 And so what I will talk about, it's about coherently diffraction imaging at nanoscale. So as you know, I'm coming from Daisy and Daisy is really a remarkable site with Petra III ring and with the flesh holes, two holes flesh and X-File option. So that starts here and then in three kilometers, it has its playground to place where we are. We do experiments, so it's really a remarkable place now for coherent and ultrafast science. And I'm happy to be at that place. So about coherence first of all, well, we all know that coherences can be presented in kind of two ways. So it's a longitudinal coherence that is all about the wavelength difference and it's related to the bandwidth of the light and special coherence that would build the most importance for today's talk and that is coming from the angular size of the source. And so coherence diffraction imaging, so it's coming from partial coherence x-rays or electrons that can be and then we pass by through the slits that define our coherent beam and then we put our sample and then we could measure either the forward direction or in the break direction depending on the type of experiment. And then we hope that, and then we substitute optics that that would be between sample and CCD. We substitute it with phasor material and we hope to get to the fraction limited microscope. And as we all know, we are not yet there but we very much hope to go towards there. So, and how we do phase retrieval. So it's typically we do free transform between the real and reciprocal space many times and we put reciprocal space constraints in the reciprocal space and we put real space constraints that are typically finite support and positivity quite often. And so some other constraints and then we get, hopefully we get a result in this case. And in simulated diffraction data we get it quite nicely. So we start with diffraction pattern and then we put support and then slowly this phase is coming of this nice lady with all the details on all the details about the hairs and everything you can see here. And it's so nice of course, in the, on the simulated data but unfortunately, as you all know that the process is going quite slow. I mean, some collecting data to real images and publication takes sometime two or three years until we are there and until we publish results because we have to understand also what is happening. And so now coherency resources. So it's APS of course, it's a new SRF EBS, it's spring gate in Japan and of course, it's better three in Hamburg. And unfortunately, Dina, I don't have max four here picture but I should have hit here max four picture of course. And so, but we do quite a bit of experiments now Petra three. And so here is a sample environment that sucks wax set up at P-10 and then here also sample area during experiment at P-10. So it's here, you could see how it's all coming. It's X-ray beams, it's leads, it's sample. And then here's some microscopes we have of course and then the beam that is passing by to detector that is in five meters typically. So and here it is a brexidized set up for when we have our detector about two meters away from here and here again, here microscope and on this stage we put our sample and be beams coming from the right side. Okay, so now we go to nano science and we, I will start first from nano crystals and the data that was done in collaboration with the university and with Petra three team at P-10. And you know that photonic crystals are quite natural in nature. So this nice colors and the wings for butterfly and to this opal samples that women like very much. It's that these colors are coming just from the fact that these color systems and then raising them on my former PhD students he started just this color those systems of the butterfly wings in this paper. And so there are artificial photonic crystals and that they can be made from one day to the engine 3D and also importantly that there is, they are also photonic but when you get materials and as we could see for certain frequencies light is propagating. So here light is propagating inside the system and to this frequency it's not propagated. So it's just reflected complicated topic. And also if you will have defects in such systems then we could manipulate light like here it is shown. So having some distortions or some special defects where we can propagate light as shown here where we can turn it around by 90 degrees. And so here are different defects in color your crystal that here is a CM image of internal facets of certain and also. So of course we need good methods to visualize the defects inside the photonic crystals. And so for that way we did the following experiments. So, and this is the way how people call. So let me see here is the point. So I have showed just before my talk that people in Brazil are just building up sucks build beam line that would be devoted also for coherence measurements. And that's exactly what we do here. So we collect by CRL will focus our beam slightly. So it's about a few micron size focusing here. Then we have a cryojet to cool our sample and then we have a carbon fiber on which we put our sample. And then we collected, as I said, then five meters we put detected and we collect the fraction patterns and we rotate samples. So it's kind of here in tomography that we are doing. And so here angle is quite small rotation is 0.5 degrees and we can collect it from zero to 180 degrees. And in this way, we have the full reciprocal space. So now it's like that. So here how to the deflection patterns looks like. You see how they evolve and how. So we have these break peaks that are also changing while rotation. And also we have some streaks here will appear at some point, I hope you