Relevant bibliographies by topics / Ultra high strenght steels

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Academic literature on the topic 'Ultra high strenght steels'

Author: Grafiati
Published: 4 June 2021
Last updated: 4 February 2022

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Journal articles on the topic "Ultra high strenght steels"

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Kah, Paul, Markku Pirinen, Raimo Suoranta, and Jukka Martikainen. "Welding of Ultra High Strength Steels." Advanced Materials Research 849 (November 2013): 357–65. http://dx.doi.org/10.4028/www.scientific.net/amr.849.357.

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The ongoing need to reduce the weight of products while increasing strength has resulted in new generation steel manufacturing using special heat treatments to produce High Strength Steels (HSS) and Ultra High Strength Steels (UHSS) with up to 1700 MPa tensile strength. The high strength level of these steels makes it possible to produce structures with a considerable weight and cost reduction, and such steels have been adopted in the automotive industry and for mobile heavy equipment. Welding of UHSS is, however, not without its complications and welding processes for these steels need careful attention. For instance, their high susceptibility to cracking and Heat Affected Zone (HAZ) softening are risks that need to be borne in mind when choosing welding parameters. This research work discusses the difficulties and challenges of successful welding of UHSS. Common welding methods used in welding of UHSS are briefly reviewed to gain a better understanding of the effects of different welding parameters and methods. The paper finds that UHSS can be satisfactorily welded with laser welding, electron beam welding, resistance welding, and conventional arc welding methods, but the quality of the weld is dependent on appropriate control of several parameters and variables of the welding processes.
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GARCIA-MATEO, C., and F. G. CABALLERO. "Ultra-high-strength Bainitic Steels." ISIJ International 45, no. 11 (2005): 1736–40. http://dx.doi.org/10.2355/isijinternational.45.1736.

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Dahmen, Martin, Benjamin Gerhards, and Stefan Lindner. "Alloyed Ultra-High Strength Steels." Laser Technik Journal 13, no. 2 (April 2016): 48–52. http://dx.doi.org/10.1002/latj.201600009.

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Arola, Anna Maija, Kari Mäntyjärvi, and Jussi A. Karjalainen. "FEM - Modeling of Bendability of Ultra-High Strength Steel." Key Engineering Materials 549 (April 2013): 333–39. http://dx.doi.org/10.4028/www.scientific.net/kem.549.333.

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Ultra-high strength steels have been widely used in different industrial applications. It is necessary to understand the behavior of these materials in common forming processes such as air bending. It is known that the bendability of ultra-high strength steels is lower than other high-strength steels but what are yet to be discovered are the parameters that define the limits of bendability of these steels. The aim of this study was to investigate the factors affecting the bendability of ultra-high strength steel using optical strain measurements and FEM-modeling of the bending process. By using the true stress-strain relation measured by optical strain measuring system the bendability of ultra-high-strength steel was modeled fairly accurately. As a result, it was noted that the strain distribution at the bend of a steel possessing better uniform strain was more widely distributed and there were no highly localized strains. On the other hand as the failure occurred the strains were considerably smaller than the true failure strain of the material in uniaxial tension. As a conclusion it was stated that the ability to withstand the localization of deformation might describe the bendability of ultra-high-strength steel better than the values of the uniform or true failure strain in uniaxial tension test.
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Väisänen, Anu, Kari Mäntyjärvi, and Jussi A. Karjalainen. "Bendability of Ultra-High-Strength Steel." Key Engineering Materials 410-411 (March 2009): 611–20. http://dx.doi.org/10.4028/www.scientific.net/kem.410-411.611.

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Utilisation of ultra-high-strength (UHS) steels is rapidly spreading from the automotive industry into many other application areas. It is necessary to know how these materials behave in common production processes such as air bending. The bendability of UHS steels is much lower compared to normal and high-strength construction steels. In this work, experimental tests were carried out using complex phase (CP) bainitic-martensitic UHS steels (YS/TS 960/1000 and 1100/1250) and S650MC HS steel in order to inspect material bendability and possible problems in the bending process. Mechanical and geometrical damages were registered and classified. The bending method used was air bending and press brake bending with an elastic lower die. The FE analysis was used to understand the stress state at different points in the material and build-up of failure. As UHS steels cannot stand large local strains, a large radius must be used in air bending. The results show that even when a large radius is used in air bending, the strain is not evenly distributed; there is a clear high strain area in the middle of the bend. It was also possible to simulate the other phenomena occurring in experimental tests, such as losing contact with the punch and ‘nut-like’ geometry, using FE analysis. Experimental test results also show that by using an elastic lower die, it is possible to avoid unwanted phenomena and obtain an almost 50% smaller punch radius, but the required force is 50% bigger than that required in air bending.
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Chen, Meng Yang, Bo Ming Hwuang, and Jer Ren Yang. "Microstructural Characterizations of Ultra-High Strength Steel Bars." Advanced Materials Research 168-170 (December 2010): 796–804. http://dx.doi.org/10.4028/www.scientific.net/amr.168-170.796.

