 Well, as Dina told you, you're talking about XPCS, mainly for the study of soft chemistry synthesis of catalysts. Well, for the design of efficient catalysts, we have to use all the tools that have available in material science. So we have to understand the properties, the mechanisms, and also be able to answer these questions. For example, how we can control hierarchical structure, what's the relationship between function and structure. And for this, we have to combine physics and chemistry. And during this presentation, I will show you how we can use the coherent x-ray scattering techniques to probe dynamics and structure that can help us to answer some of these questions. So using coherent x-rays techniques, we can study the 3D structure of the materials using the coherent x-ray fraction image. Then it will give us information about 2D and 3D morphology, porosity, defects, phase distribution, and so on. And using x-ray photocorrelation spectroscopic XPCS, we can probe dynamics. What kind of dynamics? Aggregation, phase separation, transitions are some examples. And these techniques, they can be still even more powerful if we perform in-situ and operandou study. So in-situ study, we will follow a material in a real condition. So for example, doing a synthesis of a catalyst and operandou study, we will follow a material in a work condition. So for example, a catalyst doing a reaction, we analyze the catalyst using the same control techniques. And at the same time, we will follow the result of this reaction using another technique. So this presentation, it will be most dedicated to dynamics. But it's just before going to dynamics, I would like to show you an example of operandou study of a catalyst using coherent x-ray fraction image. So this is a work I did during my postdoc when I arrived here at the Brazilian Sync Control. So the first technique that I worked based in coherent x-rays was Bragg CDI. Now I changed to XPCS, completely different techniques. But I keep the focus on material size and catalysts. So in this work, we produced the shaped controlled nanoparticles. So using a colloidal synthesis, we could produce this really nice golden nanocubes, cuboctahedron. And we went to the APS to the 34 IDC bin line to study these nanoparticles in operandou Bragg CDI during the CO oxidation reaction. So this is a model reaction, but also an important reaction that will happen in our cars every day. So when we perform coherent diffraction image in Bragg condition, in addition to the 3D morphology, we also have the 3D distribution of the displacement field and the strain. So in a crystalline material, when I have a perfect crystal x-rays, we'll be diffracted with a constant phase difference. When I have a defect, it will produce a phase offset. And using the algorithms for phase retrieval, we can obtain the 3D distribution of displacement field and also calculate the strain. Strain is really important for catalysis because when we have an strained region in a crystal, it will affect the electron properties at that region. So it will affect the binding energy and also the dissociation energy. So when we have tensile strain, it will lower the barrier of the dissociation energy. So it's more likely that the reaction will happen in these regions of tensile strain because it will alter the debent, the debent center. So we follow these nanoparticles during the reaction. And we could observe the location of the tensile strain, how it was formed during the reaction. And we could have information about the different reactivity of similar facets. And also, this reaction presents a hysteresis behavior. And we could understand better this phenomenon also in a single particle level. Well, so this was just one to give you this example. This is this nice work that we did a few years ago. And using this operandi study, we can have this information about the relationship between structure and activity. But now I'm still into catalysis, but I changed my interest to macrophorescatalyst. Macrophorescatalyst are nice materials for the production of flow micro-reactors for liquid phase reaction. And in these recent years, it's a growing demand of replace the batch reactors for flow reactors, mainly in the chemical and in the pharmaceutical industry. When you use a flow reactor, it has several advantages. It speeds the reaction rate up. It's easier for directants to assess the activity sites. And there are also no need of separation and purification steps. And so it's a more environmentally friendly process. I'm particularly interested in producing these macrophorescatalysts for the synthesis of activity pharmaceutical ingredients. For this, we have also to include the activity species that's going to be nickel, palladium, or copper. So have to be able to produce appoured materials with well-controlled porosity to allow an efficient mass transfer. And also be able to include this catalytic activity species well distributed in these macrophores materials. And in this presentation, I will show you how you can use XVS to help you to understand the formation of the porosity and also distribution of this activity space. So there are several approaches to produce this kind of material. A