The authors acknowledge the facilities, and the scientific and technical assistance, of the Australian Microscopy &amp; Microanalysis Research Facility at the Australian Centre for Microscopy and Microanalysis, The University of Sydney. This research was partially supported by funding from the Faculty of Engineering &amp; Information Technologies, The University of Sydney, under the Faculty Research Cluster Program, from the Regional Council of Champagne-Ardenne (France) through the NANOTRIBO project and from the European FEDER program.

1. Equipment and Sample Requirements
<ol>
	<li>Use an SEM equipped with an EBSD detector to carry out the experiment. 
	NOTE: Ideally the SEM should have a field emission source in order to maximize spatial resolution, but the technique will work on any type of SEM.</li>
	<li>Ensure that the specimen to be analyzed has a thickness in the range of 100 nm for optimal results17. Verify that the specimen is thin enough to be able to carry out the TKD analysis. 
	NOTE: This can be done using forescatter detectors, the thinner the specimen, the darker it will be using that imaging technique.
	<ol>
		<li>Prepare the specimen using traditional techniques for TEM foil sample preparation such as by using a dimple grinder and then either electropolishing or ion polishing or by using the lift-out technique using a focused ion beam (FIB) if the features to be analyzed are site specific. 
		NOTE: The preparation techniques are not explained in detail here as they are not the object of this paper and are the same as the well-established techniques for TEM sample preparation22. The users will need to determine what the appropriate sample preparation technique is for their own specimen. Information can be found in22.</li>
	</ol>
	</li>
</ol>
2. Experimental Set-up
<ol>
	<li>Place the specimen on a specimen holder that allows the specimen to be at 20&#176; from the horizontal once inside the SEM chamber. This will allow the specimen to be hanging over the carousel once placed in a horizontal positon after tilting the stage by 20&#176; (see step 2.4) to avoid shadowing effects during data acquisition with the EBSD camera. 
	NOTE: Special specimen holders have been designed for that purpose and an example is shown in Figure 1. If the sample is a FIB lift out sample on a TEM grid, ensure that the sample is on the lower surface of the support grid.</li>
</ol>
<img alt="Figure 1" src="/files/ftp_upload/55506/55506fig1.jpg" /> 
Figure 1. TKD specimen holder. Several specimens can be analyzed during one session without the need to re-open the SEM chamber. It is important the TEM foil is positioned such a way that no holder or support prevents the electrons to be diffracted from the specimen and to be collected by the EBSD camera. Do not use grids that will interfere with the collected signal. <a href="http://cloudfront.jove.com/files/ftp_upload/55506/55506fig1large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<ol start="2">
	<li>Place sample holder in the SEM chamber, close the chamber and start the vacuum pumping as for any other specimen by clicking on pump in the vac tab.</li>
	<li>Use in-chamber plasma cleaning to prevent contamination. 
	NOTE: This step is optional but highly recommended to improve data quality and reliability. If the technique is available with the SEM, the cleaning should be done for a couple of minutes.</li>
	<li>Tilt the SEM stage by 20&#176; clockwise such that the specimen is now at a horizontal position and normal to the electron beam. If the sample is not planar and casts shadows onto the EBSD detector phosphor screen (such as when using FIB lift out samples on a TEM support grid), tilt back to 10&#176; or 0&#176;, so that the sample is tilted away from the EBSD detector.</li>
	<li>Set the SEM conditions for optimum data acquisition: set the accelerating voltage at 30 keV by clicking EHT (&#34;Extra High Tension&#34;), select EHT ON to turn on the accelerating voltage and chose the correct value of the EHT. Go to the aperture tab of the SEM control panel and choose a high aperture (e.g. 60 or 120 &#181;m), choose the high current mode or the depth of field mode (depending on the SEM) and set the appropriate beam current (roughly 3-4 nA for a 60-&#181;m aperture and 10-20 nA for a 120-&#181;m aperture).</li>
	<li>Bring the specimen at a working distance of 6 to 6.5 mm by changing the z-position of the sample. 
	NOTE: This depends on the SEM and the configuration of the EBSD detector; the sample should be positioned just above the level of the top of the phosphor screen.</li>
	<li>Make sure that the sample holder is parallel to the x-axis of the stage to avoid any possible damage to the equipment while moving the specimen and to get the optimum signal. 
	NOTE: Do not only check by looking at the specimen position on the CCD camera, move the specimen in the x-direction and make sure that the distance with the stage has not changed.</li>
	<li>Move the stage to locate the specimen and verify that the beam is hitting the specimen at the position of interest (where the TKD scan will be performed) on the specimen using secondary electron imaging.
	<ol>
		<li>Select the secondary electron detector in the detector tab of the SEM control panel.</li>
	</ol>
	</li>
	<li>Turn on the EBSD software and insert the EBSD camera by pressing the &#34;in&#34; button on the control box of the EBSD camera to a distance of 15 to 20 mm from the specimen using the external controller or the software.</li>
	<li>If required for the analysis, insert the EDS detector within the chamber by clicking the &#34;in&#34; button on the EDS camera control panel. The optimal position may not be the same as for the usual EDS analysis, so look at the signal count, and ensure that the dead time is between 20 and 50% for optimum data collection, to determine the optimal position for that particular experimental set up. 
	NOTE: It is possible in this case to adjust the working distance to improve EDS data but that will be at the expense of the quality of the diffraction patterns collected by the EBSD camera. Figure 2 illustrates the experimental configuration for data acquisition where both the EBSD camera and the EDS detector have been inserted in the chamber.</li>
