Advanced Inspection of Surface Quality in Continuously Cast Products by Online Monitoring Alejandra Slagter Mechanical Engineering, master's level (120 credits) 2018 Luleå University of Technology Department of Engineering Sciences and Mathematics
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Advanced Inspection of Surface Quality in Continuously Cast Products by Online Monitoring
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Continuously Cast Products by Online Monitoring 2018 1 Acknowledgements I would like to express my gratitude to the European School of Materials (EUSMAT) for the financial support to carry out this Master Programme, and to the AMASE Master Program Secretary for their constant support during these two years. I would like especially thank my supervisors Esa Vuorinen and Pavel Ramirez Lopez for their guidance and support during this semester. In addition, I would like to give my sincere thanks to Rosa Pineda and Pooria Jalali that have always been there to help, for their endless support. In addition, I would like to thank Swerea MEFOS for the opportunity to carry out my master thesis in this research institute and the support during the project. Finally, to everyone that has contributed to the development of this project, technicians at Swerea MEFOS and friends and colleagues both at MEFOS and LTU, whom not only contributed with productive discussions but also have been there to support me along the way. 2 3 Abstract The present Master’s Thesis is dedicated to the study of a laser scanning system and its applicability for the detection of surface defects at the end of a casting machine in a steel production plant. Both room and high temperature trials were carried out on different carbon and stainless steel billets and slabs. For the high temperature tests, the samples were heated until a maximum temperature of 1200 C. For all trials, the surfaces were scanned with a blue laser sensor in order to generate a 3D representation of the as-cast product surface. The applicability of a blue laser sensor was proven for carbon and stainless steel surfaces, both at room and high temperature. Defects such as depressions and oscillation marks were detected, as well as some small corner cracks. Furthermore, the full transversal section of billets and slabs was reconstructed from different scans of the faces of the products. The effect of different scanning parameters on the resolution of the scans and the final results were analyzed and discussed with special focus on the scanning strategies that would be optimal for the industrial application of the sensor. A microstructural analysis was carried out in order to correlate the subsurface microstructure with the presence of depressions in the edges of a duplex stainless steel slab. The as-cast structure of columnar and equiaxed grains was clearly observed, and some special features were analyzed and discussed. Nevertheless, no clear correlation between the subsurface microstructure and the presence of the defect was found. List of Figures Figure 1 Schematic representation of a continuous casting machine. After (4). ...................................... 15 Figure 2 Typical possible process routes in the steel production. ............................................................. 17 Figure 3 Typical process route for the stainless steel production. Adapted from (9). ............................. 19 Figure 4 High-temperature region of a pseudobinary phase diagram for duplex stainless steel compositions. The shaded region represents the composition of commercial alloys. Extracted from (19). ............................................................................................................................................................... 21 Figure 5 Typical solidification structure observed in the transversal section of an as-cast steel. Chill zone, columnar zone, and equiaxed center region. Extracted from study material from the master program course “Tecnología Metalúrgica” at Universitat Polytecnica de Catalunya 2017. ..................... 23 Figure 6 As cast microstructures of a stainless steel (a) 316 (austenitic) and (b) 430 (ferritic). The presence of the equiaxed central region can be observed in the ferritic as-cast structure while it is not observed in the austenitic. Extracted from (23). ........................................................................................ 23 Figure 7 Schematic representation of the laser scanning equipment. Adapted from (31). ..................... 27 Figure 8 ScanCONTROL 3D-View 3.0 software interface (Micro-Epsilon). ............................................ 28 Figure 9 Schematic representation of the ”z coordinate” and ”moment 0” color codings. It is possible to note how the ”moment 0” representation provides a realistic image of the object. Examples provided by Senso Test. ............................................................................................................................................... 29 Figure 10 ScanCONTROL 2960-100/BL measuring range. Dimensions in mm. Extracted from (31). . 30 Figure 11 Examples of measuring fields defined in the sensor ScanCONTROL 2960-100/BL manual. 30 Figure 12 Maximum collection frequency for some of the defined measuring fields. Note that the smaller the measuring field, the higher the allowed collection frequency. .............................................. 32 Figure 13 Set up for the small scale tests. The equipment is placed in a cooling jacket (prepared for high temperature tests) and installed in a milling table arm. Test sample is placed in the milling drill table. ............................................................................................................................................................. 34 Figure 14 Schematic representation of the grinding machine used for the full scale trials. Provided by Swerea MEFOS............................................................................................................................................. 