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Steel bars used in high-rising building were developed by the addition of V and Nb in medium carbon steels. In this study, two steel bars with different diameters (16 mm and 36 mm) were analyzed via optical and transmission electron microscopy (OM and TEM)., the microstructures of the steels studuied consist of ferrite and pearlite the same as those of the conventional steel bars, but they possess higher yield strengths (over 685 MPa) in combination of considerable elongations (above 10%). The results of transmission electron microscopy reveals that the copious nano-sized (about 20 nm) carbides were interphase-precipitated in ferrite and that the inter-lamellar spacings of pearlite were extra fine, about with a scale of 100 nm. It has been estimated that the small carbides and fine pearlite provide yield strengths, approximately 300 MPa and 800 MPa, respectively. In addition, the volume fraction of ferrite was up to 40%, which offered sufficient soft phase to experience external stress. The results of tensile tests for the steels studied demonstrat that the amount of strain can be up to 1.4% as a yield stress is reached, and the apparent yield point and plateau are present in the stress-strain curves.
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Kwon, Ohjoon, Kyoo Young Lee, Gyo Sung Kim, and Kwang Geun Chin. "New Trends in Advanced High Strength Steel Developments for Automotive Application." Materials Science Forum 638-642 (January 2010): 136–41. http://dx.doi.org/10.4028/www.scientific.net/msf.638-642.136.

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The body design with light weight and enhanced safety is a key issue in the car industry. Corresponding to this trend, POSCO is developing various automotive steel products with advanced performance. Conventional advanced high strength steels such as DP and TRIP steels are now expanding their application since the steels exhibit higher strength and ductility than those of conventional solution and precipitation strengthened high strength steels. Efforts have been made to enhance the mechanical performance of these steels such as ductility, hole expansion ratio, deep drawability, etc. Current research is focused on development of extra- and ultra-AHSS. Extra-AHSS are designed to utilize nano-scale retained austenite embedded in fine bainite and martensite. Ultra-AHSS are designed to have austenite as the major phase, and the ductility is enhanced primarily by continuous strain hardening generated during forming. These steels including extra- and ultra-AHSS are believed to be the next generation automotive steels which will replace the existing high strength steels due to their extremely high strength and ductility combinations.
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Hietala, Mikko, Antti Järvenpää, Markku Keskitalo, and Kari Mäntyjärvi. "Bending Strength of Laser-Welded Sandwich Steel Panels of Ultra-High Strength Steel." Key Engineering Materials 786 (October 2018): 286–92. http://dx.doi.org/10.4028/www.scientific.net/kem.786.286.

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The study was performed to investigate the bending resistance of laser-welded sandwich panels (Vf-core). The main aim of the study was to determine the effect of the tensile strength on bending strength of the panel structures. Panels were manufactured using an ultra-high strength (UHS) and low strength (LS) steels with yield strengths of 1200 and 200 MPa, respectively. Secondly, the bending strength of the panel structures was compared with the conventional sheet steels to estimate the possibilities for weight reduction. Results showed that the UHS steel panels had significantly higher bending strength than panels of the LS steel. The bending strength in the weakest loading direction of the UHS panel was approximately four times higher than the one of LS steel panel. The panels made with UHS steel faceplates and LS steel cores had better bending strength than LS steel panels. In comparison to UHS sheet steel, 30% weight saving is estimated by using the geometry optimized UHS steel panel.
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Martinez, M. A., J. Abenojar, J. M. Mota, and R. Calabrés. "Ultra High Carbon Steels Obtained by Powder Metallurgy." Materials Science Forum 530-531 (November 2006): 328–33. http://dx.doi.org/10.4028/www.scientific.net/msf.530-531.328.