	<li>Once all the detectors are positioned and the specimen has been located, perform the beam alignment by selecting the Focus Wobble check box in the aperture tab of the SEM control panel and adjusting the horizontal and vertical knobs for the aperture alignment on the control board. Perform focus adjustment and the astigmatism correction by adjusting the horizontal and vertical knobs for the stigmation on the control board. The purpose of this step is to obtain the sharpest image possible. 
	NOTE: While collecting EDS data make sure to choose the correct specimen holder for reliable data. Do not use a specimen holder made of the same material being analyzed otherwise it will be impossible to differentiate the signal coming from the specimen from the signal coming from the sample holder and make sure there is no overlap for the diffraction peaks from the material being analyzed and from which the specimen holder is made.</li>
</ol>
<img alt="Figure 2" src="/files/ftp_upload/55506/55506fig2.jpg" /> 
Figure 2. Experimental set-up. The specimen is at a horizontal position after the rotation of the stage. This limits the interference of the stage and carousel with the signal that will be collected on the phosphorus screen of the EBSD camera. <a href="http://cloudfront.jove.com/files/ftp_upload/55506/55506fig2large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
3. EBSD Software Parameters for Data Acquisition
NOTE: The data acquisition parameters are different for specific commercially-available EBSD systems. This section is written as generally as possible, but some of the names and values of the parameters given here are only appropriate if one uses the EBSD software mentioned in the Materials List, and users of different systems will need to adjust these parameters according to their own system. Most of these steps are exactly the same as for a normal EBSD experiment.
<ol>
	<li>Make sure that the specimen geometry in the EBSD software reflects the fact that the specimen is in horizontal position. Ensure that the total tilt value is 0&#176;. If not, add a -20&#176; pre-tilt value in the specimen geometry tab.</li>
	<li>Select the phase(s) (which element or compound) to be analyzed as for a normal EBSD experiment in the phase tab.</li>
	<li>Capture an image using the EBSD software in the scan image tab by clicking on start. 
	NOTE: Forescatter detectors mounted below the EBSD detector phosphor screen can be used to produce a dark field image, assisting in the identification of thin regions and sites of interest.</li>
	<li>Adjust the settings of the EBSD camera for an optimal data acquisition by optimizing the gain and exposure values until the image is bright but not oversaturated, as for a normal EBSD experiment, in the optimization pattern tab. 
	NOTE: This step is dependent on the specimen and its quality (thickness and surface finish).</li>
	<li>Collect a background in the optimization pattern tab by clicking on collect. Ensure that enough grains are present for the background collection by adjusting the magnification, although it is important to scan across a region with similar thickness to the area to be analyzed.</li>
	<li>Check the quality of the patterns once the background has been subtracted by ensuring that static background and auto background options have been checked.
	<ol>
		<li>Although they will look distorted due to the special geometry of the set-up, ensure that diffraction bands are clearly visible (see Figure 3). Integrate successive frames in the EBSD camera to improve the signal to noise ratio in the image since the luminous intensity of the diffraction pattern on the phosphor screen is low.</li>
		<li>If the quality of the patterns is not good enough, change the camera setting (adjust gain and exposure) or change the aperture size of the SEM (use a larger aperture if possible). It might also be due to the specimen being too thick in which case thinning the specimen is the only solution (depending on the specimen this can be done by using a FIB or ion thinning).</li>
	</ol>
	</li>
</ol>
<img alt="Figure 3" src="/files/ftp_upload/55506/55506fig3.jpg" /> 
Figure 3. Kikuchi diffraction pattern obtained by TKD. The pattern appears distorted in comparison to a pattern obtained by traditional EBSD and the pattern center has been shifted downwards. <a href="http://cloudfront.jove.com/files/ftp_upload/55506/55506fig3large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<ol start="7">
	<li>Optimize the solver for pattern recognition and to improve the indexing rate by going to the optimize solver tab. 
	NOTE: In the software used here, two options are available for better TKD pattern indexing: Optimized TKD or Refined Accuracy. It is recommended to use the Optimized TKD option when the diffraction patterns are highly binned; for higher resolution patterns (e.g. 336 x 256 pixels or higher), the refined accuracy mode works best.</li>
	<li>If a high resolution analysis is required (a step size of 5 nm or smaller) leave the specimen in the present setting for 30 to 60 min to improve vacuum and thermal beam stability. Do not leave the beam though on the region of interest.</li>
	<li>Before starting the data acquisition, adjust again the focus and correct the astigmatism of the SEM by repeating step 2.11.</li>
	<li>Set the parameters (step size and size of the map) for map acquisition in the Acquire Map Data tab. 
	NOTE: The step size can be as low as 2 nm if required and if the specimen is of high quality.</li>
	<li>Start the map acquisition by pressing the start button in the Acquire Map Data tab. 
	NOTE: The data analysis will be carried out exactly the same way as for a normal EBSD scan, no adjustments are necessary. Different types of map can be obtained from the data. Euler, band contrast, inverse pole figure, phase maps can all be obtained from the data collected. Pole figures can also be drawn from these data.</li>
</ol>

