Name: atomic layer deposition of vanadium dioxide and a temperature-dependent optical model
Uploaded: 2018-05-23T13:00:00.000+00:00
Duration: 11 min 10 s
Description: Watch this Scientific Journal Video about Atomic Layer Deposition of Vanadium Dioxide and a Temperature-dependent Optical Model at JoVE.com

This work was supported by core programs at the U.S. Naval Research Laboratory.

Caution: Consult all relevant material safety data sheets (MSDS) before use, and follow all appropriate safety practices and procedures. The atomic layer deposition growth of vanadium dioxide uses an ALD reactor. The precursors used for the ALD growth are tetrakis(ethylmethylamido)vanadium(IV) (TEMAV) and ozone (generated from ultra-high purity, UHP, 99.999% oxygen gas at 0.3 slm flow and 5 psi backing pressure). In addition, UHP (99.999%) nitrogen gas is used for purging the reactor chamber. For the subsequent vacuum anneal, UHP oxygen gas is used during annealing and UHP nitrogen for venting. TEMAV is flammable and should only be used with appropriate engineering controls. Compressed oxygen gas is a hazard and should only be used with appropriate engineering controls. Compressed nitrogen gas is a hazard and should only be used with appropriate engineering controls. All gases (TEMAV, oxygen, ozone and nitrogen) are connected to the ALD reactor using appropriate engineering safety controls. Stainless steel tubing connects the ozone generator to the ALD reactor, since it is cleaner and more reliable then plastic tubing. Separate UHP oxygen and nitrogen sources are connected to the vacuum annealing chamber using appropriate engineering safety controls before beginning the procedure. Acetone and 2-propanol are irritants and should only be used with appropriate personal protective equipment and safety procedures (e.g., gloves, fume hood, etc.)
1. Atomic Layer Deposition of Vanadium Dioxide on Sapphire Substrates
<ol>
	<li>Clean a c-Al2O3 (sapphire) substrate as follows: Solvent clean the substrate in acetone at 40 &#176;C in sonicator for 5 min, then transfer it directly (no rinse) to 2-propanol at 40 &#176;C and sonicate for 5 min. Rinse the substrate in running deionized water for 2 min, and dry it with nitrogen gas.</li>
	<li>Ensure that ALD reactor chamber is at 150 &#176;C and vent the ALD reactor with nitrogen gas.</li>
	<li>Load cleaned sapphire substrate into the reactor, close the reactor, and pump to &#60;17 Pa vacuum. Wait at least 300 s to ensure that the sample reaches 150 &#176;C.</li>
	<li>Prepare the ALD chamber by flowing 20 sccm UHP nitrogen into the chamber (the base pressure should not exceed 36 Pa), and then pulse ozone for 15 saturated cycles, where one cycle is a 0.05-s pulse followed by a 15 s purge.</li>
	<li>To grow vanadium dioxide, pulse TEMAV for 0.03 s followed by a 30 s purge, then pulse ozone for 0.075 s followed by a 30 s purge. Repeat this pulse and purge cycle until desired growth is reached. 
	NOTE: This process is nearly linear with a growth rate of 0.7-0.9 &#197; per cycle.</li>
	<li>Remove the sample from the ALD reactor by first venting the ALD reactor chamber with UHP nitrogen gas. Place the sample on a metal plate (heat sink) to cool it to room temperature. Close the ALD reactor and pump to &#60;17 Pa vacuum. The sample now contains an amorphous vanadium oxide film on sapphire substrate. 
	Caution: Remove the sample carefully, since the sample is heated to 150 &#176;C.</li>
</ol>
2. Annealing
NOTE: VO2 films grown by the ALD technique in step 1 produce amorphous VO2. To create oriented polycrystalline VO2 films, the samples are annealed in a custom ultra-high vacuum annealing chamber with a six-way cross. To keep the annealing chamber clean, a load lock is created to insert and remove samples. A 3&#34; diameter oxygen resistant heater is composed of a custom platinum wire heater. This heater provides radiative heating of an oxidized Inconel sled, to which the samples are mounted. The sled has high emissivity for good heat transfer from the heater to the samples.
<ol>
	<li>Ensure that the sled is in load lock, then vent the load lock with UHP nitrogen gas, and open the load lock. Place the sample on the sled in load lock and close load lock chamber.</li>
	<li>Pump the load lock to ~0.1 Pa using roughing pump. Next, switch to turbo pump and pump load lock to &#60;10-4 Pa. Open the gate valve and transfer the sled to the annealing chamber, and pump the annealing chamber to &#60;10-5 Pa.</li>
	<li>Flow 1.5 sccm ultra-high purity (UHP, 99.999%) oxygen into the annealing chamber. 
	NOTE: Run oxygen through 5 sccm mass flow controller to ensure a low flow rate. The pressure must be between 1x10-4 and 7x10-4 Pa. This pressure must be achieved before the sample reaches 150 &#176;C.</li>
	<li>Heat the sled to 560 &#176;C (measure with pyrometer and thermocouple) using a heating ramp rate of ~20 &#176;C/min. Hold the sled at 560 &#176;C for 2 h (for 300 &#197; film). 
	NOTE: The annealing time is thickness dependent. Empirical data suggests annealing 1 h for samples &#60;250 &#197; thick, 2 h for samples &#62;250 &#197; but &#60;500 &#197; thick, and 3 h for samples &#62;500 &#197; thick.</li>
	<li>Quench the sample by turning off the heater and removing the sled from the heater assembly (toward load lock).</li>
	<li>Keep the sample in the oxygen environment until the sample temperature becomes less than 150 &#176;C (e.g., use pyrometer in load lock to measure sample temperature). 
	NOTE: Better samples are achieved by waiting until even lower temperatures. Once the sample is &#60;150 &#176;C, turn off the oxygen flow and close the gate valve.</li>
	<li>Vent with UHP nitrogen gas. Remove sample at &#60;50 &#176;C and place the sample on metal plate (heat sink) to cool to room temperature. Close load lock with the empty sled and pump to 0.1 Pa using roughing pump. Switch to turbo pump and pump load lock to &#60;10-4 Pa.</li>
</ol>
3. Characterization
<ol>
	<li>Examine the sample using Raman spectroscopy with a 532-nm laser excitation source.
	<ol>
		<li>Load the sample into a microscope and bring it into focus. Verify the sample focus of the camera image in the software. Set the scan Laser Power to 4 mW, Exposure Time to 0.125 s, Number of Scans to 10, and preview size to 40 &#181;m.</li>
		<li>Click Live Spectrum to observe Raman spectrum. Optimize focus, laser power, exposure time, and number of scans to maximize signal to noise ratio. Click Save spectrum to save the data. 
		Open Spectrum in OMNIC. Click the &#34;Find Pks&#34; button to identify peaks. Determine crystallinity, phase (VO2 vs. VO, V2O3, V2O5, etc.), and strain by comparing peaks to reference data for vanadium oxides12,13. 
		NOTE: Narrow peaks indicate high crystalline quality, while hardening of Raman phonon modes 193, 222, and 612 cm-1 and/or softening of the 389 cm-1 mode are indicators of tensile strain in the VO2 crystal.</li>
	</ol>
	</li>
	<li>Determine orientation, crystallinity, and phase by X-ray diffraction (XRD). 
	NOTE: The appearance of peaks in the XRD spectra indicates the nature of the crystalline structure, specifically the crystal structure and orientation. Determine the orientation of VO2 by matching the 2&#920; angle of the XRD data peak to the Inorganic Crystal Structure Database (ICSD) cards for different planes of VO2. Determine the phase by matching data peaks to cards of different vanadium oxide phases. Manual comparison of experimental peaks to the standard database was performed in this work. A single VO2 peak at 39.9 degrees verifies the VO2 crystal quality and demonstrates the monoclinic (020) orientation.</li>
	<li>Determine stoichiometry and impurity levels by X-ray photoelectron spectroscopy (XPS)
	<ol>