very attractive approach, synthetic approach, is the use of the sol-gel synthesis. Using this method, we can prepare a catalyst in very few steps. We do not need high temperature or high pressure. The solvents are usually water or ethanol. And in this method, we start from a coaxide or a metal, a salt metal. And then it will go into reaction of hydrolysis and polycondensation forming the gel network. To prepare a supported catalyst using this method, we can include the precursors, the metallic precursors, during the synthesis of the gel. And then we will have the metallic species well dispersed in the gel structure. So it will allow us to have a higher dispersion than the impregnation of a metal after the formation of the porous materials. And also it will allow us to obtain more stable activity spaces almost generally dispersed. The macroscopic properties of these materials will strongly depend on the microscope organization and mobility. So it's very important to understand the dynamics and these transitions. So this is a good method to produce a supported catalyst. If you want to include the macropores in this material, we can combine the salt-gel transition and phase separation, spinodal decomposition. So for this, we will add a polymer that will work as a phase separation inducer. When the gelation is progressed, it will increase the tendency of phase separation between a gel-rich phase and the solvent-rich phase. Then we can remove the solvent-rich phase by heat treatment and to obtain a macropores materials. So the important thing in this process is to combine the gelation time and the phase separation. Because when we have the gelation, we have the solidification of this material that will frozen this transient structure. Then we can remove the solvent phase and obtain this interconnected macropores structure. And the control of the domain size distribution, it will depends on the dynamic and kinetics of this both process, gelation and the phase separation. So in this systems, we have a complex dynamics because it involves network formation during gelation and also dynamic asymmetries between the two phases. And you have several dynamic process going on at the same time from nanometer scale to micrometer scale. So at the early stage of gelation, we will have the aggregation of the small clusters. Then we're going to have the gel network formation and then the phase separation. So to understand this process, we have to be able to probe length scale from nanometers to micrometers and a broad time scale as well from milliseconds to minutes to hours. And XPCS is a technique that will allow us to cover this broader range of size and time. Well, XPCS, it's similar to dynamic light scattering, but using X-rays, we have the advantage to not be limited to the transparent samples. It is not the case of this material at all because they're opaque white gels. And we can also cover a larger length scale. Well, so I know that in these web series seminars, you had really nice presentations about XPCS. I attended some of them. But I will talk in a few words about the XPCS just to remember and for those who are here for the first time. So in the XPCS experiment, we're going to illuminate the sample with X-ray coherent beam. It will produce eye speckle pattern that carries out the exactly arrangement, special arrangement of the sample. Then if we collect several images, like hundreds of thousands of images with a constant time difference between them, we can select a region of interest and we will have the fluctuation of the intensity. And then using the out-correlation function, we can calculate the out-correlation curve. So here we're going to use the intensity of similar pixels with the same q vector and also the same delay time and we average and we can obtain this correlation curve. This correlation curve will give us many information about dynamics. So well, the correlation function has a exponential decay. That's the case with the baseline. Here we can all obtain the relaxation time and this speckle contrast is related with the instrument. The shape of this exponential decay, it will give you as information about the nature of the relaxation process going on the sample. So the simple example is when you have a single exponential decay, so the gamma exponent is equal to 1. It's observed when we have a single relaxation time, a free diffusion, a Brownian motion. When you have a strategy, a exponent, gamma smaller than 1, it's typical observed when we have a distribution of relaxation times. So for example, it's observed in supercooled liquids, where the same sample will have different regions of the sample relaxing with different times. And when you have a compressed exponent, it's characteristic when you have super diffusion motion or ballistic motion. It's commonly observed in soft solids like gels, colloids, polymers, when you have internal stress relaxation. So fit in our correlation function, we can obtain this exponent that can help us to understand the nature of our relaxation process. So now I will move to the results, the most interesting part. So we use a combination of X-VCS and USACs, ultra-small angle X-ray scattering, to study in situ the social