. (F) FT of panel E, showing the two sets of peaks QAFM1 and QAFM2. (G) Inverse Fourier transform (iFT) of the QAFM1 peaks from panel F. The red color corresponds to the high intensity of the QAFM1 peaks. (H) iFT of the QAFM2 peaks from panel F. The domain boundary is clearly distinct from the images shown in panels G and H. The inverse Fourier filtering method has been used in subsequent figures to identify the different domains. Please click here to view a larger version of this figure.

Figure 5
Figure 5: Imaging twin domains in unstrained Fe1+yTe. (A) A 0.75 µm x 0.25 µm topographical image showing twin boundaries. The data was acquired in three adjacent topographical images, each 0.25 µm x 0.25 µm. (B) Using iFT, the domain boundaries are distinctly evident. (C-E) Zoom-ins of the images marked with an (X) and a yellow-colored dotted box are shown with highlighted, dotted, colored boxes around the boundaries. Please click here to view a larger version of this figure.

Figure 6
Figure 6: Imaging multiple domains from unstrained Fe1+yTe. (A) A 0.10 µm x 0.10 µm topographical image of an unstrained Fe1+yTe. (B) The FT of panel A, which shows peaks in both directions, namely QAFM1 and QAFM2. (C) The iFT image of panel A, indicating the different domains. (D and E) Zoom-ins of the highlighted yellow- and orange-dotted boxes in panel A. Please click here to view a larger version of this figure.

Figure 7
Figure 7: Imaging twin domains from unstrained Fe1+yTe. (A) Topographical images spanning an area of 0.75 µm x 0.5 µm. (B-D) Line cuts of the topograph taken across the black, purple, and green arrows in panel A. (E-G) Zoom-in of the areas highlighted in the green, brown, and yellow (X) marks in panel A. (H) iFT of panel A, showing the twin domains. The white-dotted lines are the step edges/boundaries. The domains are unaffected by these structural features. Please click here to view a larger version of this figure.

Figure 8
Figure 8: Imaging detwinned domains in strained Fe1+yTe. (A) A large 1.750 µm x 0.50 µm topography taken on a strained Fe1+yTe sample. (B and C) The FT of the two largest (0.50 µm x 0.50 µm) single topographs acquiring on one pair of AFM peaks in one direction. (D) The Fourier-filtering and iFT process is applied to the images in panel A, which shows only a single domain as expected. The dotted line in panel D is a step which does not affect the unidirectional domain. (E) A zoom-in of the highlighted region in the yellow (X) showing unidirectional stripes. (F) A zoom-in of panel E, also showing clearly the unidirectional stripes of the detwinned sample. (G) The FT of panel E. The AFM peaks appear only in one direction, which agrees with the real-space structure in panel E. Please click here to view a larger version of this figure.

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Discussion

All operations required to move the samples into and inside the STM are carried out using sets of arm manipulators. The STM is maintained at low temperatures by liquid nitrogen and liquid helium, and the sample cools down for at least 12 h before being approached. This allows the sample and microscope temperature to reach thermal equilibrium. To isolate electric and acoustic noise, the STM is placed in an acoustic and radio frequency shielded room. The microscope head is further suspended from springs for optimized instrumental stability. The sample stage can be translated by several millimeters that enable access to different parts of the 1 mm strained samples.

Since uniaxial pressure is the tuning parameter in the experiment described here, it is imperative that the thermal stress generated from cooling down is not transferred directly to the sample. For this, we employ a series of Belleville spring disks. Using the working load of the Belleville spring disks of 67 N, and the deflection at working load of 50 µm, we calculate the spring constant for each disk as k = 1.3 x 106 N/m, which yields a total spring constant of k = 1.625 x 105 N/m for 4 pairs of springs in series. This ensures the thermal stress on the sample through cooling from room temperature to 4 K to be less than 0.05% for an applied strain of 1% and therefore negligible. In the experiment, we rotate the micrometer screw by 50° which corresponds to Δx = 50 µm. The force applied on the sample through the springs can be calculated to be F = kΔx = 8 N. The pressure is therefore p =F/A = 8 N/(0.1 x 10-6 m2) = 0.08 GPa. For a Young's modulus of 70 Gpa for FeTe37, the applied uniaxial pressure corresponds to 0.1% strain.

A major challenge in integrating the strain devices with the STM is the application of strain without breaking or introducing cracks in the sample. Test experiments on several samples of Bi-2212, Sr3Ru2O7, and Fe1+yTe have shown that, depending on the sample thickness, the samples withstand strains of up to ~0.8%-1.0%, corresponding to ~1 GPa of applied pressure. No indications of cracks on the sample surface are observable below this value as seen visually by an optical microscope. Recent work following the same principles has successfully demonstrated the application of ±1% strain on Sr2RuO4 9.

The success of this technique lies in the careful execution of the correct alignment of the sample across the 1 mm gap and application of the strain on the sample without breaking or bending it. Another important consideration is the cleaving process, which allows the exposure of a clean flat surface. This is a random process and works best for materials that cleave easily. A last consideration is having a sharp tip that yields atomic resolution and can pick up some excess iron atoms to achieve magnetic contrast.

In conclusion, the experiments and analysis described here successfully demonstrate the incorporation of our strain device with STM, providing a new tuning parameter that can be invaluable in the study of competing orders in correlated electron systems. The advantage of the current device is the wide range of positive and negative strain that can be applied to the sample. This demonstration may impact other spectroscopic experiments such as ARPES.

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Disclosures

The authors have nothing to disclose.

Acknowledgments

P.A. acknowledges support from the U.S. National Science Foundation (NSF) CAREER under award No. DMR-1654482. Material synthesis was carried out with the support of the Polish National Science Centre grant No 2011/01/B/ST3/00425.

Materials

Name Company Catalog Number Comments
Belleville spring disks McMaster Carr
Fe(1.1)Te Single Crystal
H20E Epoxy Technology
H74F Epoxy Technology
Micrometer screws McMaster Carr
Stainless Steel sheets (416) McMaster Carr

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