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The objective of the present work is to study the manufacturing process of steels with high carbon content (1.5–2.1wt%) obtained by powder metallurgy. The reference material was the Damascus steel, which was employed to manufacture swords named after it and has been widely known due to its very good mechanical properties. The main reasons of the success of this product are: the high carbon content of the initial steel and the thermomechanical treatment (forge and quenching) that ancient iron forgers kept secretly during centuries. Different carbon contents (2 to3 wt%) were added to the same Fe powder matrix (ASC 300), and compacted and sintered steels are heat laminated (750°C) with a reduction of 20%. For 2% carbon content, the result is a steel with yield strength of 450 MPa, Young’s Modulus of 14.3 GPa and hardness of 109 HV(30).
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Hlebová, Stanislava, and Ladislav Pešek. "Toughness of Ultra High Strength Steel Sheets ." Materials Science Forum 782 (April 2014): 57–60. http://dx.doi.org/10.4028/www.scientific.net/msf.782.57.

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Currently only few methods exist for thin steel sheet testing, especially based on fracture mechanics concept. Charpy impact test is one of the most used method for testing notch toughness and fracture behaviors because of the simplicity and the other advantages [. This article deals with toughness testing of automotive ultra high strength steel sheets (UHSS). Several standard types of toughness test that generate data for specific loading conditions and/or component design approaches exist. Two definition of toughness will be discussed: i) Charpy V-notch toughness, method includes joining of thin steel sheets to one compact unit and ii) material (tensile) toughness [. Two steels were used, DP1000 and 1400M of 1,8 mm thickness and two joining techniques: bonding with adhesives and joining with holders. Effect of material, joining technology, structural adhesives, and number of joined plates on the toughness values was quantified at the room temperature. Toughness of steels by the tensile test was added for comparison. Fracture surface was observed using scanning electron microscope analysis.
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Dissertations / Theses on the topic "Ultra high strenght steels"

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Tolf, Erik. "Challenges in Resistance Welding of Ultra High Strength Steels." Licentiate thesis, KTH, Svetsteknologi, 2015. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-167985.

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Increasing the use of Ultra High Strength Steels (UHSS) in vehicle bodystructures is important for reducing weight and cutting CO2 emissions. This thesis investigates challenges in resistance welding that can be a barrier to implementing UHSS as a replacement for low strength steels in vehicle structures. Empirical research has been performed to offer new approaches for improved joint strength and to increase knowledge on cracking mechanisms in resistance projection welding and resistance spot welding of UHSS. By optimising the current build-up phase and peak current during the first milliseconds of weld time, it was shown that the strength could be improved by up to two-fold for projection welded joints. An approach to improve the ductility and strength of resistance spotwelds in UHSS using reduced cooling time was unsuccessful. The reduced cooling rate after weld metal solidification did not fully create the desired softened microstructure. The study on the surface cracking mechanism in resistance spot welded dual-phase UHSS showed that cracking is linked to the galvanization method. It is proposed that formation of aluminium oxide layers on the electrode tips increases the surface temperature and thereby increases the probability for liquid metal embrittlement and surface cracking.

QC 20150526

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Ali, Ashraf. "Widmanstätten ferrite and bainite in ultra high strength steels." Thesis, University of Cambridge, 1991. https://www.repository.cam.ac.uk/handle/1810/221885.

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Figueroa-Gordon, Douglas J. "Hydrogen re-embrittlement susceptibility of ultra high strength steels." Thesis, Cranfield University, 2005. http://dspace.lib.cranfield.ac.uk/handle/1826/1433.