process and phase separation for the synthesis of macro-polysilica and the nickelsilica materials. So when we perform X-VCS experiment, we will collect a lot of images to calculate the out-correlation function. If you average this image and integrate it, we also obtain the SACs curve during the same experiment. And we can combine this structure information and dynamic information to understand the mechanism of the sample. So the main goal of this work was to understand the structure evolution and the nanoscopic dynamics at the late stage of the gelation and phase separation. We'd like to understand this moment when we have this phase separation and the solidification of this gel network that will arrest this transient state that will form then the macro-polysilica structure. So to produce this material, we use this cell gel and phase separation synthesis. We used a polymer PO as the phase inducer. So after stirring, aging, drying, and we perform the calcination to remove the solvent and the polymer, and we obtain these materials. So when we do not include a polymer in the systems, we have a no macro-polysilica structure, including a correct amount of the polymer. We observe the formation of this really nice interconnected macro-polysilica structure with the median size around 600 nanometer. We could also include the nickel. Successfully include the nickel in the synthesis. It did not lead to the collapse of the gel. It can happen. It's challenge to find these conditions. And we will obtain a high surface area material. And we observe a decrease of the surface area in the addition of a nickel. Looking closer to this nickel sample, here we can observe this test texture here. It's also this really small mesopores, about 3.5 nanometers that are formed in this voids in the gel network naturally, even in the sample without the polymer. And we can observe the nickel nanoparticles well distributed in the gel structure. We have some very small nanoparticles and also some agglomerates. So we went to the catheter table line. We studied this process in CETO. So we used a sample to detect a distance of 15 meters, the energy 9 kev. The temperature was 40 degrees. We followed this reaction during 360 minutes. And as we were interested in the late stage of the reaction, we studied the slow dynamics using a frequency of 1 hertz. So here you have a photo of the catheter experimental hutch. And here you can see the vacuum chamber where the detector is placed inside. So we follow the dynamics during the synthesis of this material. We observed that up to 290 minutes, we have a really fast dynamic. So we could not follow these dynamics. But with time, this dynamic starts to slow down during the late stage of the reaction. So after 300 minutes, this is the constrained motion of these catheter clusters in the geonetwork. We can obtain more information about this dynamic if you look the Q dependence of the relaxation time and the gamma exponent. So here I selected this green curve at 330 minutes. And here is the correlation function in function of Q. And we observed for this sample have, at this point, bigger than 1, which is widely observed in sorted soft solids. So we have this compressed exponent. This is characterized of hyperdiffusive motion when you have the relaxation of heterogeneous internal stress. And this stress in the geonetwork, they can be built during the cluster aggregation to form this geonetwork. So it seems that here after 300 minutes, we have this geostructure. And we could follow this stress of this network. To have more information about the time evolution of this dynamics, we can also look to the true time correlation function. So as I show you, when we calculate the one-time correlation function, we average the correspondence time. But when you have heterogeneous dynamics, this becomes a problem. So in this case, we do not average and we correlate all the image in relation of each other. And we will obtain this true time correlation map. This map will give you as information about the different states in the sample. So when you have an equilibrium systems, the contour lines are parallel. When you have a slow down dynamics, we observe a broadening of these contour lines. And when you have acceleration process, they will narrow with time. So here, I present you the true time correlation maps for the sample during the late stage of the dilation. What we observed in the beginning, it's that gradual slowing down of the dynamics. So this is expected as the dilation geonetwork fluctuations are greatly suppressive. And then it seems that the really late states, we have an arrest dynamics. So it could be the arrest of safe phase separation. Well, to have more information about this time-dependent evolution, we can also observe how the relaxation time in the gamma exponent will evolve with time. So it's interesting to observe at 330, we observe a change in dynamics. It goes from a stretch exponent to a compressed exponent. And we also observe this change in the relaxation time evolution. So it seems something really changed in the sample in these last minutes. And we can look to the structure of the sample to try to understand better what changed. So here, it's the