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The authors have nothing to disclose.

All the data presented in this paper were obtained using a standard, commercial EBSD system. Such a system is available in many laboratories around the world, which means that this technique can readily be applied in these laboratories without having to make any further investment. No modification in the configuration of the SEM and no additional software are necessary to use the EBSD system to collect TKD data. Therefore the transition from traditional EBSD to TKD is very easy. The data acquisition rate for TKD is similar to that of EBSD, which currently reaches up to approximately 1,000 patterns/s19. This high rate is partially due to the very high level of automation of the technique, including calibration for pattern center position and pattern center change during scanning19. TKD will benefit from all of these advantages. Additionally, TKD like EBSD, can be coupled easily with EDS to obtain additional chemical information (see Figure 7).
Sample preparation is very important to obtain data in TKD, therefore time should be spent on step 1.2 to insure that the specimen is thin enough to be analyzed. Otherwise there is no point in starting the experiment. Properly setting the parameters of the SEM is paramount in obtaining reliable data. Users should particularly pay attention to steps 2.5 and 2.11 and the values for the parameters given in the protocol might need to be adjusted to specific SEM, EBSD systems and specimens. The parameters to optimize pattern recognition (step 3.7) are also very important to ensure good quality of the data collected. These parameters need to be tested for various patterns in different regions of the area to be scanned to make sure that the complete area of interest can be scanned properly with a high indexing rate.
The different examples presented in this paper attest to the high resolution capability of the technique in comparison with traditional EBSD. Despite the progress made with the hardware and software of the SEM and EBSD systems, the resolution of the EBSD technique cannot reach values below 20 nm for high density materials17, which means that characterizing features smaller than 50 nm in these materials will be impossible. Working with less dense materials will increase the size of the smallest resolvable feature to the 100 nm mark. Figure 6b shows that it is possible to use TKD to characterize features, such as the hcp laths present in the deformed Co-Cr-Mo alloys, which are as small as 10 to 20 nm, as the spatial resolution of the technique can be as low as 2 nm17.
Geological materials are usually non-conductive or semi-conductive, which often poses some difficulties when they need to be characterized using traditional EBSD. This problem does not present itself while using TKD. The interaction volume during the analysis is so small given the thin geometry of the specimen that there is no problem of conductivity. This small interaction volume is also an advantage while working with highly deformed materials as normally high dislocation densities makes it impossible to obtain patterns that can be indexed using traditional EBSD. As can be seen in Figure 8, the highly deformed diamond could be characterized using TKD despite the high dislocation densities present in its grains.
One limitation of the technique concerns sample preparation. It is harder to obtain a good specimen for TKD than it is for EBSD. The sample preparation techniques are the same as for TEM sample preparation, which means they are difficult and time-consuming. Finding the correct area to analyze is also a challenge that can be addressed using site specific techniques such as by using a FIB if it is adequate for the type of specimen to be studied. The spatial resolution is improved quite significantly with TKD in comparison with EBSD but is still not as good as what can be attained using TEM17,19.
This paper has demonstrated that TKD is a valuable technique to characterize nanocrystalline and UFG materials from diverse origins. Its ease of application, speed, resolution and flexibility in term of conductivity outweigh the difficulty in sample preparation. The future of the technique resides in in situ characterization. By using an in situ mechanical testing rig while carrying out TKD analysis, it will be possible to observe how these nano- and ultra-fine microstructures change under external loading. This will increase our knowledge on the deformation mechanisms of nanocrystalline and UFG materials.

One of today&#39;s research frontiers in advanced materials is seeking to actively design materials with tailored physical, chemical and mechanical properties suitable for high-end applications. The modification of the material&#39;s microstructure is an effective way to tailor its properties to reach specific high performance. In this paradigm, refining the grain size of crystalline materials to produce ultra-fine grained (UFG) or nanocrystalline materials has been shown to be an effective technique to increase their strength1,2. Such refined microstructure can be achieved through processes involving severe plastic deformation3,4, or through consolidating ultra-fine or nano-sized powders into bulk materials using various powder metallurgy processes5,6. Research in this field has been increasing in the past ten years, with the main objectives being to scale up the processes and to understand the deformation mechanisms of such materials.
UFG and nanocrystalline materials are, however, not limited to modern applications in materials science since nature has its own way of producing such refined crystalline materials. Geological fault zones are known to produce nanocrystalline regions; although often assumed to be amorphous on the basis of light microscopy studies, high resolution transmission electron microscopy (TEM) and scanning electron microscopy (SEM) analyses have frequently shown that grain sizes can be on the scale of tens of nanometers7. High strain rate deformation episodes, like those during meteorite impacts, can also produce nanocrystalline structures as well as extremely high defect densities8. Deformation is not always a requirement for nanostructures in nature. Pearce et al. have presented evidence of deposition of large volumes of gold from a colloidal source in an orogenic gold deposit through the characterization of Au and Pt/PtFe nanoparticles in minerals extracted from gold mines9. Shell structures, such as nacre, are formed by regular arrangement of crystalline units on the scale of a few 100 nm10. Even meteorites have been shown to contain UFG mineral structures11.
Whatever the provenance of the materials possessing these UFG or nanocrystalline structures, characterizing them poses a challenge which has prompted the development of improved characterization tools at the nanoscale. One promising avenue that has been investigated is electron microscopy. Such a technique appears perfectly adapted for this task, since the inherently small electron wavelength, associated with its use, offers the possibility to analyze the atomic structure of the material12. It has already been shown that Electron Backscatter Diffraction (EBSD) can be used to characterize UFG materials with grain sizes down to the sub-micron scale13,14,15,16. However, the spatial resolution of the EBSD technique, even using the current most advanced SEMs, is limited to 20 to 50 nm depending on the material17. It is therefore not surprising that initially, researchers sought solutions to characterize these materials with ultra-fine microstructure by using TEM. Crystallographic orientation determination using diffraction modes in TEM, such as Kikuchi patterns and spot patterns, can reach spatial resolutions of the order of 10 nm and in some cases below that value12,18,19. However, some drawbacks have been identified with the use of these techniques such as their speed and angular resolutions, especially when compared to the possibilities offered by EBSD12,19. Although automated precession-based TEM diffraction techniques can achieve similar indexing speeds as EBSD, most TEM techniques suffer from relatively low levels of automation19. In addition, TEM techniques generally require critical and time-consuming alignments of the instrument&#39;s lens system to achieve optimum performance.
More recently, the interest has shifted towards improving resolution of the Kikuchi diffraction technique within the SEM, by changing the way the signal is obtained and analyzed. Keller and Geiss presented a new form of low-energy transmission Kikuchi diffraction performed in the SEM20. The method, which they named transmission-EBSD (t-EBSD), necessitates an EBSD detector and associated software to capture and analyze the angular intensity variation in large-angle forward scattering of electrons in transmission. Using that technique, they were able to collect Kikuchi patterns from nanoparticles and nano-grains with sizes as low as 10 nm in diameter. The fact that the diffracted electrons analyzed in this case go through the specimen and are not ejected back from the surface of the specimen, prompted a change in terminology to more appropriately describe the technique; it is now called Transmission Kikuchi Diffraction or TKD. The TKD technique was optimized by Trimby to allow better resolution and the automatic acquisition of orientation maps17. This technique can also be coupled with energy dispersive X-ray spectroscopy (EDS) to collect chemical information while carrying out the crystallographic orientation analysis21.
This paper provides the requirements in terms of equipment and specimens to conduct TKD experiments, describes the different steps necessary for data acquisition, and presents results collected on four different specimens to show the extent of the possible applications of the technique. The examples presented here are either metallic alloys that have been subjected to severe plastic deformation to create UFG/nanocrystalline materials or geological materials that have also been subjected to severe plastic deformation and present refined microstructures.