		<li>Load the sample onto the sample holder. Open software and click vent load lock. Insert sample holder into load lock, and click pump down. Wait until pressure &#60;4x10-5 Pa. Click the transfer button to move the sample holder into the chamber. Verify the chamber pressure is &#60;7x10-6 Pa.</li>
		<li>Input measurement parameters into the experiment tree. Turn on X-ray gun with 400 &#181;m spot size and then turn on flood gun. Add a point for survey measurement, and then add points for high resolution scans of precursor elements (C and N) as well as the film elements (V and O). For each measurement, add pass energy (200 eV for survey and 20 eV for high-resolution scans) and number of scans (2 or more for survey and 15 for high resolution).</li>
		<li>Place crosshairs for point measurement at the desired location on the sample. Click and highlight the experiment tree title and then click &#34;Experimental Run&#34; on the menu bar to execute all measurement scans.</li>
		<li>Execute the survey ID procedure to identify and analyze the elements in the film. Select Manual Peak Add followed by Peak Fit buttons to analyze bonding in high-resolution data scans. Determine stoichiometry by taking the ratio of the integrated peak intensities according to the XPS Handbook14.</li>
		<li>When finished, shutdown the guns, then click the transfer button to move the sample holder into the load lock. Once the sample is in the load lock, click vent load lock and unload the sample. 
		NOTE: This identifies the presence of all elements in survey, thereby identifying impurities. XPS peaks at specific binding energies show the valences of vanadium oxides, as shown in Figure 1. For example, these results show two representative XPS measurements obtained by depth profiling with a cluster ion gun etching the as-deposited sample. The XPS measurement of the surface shows a peak at ~518 eV demonstrating the presence of V2O5, while the XPS measurement of the etched sample (in the film&#39;s bulk) shows a peak at ~516 eV demonstrating the presence of VO2. The full-width-at-half-max indicates the bonding uniformity of the vanadium in the films (in other words, the phase purity). In addition, the analysis of the other energy peaks enables identification of contaminates (&#62;1 %).</li>
	</ol>
	</li>
	<li>Determine morphology by using atomic force microscopy (AFM)
	<ol>
		<li>Turn on the computer and AFM electronics. Start the Nanoscope program and select Tapping Mode, then select load Experiment. Initialize Stage.</li>
		<li>Follow the experimental order on the left side of the screen and click Setup Menu. Use focus controls to focus optics on the cantilever. Align the laser on the probe by clicking Optimize Laser Position. Click Autoalign detector button, and then click the Autotune cantilever.</li>
		<li>Load sample and turn on vacuum.</li>
		<li>Click Navigate button and use the trackball to place the sample under the head. Click Tip Reflection and lower the head to the sample surface using Trackball, while holding the focus button down until the tip is in focus. Click the Sample button and close the AFM hood.</li>
		<li>Click the Check Parameter Menu. Ensure the scan size is &#60;1 &#181;m and set the samples/line to 512. Click the Engage Menu button. Wait 20 s.</li>
		<li>Set the Scan size for 3 &#181;m and leave the scan speed at 3.92 Hz. Optimize the image, if necessary, by changing parameters: drive amplitude, amplitude set point, integral and proportional gains.</li>
		<li>Capture the desired image by clicking the Frame Down button followed by the Capture Button. Following the scan, click the Withdraw button.</li>
		<li>Double click on the desired image to open it in analysis software. To determine morphology, click the Flatten button and then click execute. Extract statistical parameters by clicking Roughness to calculate surface roughness and click Particle Analysis to calculate the depth histogram and mean grain size.</li>
		<li>Click the Navigate Menu and click the Sample Load Position. Turn off the vacuum and unload the sample. 
		NOTE: For consistency from sample to sample, keep the same AFM scan parameters.</li>
	</ol>
	</li>
	<li>Determine optical transmittance and reflectance.
	<ol>
		<li>Use a tunable optical source and measure optical transmittance and reflectance at (or near) normal incidence in the near-infrared region. Calibrate the system without sample for 100% transmittance and with a gold mirror for near 100% reflectance.</li>
		<li>Load the VO2 sample onto the temperature controlled stage. Stabilize the sample at the desired temperature. Measure transmittance and reflectance over the desired spectral range, for example, throughout the near infrared region. 
		NOTE: For optimal results, the temperature should be varied at least 20 &#176;C above and below the transition temperature of VO2 (usually, 68 &#176;C).</li>
	</ol>
	</li>
</ol>
4. Modelling Optical Constants (Permittivity and Refractive Index)
<ol>
	<li>Model the complex dielectric permittivity, &#949;, as a function of photon energy, E, using the following equation (where &#949;&#8734; is the high frequency permittivity followed by the sum of n oscillators where An is the oscillator amplitude, En the oscillator energy, and Bn the oscillator damping): 
	<img alt="Equation 1" src="/files/ftp_upload/57103/57103eq1.jpg" /> 
	NOTE: Custom Matlab programs analyzed and modelled the data.</li>
	<li>Enter known parameters for sapphire substrate in step 4.1, and use these to calculate the dielectric permittivity as a function of optical wavelength. Then calculate the refractive index (n = &#8730;&#949;), and using the refractive index, calculate the reflectance and transmittance of the substrate.</li>
	<li>Compare the results of step 4.2 with the measured data, and then employ an optimization technique (such as Nelder Mead15) to update the input parameters of step 4.2 in order to reduce the error between the measured and calculated results, thereby optimizing the parameters for the sapphire substrate.</li>
	<li>Estimate parameters for VO2 in the equation in step 4.1, and use these to calculate the dielectric permittivity. Then calculate the refractive index (n = &#8730;&#949;) and use that, along with the VO2 thickness, substrate thickness, refractive index (from step 4.3), optical wavelength, optical polarization, and angle of incidence as inputs to the transfer16 to obtain the reflectance and transmittance of the VO2 coated substrate. Employ an optimization technique (such as Nelder Mead15) to update the VO2 input parameters and reduce the error between the measured and calculated results, thereby optimizing the parameters for the VO2.</li>
	<li>Perform steps 4.2 to 4.4 at several temperatures spanning the insulating and metallic states of vanadium dioxide (temperatures from 30 to 90 &#176;C). Model the temperature dependence of the refractive index of VO2 as follows: 
	<img alt="Equation 3" src="/files/ftp_upload/57103/57103eq3.jpg" /> 
	where &#949;VO2(T) is the refractive index of VO2 as a function of temperature, &#949;ins and &#949;metal are the dielectric permittivity of the insulating and metallic phases, and f(T) is a temperature-dependent function governing the distribution of insulating and metallic optical properties. Use a Fermi-Dirac-like function for f(T) to govern the transition between insulating and metallic state, similar to effective-medium approximations17,18,19, given by: 
	<img alt="Equation 4" src="/files/ftp_upload/57103/57103eq4.jpg" /> 
	where Tt is the transition temperature and W controls the width of the transition.</li>
	<li>Employ an optimization technique to update the parameters (W and Tt) in the equation for f(T) to reduce the error between the measured and calculated results, thereby optimizing the transition temperature and width. This results in a temperature and wavelength dependent model for the dielectric permittivity and refractive index of VO2.</li>
</ol>