36 Figure 15 Top and lateral schematic view of the elements during the scanning of the top surfaces of the samples. ........................................................................................................................................................ 36 Figure 16 Schematic view of the elements during the lateral scanning of the samples. .......................... 37 Figure 17 Image of the grinding table were the blue laser is installed. ..................................................... 37 Figure 18 Images of some of the defects that were present on the surface of the steel products. Images in the right side show a depression in the inner bow (wide face) of a stainless steel slab, with a sharp edge at approximately 120 mm from the border (from the narrow face). Images in the left show a depression in the outer bow (wide face) of the same stainless steel slab, where the sharp edge is not present, but a more continuous curvature can be seen. In the interior of both depressions some oscillation marks are visible. ....................................................................................................................... 38 Figure 19 Image of the slab from which samples were taken for metallographic analysis. ..................... 41 Figure 20 Schematic representation of the area from which the samples were taken for metallographic analysis. ........................................................................................................................................................ 42 Figure 21 Results of a variation in the frequency of data collection. Both images show the same region on the surface where a small piece of scale can be seen. Both images were collected at a scanning speed 6 of 1 m/s and with 240 mm working distance; (a) 400 profiles per second, the image in the scanning direction is constructed with approximately 280 points; (b) 50 profiles per second, the image in the scanning direction is constructed with approximately 35 points.............................................................. 43 Figure 22 Example of how different scanning parameters can lead to the same resolution in the scanning direction. (a) Collected with 1 m/s and 400 profiles per second; (b) 0.2 m/s and 80 profiles per second. .................................................................................................................................................... 44 Figure 23 Resolution in the direction of the laser line remains constant even with a change in scanning parameters. Both images were collected at a scanning speed of 1 m/s and with 240 mm working distance; (a) 400 profiles per second; (b) 50 profiles per second. ............................................................ 44 Figure 24 (a) 2D representation of results for the smalls cale trials; (b) augmentation of a small area in (a). The color coding represents the height of the sample. Dark areas correspond to valleys while of brigth areas are associated with peaks. Oscillation marks are easily observed. ....................................... 45 Figure 25 Area of the sample with corner cracks; color coding indicates in dark regions of the sample with low z values and in brigth regions of the surface with high z value. ................................................. 45 Figure 26 Area of the sample with corner cracks; color coding ”Moment 0” provides a realistic representation of the surface. ...................................................................................................................... 46 Figure 27 Image of the grinding machine during the high temperature trials (left) and image of the blue laser on the surface of a high temperature sample during the trials (right). ................................... 47 Figure 28 Results from high temperature full scale trials. Area around a depression in the inner bow of 2101 steel slab. .............................................................................................................................................. 47 Figure 29 Results from full scale high temperature trials. Complete scan of a 2101 steel slab with depressions. The surface corresponds to the inner bow of the slab and the width of the scan is equivalent to the width of the blue laser line.............................................................................................. 48 Figure 30 Results for room temperature full scale trials. Region of the surface of a 304 stainless steel slab in which oscillation marks are visible. ................................................................................................ 48 Figure 31 Results for high temperature full scale trials. Region of the surface of a carbon steel billet. Some scale at the bottom of the scan can be recognized and variations in the surface profile are also detected......................................................................................................................................................... 49 Figure 32 Slab cross section constructed from multiple profiles of different faces for one of the grade 2101 slab sample. The height variations in the profiles are exaggerated to generate a better perspective. Dimensions in mm. ...................................................................................................................................... 49 Figure 33 Billet cross section constructed for multiple profiles from different faces. The height variations in the profiles are exaggerated to generate a better perspective. Dimensions in mm. ........... 50 Figure 34 Slab cross section constructed for multiple profiles from different faces for the grade 304 slab sample. The height variations in the profiles are exaggerated to generate a better perspective. Dimensions in mm. ...................................................................................................................................... 50 Figure 35 Macro etching results for a 200x200 mm section of a stainless steel slab (left); augmentation of an area in the narrow face in which a transition inside the columnar zone can be distinguished (right). Marble’s reagent etching................................................................................................................. 