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300M ultra high strength steel has been widely used for over forty years as a structural material in aerospace applications where a high strength is required. These parts are generally protected from corrosion by electroplated cadmium sacrificial coatings. However, there are concerns over this coating material due to its high toxicity and alternative coatings including Zinc-14%Nickel and SermeTel®1140/962 have been considered. It is known that applying electrodeposited coatings causes atomic hydrogen to be absorbed by the steel substrate producing delayed failure by direct hydrogen embrittlement. Hydrogen is also absorbed when a sacrificial coating undergoes corrosion in service and this process is known as re-embrittlement. The effect of electroplated Zinc-14%Nickel and aluminium based SermeTel®1140/962 sacrificial coatings in causing hydrogen embrittlement and re-embrittlement of 300M steel have been compared to that of conventional electroplated cadmium. AerMet®100 ultra high strength steel has been also considered as alternative replacement for the conventional 300M. Hence, the hydrogen embrittlement and re-embrittlement susceptibilities of AerMet®100 were studied when coated with cadmium, Zinc-14%Nickel and SermeTel®1140/962. In addition, two alternative alloys GifloM2000 and CSS-42LTM were also taken into consideration and only the extent of hydrogen re-embrittlement was assessed when coated with cadmium and SermeTel®1140/962, respectively. Slow strain rate tests, SSRT, were carried out for plated, plated and baked as well as plated, baked and corroded tensile specimens. The time to failure values were compared using a Weibull distribution, statistical ttests and embrittlement indices. Differences in hydrogen susceptibility of the high strength steels considered might depend upon their intrinsic hydrogen transport characteristics. These properties were studied and compared in terms of hydrogen diffusivity and solubility.
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Haglund, Adam. "Reduction of hydrogen embrittlement on Electrogalvanized Ultra High Strength Steels." Thesis, Uppsala universitet, Institutionen för kemi - Ångström, 2014. http://urn.kb.se/resolve?urn=urn:nbn:se:uu:diva-236603.

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Ultra-high strength steels is known to be susceptible for hydrogen embrittlement at very low concentrations of hydrogen. In this thesis three methods to prevent or reduce the hydrogen embrittlement in martensitic steel, with tensile strength of 1500 MPa, were studied. First, a barrier layer of aluminium designed to prevent hydrogen to enter the steel, which were deposited by vacuum evaporation. Second, a decarburization process of the steels surface designed to mitigate the induced stresses from cutting. Last, a hydrogen relief treatment at 150°C for 11 days and 200°C for 4 days, to reduce the hydrogen concentration in the steel. The effect of the hydrogen embrittlement was analyzed by manual measurements of the elongations after a slow strain rate testing at 5*10-6 mm/s, and the time to fracture in an in-situ constant load test with a current density of 1.92 mA/cm2 in a 0.5 M Na2SO4 solution. The barrier layer showed an increase in time to fracture, but also a decrease in elongations. The decarburized steel had a small increase in the time to fracture, but not enough to make it a feasible process. The hydrogen relief treatment showed a general decrease in hydrogen concentrations, but the elongation measurements was irregular although with a tendency for improvement. The simplicity of the hydrogen relief treatment makes it an interesting process to reduce the influence of hydrogen embrittlement. However, more investigations are necessary.
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Pan, Xin. "Development of lean maraging steels for ultra high strength applications." Thesis, University of Sheffield, 2017. http://etheses.whiterose.ac.uk/20511/.