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The authors have nothing to disclose.

The growth methods described here provide reproducible results with regards to uniformity, chemistry, structure, and morphology. The vanadium precursor is critical to producing the correct stoichiometry of as-deposited ALD films. This particular precursor promotes the +4 vanadium valence state, unlike many of the others listed in the literature that promote the more common +5 valence state. Additionally, this particular precursor has a fairly low vapor pressure and requires heating to provide a sufficient dose to saturate under the conditions given. Since this precursor starts to degrade around 175 &#176;C, this sets an upper temperature limit to both heating of the precursor and ALD growth. Another critical aspect to achieving correct stoichiometry is the ozone concentration (~125 mg/L here) during dosing. Often the concentration of ozone produced by a generator under particular conditions degrades or drifts over time. If this happens, the ozone pulse and purge durations will have to be adjusted to maintain stoichiometry, morphology, and wafer uniformity. What is described here is how to grow ALD VO2 on c-plane sapphire substrates, which includes in-situ ozone pre-treatment. The steps prior to growth for cleaning and nucleation are dependent on the substrate; however, the process described here works for most substrates (inert, oxides, metals, etc.) To determine the best termination cleaning and preparation for VO2 growth, one should consider reactivity between species termination and the vanadium precursor while minimizing any native oxide on the substrate. Finally, this process has been demonstrated on high aspect ratio substrates (up to ~100) but for extreme cases, one should consider an exposure or static ALD method to enhance conformality further.
The ability to achieve high quality, crystalline ALD VO2 films is quite dependent on the post-deposition annealing parameters. The most critical aspect is the pressure, specifically the partial pressure of oxygen. High oxygen pressures lead to faceting and grain growth, eventually causing nanowire formation, as well as results in the V2O5 phase. If the oxygen pressure is too low, oxygen is annealed out of the films resulting in V2O3 phase. Thus, to maintain the correct phase and minimize film roughness, the oxygen pressure should be maintained in the range of 1x10-4 to 7x10-4 Pa. Similarly, the temperature is critical to both being able to crystallize the film, maintain stoichiometry, and minimize roughening of the film. While the temperature of the VO2 film is difficult to measure, empirical findings suggest that crystallization requires stage temperatures greater than 500 &#176;C. At higher temperatures, it is harder to maintain the correct stoichiometry and phase and produce pinhole free films. There is also a trade-off between temperature and anneal time, specifically higher temperatures can reduce the anneal time. Additionally, the anneal duration is directly tied to the thickness of the film. Thicker films require longer times to achieve maximum crystallization. Thus, the oxygen pressure, anneal temperature, and anneal time described in the methods above were optimized to produce high quality VO2 films that exhibit the largest change in optical properties at a nearly ideal transition temperature. Finally, the ramping and cooling rates during the oxygen anneal have an effect on roughness and morphology; the slower these are, the smoother the films.
ALD deposition and subsequent anneal of VO2 produces oriented polycrystalline films with large area uniformity. ALD offers conformally grown films on three-dimensional nanoscale morphologies of almost any substrate. This enables VO2 integration into novel applications, and is especially well suited for optical devices.
Following growth and optical measurements, a model is created which provides a good fit to the data for both the transmittance and reflectance of VO2 in its metallic and insulating phases in the near infrared spectral region (R2 = 0.96-0.99). The reflectance of the infrared insulating phase is the most challenging process in creating this model. Additional oscillator terms were added, but this increased model complexity, only marginally improve the fit in this region. It should be noted that in this model, the superposition of Lorentz oscillators is a common optical model and do not necessarily correspond to specific electronic transitions. Initially, the models included a Drude term, however, after mathematical optimization, the Drude term was essentially eliminated. For this reason, several minimization techniques were examined. However, these different techniques converged upon similar solutions that did not involve a Drude term. The absence of a Drude term in the ALD VO2 could be due to a number of factors, such as 1) doped-semiconductor-like resistivity, or 2) a plasma frequency shift to lower energies and/or large collision rate (damping term), in agreement with the metallic properties of these films.
In the insulating phase, T&#60;60 &#176;C, the permittivity and refractive index of the ALD VO2 agree well with the other fabrication methods (sputtered4,20,21 and pulsed-laser deposition22,23). In the metallic state, T&#62;70 &#176;C, these ALD films exhibit lower loss than the VO2 fabricated by other methods. It is important to note that while different fabrication methods produce somewhat different values for the permittivity and refractive index of VO2, all films show similar trends.
The model in this paper of the temperature and wavelength dependence of the optical permittivity and refractive index agrees well with the experimentally measured data. This model&#39;s ability to produce a good quality fit to the measured optical data demonstrates it can reliably predict the optical properties of VO2 as the phase changes from an insulator to a metal. Using these models, the optical properties of VO2 can be predictably tuned by temperature, thickness, and wavelength to design optical systems that achieve static and dynamic goals. These models enable the design and development of optical systems using VO2 in passive and active systems by modifying the film&#39;s thickness as well as temperature.

