Cinema 4d Metal Material Pack Free Download
Cecila Dammrich
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i was on the search ,for a good and simple index of refraction equation,that can calculate complex IOR with n and k extinction values,and that i can use for the thin film shader.i found some usefull equation ,that i was testing as stand alone conductor shader,to see if its accurate enough ,for the thin film shader implementation in cycles.
first testrender with gold values from the refractive index website.i used the 0.6 for red, 0.56 for green and 0.45 um for blue on the website and put the given n and k values into the shader.here the result.
UPDATE 2.0: Updated for my presentation at the Blender Conference 2022 I updated the OSL script to use the current language features and made GPU-compatible nodes from it with OSLPy. The output is fully benchmarked against optical models I used as a...
For instance this is using your thin film shader to emulate the thin layers of oxide that form on iron as it heats up - guesswork on the IoR and thickness values to get approximate color bands.
hotmetal.png960540 669 KB
Keep up the great work, it is VERY much appreciated.
in the past weeks i have learned alot about thin film,dielectrics and conductor materials.the first most confusing thing, with the extinction value is,that it behaves different on metal vs dielectric materials.so for dielectrics there is no use of a k value.if there is a need for absorption in dielectrics,than the beer lambert equation fits very well for this(like the refraction shader or sss shader).in metal the extincion works the otherway way simply sayed.if the transmitted light hits the metal,and the higher the k value is,the less the light gets transmitted,so its gets reflected more,simply explaned.
RickyBlender,corrosion is like another metal,so no.but you can mix it with different settings ,with/like all other shaders sure(pointness grunge come to mind).
at this state it is simply one air/metal equation,one layer.
sample file maybe later.the main reason for this thread is to ask for reference datas for comparsion.if the equation is close enough i post the blendfile,otherwise i dont want to post a shader that gives wrong results.
i am not sure, what you mean with Principle shader has better Fresnel correction,i havent used a clear coat on top or anything .anyway you can connect the shader output, to every input you want to your need.btw the shader it self ,is a Fresnel equation.
if i can implement this equation to the thinfilm shader,than you can play with dielectric/metal layer and thickness variations.that should give maybe some possiblitys.later than maybe i make another thinfilm shader with metal/metal layer.
I found the old file
yes I think it was done with some group nodes
one for each metal type
and in group node you have metal name which call the right group
so very user friendly and easy to select
if we want the whole wavelength spectrum from the database.then a complete different code are needed, at least for the thin film (or if you think of filter out the usefull datas, from the database.this script alone is maybe bigger than the shader code).for me thats to complicated.and btw at least the CIE XYZ ,for better wavelength calculation,is still a missing feature in cycles.same goes for the lack of vector calculations with the math nodes.
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Nanometer-thick passive films on metals usually impart remarkable resistance to general corrosion but are susceptible to localized attack in certain aggressive media, leading to material failure with pronounced adverse economic and safety consequences. Over the past decades, several classic theories have been proposed and accepted, based on hypotheses and theoretical models, and oftentimes, not sufficiently nor directly corroborated by experimental evidence. Here we show experimental results on the structure of the passive film formed on a FeCr15Ni15 single crystal in chloride-free and chloride-containing media. We use aberration-corrected transmission electron microscopy to directly capture the chloride ion accumulation at the metal/film interface, lattice expansion on the metal side, undulations at the interface, and structural inhomogeneity on the film side, most of which had previously been rejected by existing models. This work unmasks, at the atomic scale, the mechanism of chloride-induced passivity breakdown that is known to occur in various metallic materials.
Corrosion is one of the major causes of material failure and hence leads to a huge cost to our society1. The nanometer-thick passive film on metals resists a general corrosion, but it is susceptible to severe localized attack in certain aggressive media2. The best-known inducer of localized passive film breakdown is the chloride ion. Despite the enormous amount of experimental data and diverse hypotheses and models proposed till date1,2,3,4,5,6,7,8,9,10,11,12,13, the breakdown of the passive film is still not sufficiently understood and remains one of the most important and basic problems in corrosion science.
Without doubt, deciphering the interactions of the chloride ion with the passive film, including chloride-induced modifications to the properties of the passive film at the atomic scale, is key to understanding the precise mechanism of passivity breakdown. In the present work, using aberration-corrected TEM (Cs-corrected TEM) and a fast and precise super X-ray energy-dispersive spectrometer (Super-X EDS) analysis with four detectors, we simultaneously investigate the film and metal matrix as well as their interface via cross-sectioning in real space. We find the chloride accumulation within the inner layer of the passive film and the associated fluctuations at the matrix/passive film interface. We provide direct evidence on the location of chloride and the resultant phenomena of the lattice expansion on the metal side, undulations at the interface, and structural inhomogeneity on the film side. The present findings allow for the atomic-scale mechanism of passivity breakdown to be revisited on the basis of real-space imaging in multi-dimensions.
The TEM observation in the high-angle annular-dark-field (HAADF) mode and Super-X EDS analysis on the passive film were performed and the results are shown in Figs. 1 and 2. Figure 1a is the HAADF scanning transmission electron microscopic (HAADF-STEM) image showing the passive film on FeCr15Ni15 single crystal formed in H2SO4 electrolyte (condition 1). According to the contrast difference, the film seems to be tri-layer structured. Whereas the EDS mapping analysis (Fig. 2a) indicates a well-defined bi-layer structure with the inner Cr-rich layer and the outer Fe-rich layer, as generally accepted29,47,48,49,50,51. Interestingly, after aging the specimen in air for a few days, we also subjected the aged specimen again to TEM observation and we found that the contrast had become homogeneous, following disappearance of the middle darker-contrast layer (Fig. 1b). The implication is that the outer layer of the passive film, formed by precipitation of the hydrolyzed metal cations, is transformed to the metal oxide by a dehydration reaction, which was confirmed by XPS analysis34,38,39,50,51. It is worthwhile to mention that the HAADF mode image provides an incoherent image using high-angle scattered electrons, where the contrast is strongly dependent on the scattering ability of heavy atoms. Thus the much denser metal matrix would show the brightest contrast, followed by the metal oxide, with metal hydroxide displaying the darkest contrast. From the foregoing and taking into consideration of the EDS mapping results, the inner layer is a Cr-rich oxide, while the outer layer, with the darkest contrast should be Fe-rich hydroxides. The unavoidable exposure in air going from passivation in the electrolyte to TEM observation allows the outmost hydroxide layer to be partially dehydrated yielding the brighter oxide, thus giving the film an apparent tri-layered structure in the HAADF-STEM image. With prolonged exposure, the hydroxide layer became completely dehydrated and the passive film correspondingly reverted to an oxide film. Although the oxide film has a bi-layered structure distinguished from the Cr-rich and Fe-rich layer (Fig. 2a), it can be hardly identified in the image taken with the HAADF mode (Fig. 1b), since the contrast in the HAADF image is strongly dependent on the scattering ability of heavy atoms that is associated with the atomic number. Here the atomic number of Fe and Cr is rather close, making the contrast of Cr-rich oxide layer and Fe-rich oxide layer seems homogeneous. The above results provide direct experiment evidence of a dehydration model.
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