will see it. No, you don't see it yet. And then you can put it into 3D in this image and here you can see streaks connecting break peaks. And so from that, you could already guess that there are some defects, some plain defects in the sample. Okay. And so then we do phasor retrieval. And first of all, we'll look on the break peaks on the break peaks that is highlighted here. And actually wherever it's over six break peaks over six break peaks. And so here is the break peak reflection. And after performing reconstruction, we get the shape of our sample space. And then we're using the shape as our support. Then we can construct, use the construction of the full data space that was collected in 3D. And then we can obtain this beautiful pattern that shows already as you can see the layers of the colloidal crystals here. And also the positions of all the particles inside the system. And so here you could see one cut through them 001 crystalline plane. And you can see it very nicely. This hexagonal order that is very well seen here. And also when we, and also where we could see stacking ABC staking or ABA staking that is the first one is FCC. And then HCP staking it quite often it's broken this or this broken it. Then it's the HCP staking when it's ABC and then it would come there. And if we project in this direction, then we can get the full staking. So as you can see, it's quite complicated here. It's only here ABC, ABC, ABC, but otherwise it's all different. So it's really with the HCP staking here. And also what we can see here, we can see that the double atoms or some vacancies here as you can see here. So it's really interesting to examine it some point. Okay. So then I mean that's the consistency is visualized. And then of course, it's a question of the resolution that that is very important. So on the text at that time when we were measuring, so we obtained the maximum Q value gave us a resolution of 56 nanometers. It is nice, but not so nice, of course, it's not so exciting, but we have seen that took a little particles with the size of 70 nanometers of our results according to really criterion and distances more than 18 nanometers. That's already something, not very good, of course, but something, but then we identified the position of each individual colloidal particle in the lattice was determined with an accuracy better than nine nanometers. That is already quite something. Okay. So, and recently we continue to this experiment on a little bit different system. So it was not colloidal grain, but it was mesocrystal go-go grains. So this is a paper. And so mesocrystals is a structure composed of numerous small crystals of similar size and shape, which are arranged in the regular periodic pattern. And what is important that they're all connected with some organic molecules. So typically it's long organic molecules. Typically it's also like X and S. And so experiment was quite similar. So we have a source, we have CRL, but which will focus the beam. We have a sample and we have a cryojet again and then we're rotating our sample. And then on five meters it was our detector. So then nanoparticles go to the cubic shape as you could see here. And today we're about 16 nanometers inside. Then we had such very nice cube, but it was a little bit big for our measurements. And so from that way we drilled actually in the middle, we drilled it with the focused iron beams and we took a grain of this crystalline particle. And of course, while cutting it by a fib, it didn't look so nice in the CM as we can see here. Okay, and so here we measured again reciprocal space as we could see here again, we could see break peaks. And here fringes we could see from different facets of the crystalline sample. And we can see that there are some defects here maybe because break peak is divided into two break peaks. And so here it's an average, and here this break peak is that is shown here. And here again reciprocal space in movies, so you can see how it's changing here. Well, okay, and after reconstruction, so reconstruction was made by Jirong Harnes. And so here we could see results of construction and here's some cuts from the, here you could see some cuts through the middle of this grain and you could see here cracks, you could see here cracks and some point defects and some lattice bending. So it's quite complicated structure that was finally. But it's important to understand this structure. And so you could see how it looks like and you could see some items on the surface and some voids here. So that's quite important. And so then we made very careful analysis. So it's a displacement map with the red arrows is shown in displacement map of 3D super lattice and also you can assign by running directly a polyhedron, you can assign different type of stretching, different parts of the sample actually. And then you can make also from that after you have the full displacement map you can map out 3D dilation map of this super lattice that is some of strain components of epsilon xx epsilon yy and epsilon zz. And you could see that grain is really quite complicated, strained in very complicated way. And here it's just individual components here as shown and you could see that it's really that strain tensor is quite complicated. But important to understand this structure but importantly after this results you can obtain the full strain tensor. And here how dilation map looks like 3D. Okay, so same that. So I will go now to break the hermit CDI and then so and this as I said already so you are coming to the same way with the hermit beam you put sample but now you measure your break geometry. And so here are a few equations I put just for in the kinematic approximation has amplitude