Vanadium dioxide undergoes a crystalline phase transition near 68 &#176;C. This produces a structural crystal change from monoclinic to tetragonal. The origin of this transition remains controversial1, however recent research is helping develop an understanding of the processes that produce this transition2,3,4 . Irrespective of the origin, the phase transition changes the optical properties of VO2 from an insulator (transmitting light) at room temperature to a more metallic material (reflecting and absorbing light) above the transition temperature2.
A variety of methods have been used to fabricate VO2 in the past (sputtering, physical vapor deposition, chemical vapor deposition, molecular beam epitaxy, solution, etc.)5. The properties of VO2 largely depend on the technology used to fabricate the films6, which has produced significant variability between different growth techniques and subsequent anneal and led to varying crystallinity and film properties. This work investigates the optical properties of atomic layer deposited (ALD) grown films, however, the approach is applicable to modeling all types of VO2 films.
Recently, groups are constructing optical devices by incorporating thin films of VO2 onto optical substrates. As a rapidly growing new deposition method, ALD can assist in fabricating these optical devices and has several advantages over alternative techniques, such as large-area uniformity, angstrom level thickness control, and conformal film coverage7,8,9. ALD is the preferred technique for applications requiring a self-limiting layer-by-layer deposition approach, fabrication on a wide variety of substrate materials (e.g., for heterogeneous integration), or conformal coating of 3D structures10. Finally, the conformal coating of 3D structures of ALD process is particularly useful in optical applications.
For the experiments in this paper, ultrathin, amorphous ALD films were grown on double-side-polished, c-plane sapphire substrates at low temperatures and annealed in an oxygen environment to produce high-quality crystalline films. Using the experimental measurements, a model is created for temperature and wavelength dependent optical changes in VO2 to enable its use as a tunable refractive index material11.

<table><tbody><tr><td>c-Al2O3</td><td></td><td></td><td></td></tr><tr><td>UHP Oxygen</td><td>Air Products</td><td></td><td></td></tr><tr><td>UHP Nitrogen</td><td>Air Products</td><td></td><td></td></tr><tr><td>Tetrakis (ethylmethylamido)vanadium(IV) (TEMAV)</td><td>Air Liquide</td><td></td><td></td></tr><tr><td>Acetone</td><td>Fischer Scientific</td><td>A18-4</td><td></td></tr><tr><td>2-propanol</td><td>Fischer Scientific</td><td>A416P-4</td><td></td></tr><tr><td>Savannah S200-G2</td><td>Veeco - CNT</td><td>Savannah S200-G2</td><td></td></tr><tr><td>ozone generator</td><td>Veeco - CNT</td><td>ozone generator</td><td></td></tr><tr><td>Platinum wire heater</td><td>HeatWave Labs</td><td>custom</td><td></td></tr></tbody></table>

atomic layer deposition of vanadium dioxide and a temperature-dependent optical model

Vanadium dioxide is a material that has a reversible metal-insulator phase change near 68 &#176;C. To grow VO2 on a wide variety of substrates, with wafer-scale uniformity and angstrom level control of thickness, the method of atomic-layer deposition was chosen. This ALD process enables high-quality, low-temperature (&#8804;150 &#176;C) growth of ultrathin films (100-1000 &#197;) of VO2. For this demonstration, the VO2 films were grown on sapphire substrates. This low temperature growth technique produces mostly amorphous VO2 films. A subsequent anneal in an ultra-high vacuum chamber with a pressure of 7x10-4 Pa of ultra-high purity (99.999%) oxygen produced oriented, polycrystalline VO2 films. The crystallinity, phase, and strain of the VO2 were determined by Raman spectroscopy and X-ray diffraction, while the stoichiometry and impurity levels were determined by X-ray photoelectron spectroscopy, and finally the morphology was determined by atomic force microscopy. These data demonstrate the high-quality of the films grown by this technique. A model was created to fit to the data for VO2 in its metallic and insulating phases in the near infrared spectral region. The permittivity and refractive index of the ALD VO2 agreed well with the other fabrication methods in its insulating phase, but showed a difference in its metallic state. Finally, the analysis of the films&#39; optical properties enabled the creation of a wavelength- and temperature-dependent model of the complex optical refractive index for developing VO2 as a tunable refractive index material.