<table border="0" cellpadding="0" cellspacing="0" width="766">
	<tbody>
		<tr height="84">
			<td height="84" style="height:84px;width:216px;">Scanning electron microscope</td>
			<td style="width:112px;">&#160;Zeiss&#160;</td>
			<td style="width:119px;"></td>
			<td style="width:319px;">Preferably equipped with a&#160; field emission source in order to maximize spatial resolution. The one used here is a Zeiss Ultra plus field emission-SEM</td>
		</tr>
		<tr height="105">
			<td height="105" style="height:105px;width:216px;">Electron backscatter diffraction detector</td>
			<td style="width:112px;">Oxford instruments</td>
			<td style="width:119px;"></td>
			<td style="width:319px;">Different system are available on the market. The one is in this work is a Nordlys-nano EBSD detector from Oxford instruments. Forescatter detectors are mounted belown the detector phospor screen which is an option.</td>
		</tr>
		<tr height="63">
			<td height="63" style="height:63px;width:216px;">Electron backscatter diffraction software for data acquisition and analysis</td>
			<td style="width:112px;">Oxford instruments</td>
			<td style="width:119px;"></td>
			<td style="width:319px;">The protocal is described here for the usage of the AZtecHKL EBSD software but other software can be used as well</td>
		</tr>
		<tr height="63">
			<td height="63" style="height:63px;width:216px;">EDS dector</td>
			<td style="width:112px;">Oxford instruments</td>
			<td style="width:119px;"></td>
			<td style="width:319px;">This is optional. The one used here is a X-Max 20mm2 silicon drift EDS detector from Oxford instruments</td>
		</tr>
		<tr height="105">
			<td height="105" style="height:105px;width:216px;">sample holder for TKD</td>
			<td style="width:112px;">ANY</td>
			<td style="width:119px;"></td>
			<td style="width:319px;">As long as it can handle thin specimen and can be placed in the correct orientation within the microscope. Different companies sell specific sample holders for TKD analysis if required by the user.</td>
		</tr>
		<tr height="63">
			<td height="63" style="height:63px;width:216px;">Plasma cleaner</td>
			<td style="width:112px;">Evactron</td>
			<td style="width:119px;"></td>
			<td style="width:319px;">This is optional. The one used here is Evactron Model 25 RF Plasma Decontaminator for FIB/SEM and Vacuum Chambers</td>
		</tr>
	</tbody>
</table>

characterization of ultra-fine grained and nanocrystalline materials using transmission kikuchi diffraction

One of the challenges in microstructure analysis nowadays resides in the reliable and accurate characterization of ultra-fine grained (UFG) and nanocrystalline materials. The traditional techniques associated with scanning electron microscopy (SEM), such as electron backscatter diffraction (EBSD), do not possess the required spatial resolution due to the large interaction volume between the electrons from the beam and the atoms of the material. Transmission electron microscopy (TEM) has the required spatial resolution. However, due to a lack of automation in the analysis system, the rate of data acquisition is slow which limits the area of the specimen that can be characterized. This paper presents a new characterization technique, Transmission Kikuchi Diffraction (TKD), which enables the analysis of the microstructure of UFG and nanocrystalline materials using an SEM equipped with a standard EBSD system. The spatial resolution of this technique can reach 2 nm. This technique can be applied to a large range of materials that would be difficult to analyze using traditional EBSD. After presenting the experimental set up and describing the different steps necessary to realize a TKD analysis, examples of its use on metal alloys and minerals are shown to illustrate the resolution of the technique and its flexibility in term of material to be characterized.