that is connected to electron density and it's free transfer of electron density. And then as soon as there's a crystal we put here periodic electron density of the crystal. And then you can show this scattered amplitude near one of the break peaks. It says given by this function where this S of H is a shape function that is equal to one inside the crystal and zero outside the crystal. And what is important here it's this phase factor that is projected strain field in the crystal. And so for crystallographic sample we get from distribution of strain and that's where the whole method is going and we know a lot of people that use this nowadays. And but what is important to remember that in break CDI we do not get information about electron density but we reconstruct the amplitude and phase of so-called crystalline function associated with the given reflection. And that this would be clear from the examples that I will show just now. Okay, and here it's in Robinson likes such pictures so where he shows how this strain, this phase is appearing so it will have lattice and then displaced lattice and then it's shifted by this formation field and that that's how this phase is appearing here. Okay, and also sensitivity to strain can be shown in this model. So here is in one model it's just ideal lattice and here is a lattice with some shifted planes and you could see here it's a really ideal copy of all the break peaks and here some deviations are appearing. You can see here for example that is showing that it is not an ideal lattice. And this gives you an idea of how you make in 3D that this measurements or in this case you just rotate it around your break angle and then your CCD is passing by through the reciprocal space and then you measure the full reciprocal space this way. Okay, and so applications to catalysis and catalysis is very important issue nowadays so basically it goes by a rainy situation and by putting catalysis we just changed the barrier for some chemical reactions so below with this barrier and that is important because any chemical reaction is going by this rainy situation as soon as your barrier is smaller than your chemical reaction is going faster. And so as we're now increasing the rate of chemical reaction by lowering the transition barrier in terms of the kinetics or speed of the chemical reaction. So here are some different calculations of different reactions and of course it's a big thing. It's a big factor that I did for that and the catalysis particles are quite small some of them about one micron small of course about a few nanometers. Okay, so then present use of catalysis it's cell light crystals and small hydrocarbons and nickel particles and also platinum is very popular. And so we've made a few experiments here on that line. So it's a chemical infection of single nano platinum nano particle that there in the reaction conditions and this was done together with the HDL group and there's a nano lab and it was done at the surgery. And so here are some gifting calculations that shows how platinum is really reacting on different conditions and how the list extraneous evolving in particle inside the particle. And so we considered different atmospheric conditions argon and argon plus co. So energy of the beam was 8.5 kV and beam size was 300 nanometers. Simple detector distance was 0.68 meters. And here it was shown how you collect break peaks. And so here it's also it's a dome here where you have different atmosphere and here's platinum particle which you do your experiment. And so here is the fraction pattern and then you can face the retrieval and then finally you get your reconstructed particle and here you see the gap. This gap is especially here that is well seen. So then what is the origin of this gap? It's just some part that scatters in some other direction. It's not one one one direction where most of the particle is scattering but that scatters to another direction. So there are probably some stagnant faults and due to that this part of the crystal it's invisible. The electron density of course it's uniform. It's going from one part of the crystal to another part of the crystal. So okay, so oops. So in argon atmosphere here that was a particle in argon atmosphere and in argon sewer it's slightly changes and then we could see the strain part. So here is, so shape is imposed together with the strain part. So strain is in color here as shown and here you could see to the images through the center of the particle in this direction cut and you could see this part that is not visible. Now the case and slight strain changes here. And so in order to visualize it's better we will put histogram of the bulk strain and histogram of the surface strain. And so here you could see that when you saw different. Okay, so then I will go to second paper. So it was Kegelsen desegregation and platinum rodium nanoparticles and it was done in collaboration with Hordu U group and Andre Stirli group. There's a nano lab and experiment was done at the APS of being like 44 IDC. And so here is a same picture of the platinum rodium nanoparticle and the small guys here these are rodium nanoparticles that are scattered around on the surface. And here is the fraction pattern of this particle and here the shape that was reconstructed. And here again we have different gas conditions so it was helium initially then it was oxygen of different concentration 2.7% of oxygen 5% of oxygen and then 3.8% of hydrogen then. And we could see that in the hydrogen atmosphere the shape started to change and also here is a strange results and also and strange here is represented by the and by the concentration of rodium particles. And so when it's read it's more rodium