USACS curve obtained during the same experiment. We observed this, the Guinea plateau that it's increasing in times with time and shifting to low q. So we calculated the Guinea gyrate ranges. It's interesting to note that during the dilation, the ratio is growing slowly. It could be the clusters that are growing as a result of the pod condensation reactions. And then suddenly, it increased and formed structures of more than 400 nanometers. And then it's stabilized. So what to believe at this point? So combine the structure evolution and dynamic evolution where we have a really difference between 320 and 330 minutes, we believe that at this point, we have the phase separation. So we have the geonetwork that's low in growing. It's in those phase separation that's this point to have the phase separation. And then the slow down of the dynamic could be related with the coarsening of these phase-separate domains. So it seems that it's a really slow process, the phase separated. And one, it's happening when the dilation, it's really solid, it's a solid network that will freeze this transient of phase separated. Well, when we include nickel in the systems, it completely changed the dynamics. What we observed, it's alternate correlated and uncorrelated states. So it could be related with the intermittent fluctuation, indicates that you have a large-scale rearrangement when you have the nickel in this geonetwork. So as we saw in microscopy, the nickel, it is well-spurred in this geonetwork. We believe that these nickel centers created a higher stress in this location. And it's why we saw this alternate correlated and uncorrelated states. When you look to the sex, to the structure evolution, at the early stage of dilation, nickel seems to also affect the structure. But at the late stage of gelation, it's very similar to the sample without nickel. It makes sense because even if a nickel is created, a lot of stress in the geonetwork, we obtain macropores structure even with nickel. So it's a stress network. It's affected more the geonetwork than the phase separation. So I'll combine the MC2-XPCS and USACs. We could understand better the mechanisms of the soil-gel and phase separation. Even though this is a well-established method to produce chromatograph columns for high-performance liquid chromatograph, it's basically a trial-and-error experiment. So people, they change the concentration of polymer and solvent and they try to find the condition where you will obtain macropores. And with this study, we'd like to show better the mechanisms, the time when the different process is happening and understand better this mechanism that we can optimize the synthesis and produce the materials with optimized structure. So combining the dynamics and structure, you saw that the gelation, it's really a slow process with a slow growth of these small clusters. We could not see dynamics because there are two small dynamics, two fast. Then after this time, we have the progress of the polycondensation reaction. We will do the phase separation. And once the phase separation takes place, this special arrest of this transient state, the dynamic is slowed down and you have these frozen systems of gel with a transient phase separate inside. The introduction of nickel strongly affects the dynamic and early stage of the gelation. Well, so this is an ongoing study. It's very recent results. We still have a lot of questions to answer. And the next step, we would like to study the early stage of gelation. So for this, we need to acquire data with a higher frequency to follow the dynamics of these smaller clusters during the gelation. And also, I just show one example. But to change this polymer concentration, we will change a lot the process of the material. So we also interested in understanding better the effect of the phase separation inducer in the gelation and also in the phase separation. Then we can figure out the whole picture of the systems. And also for the introduction of metal, we would like to try other nickel precursors to try to see if we can obtain less stressed gel in presence of nickel and then avoid to lose surface area. That it's very important for catalysis. Well, so this was an example of the state of this is low dynamics during the late stage of gelation and phase separation. In this last part of the presentation, I'd like to talk a little bit more about the catheter tab in line. So the catheter tab in line is dedicated to the coherent and time result scattering. We work with three main techniques, so the coherent x-ray imaging. We're doing most typography and also commissioning plane wave. Also, we can perform exegesis, as I show you the example, and usax. So here we have this long chamber, vacuum chamber that allow us to work at different samples to take distance. The beam size that we measured during commission, it's around 40 microns. And here I have information about the energy flux available and also the energy range, the coherent flux and the energy range. So here we have illustration of the location of the main components of catheter tab in line. Here we have the vertical focus mural, the horizontal focus murals, the 4CM monochromator that can be retractable and we