The data presented here have been collected using the SEM, EBSD system and software mentioned in the Materials List. Depending on the features of interest, scans were run with different step sizes and the specific step size is indicated for each specimen shown in this work.
The two first examples of TKD application presented here are related to grain refinement of metallic alloys in order to increase their mechanical properties. Stainless steels and Cobalt-Chromium-Molybdenum alloys are commonly used for biomedical applications due to their high corrosion resistance, good mechanical properties under static loading and biocompatibility23,24. However, both these materials have drawbacks: stainless steels have low hardness and wear resistance while Co-Cr-Mo alloys can fail due to tribocorrosion phenomena. One way to address these materials&#39; short-comings is to change their surface properties by microstructure refinement. Stainless steel and Co-Cr-Mo alloy specimens were subjected to Surface Mechanical Attrition Treatment (SMAT), which is a surface treatment that generates, by severe plastic deformation, a nanocrystalline surface layer that enhances the surface mechanical, tribological, and corrosion properties of bulk materials without changing their chemical composition25. Using TKD, the microstructure below the treated surface was analyzed for the different materials to link the change of microstructure to the improved properties.
Microstructure characterization using TKD has proven that subjecting a stainless steel specimen to SMAT created a region, 1 &#181;m thick below the treated surface, where a mixture of equiaxed nano-grains and slightly elongated nano-grains were present23. Figure 4 presents one of the TKD scans that were run on a treated sample. The TKD specimen was prepared by using a FIB as the area of interest was just at the surface of the sample. Figure 4 shows that, in the first region below the treated surface, the equiaxed grains are smaller than 100 nm in diameter while the elongated grains present thicknesses of 100 to 200 nm for lengths that can reach 500 nm. Below this first region, a UFG region of elongated sub-micron sized grains can also be seen on the figure. This was the first time that the nano-grain region was properly characterized in a specimen subjected to SMAT. For comparison, another specimen of stainless steel subjected to SMAT was analyzed using traditional EBSD and the results of one of the scans are shown in Figure 5. Both the band contrast and IPF maps show the presence of an UFG region at the surface. However, although a step size of 15 nm was used to run the scan, the grains in that region could not be successfully indexed due to the larger interaction volume that is analyzed at each location during the scan. This shows the limit of the EBSD technique for characterizing UFG and nanocrystalline materials.
<img alt="Figure 4" src="/files/ftp_upload/55506/55506fig4.jpg" /> 
Figure 4. TKD data collected from a stainless steel specimen after SMAT. The data was collected using a step size of 5 nm on a 100 to 120 nm thick specimen. (a) Band contrast map giving an indication of the quality of the collected pattern (the lighter the grey the better the pattern); (b) Inverse Pole Figure (IPF) map showing the different crystallographic orientations of the grains according to the color scheme represented on the right of the map. The surface treated is on the top of the maps. <a href="http://cloudflare.jove.com/files/ftp_upload/55506/55506fig4large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
<img alt="Figure 5" src="/files/ftp_upload/55506/55506fig5.jpg" /> 
Figure 5. EBSD data collected from a stainless steel specimen after SMAT. The data was collected using a step of 15 nm. (a) Band contract map; (b) IPF map. <a href="http://cloudflare.jove.com/files/ftp_upload/55506/55506fig5large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
Figure 6 illustrates the results of the TKD characterization of a Co-Cr-Mo alloy sample subjected to SMAT. The TKD specimen was prepared using a FIB and the analyzed area was located roughly 10 &#181;m below the treated surface. The results show that a refinement of the microstructure took place via phase transformation24. Initially, the material possessed a single face-centered cubic (fcc) phase and had an average grain size of 10 &#181;m. Figure 6 shows that two phases in this deformed region are present: hexagonal close-packed (hcp) laths are seen inside the fcc grains. The thickness of these laths can be as small as 10 to 20 nm. This refinement of the microstructure explains the three-fold increase in the measured hardness of the material just below the treated surface24.
<img alt="Figure 6" src="/files/ftp_upload/55506/55506fig6.jpg" /> 
Figure 6. TKD data collected from a Cobalt-Chromium-Molybdenum alloy specimen after SMAT. The data was collected using a step size of 5 nm on a 100 to 120 nm thick specimen. (a) Band contrast map; (b) phase map showing the distribution of the two phases present in the alloy after plastic deformation, the red color represents the hcp phase, while the blue color shows the fcc phase; (c) IPF map showing the different crystallographic orientations of the grains of the hcp phase according to the color scheme represented on the left of the map; (d) IPF map showing the different crystallographic orientations of the grains of the fcc phase according to the color scheme represented on the right of the map. <a href="http://cloudflare.jove.com/files/ftp_upload/55506/55506fig6large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
The last two examples presented here are related to the field of geology. Sub-micron structures can be present in minerals due to the severe plastic deformation they are subjected to within the Earth&#39;s mantle or during earthquakes, for example. These materials can present high dislocation densities that make their characterization using traditional EBSD impossible. Detailed study of their microstructure is however paramount to determine the background of these minerals and to understand the different chemical and physical processes to which they have been subjected. For example, it is possible to follow the carbon cycle in the deep Earth by studying diamonds and their inclusions. Figure 7 illustrates one of these studies, where Jacob et al. investigated the microstructure and composition of FeNi-sulfide inclusions in a polycrystalline diamond aggregate that displays a nanogranular magnetite reaction corona26. The TKD analysis revealed the distribution of the different phases present in the specimen (Figure 7b), and showed the nano-structures of the magnetite (Figure 7a). By coupling TKD with EDS, the distribution of the different elements (here showing only Fe and Cu distributions in Figures 7c and d) within the different phases was determined. The study proved that the diamond formed and nucleated by a redox reaction involving the diamond-forming fluid and the FeNi sulfide that formed magnetite and diamond26.
<img alt="Figure 7" src="/files/ftp_upload/55506/55506fig7.jpg" /> 
Figure 7. TKD and EDS data collected from FeNi-sulfide inclusions in a polycrystalline diamond aggregate. The data was collected using a step size of 10 nm on an 80 to 100 nm thick specimen. (a) Band contrast map; (b) phase map showing the distribution of the different phases present in specimen, diamond is indicated in yellow, magnetite in red, pyrrhotite in green and chalcopyrite in blue; (c) chemical composition map showing the distribution of Fe in the specimen; (d) chemical composition map showing the distribution of Cu in the specimen. <a href="http://cloudflare.jove.com/files/ftp_upload/55506/55506fig7large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>
Many geological samples are subjected to high plastic deformation, although this is not always associated with the Earth&#39;s tectonic processes. Impact structures are observed in many meteorite craters on the surface of the Earth, occasionally associated with high enough pressures to transform graphite into diamond27. The structure of these diamonds is highly deformed with very high dislocation densities due to the high energy impact caused by the meteorite. Figure 8 shows an example of an impact diamond characterized using TKD. The large plastic deformation seen by the specimen explains the presence of sub-micron sized grains, a high proportions of twins (see Figure 8b) and gradients of crystallographic orientations within the grains (these gradients are due to high dislocation densities within the grains).
<img alt="Figure 8" src="/files/ftp_upload/55506/55506fig8.jpg" /> 
Figure 8. TKD data collected from a meteorite impact diamond. The data was collected using a step size of 10 nm on an 80 to 100 nm thick specimen. (a) Band slope map giving an indication of the quality of the collected pattern (the lighter the grey the better the patter); (b) IPF map showing the different crystallographic orientations of the grains according to the color scheme represented on the right of the map. The red lines represent twin boundaries, with a 60&#176; rotation about &#60;111&#62;. <a href="http://cloudflare.jove.com/files/ftp_upload/55506/55506fig8large.jpg" target="_blank">Please click here to view a larger version of this figure.</a>