so it's mostly on the surface and it's depleted from the center. And this results was from 515 degrees C and here is temperature at 700 degrees C and so this temperature gives us a different path length for the rodium particles from migration of the rodium particles. And so we could see how this is changing again helium and oxygen and hydrogen atmosphere. And so we could see that we have really a certain segregation here on the surface of the particle of the rodium. And this was even better revealed when we did certain analysis. So this is distance from the surface this is on the surface and this is going to the center of the particle. And so here for hydrogen you could see for 550 degrees in hydrogen it has a jump here of rodium. And here at 700 degrees it's more or less the same and to go in hydrogen it is still a little bit high here. Okay. And to rethink that the following is happening so that as soon as these particles were exposed to air so then rodium oxide is formed in this for the small particles and for the big platinum rodium alloy particles it's all covered by rodium oxide in oxygen atmosphere this oxide is becoming even thicker but then in hydrogen environment it happened in a repulsion of rodium oxide and then particles start to come to this big particle and so here we have more rodium it's becoming the surface of this particle it's becoming more rich. Okay. And the last experiment that I will be talking it was a single alloy nano particle it's imaging during the deterioration and this was in collaboration with Andrea Stirligrup at the Nanolab and KIT in Kalsyroa and it was done at SRF-ID1. And so here we started platinum rodium nanoparticles as I said already and so the position was 60 to 40 approximately of platinum rodium and particularly on struts and titanate substrate size where the particle was about 600 nanometers and we went immediately to 700K and here conditions were the following. So it was argon, then argon plus CO, then argon CO and oxygen and then again argon CO again and here is a CM picture of the particle and here is a wolf plot of the equilibrium shape of the particle and you can see that it's very close to this equilibrium shape. Okay, so experiment was done in the same way like we do with the SRF and here is the intensity distribution of the particle in 3D and so then here is a series for different gas conditions for the particle and here the cuts shown here, blue, yellow and red cut and you could see how it looks like and clearly we see that resolution in the vertical direction is much higher than in the transverse directions. Okay, and then we made phase retrieval and here is the result of the phase retrieval so that's the shape of the particle that was shown here on 0.55. So it was cut at 0.55 and here is a strain also shown at the same cutting value and so you could see some evolution of the strain as soon as we're changing the gas conditions and here we look inside of the particle and strangely so we have quite a bit of strain inside the particle as we could see here and also on the surface and on the bottom and I think that that is related to the effect of that it's probably particle is stuck at some point where some defects on the surface. Okay, and here it is very important so we performed a phase-phase strain analysis and we could see how the changes are happening for different facets so that these are 1-0-0 facets and we could see that here it's about strain is about zero but then as we change argon or so it's shifting here we could see that in oxygen condition it is shifting to highest strain values and then it's again relaxed and goes to negative strain values and also here for 1-1-1 direction so it's first it's positive strain and then it's more in oxygen conditions it's more zero strain and it stays more like that in argon-co conditions and the same is valid for 1-1 conditions and here is surface and bottom particles so these are the surface on the top and on the bottom, on the bottom you can see that air bubbles are not much higher than for the top surface and here we see opposite things so here it's positive and here it's becoming more oxygen it's even more positive and then it comes back. Okay, and here an interesting point came out so here we tried to understand how what was a resolution for different facets and then we found out this nice paper that was made at EPS actually and so then we performed similar analysis in this paper and we obtained that we have a resolution from five to six, seven nanometers and sometimes above just three nanometers in the vertical and bottom conditions so it's a very high resolution record here. Okay, and in the end I will spend a few minutes about and we'll talk about the fraction-limited storage rings and so as you know, the brilliance is defined by this equation where sigma stays for the total floating soil size that includes horizontal and vertical directions and that includes radiation from a single electron and size and derivations of electron beam. And then here in flux is nothing else as example, half squared multiplied by brilliance. And to then here we could implement the meetings for example, in particular direction and then due to Heisenberg principle, emittance is always higher than a number of four pi squared and so if we get equality here then we are so-called in the fraction-limited storage ring situation and how to get there is clear so that you have to minimize your emittance from the beam. And that is a nice plot that is showing how brightness is the same like brilliance, how it is changing. And so we have first generation, second generation rings, third generation rings and now we have this, so here they were called alternate rings or