51 Figure 36 Area of the cross section presented in Fig.30 in which the angle between columnar grains and surface of the slab can be clearly seen. Marble’s reagent etching. ..................................................... 51 Figure 37 Microstructure of an area of the sample close to the surface (a); and microstructure in the equiaxed region of the material (b). Etching with Beraha’s: Ferrite dark, austenite white. .................... 53 7 Figure 38 Microstructure of the material in a large region (aprox. 30 mm from the surface). The surface of the material is on the left while the equiaxed region can be noted on the right. Beraha’s etching: Ferrite dark, austenite white. ........................................................................................................ 53 Figure 39 Microstructure of the material in a large region including the surface of the material in the wide face. Beraha’s etching: Ferrite dark, austenite white. ....................................................................... 53 Figure 40 Results from a Thermocalc simulation of the amount of phases against temperature for a steel within the compositional ranges presented in Table 5...................................................................... 54 8 9 dy Distance between consecutive collected profiles in the scanning direction vs Scanning speed Cr Chromium weight percent Mo Molybdenum weight percent Nb Niobium weight percent Ni Nickel weight percent C Carbon weight percent N Nitrogen weight percent Nieq Nickel equivalent number δ Delta ferrite phase γ Austenite phase V Velocity at which the solid phase grows from the liquid K Thermal gradient ASTM American Society for Testing and Materials FEPA Federation of European Producers of Abrasives CCD Charged Coupled Device 3. Background .............................................................................................................19 3.2. Stainless Steel Solidification during Continuous Casting ................................. 20 3.2.1. Solidification Structure ................................................................................ 22 3.2.2. Surface Quality ............................................................................................. 24 3.3.2. Laser Scanning ............................................................................................. 26 3.4. Metallographic Techniques ............................................................................... 33 4. Experimental Procedures ...................................................................................... 33 4.1.2. Procedure ..................................................................................................... 35 4.2.1. Apparatus ..................................................................................................... 35 4.2.2. Materials ...................................................................................................... 37 4.2.3. Procedure ..................................................................................................... 38 14 1. Introduction Continuous casting (CC) is an established technology for the production of steel and is responsible for the solidification of most of the millions of tons of steel that are produced in the world every year (1). In the continuous casting process, the liquid steel is poured into a tundish and from the tundish it flows to a bottomless copper mold, Figure 1. Once in the mold, the molten steel solidifies against the water-cooled copper walls and forms a solid shell (1). The solidifying metal is withdrawn from the mold at a given casting speed, which also matches the liquid metal flow into the mold (1). The tundish holds the molten steel and provides a control flow of metal into the mold (2), and while in slab casting usually one mold is served by one tundish, several billet molds can be supplied by the same tundish. The mold level is a key parameter in the casting process since it exerts a large influence on the liquid flow to the mold and especially in the formation of vortex in the tundish, which could incorporate air or slag in the melt (2). The liquid steel is transported to the mold trough pouring nozzles located along the bottom of the tundish. The design of these nozzles controls the volume and flow of the steel to the mold and also plays a key role in the fluid control. Nevertheless, the mold is the most important component in the continuous casting process (2). It has the primary function of extracting heat from the molten steel as efficiently as possible. It is also continuously oscillating in the vertical direction in order to avoid the adherence of the solidified metal to the copper surface, with oscillation frequencies that can be in the order of 100-200 cycles per minute (2). The frequency of mold oscillation together with the oscillation characteristics (mold velocity, mold displacement, and time for upward and downward movement) has a strong influence on the formation of surface defects, such as oscillation marks (3). Figure 1 Schematic representation of a continuous casting machine. After (4). The continuous casting makes possible not only high productivity but also lower energy consumption, better labor efficiency and quality assurance when compared Ladle Tundish Mold 16 with earlier ingot casting techniques (1-3). Since its first appearance in the last century, an extensive amount of work has been devoted to improve the productivity as well as the quality and cost of steel products. From the first mold oscillation introduced by Junghans (7) (with the purpose of overcoming the sticking of the initially solidified shell) to the more recent introduction of continuous casting modeling to improving the yield and quality of steel production (8), the list of technological improvements is vast. The development of refractories with better performance, the invention of refining methods such as argon oxygen decarburization (AOD) and