Watch this Scientific Journal Video about Characterization of Ultra-fine Grained and Nanocrystalline Materials Using Transmission Kikuchi Diffraction at JoVE.com

Characterization of Ultra-fine Grained and Nanocrystalline Materials Using Transmission Kikuchi Diffraction

This paper provides a detailed method to characterize the microstructure of ultra-fine grained and nanocrystalline materials using a scanning electron microscope equipped with a standard electron backscatter diffraction system. Metal alloys and minerals presenting refined microstructures are analyzed using this technique, showing the diversity of its possible applications.

One of the challenges in microstructure analysis nowadays resides in the reliable and accurate characterization of ultra-fine grained (UFG) and ...

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13.2K Views.  The University of Sydney.  В настоящем документе представлен подробный способ охарактеризовать микроструктуру ультра-мелкозернистых и нанокристаллических материалов с использованием сканирующего электронного микроскопа, оснащенного стандартной системой дифракции электронов об?...

Video: Characterization of Ultra-fine Grained and Nanocrystalline Materials Using Transmission Kikuchi Diffraction

Revealing Dynamic Processes of Materials in Liquids Using Liquid Cell Transmission Electron Microscopy

The recent development for in situ transmission electron microscopy, which allows imaging through liquids with high spatial resolution, has attracted significant interests across the research fields of materials science, physics, chemistry and biology. The key enabling technology is a liquid cell. We fabricate liquid cells with thin viewing windows through a sequential microfabrication process, including silicon nitride membrane deposition, photolithographic patterning, wafer etching, cell bonding, etc. A liquid cell with the dimensions of a regular TEM grid can fit in any standard TEM sample holder. About 100 nanoliters reaction solution is loaded into the reservoirs and about 30 picoliters liquid is drawn into the viewing windows by capillary force. Subsequently, the cell is sealed and loaded into a microscope for in situ imaging. Inside the TEM, the electron beam goes through the thin liquid layer sandwiched between two silicon nitride membranes. Dynamic processes of nanoparticles in liquids, such as nucleation and growth of nanocrystals, diffusion and assembly of nanoparticles, etc., have been imaged in real time with sub-nanometer resolution. We have also applied this method to other research areas, e.g., imaging proteins in water. Liquid cell TEM is poised to play a major role in revealing dynamic processes of materials in their working environments. It may also bring high impact in the study of biological processes in their native environment.

We have developed a self-contained liquid cell, which allows imaging through liquids using a transmission electron microscope. Dynamic processes of nanoparticles in liquids can be revealed in real time with sub-nanometer resolution.

The recent development for in situ transmission electron microscopy, which allows imaging through liquids with high spatial resolution, has attracted ...

Characterization of Electrode Materials for Lithium Ion and Sodium Ion Batteries Using Synchrotron Radiation Techniques

Intercalation compounds such as transition metal oxides or phosphates are the most commonly used electrode materials in Li-ion and Na-ion batteries. During insertion or removal of alkali metal ions, the redox states of transition metals in the compounds change and structural transformations such as phase transitions and/or lattice parameter increases or decreases occur. These behaviors in turn determine important characteristics of the batteries such as the potential profiles, rate capabilities, and cycle lives. The extremely bright and tunable x-rays produced by synchrotron radiation allow rapid acquisition of high-resolution data that provide information about these processes. Transformations in the bulk materials, such as phase transitions, can be directly observed using X-ray diffraction (XRD), while X-ray absorption spectroscopy (XAS) gives information about the local electronic and geometric structures (e.g.&#160;changes in redox states and bond lengths). In situ experiments carried out on operating cells are particularly useful because they allow direct correlation between the electrochemical and structural properties of the materials. These experiments are time-consuming and can be challenging to design due to the reactivity and air-sensitivity of the alkali metal anodes used in the half-cell configurations, and/or the possibility of signal interference from other cell components and hardware. For these reasons, it is appropriate to carry out ex situ experiments (e.g.&#160;on electrodes harvested from partially charged or cycled cells) in some cases. Here, we present detailed protocols for the preparation of both ex situ and in situ samples for experiments involving synchrotron radiation and demonstrate how these experiments are done.