fraction-limited rings that have this gain here and then for if you also have even bigger gain here and here what is interesting that it's related to the photon degeneracy parameter that is for one extra is calculated for one extra and you could see that it will have for third generation rings, it's about 1% then for the second generation ring we have about two, three probably and no, no, it's, so it's 10 to two, so it's about 100 or 200 and here we would have 10 to two, so then you could think about here in the optics experiment. Okay, and so we'll try to analyze this, it was done in this work and we have analyzed it very carefully with the XRT program that was very valuable for us and then we understood that asymptotic limit for photon emittance is a rather number over two pi and not number four pi as we thought initially and you could see here how it's asymptotically coming here and different colors means different energy spreads. So for at zero energy spread and then here it's one 10 million, here is two 10 million and if we look on the coherent, we can stop this button, I don't know. Okay, so if we look on the coherent fraction that we could see that for 500 TV which really will come to one for coherent fraction and if we have one pin, it's a little bit lower and two pin is lower, but still for 500 TV we are very close to the fraction limit case for 12 TV we are less, the fraction limited less at 24 and less at 50 TV but we are still much, much, much higher than at Petra 3 ring, for example where we have only 1% of coherence in fact. So to reach the fraction limited, how the emittance should be reduced to one peak emitter radian and below but at the moment we are not yet to the technology career and here it is shown number of modes that were obtained here so for 500 TV, it's about three, four modes and we estimate contribution but when it's above 1% and unfortunately for 12 TV we have already about from 13 to 20 modes will contribute to the beam and for as soon as energy is higher than more and more modes contribute to the beam and to do energy spread effects so I observed that more modes and reduced coherence will be attained. And so, nevertheless, we are planning to build up Petra 4 ring and so it will cover tender to work hard x-rays and it's 6G electron energy. We are planning to increase the nuclear infection by terms of magnitude and the aim is for 200, sorry, to 20 peak emitter radian horizontal emittance and that's extrapolation of the present day techniques and increase of number of unweighted ports. So we plan that we would have 35 unweighted ports and 28 planned at the moment. There are some three ports that's special. And so we're planning to build an additional experimental hole that is shown here. So that these are existing holes it's much from the lower hole, it was the first hole. Then there were two extensions here, more extensions and so on and here is additional experimental hole that is planned to build. And here is a time plan. So we plan, so we are now in so-called TDR phase that's planned for two years, about two years. So we finished the TDR phase and we have TDR on the project. And then we start or we plan to start on somewhere in middle of 2023. And to the end we have a dark time from 26 to 27 and from 27, from 28 on we start Petra 4 operation. At the moment it's planned to like that but of course it will depend on the politics and on many other things. Okay, so I'm coming to my summary. So Cartesian deflection imaging is a revolutionary technique. It allows the emission forward geometry in theory, non-periodic samples, colloidal crystals, mesocrystalline grains. It allows the emission bright geometry in nano crystals under different external conditions in shape and strain you can obtain and nano crystals under catalytic conditions and deflection limited sources are especially those huge for this technique. And here are members of the group like it was three years ago at the moment. It's only three people in the group. And here are former members that listed kind of longer and longer. And so thank you for your attention. Thank you very much even for this overview on the technique and on the applications and the work that you and your collaborators have done recently. So the session is open for questions. I hope actually also newcomers to the technique can ask questions to even see that he has done some proposed some introduction to the technique again. You can use the chat, you can raise your hand. I have a question about the... You should start running to hit the audience a little bit. Yes, I have a question about the colloidal crystals, actually, I mean, you're analyzing micron size crystals. Yeah, yeah. So what is the information that you're hoping to extract and how this can be useful then for real application? Well, information that we extract in this case. So let's second, oops, I have to share a screen from there. So let's second our screen back and... So as I said, for colloidal crystals, it's really important to understand this defects structure in the crystals. And especially, you know, all these defects inside are very important today because people are thinking about you're using it for manipulation of this crystalline or this colloidal systems. And they were made by kind of simple technique when you put your glass substrate into the colloidal solution and then by time it grows up and then it grows just by time and that's temperature control has to be very careful. And so this is very simple technique, but you should be careful that all colloidal samples will be in a very small size distribution that then it will go through. We don't hear you. Yeah, sorry. But in terms of feedback, then onto the fabrication