the vacuum oxygen decarburization (VOD) are milestones in the development of continuous casting technologies; as have also been the electromagnetic stirring, the better understanding and design of the secondary cooling zone and, nowadays, the implementation of advanced modelling to control and predict the quality of the steel produced (9). Nevertheless, there are plenty of defects that still plague the industry and that affect both the quality of the final product and productivity (9). In a conventional steel plant, the continuous casting of slabs is usually followed by the hot rolling, which not only reduces its width to approach the dimensions of the final product but also breaks the casting structure and promotes chemical and microstructural homogenization. After the liquid steel with the proper composition has been obtained, the liquid is continuously cast to form billets, blooms or slabs. The following step is the hot rolling of the steel product and different process routes between the casting and the hot rolling are possible, Figure 2. The most energetically efficient routes are the direct rolling, which consists the hot rolling of the material directly after the casting, and the direct rolling, which involves an intermediate stage in a furnace in order to control the temperature and add time and flexibility to the processing. Other possible routes include the storage of the material either for a short or a long term. Since the presence of severe defects in the cast products can lead to problems during the hot rolling, both the direct rolling and the direct charging require a cast product with a high surface quality (5). As a consequence, it is very common that the billets and slabs after the casting are cooled down to room temperature, inspected, ground if necessary, and then reheated to be hot rolled with an evident increase in energy consumption (10). 17 Figure 2 Typical possible process routes in the steel production. An extensive effort has been done in the past years to better understand and predict the formation of surface defects, which are usually generated in the mold or in the secondary cooling zone (11, 12). The evolution of computer systems and the invaluable work of technologists and researchers have made it possible to gain understanding in the complexity of the high temperature solid-liquid interaction of slag, molten steel and copper mold. More than two decades ago, Brimacombe dreamed with the idea of the “intelligent mold”, capable of “thinking” and taking process decisions based on the temperature “feelings” and the “observation” of mold level and other process parameters (13). Motivated by the necessity to empower the workforce with the knowledge of the fundamental rules that govern the solidification of the metal and determine the quality of the product, he had worked and developed the expert system CRAC/X. This computer program, focused on both internal and external cracks, condensed a large amount of information regarding billet defects, and linked the presence of one (or more) of them with the casting parameters to help the machine operator in correcting operational problems and improve the product quality (14). Naturally, the crack length(s), and type(s) are user’s inputs in the program. Further work has been done in this direction in the past years. The general concept is that, with the help of computers, quality predictions can be me made considering the real, on-time, casting parameters (15). The result is that not only decisions can be made with respect to the process downstream (hot rolling, direct charging, grinding, discard) but it is also possible to control the system to eradicate future defects. Nevertheless, in order to correlate defects with operating conditions, the model has to be trained to associate a specific defect and its appearance with different casting parameters, and nowadays this can only be done with the invaluable help of experienced operators (15). 2. Aim and Objectives At the present time, there are no commercially available systems capable of assessing the as cast surface quality in a reproducible and reliable way, and this task is usually performed in the plant by experienced operators. Nevertheless, even with the best- trained personnel, it is not possible to inspect the product online, since the visual inspection can only be performed at room temperature after the as-cast products have been cooled down, which necessary means time and additional cost. Even more, different defect severity criteria may still be present as they depend on the operator and in some cases the severity of the defect is not assessed. For example, a common practice is to divide the slab surface into 3 areas, left edge, center and right edge. A typical report contains the slab number (from the cast sequence) and a statement about the presence of defects in the different areas of the slab, such as “longitudinal cracks”, “inclusions”, and “deep oscillation marks”, “depressions” “transversal cracks”, etc., always associated with the position on the slab in which they are observed (15). If a severity criterion is also included, and depending on the plant or industry standards; a classification into severe, medium and light can be established for cracks based on the opening of the mouth, the crack density or the crack length, or for example based on the depth for oscillation marks. It is important to note that the fact that the severity is assessed by visual inspection may lead to differences between the results when different persons are performing the inspection. All these inconveniences can be overcome with the use of adequate inspection techniques in the form of systems installed on-line in the plant. Although some surface inspection systems have been developed for their use in rolling mills or mapping samples offline (16-18) transferring them to online monitoring of continuous casting is difficult because of the higher topography variations on the as- cast surface compared with the more defined surface after rolling. In addition, the high temperature of the solidified slab,…