We describe the use of synchrotron X-ray absorption spectroscopy (XAS) and X-ray diffraction (XRD) techniques to probe details of intercalation/deintercalation processes in electrode materials for Li-ion and Na-ion batteries. Both in situ and ex situ experiments are used to understand structural behavior relevant to the operation of devices

Intercalation compounds such as transition metal oxides or phosphates are the most commonly used electrode materials in Li-ion and Na-ion batteries. ...

Characterization of Thermal Transport in One-dimensional Solid Materials

The TET (transient electro-thermal) technique is an effective approach developed to measure the thermal diffusivity of solid materials, including conductive, semi-conductive or nonconductive one-dimensional structures. This technique broadens the measurement scope of materials (conductive and nonconductive) and improves the accuracy and stability. If the sample (especially biomaterials, such as human head hair, spider silk, and silkworm silk) is not conductive, it will be coated with a gold layer to make it electronically conductive. The effect of parasitic conduction and radiative losses on the thermal diffusivity can be subtracted during data processing. Then the real thermal conductivity can be calculated with the given value of volume-based specific heat (&#961;cp), which can be obtained from calibration, noncontact photo-thermal technique or measuring the density and specific heat separately. In this work, human head hair samples are used to show how to set up the experiment, process the experimental data, and subtract the effect of parasitic conduction and radiative losses.

The TET (transient electro-thermal) technique is an effective approach developed to measure the thermal diffusivity of solid materials.

The TET (transient electro-thermal) technique is an effective approach developed to measure the thermal diffusivity of solid materials, including ...

In Situ Neutron Powder Diffraction Using Custom-made Lithium-ion Batteries

Li-ion batteries are widely used in portable electronic devices and are considered as promising candidates for higher-energy applications such as electric vehicles.1,2 However, many challenges, such as energy density and battery lifetimes, need to be overcome before this particular battery technology can be widely implemented in such applications.3 This research is challenging, and we outline a method to address these challenges using in situ NPD to probe the crystal structure of electrodes undergoing electrochemical cycling (charge/discharge) in a battery. NPD data help determine the underlying structural mechanism responsible for a range of electrode properties, and this information can direct the development of better electrodes and batteries.
We briefly review six types of battery designs custom-made for NPD experiments and detail the method to construct the &#8216;roll-over&#8217; cell that we have successfully used on the high-intensity NPD instrument, WOMBAT, at the Australian Nuclear Science and Technology Organisation (ANSTO). The design considerations and materials used for cell construction are discussed in conjunction with aspects of the actual in situ NPD experiment and initial directions are presented on how to analyze such complex in situ data.

In Situ Neutron Powder Diffraction Using Custom-made Lithium-ion Batteries

We describe the design and construction of an electrochemical cell for the examination of electrode materials using in situ neutron powder diffraction (NPD). We briefly comment on alternate in situ NPD cell designs and discuss methods for the analysis of the corresponding in situ NPD data produced using this cell.

Li-ion batteries are widely used in portable electronic devices and are considered as promising candidates for higher-energy applications such as electric ...

Characterization of Full Set Material Constants and Their Temperature Dependence for Piezoelectric Materials Using Resonant Ultrasound Spectroscopy

During the operation of high power electromechanical devices, a temperature rise is unavoidable due to mechanical and electrical losses, causing the degradation of device performance. In order to evaluate such degradations using computer simulations, full matrix material properties at elevated temperatures are needed as inputs. It is extremely difficult to measure such data for ferroelectric materials due to their strong anisotropic nature and property variation among samples of different geometries. Because the degree of depolarization is boundary condition dependent, data obtained by the IEEE (Institute of Electrical and Electronics Engineers) impedance resonance technique, which requires several samples with drastically different geometries, usually lack self-consistency. The resonant ultrasound spectroscopy (RUS) technique allows the full set material constants to be measured using only one sample, which can eliminate errors caused by sample to sample variation. A detailed RUS procedure is demonstrated here using a lead zirconate titanate (PZT-4) piezoceramic sample. In the example, the complete set of material constants was measured from room temperature to 120 &#176;C. Measured free dielectric constants <img alt="Equation 1" src="/files/ftp_upload/53461/image001.jpg" /> and&#160;<img alt="Equation 2" src="/files/ftp_upload/53461/image002.jpg" /> were compared with calculated ones based on the measured full set data, and piezoelectric constants d15 and d33 were also calculated using different formulas. Excellent agreement was found in the entire range of temperatures, which confirmed the self-consistency of the data set obtained by the RUS.

This protocol describes the procedure of measuring the temperature dependence of the full set material constants of piezoelectric materials using resonant ultrasound spectroscopy (RUS).

During the operation of high power electromechanical devices, a temperature rise is unavoidable due to mechanical and electrical losses, causing the ...