techniques, this is an important information, right? Right, right. The problem is that we have to also, I mean, these are small samples that we could investigate by this technique because that's actually a good thing to think about PETRA-4 because the PETRA-4, we would have here in Slant much bigger than PETRA-3 and also the distances will be hopefully much larger so that they plan like 20 or 40 meters for the hole for the adherence scattering. So in this case, we could measure larger grades and that would be very important because at the moment we just scratch small grains from the plate that is grown and just take one of them and study it. And so I guess it could go into some larger samples and could be become quite important to HIK in future. Yeah, I see Dmitry. Please unmute yourself, Dmitry, and ask your question. Thank you. Thanks for the nice talk, Ivan. I have a question actually. Maybe I just don't understand correctly. You showed the imaging of this mesocrystal. I don't remember what were the scales in all three dimensions but do you have any problems with the longitudinal adherence? Like shortage, basically. Yeah, yeah, yeah, so... Or it's not applied in this type of image. No, no, no, that's a good question. So it's about here is one micron. So it was about two, three microns probably. I don't remember exactly the size but that's a good question. So we should be careful with longitudinal adherence but luckily here we're measuring the forward direction and in the forward direction we are kind of more forgiving for us. So from the point that in the break we have to be careful with scattering from the top surface and the bottom surface and it gives you certain path length difference but here as soon as we are in the forward direction so the path length difference is given just by the thickness of the crystal and coherence is about two, three microns. We have longitudinal coherence here in this case. I mean it's on the scale of single microns, right? So we need to see how to reconstruct something meaningful. Right, right, right, right. So it's about the same size. So we're kind of on the safe side here, right? But in principle, you are right. So if we will go for larger samples then we should be more careful even in the forward direction because then we could have some troubles in this case, right? But I think again in the forward, I recall it that in the forward direction we are less sensitive to when you do know here and so that's a very good case for us. But in the break we should be extremely careful that that's why we are limited. So there are a few things whereby we are limited to let's say 200, 500 nanometer samples because otherwise we have either diffraction effects or we have longitudinal coherence effects or some other effects that could spoil our results. That's clear. Okay, thank you. I see you Nying, unmute yourself. Did you want to ask a question? Actually, yeah. I have a question for him this page. By the way, it's very nice to talk. I mean you cover many different aspects. Now in this slide, two questions. One is what is the real application of such old major crystals? And secondly, these are all real. I mean, not really artifact but all the small particles on the surface is real. That is the case. Yeah, it's real. You could see it here. So I showed it in 3D, but you could see it also in this image. You could see it at nanoparticle. So I think it's all real and all the cracks are real. And unfortunately it was quite damaged and I am afraid that it was damaged, especially by FIP that we used, you know, because initially as it was here, initially you can see that it's quite nice crystal. It was grown quite nicely. But size was a little bit large here. You see it's 400 nanometer scale. So it was about, yeah, probably a few micron size. It was, yeah. And so, yeah, that was a bit of an unfortunate for us. And that's why we took just central part of it and looked on it in this way. And then we could obtain all these details. And so here, probably here. And here we tried to understand this all by putting the displacement map and especially by calculating strain in all three directions. So here how it was made. So our collaborators actually, so it was not our part of the work, but they took the average structure that we determined for this crystal and put it all in the center of the reconstructed grain and then calculated just shifts from this ideal structure to each position. So this red arrow shows this shifts. And then from that, you can obtain strain in all three directions. So that's a little bit different from Brexit. I went by obtained strain also only in the direction of the scattering factor. And so this is, I think it's very important in future it would be very important, but again, so it was a small grain and we continued this work. And so I think at some point we could come to some nice applications also. But is this good for catalysis or what? No, no, no, it is not related to catalysis and no, no. So the catalysis, it was quite separate work and where we look on a single nanoparticles of platinum, platinum, rhodium nanoparticles it's absolutely separate. At the moment that separate, I don't know, hopefully in future it would be also interesting to study this. And here it's actually, it's quite interesting point here. So I would probably go back to the fraction pattern. One interesting thing we have observed. So when we have for this 16 nanometers particles that we looked on, yeah? And so that they will cubic shape and they formed cubic lattice. And you could see very nice break peaks from the cubic lattice and also some fringes here coming from the surface. So it all worked here. But as soon as we looked on magnetite particles