To identify the quality of the ALD grown vanadium oxide, X-ray photoelectron spectroscopy (XPS) was performed on the as-deposited, primarily amorphous VO2 films (Figure 1) as well as annealed crystalline VO2 films (not shown). X-ray diffraction (XRD) was performed on the annealed VO2 films (Figure 2). In addition, to help quantify the vertical profile of the chemistry within the film, depth profiling was performed with a cluster ion source to minimize preferential etching of cation/anion species. Two representative traces are shown in Figure 1, one at the surface and one in the bulk. The depth profile and subsequent XPS measurements show that the top 1-nm of the as-deposited film is not VO2 due to excess environmental (adventitious) oxygen and carbon, but after a more controlled annealing procedure in low-pressure oxygen even the surface stabilizes to VO2. X-ray diffraction measurements were performed with a Cu K-alpha X-ray energy source and show, in Figure 2, a single VO2 peak at 39.9&#730;. The signature of this peak verifies the quality of the ALD-grown VO2 as well as that the (020) crystal orientation aligns with the sapphire substrate&#39;s peak.
To analyze the crystallinity, phase, and strain, Raman spectroscopy was performed using a 532-nm laser for excitation. Figure 3 shows a Raman spectrum of the VO2 film and shows narrow peaks which indicate high crystalline quality. In addition, the increased energy in the vanadium-vanadium low-frequency phonons (193 and 222 cm-1) and the 612 cm-1 mode, as well as the decreased energy of the 389 cm-1 mode, suggest tensile strain in these films12,13.
The morphology was observed by atomic force microscopy (AFM). Figure 4 shows crystal grain sizes on the order of 20-40 nm and a root-mean-square (RMS) roughness of 1.4 nm for as-deposited films (Figure 4A) and an RMS roughness of 2.6 nm for annealed films (Figure 4B).
Optical transmittance and reflectance data were obtained using a white light source with a scanning monochromator and a photodetector, which provided coverage in the visible and near infrared region. Figure 5 shows the temperature dependence of the film as it transitions from an insulator to a metal, demonstrating a transition temperature of 61 &#176;C. Analyzing the experimental data enables the modeling of the temperature and wavelength dependent permittivity of the VO2 as it transitions from insulator to metal. Figure 5 shows how the model accurately predicts the optical behavior when using the parameters in Table 1.
<img alt="Figure 1" class="xfigimg" src="/files/ftp_upload/57103/57103fig1.jpg" /> 
Figure 1: Representative XPS measurements of 35-nm thick VO2 on c-Al2O3. XPS shows that the bulk of the film is VO2 while the surface, which contains C and O contaminates, is shifted more towards V2O5. Stoichiometry suggests VO2. <a href="/files/ftp_upload/57103/57103fig1large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<img alt="Figure 2" class="xfigimg" src="/files/ftp_upload/57103/57103fig2v3.jpg" /> 
Figure 2: XRD measurements of 35-nm thick VO2 on c-Al2O3. This XRD measurement shows a single VO2 peak at 39.9&#730; that independently verifies the crystal quality and demonstrates the monoclinic (020) orientation is aligned with the underlying sapphire peak. <a href="/files/ftp_upload/57103/57103fig2v3large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<img alt="Figure 3" class="xfigimg" src="/files/ftp_upload/57103/57103fig3.jpg" /> 
Figure 3: Raman spectra of VO2 on c-Al2O3. This Raman spectrum has narrow peaks, indicating high crystalline quality, and shows a slight tensile strain. <a href="/files/ftp_upload/57103/57103fig3large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<img alt="Figure 4" class="xfigimg" src="/files/ftp_upload/57103/57103fig4.jpg" /> 
Figure 4: Morphology of VO2 on c-Al2O3. The AFM images show uniform, continuous films with grain sizes on the order of 20-40 nm and RMS roughnesses of (A) 1.4 nm for the as-grown film and (B) 2.6 nm for the annealed film. <a href="/files/ftp_upload/57103/57103fig4large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<img alt="Figure 5" class="xfigimg" src="/files/ftp_upload/57103/57103fig5.jpg" /> 
Figure 5: Near-infrared optical transmittance and reflectance of 35-nm thick VO2 on c-Al2O3. The temperature-dependent behavior of the optical transmittance and reflectance of vanadium dioxide film are show at 40, 60, 70, and 90 &#176;C. The open circles in the plot are the measured transmittance, reflectance, and calculated absorptance of the VO2 on sapphire structure at various temperatures, while the solid lines are the predicted values from the two-dimensional temperature- and wavelength-dependent model of VO2. <a href="/files/ftp_upload/57103/57103fig5large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<table border="1" fo:keep-together.within-page="1" fo:keep-with-next.within-page="always">
	<tbody>
		<tr>
			<td></td>
			<td>&#949;&#8734;</td>
			<td></td>
			<td>osc. 1</td>
			<td>osc. 2</td>
		</tr>
		<tr>
			<td>Insulator</td>
			<td colspan="4"></td>
		</tr>
		<tr>
			<td rowspan="3"></td>
			<td rowspan="3">3.4</td>
			<td>En</td>
			<td>3.8</td>
			<td>1.2</td>
		</tr>
		<tr>
			<td>An</td>
			<td>33</td>
			<td>2.1</td>
		</tr>
		<tr>
			<td>Bn</td>
			<td>1.4</td>
			<td>1.3</td>
		</tr>
		<tr>
			<td>Metal</td>
			<td colspan="4"></td>
		</tr>
		<tr>
			<td rowspan="3"></td>
			<td rowspan="3">4.5</td>
			<td>En</td>
			<td>3.2</td>
			<td>0.6</td>
		</tr>
		<tr>
			<td>An</td>
			<td>13</td>
			<td>5.3</td>
		</tr>
		<tr>
			<td>Bn</td>
			<td>1.1</td>
			<td>1</td>
		</tr>
	</tbody>
</table>
Table 1: Representative model parameters for VO2. These parameters are representative of those used in an oscillator model to estimate the permittivity of VO2 in its metallic and insulating phases.