can work with monochromatic beam or with pinkie beam. I put some more information about the detector because it is a new house development between a Brazilian company called P-TECH and the L&Ls. So this is a detector based on the Medpix technology. It's a large area detector with 3,072 pixels by 3,072 pixels. That's very important for XPCS where we illuminate only a very small part of the detector, but it is very important for imaging techniques. And we have a small size of pixel with 50-50 microns. For XPCS, the maximum frame rate available today, it's 1 kilohertz and there is a possibility to uprograde to 200 hertz. So I showed you an example of its low dynamics, but as I just mentioned, we can also set faster dynamics. So here's an example of dynamics of a colloid of golden nanoparticles in a mixture of glycerol and water. So these measurements were done at 1 kilohertz and we can here have the SACS curve, the scattering pattern, the average one. Here the correlation function and we from the correlation curves, we will obtain the hydrodynamic radials that fits well the expected value. In Katerete, we also have the opportunity to work with monochromatic bin or peak bin. So we try to characterize the impact of this to different modes in XPCS. So when we use pink bin, well, the signal, it's much stronger, but we lose speckled contrast. So it seems that we improve the signal to noise rate, but we lose speckled contrast. But anyway, it can be interesting for samples that are very diluted or do not scatter well, but for sure in this case, for samples that are not sensible to radiation damage. So there are just two opportunities. And I also would like to show you some recent results from users. So as I was talking to Dina, last year we started to have users during commissioning. And we had this group from a Brazilian university at Rio de Janeiro. They studied the phase is the liquid-leaked phase separation of proteins. So this liquid-leaked phase separations is a natural mechanism in the cell that cell use to organize. However, it's also associated with a variety of diseases. And it's not when you have this liquid-leaked phase separation of proteins, they do not form simple liquid. And it can be liquid, gel, even glass, solid. And the state of this protein condensate will affect the function of the proteins in the cell. And it's related with this disease. So we used species to probe these viscoelastic properties and relaxation behavior of these condensates and then understand better what was the state. So in this work, they studied the prior protein liquid-leaked phase separation. And they were interested in understanding the better what was the effect of different ligands. So we studied these proteins condensate that were formed in presence of copper and the condensates formed in the presence of copper and peroxide. Looking at the outcorrelation function, we can clearly see the difference. In this case, we do not follow the phase separation. The sample was already separated and we are interested in the dynamics of the condensate. So it's relatively slow dynamics. And with the addition of copper, we have a compressed exponent. And when we add also peroxide, we have this stretched exponent. And when we add peroxide, we have this compressed exponent. What's analyzing the key dependence of relaxation rates and gamma exponents, we could observe that in this case with introduction of copper, it seems that the dynamic that we are looking for, it's the dynamic related with the coarsening process of the protein droplets. And when they add also peroxide, it will form a gel-like phase. So we can obtain hardening condensates. And it's important for them to understand better what to change the function of this protein inside the cell when I have this still liquid phase or this really more solid, soft, solid phase. So this work was submitted a few weeks ago and the preprint is already available. Well, so to summarize this presentation, I hope I could show you how we can use XPCS to understand dynamics over a large length scale and time scale. And this will help us understand out of equilibrium state in heterogeneous systems as this example of this complex systems that it's composed by a gel network and also phase-separated regions. So using the coherent X-ray techniques, imaging XPCS, we can understand better dynamics and structure in the large different kind of materials from organic inorganic, liquids, gels, different kind of materials, understand better the local dynamics. We can understand global kinetics and the collective phenomena that are going on the sample. And last slide, I just want to say that there are six bin lines in operation at Cedius. So last December, we have our first proposal, regular call for proposals. So we should have another one soon. If you are interested in coming to perform your experiment in Cedius, we have these six bin lines available with these different techniques. You'll be welcome. And I'd like to thank you for your attention. Thank you, Cathedra Tech Group, for all the work. It was hard these last years of commissioning, but we are really happy that now we are having users and we start to operate in the regular conditions. And thank you.