Comprehensive Characterization of Extended Defects in Semiconductor Materials by a Scanning Electron Microscope

Extended defects such as dislocations and grain boundaries have a strong influence on the performance of microelectronic devices and on other applications of semiconductor materials. However, it is still under debate how the defect structure determines the band structure, and therefore, the recombination behavior of electron-hole pairs responsible for the optical and electrical properties of the extended defects. The present paper is a survey of procedures for the spatially resolved investigation of structural and of physical properties of extended defects in semiconductor materials with a scanning electron microscope (SEM). Representative examples are given for crystalline silicon. The luminescence behavior of extended defects can be investigated by cathodoluminescence (CL) measurements. They are particularly valuable because spectrally and spatially resolved information can be obtained simultaneously. For silicon, with an indirect electronic band structure, CL measurements should be carried out at low temperatures down to 5 K due to the low fraction of radiative recombination processes in comparison to non-radiative transitions at room temperature. For the study of the electrical properties of extended defects, the electron beam induced current (EBIC) technique can be applied. The EBIC image reflects the local distribution of defects due to the increased charge-carrier recombination in their vicinity. The procedure for EBIC investigations is described for measurements at room temperature and at low temperatures. Internal strain fields arising from extended defects can be determined quantitatively by cross-correlation electron backscatter diffraction (ccEBSD). This method is challenging because of the necessary preparation of the sample surface and because of the quality of the diffraction patterns which are recorded during the mapping of the sample. The spatial resolution of the three experimental techniques is compared.

The optical, electrical, and structural properties of dislocations and of grain boundaries in semiconductor materials can be determined by experiments performed in a scanning electron microscope. Electron microscopy has been used to investigate cathodoluminescence, electron beam induced current, and diffraction of backscattered electrons.

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Samples fully embedded in liquid can be studied at a nanoscale spatial resolution with Scanning Transmission Electron Microscopy (STEM) using a microfluidic chamber assembled in the specimen holder for Transmission Electron Microscopy (TEM) and STEM. The microfluidic system consists of two silicon microchips supporting thin Silicon Nitride (SiN) membrane windows. This article describes the basic steps of sample loading and data acquisition. Most important of all is to ensure that the liquid compartment is correctly assembled, thus providing a thin liquid layer and a vacuum seal. This protocol also includes a number of tests necessary to perform during sample loading in order to ensure correct assembly. Once the sample is loaded in the electron microscope, the liquid thickness needs to be measured. Incorrect assembly may result in a too-thick liquid, while a too-thin liquid may indicate the absence of liquid, such as when a bubble is formed. Finally, the protocol explains how images are taken and how dynamic processes can be studied. A sample containing AuNPs is imaged both in pure water and in saline.

This protocol describes the operation of a liquid flow specimen holder for scanning transmission electron microscopy of AuNPs in water, as used for the observation of nanoscale dynamic processes.

Samples fully embedded in liquid can be studied at a nanoscale spatial resolution with Scanning Transmission Electron Microscopy (STEM) using a ...

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A method for producing simple and efficient thermally-activated delayed fluorescence organic light-emitting diodes (OLEDs) based on guest-host or exciplex donor-acceptor emitters is presented. With a step-by-step procedure, readers will be able to repeat and produce OLED devices based on simple organic emitters. A patterning procedure allowing the creation of personalized indium tin oxide (ITO) shape is shown. This is followed by the evaporation of all layers, encapsulation and characterization of each individual device. The end goal is to present a procedure that will give the opportunity to repeat the information presented in cited publication but also using different compounds and structures in order to prepare efficient OLEDs.

A protocol for the production of simple structured organic light-emitting diodes (OLEDs) is presented.

A method for producing simple and efficient thermally-activated delayed fluorescence organic light-emitting diodes (OLEDs) based on guest-host or exciplex ...

Processing of Bulk Nanocrystalline Metals at the US Army Research Laboratory

Given their potential for significant property improvements relative to their large grained counterparts, much work has been devoted to the continued development of nanocrystalline metals. Despite these efforts, the transition of these materials from the lab bench to actual applications has been blocked by the inability to produce large scale parts that retain the desired nanocrystalline microstructures. Following the development of a method proven to stabilize the nanosized grain structure to temperatures approaching that of the melting point for the given metal, the US Army Research Laboratory (ARL) has progressed to the next stage in the development of these materials - namely the production of large scale parts suitable for testing and evaluation in a range of relevant test environments. This report provides a broad overview of the ongoing efforts in the processing, characterization, and consolidation of these materials at ARL. In particular, focus is placed on the methodology used for producing the nanocrystalline metal powders, in both small and large-scale amounts, that are at the center of ongoing research efforts.

This paper provides a brief overview of the ongoing efforts at the Army Research Laboratory on the processing of bulk nanocrystalline metals with an emphasis on the methodologies used for the production of the novel metal powders.

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Method Development for Contactless Resonant Cavity Dielectric Spectroscopic Studies of Cellulosic Paper

The current analytical techniques for characterizing printing and graphic arts substrates are largely ex situ and destructive. This limits the amount of data that can be obtained from an individual sample and renders it difficult to produce statistically relevant data for unique and rare materials. Resonant cavity dielectric spectroscopy is a non-destructive, contactless technique which can simultaneously interrogate both sides of a sheeted material and provide measurements which are suitable for statistical interpretations. This offers analysts the ability to quickly discriminate between sheeted materials based on composition and storage history. In this methodology article, we demonstrate how contactless resonant cavity dielectric spectroscopy may be used to differentiate between paper analytes of varying fiber species compositions, to determine the relative age of the paper, and to detect and quantify the amount of post-consumer waste (PCW) recycled fiber content in manufactured office paper.

A protocol for the non-destructive analysis of the fiber content and relative age of paper.

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