Watch this Scientific Journal Video about Atomic Layer Deposition of Vanadium Dioxide and a Temperature-dependent Optical Model at JoVE.com

Atomic Layer Deposition of Vanadium Dioxide and a Temperature-dependent Optical Model

Thin films (100-1000 &#197;) of vanadium dioxide (VO2) were created by atomic-layer deposition (ALD) on sapphire substrates. Following this, the optical properties were characterized through the metal-insulator transition of VO2. From the measured optical properties, a model was created to describe the tunable refractive index of VO2.

Vanadium dioxide is a material that has a reversible metal-insulator phase change near 68 &#176;C. To grow VO2 on a wide variety of substrates, with ...

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11.8K Views.  Naval Research Laboratory. Thin films (100-1000 Å) of vanadium dioxide (VO2) were created by atomic-layer deposition (ALD) on sapphire substrates. Following this, the optical properties were characterized through the metal-insulator transition of VO2. From the measured optical properties, a model was created to describe the tunable refractive index of VO2.

Video: Atomic Layer Deposition of Vanadium Dioxide and a Temperature-dependent Optical Model

Chemical Vapor Deposition of an Organic Magnet, Vanadium Tetracyanoethylene

Recent progress in the field of organic materials has yielded devices such as organic light emitting diodes (OLEDs) which have advantages not found in traditional materials, including low cost and mechanical flexibility. In a similar vein, it would be advantageous to expand the use of organics into high frequency electronics and spin-based electronics. This work presents a synthetic process for the growth of thin films of the room temperature organic ferrimagnet, vanadium tetracyanoethylene (V[TCNE]x, x~2) by low temperature chemical vapor deposition (CVD). The thin film is grown at &#60;60 &#176;C, and can accommodate a wide variety of substrates including, but not limited to, silicon, glass, Teflon and flexible substrates. The conformal deposition is conducive to pre-patterned and three-dimensional structures as well. Additionally this technique can yield films with thicknesses ranging from 30 nm to several microns. Recent progress in optimization of film growth creates a film whose qualities, such as higher Curie temperature (600 K), improved magnetic homogeneity, and narrow ferromagnetic resonance line-width (1.5 G) show promise for a variety of applications in spintronics and microwave electronics.

We present the synthesis of the organic-based ferrimagnet vanadium tetracyanoethylene (V[TCNE]x, x~2) via low temperature chemical vapor deposition (CVD). This optimized recipe yields an increase in Curie temperature from 400 K to over 600 K and a dramatic improvement in magnetic resonance properties.

Recent progress in the field of organic materials has yielded devices such as organic light emitting diodes (OLEDs) which have advantages not found in ...

Chemistry

Formation of Thick Dense Yttrium Iron Garnet Films Using Aerosol Deposition

Aerosol deposition (AD) is a thick-film deposition process that can produce layers up to several hundred micrometers thick with densities greater than 95% of the bulk. The primary advantage of AD is that the deposition takes place entirely at ambient temperature; thereby enabling film growth in material systems with disparate melting temperatures. This report describes in detail the processing steps for preparing the powder and for performing AD using the custom-built system. Representative characterization results are presented from scanning electron microscopy, profilometry, and ferromagnetic resonance for films grown in this system. As a representative overview of the capabilities of the system, focus is given to a sample produced following the described protocol and system setup. Results indicate that this system can successfully deposit 11 &#181;m thick yttrium iron garnet films that are &#160;&#62; 90% of the bulk density during a single 5 min deposition run. A discussion of methods to afford better control of the aerosol and particle selection for improved thickness and roughness variations in the film is provided.

This report describes the use of a custom-built system to perform aerosol deposition of thick films of yttrium iron garnet onto sapphire substrates at RT. The deposited films are characterized using scanning electron microscopy, profilometry, and ferromagnetic resonance to give a representative overview of the capabilities of the technique.

Aerosol deposition (AD) is a thick-film deposition process that can produce layers up to several hundred micrometers thick with densities greater than 95% ...

Improved Heterojunction Quality in Cu2O-based Solar Cells Through the Optimization of Atmospheric Pressure Spatial Atomic Layer Deposited Zn1-xMgxO

Atmospheric pressure spatial atomic layer deposition (AP-SALD) was used to deposit n-type ZnO and Zn1-xMgxO thin films onto p-type thermally oxidized Cu2O substrates outside vacuum at low temperature. The performance of photovoltaic devices featuring atmospherically fabricated ZnO/Cu2O heterojunction was dependent on the conditions of AP-SALD film deposition, namely, the substrate temperature and deposition time, as well as on the Cu2O substrate exposure to oxidizing agents prior to and during the ZnO deposition. Superficial Cu2O to CuO oxidation was identified as a limiting factor to heterojunction quality due to recombination at the ZnO/Cu2O interface. Optimization of AP-SALD conditions as well as keeping Cu2O away from air and moisture in order to minimize Cu2O surface oxidation led to improved device performance. A three-fold increase in the open-circuit voltage (up to 0.65 V) and a two-fold increase in the short-circuit current density produced solar cells with a record 2.2% power conversion efficiency (PCE). This PCE is the highest reported for a Zn1-xMgxO/Cu2O heterojunction formed outside vacuum, which highlights atmospheric pressure spatial ALD as a promising technique for inexpensive and scalable fabrication of Cu2O-based photovoltaics.