that were 16, 16 nanometer size, then we failed to reconstruct. So we managed to reconstruct the total shape but we failed to reconstruct position of each particle. And so that is a good point really in order for understanding where were the limits of the methods and where were, and why it was happening because break peaks were on the minimum of the length on the minimum of the form factor. And so then we had trouble to reconstruct properly. So I don't know, probably it gives measure of limits for the technique, I don't know. Could it have been the longitudinal coherence hurting you there? Cause the 16 nanometer crystals would give very large- No, no, no, it was 16 nanometer particles that were assembled again in the same way to form mesocrystal. And so the form factor of individual particle was having minima exactly at the position where break peaks were, you know? That was, so break peaks were kind of lowered due to the form factor, you know? And so that was unfortunate in this case. And so that we have kept in mind such kind of things. But when particles are bigger, so then we have a hope to construct and to obtain each particle position. And at some point you talked about the resolution of this image or was it one of the other images? And I didn't quite understand the nine nanometers. You said you located the particles to nine nanometer resolution. Yeah, yeah. So here, for example, in this case, we calculated distribution function. And we looked on the width of the pair distribution function and we saw that the distribution function is sigma values, six nanometers, seven. So here we obtained even higher resolution as we understand that positions of which part was determined with this six nanometer. On average. RMS, yeah, yeah, on average, of course. Actually, I find this an interesting approach. I had a similar question on the colloidal. I think you were talking about the resolution on the colloidal. So I assume that the particles are spherical for this. Yes, yes, the particles were spherical. Yes, yes, yes, they're there, they were spherical, yeah. And they were quite large in size and they were about 213 nanometers inside there. So they were quite large, yeah. And again, so as we have seen, so for large particles when break peaks are closer, so that then we have nicer construction, so for 60 nanometers we also get the construction. But when we're lower the size of particles to 16 nanometers, then we fail to reconstruct. And I don't know whether it's some generality in this rule or it's just was occasional. It's things to explore stuff. So Ivan, can you remind me again why was the resolution limited to 56 nanometers? It's like the scattering power. It was just scattering pattern, it was, yeah, so in this case, yeah. So here Q-max was just so that the X was an estimate of the resolution was given because 56 nanometers. But then when we looked on them, how we do particles with the size of 70 nanometers, so that was an average size that we see here, that was 70 nanometers. And then, so according to two, like, criteria, distances should be about 18 nanometers. Then you resolve them according to criteria. But then again, with nine nanometers, so that that was position of each particle in the crystalline lattice, you know, it was determined better than nine nanometers. Actually, I think there is an analogous for scanning diffraction microscopy if you have a very wide peak in reciprocal space. You can still evaluate the center of mass on the detector, even if it's over many pixels, and you have a sub-pixel. So it's very, very interesting. Passos, I see that you unmuted yourself. Any questions? Yeah, I have a question. You initiated more questions by asking questions. So I guess these peaks that we see originate from the scatterers, the individual crystals, right? Right, right. So if you just went and you picked one black peak of those and you faced that black peak, you would get only one component of the displacement. Yeah, so that's no. So if you go to one break peak, so as I showed it here, so then you will get the shape of the particle, right? So if you go to one break peak that is shown here, then after reconstruction, you will get the shape of the whole structure. The whole structure, yeah. Right. And then we used this as support to reconstruct the particle. For the support. Yeah, yeah. So this was used as support. And then we used the full map in order to obtain this already position of each color book part. OK, so let's say you showed a tarot for the resolution. Right. That defines the resolution. But I was wondering if you got a read of a few break peaks. Let's say if you what? If you deleted some signal. No, that was the total scattering here, you see. So here, so the break peaks are here. They are small, but here it's the full. So detector was small at that time, you know? So it was maxi peaks, I think. And it was small detector. So as you could see that our break peak, so our scattering is larger than the part that is on the detector. And that was the maximum Q max that we see. My question is, if you delete some signal from a few break peaks, have you tried the phasing that and seeing if it works? No, we haven't tried it. Because you delete the center from what I see, right? No. So here there were some mess here, but then they were recovered. So intensity was rescaled here. And then it was continuous in intensity here in the center. Thank you. Any other questions or comments for even? I think that this discussion was quite rich. And I would like to thank Ivan again for the talk and overview and everybody for participating to the discussion, which is the most interesting part of this. Thanks again, and we'll see you in a couple of weeks.