Improved Heterojunction Quality in Cu2O-based Solar Cells Through the Optimization of Atmospheric Pressure Spatial Atomic Layer Deposited Zn1-xMgxO

Here we present a protocol for synthesizing Zn1-xMgxO/Cu2O heterojunctions in open-air at low temperature via atmospheric pressure spatial atomic layer deposition (AP-SALD) of Zn1-xMgxO on cuprous oxide. Such high quality conformal metal oxides can be grown on a variety of substrates including plastics by this cheap and scalable method.

Atmospheric pressure spatial atomic layer deposition (AP-SALD) was used to deposit n-type ZnO and Zn1-xMgxO thin films onto p-type thermally oxidized Cu2O ...

Synthesis and Characterization of High c-axis ZnO Thin Film by Plasma Enhanced Chemical Vapor Deposition System and its UV Photodetector Application

In this study, zinc oxide (ZnO) thin films with high c-axis (0002) preferential orientation have been successfully and effectively synthesized onto silicon (Si) substrates via different synthesized temperatures by using plasma enhanced chemical vapor deposition (PECVD) system. The effects of different synthesized temperatures on the crystal structure, surface morphologies and optical properties have been investigated. The X-ray diffraction (XRD) patterns indicated that the intensity of (0002) diffraction peak became stronger with increasing synthesized temperature until 400 oC. The diffraction intensity of (0002) peak gradually became weaker accompanying with appearance of (10-10) diffraction peak as the synthesized temperature up to excess of 400 oC. The RT photoluminescence (PL) spectra exhibited a strong near-band-edge (NBE) emission observed at around 375 nm and a negligible deep-level (DL) emission located at around 575 nm under high c-axis ZnO thin films. Field emission scanning electron microscopy (FE-SEM) images revealed the homogeneous surface and with small grain size distribution. The ZnO thin films have also been synthesized onto glass substrates under the same parameters for measuring the transmittance.
For the purpose of ultraviolet (UV) photodetector application, the interdigitated platinum (Pt) thin film (thickness ~100 nm) fabricated via conventional optical lithography process and radio frequency (RF) magnetron sputtering. In order to reach Ohmic contact, the device was annealed in argon circumstances at 450 oC by rapid thermal annealing (RTA) system for 10 min. After the systematic measurements, the current-voltage (I-V) curve of photo and dark current and time-dependent photocurrent response results exhibited a good responsivity and reliability, indicating that the high c-axis ZnO thin film is a suitable sensing layer for UV photodetector application.

We offered a method to directly synthesize high c-axis (0002) ZnO thin film by plasma enhanced chemical vapor deposition. The as-synthesized ZnO thin film combined with Pt interdigitated electrode was used as sensing layer for ultraviolet photodetector, showing a high performance through a combination of its good responsivity and reliability.

In this study, zinc oxide (ZnO) thin films with high c-axis (0002) preferential orientation have been successfully and effectively synthesized onto ...

Seedless Growth of Bismuth Nanowire Array via Vacuum Thermal Evaporation

Here a seedless and template-free technique is demonstrated to scalably grow bismuth nanowires, through thermal evaporation in high vacuum at RT. Conventionally reserved for the fabrication of metal thin films, thermal evaporation deposits bismuth into an array of vertical single crystalline nanowires over a flat thin film of vanadium held at RT, which is freshly deposited by magnetron sputtering or thermal evaporation. By controlling the temperature of the growth substrate the length and width of the nanowires can be tuned over a wide range. Responsible for this novel technique is a previously unknown nanowire growth mechanism that roots in the mild porosity of the vanadium thin film. Infiltrated into the vanadium pores, the bismuth domains (~ 1 nm) carry excessive surface energy that suppresses their melting point and continuously expels them out of the vanadium matrix to form nanowires. This discovery demonstrates the feasibility of scalable vapor phase synthesis of high purity nanomaterials without using any catalysts.

A protocol for seedless and high yield growth of bismuth nanowire arrays through vacuum thermal evaporation technique is presented.

Here a seedless and template-free technique is demonstrated to scalably grow bismuth nanowires, through thermal evaporation in high vacuum at RT. ...

Aerosol-assisted Chemical Vapor Deposition of Metal Oxide Structures: Zinc Oxide Rods

Whilst columnar zinc oxide (ZnO) structures in the form of rods or wires have been synthesized previously by different liquid- or vapor-phase routes, their high cost production and/or incompatibility with microfabrication technologies, due to the use of pre-deposited catalyst-seeds and/or high processing temperatures exceeding 900 &#176;C, represent a drawback for a widespread use of these methods. Here, however, we report the synthesis of ZnO rods via a non-catalyzed vapor-solid mechanism enabled by using an aerosol-assisted chemical vapor deposition (CVD) method at 400 &#176;C with zinc chloride (ZnCl2) as the precursor and ethanol as the carrier solvent. This method provides both single-step formation of ZnO rods and the possibility of their direct integration with various substrate types, including silicon, silicon-based micromachined platforms, quartz, or high heat resistant polymers. This potentially facilitates the use of this method at a large-scale, due to its compatibility with state-of-the-art microfabrication processes for device manufacture. This report also describes the properties of these structures (e.g., morphology, crystalline phase, optical band gap, chemical composition, electrical resistance) and validates its gas sensing functionality towards carbon monoxide.

Columnar zinc oxide structures in the form of rods are synthesized via aerosol-assisted chemical vapor deposition without the use of pre-deposited catalyst-seed particles. This method is scalable and compatible with various substrates based on either silicon, quartz or polymers.

Whilst columnar zinc oxide (ZnO) structures in the form of rods or wires have been synthesized previously by different liquid- or vapor-phase routes, ...

Growth and Electrostatic/chemical Properties of Metal/LaAlO3/SrTiO3 Heterostructures

The quasi 2D electron system (q2DES) that forms at the interface between LaAlO3 (LAO) and SrTiO3 (STO) has attracted much attention from the oxide electronics community. One of its hallmark features is the existence of a critical LAO thickness of 4 unit-cells (uc) for interfacial conductivity to emerge. Although electrostatic mechanisms have been proposed in the past to describe the existence of this critical thickness, the importance of chemical defects has been recently accentuated. Here, we describe the growth of metal/LAO/STO heterostructures in an ultra-high vacuum (UHV) cluster system combining pulsed laser deposition (to grow the LAO), magnetron sputtering (to grow the metal) and X-ray photoelectron spectroscopy (XPS). We study step by step the formation and evolution of the q2DES and the chemical interactions that occur between the metal and the LAO/STO. Additionally, magnetotransport experiments elucidate on the transport and electronic properties of the q2DES. This systematic work not only demonstrates a way to study the electrostatic and chemical interplay between the q2DES and its environment, but also unlocks the possibility to couple multifunctional capping layers with the rich physics observed in two-dimensional electron systems, allowing the fabrication of new types of devices.

Growth and Electrostatic/chemical Properties of Metal/LaAlO3/SrTiO3 Heterostructures

We fabricate metal/LaAlO3/SrTiO3 heterostructures using a combination of pulsed laser deposition and in situ magnetron sputtering. Through magnetotransport and in situ X-ray photoelectron spectroscopy experiments, we investigate the interplay between electrostatic and chemical phenomena of the quasi two-dimensional electron gas formed in this system.

The quasi 2D electron system (q2DES) that forms at the interface between LaAlO3 (LAO) and SrTiO3 (STO) has attracted much attention from the oxide ...

Production of Single Tracks of Ti-6Al-4V by Directed Energy Deposition to Determine the Layer Thickness for Multilayer Deposition

Directed Energy Deposition (DED), which is an additive manufacturing technique, involves the creation of a molten pool with a laser beam where metal powder is injected as particles. In general, this technique is employed to either fabricate or repair different components. In this technique, the final characteristics are affected by many factors. Indeed, one of the main tasks in building components by DED is the optimization of process parameters (such as laser power, laser speed, focus, etc.) which is usually carried out through an extensive experimental investigation. However, this sort of experiment is extremely lengthy and costly. Thus, in order to accelerate the optimization process, an investigation was conducted to develop a method based on the melt pool characterizations. In fact, in these experiments, single tracks of Ti-6Al-4V were deposited by a DED process with multiple combinations of laser power and laser speed. Surface morphology and dimensions of single tracks were analyzed, and geometrical characteristics of melt pools were evaluated after polishing and etching the cross-sections. Helpful information regarding the selection of optimal process parameters can be achieved by examining the melt pool features. These experiments are being extended to characterize the larger blocks with multiple layers. Indeed, this manuscript describes how it would be possible to quickly determine the layer thickness for the massive deposition, and avoid over or under-deposition according to the calculated energy density of the optimum parameters. Apart from the over or under-deposition, time and materials saving are the other great advantages of this approach in which the deposition of multilayer components can be started without any parameter optimization in terms of layer thickness.

In this research, a rapid method based on melt pool characterization is developed to estimate the layer thickness of Ti-6Al-4V components produced by directed energy deposition.

Directed Energy Deposition (DED), which is an additive manufacturing technique, involves the creation of a molten pool with a laser beam where metal ...

Bulk and Thin Film Synthesis of Compositionally Variant Entropy-stabilized Oxides

Here, we present a procedure for the synthesis of bulk and thin film multicomponent (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O (Co variant) and (Mg0.25(1-x)Co0.25(1-x)Ni0.25(1-x)CuxZn0.25(1-x))O (Cu variant) entropy-stabilized oxides. Phase pure and chemically homogeneous (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O (x = 0.20, 0.27, 0.33) and (Mg0.25(1-x)Co0.25(1-x)Ni0.25(1-x)CuxZn0.25(1-x))O (x = 0.11, 0.27) ceramic pellets are synthesized and used in the deposition of ultra-high quality, phase pure, single crystalline thin films of the target stoichiometry. A detailed methodology for the deposition of smooth, chemically homogeneous, entropy-stabilized oxide thin films by pulsed laser deposition on (001)-oriented MgO substrates is described. The phase and crystallinity of bulk and thin film materials are confirmed using X-ray diffraction. Composition and chemical homogeneity are confirmed by X-ray photoelectron spectroscopy and energy dispersive X-ray spectroscopy. The surface topography of thin films is measured with scanning probe microscopy. The synthesis of high quality, single crystalline, entropy-stabilized oxide thin films enables the study of interface, size, strain, and disorder effects on the properties in this new class of highly disordered oxide materials.

The synthesis of high quality bulk and thin film (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O and (Mg0.25(1-x)Co0.25(1-x)Ni0.25(1-x)CuxZn0.25(1-x))O entropy-stabilized oxides is presented.

Here, we present a procedure for the synthesis of bulk and thin film multicomponent (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O (Co variant) and ...

Niobium Oxide Films Deposited by Reactive Sputtering: Effect of Oxygen Flow Rate

Reactive sputtering is a versatile technique used to form compact films with excellent homogeneity. In addition, it allows easy control over deposition parameters such as gas flow rate that results in changes on composition and thus in the film required properties. In this report, reactive sputtering is used to deposit niobium oxide films. A niobium target is used as metal source and different oxygen flow rates to deposit niobium oxide films. The oxygen flow rate was changed from 3 to 10 sccm. The films deposited under low oxygen flow rates show higher electrical conductivity and provide better perovskite solar cells when used as electron transport layer.

Here, we present a protocol for niobium oxide films deposition by reactive sputtering with different oxygen flow rates for use as an electron transport layer in perovskite solar cells.

Reactive sputtering is a versatile technique used to form compact films with excellent homogeneity. In addition, it allows easy control over deposition ...

Atomic Layer Deposition of Vanadium Dioxide and a Temperature-dependent Optical Model

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