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Lean maraging steels were designed for several application sectors by providing very high strength and ductility, with the addition of relatively cheaper elements like manganese. In this work, the microstructural and mechanical properties of four niobium-containing (0.035 wt. %) and vanadium-containing (0.02 wt. %) Fe-7Mn-2Ni-1Ti-1Mo-0.03C (in wt. %) with different content of aluminium (1~2 wt. %) aged at different temperatures between 420 °C and 570 °C were investigated. As-quenched Fe-7Mn alloys exhibited a good combination of high strength (~700 MPa of 0.2 proof strength, ~ 850 MPa of UTS) and ductility (~ 10 % tensile elongation). The as-quenched microstructure consisted of lath martensite and a small amount (~ 0.3 vol. %) of micronsized (Ti, Mo, Nb/V)C carbides. The aging process significantly strengthened/hardened the Fe-7Mn alloys which is due to the formation of nano-sized Nix(Ti, Mn, Al) precipitates. Nix(Ti, Mn, Al) precipitates exhibit a very high number density (52.9×1014/m2 in the peak-aged state of Alloy 2, aged at 500 °C for 24 h) and fine size (average diameter was 17.4 ± 4.2 nm after aged at 500 °C for 168 h). The Vickers hardness increased with aging time in the under-aged stage which was due to the precipitate growth and the alloy was strengthened by Orowan bypassing mechanism. The hardness decreased with aging time after the peak hardness as the precipitate coarsened. There were two types of the crystal structure observed for Nix(Ti, Mn, Al) precipitates: The L21-Ni2(Ti, Mn, Al) phase (lattice parameter, a = 0.5863 ~ 0.5895 nm, which is co-planar with martensite matrix, with only 1.72 % of lattice misfit. And the L12-Ni3(Ti, Mn, Al) structure ( a = 0.3598 ~ 0.3613 nm). A short time-aging resulted in a yield strength above 1 GPa but led to embrittlement of Fe-7Mn alloys, which was believed to be due to the segregation of Mn to the grain boundaries. Both carbides and nano-precipitates formed along grain boundaries were likely to reduce the cohesion across the boundary plane, as well as resulted in stress-strain incompatibilities. However, the prolonged aging resulted in the formation of reverted austenite (RA) in the over-aged stage, which led to the recovery of ductility when aged at 570 °C as the austenite reversion removed the Mn solute from the grain boundaries. Reverted austenite exhibited lath-like shape with the length between 50 and 2000 nm. Both the size and volume fraction of RA increased with the increasing aging time and aging temperature. RA was formed with the diffusion-controlled mechanism, and it was observed exhibiting a Kurdjumov-Sachs (K-S) orientation relationship with the neighbouring aged martensite grains with an enrichment of Mn and Ni. Higher content of Al addition resulted in ~ 25 vol. % of δ-ferrite in the as-quenched microstructure, which was stable during aging. 2 wt. % of Al also resulted in higher volume fraction of nano-precipitates and increased the dissolution temperature of precipitates, however, it delayed the peak-aging time and austenite reversion. Nb-containing alloys exhibited relatively finer size of prior austenite grains and (Ti, Mo, V)C carbides, larger size and higher number density of Ni(Ti, Mn, Al) precipitates, but slightly lower austenite fraction, compared to V-containing alloys. Based on the results, it is suggested that Alloy 3 aged at 570 °C for 2~6 h gives the optimized mechanical properties.
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Kim, Bij-Na. "Design and modelling of ultra-high strength steels : nanoprecipitation and plasticity." Thesis, University of Cambridge, 2014. https://www.repository.cam.ac.uk/handle/1810/245234.

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Understanding the changes occurring in the mechanical properties during martensite tempering is essential in the development of new industrial grades. The aim of this research was to develop new ultra-high strength steels via nanoprecipitation control, which requires an understanding of the processing-microstructure-property relationship in medium carbon (0.5-0.6 wt.%) steels throughout tempering. Much of the work has been centred in understanding the role of silicon at the precipitation level and in the recovery of martensite. By using an existing spring steel grade, the effect of interrupted ageing (IA) in tempered martensite has been studied. In IA, an intermediate step between quenching and tempering is introduced, where quenched martensite is left to rest at room temperature for a defined period of time. By allowing carbon segregation into dislocation cores, the incorporation of IA resulted in a more stable microstructure and hardness improvement. The effect of silicon in the epsilon to cementite carbide transition has also been studied. The classical nucleation theory was applied in order to model cementite formation under paraequilibrium conditions, thus incorporating silicon during nucleation. Characterisation using high energy X-rays showed the inhibiting effect of silicon in the overall cementite precipitation. The second effect of silicon was observed in the martensite recovery. A series of experiments were carried out in order to capture the various microstructural changes taking place during tempering: precipitation, grain size and dislocation density evolution. It was observed that the addition of silicon reduces the rate of martensite recovery, owing to the reduced cross-slip in the ferrite lattice. A plasticity model based on irreversible thermodynamics and EBSD characterisation was applied to identify the effective grain size. The results from these two techniques require further research. Nevertheless, based on the post-failure analysis by TEM, it appears that at relatively early tempering stages, even low angle lath boundaries can contribute to strengthening, where piled-up dislocations have been observed at lath boundaries.
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Ratanathavorn, Wallop. "Dissimilar joining of aluminium to ultra-high strength steels by friction stir welding." Doctoral thesis, KTH, Svetsteknologi, 2017. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-207356.

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Multi-material structures are increasingly used in vehicle bodies to reduce weight of cars. The use of these lightweight structures is driven by requirements to improve fuel economy and reduce CO2 emissions. The automotive industry has replaced conventional steel components by lighter metals such as aluminium alloy. This is done together with cutting weight of structures using more advanced strength steels. However, sound joining is still difficult to achieve due to differences in chemical and thermal properties.   This research aims to develop a new innovative welding technique for joining aluminium alloy to ultra-high strength steels. The technique is based on friction stir welding process while the non-consumable tool is made of an ordinary tool steel. Welding was done by penetrating the rotating tool from the aluminium side without penetrating into the steel surface. One grade of Al-Mg aluminium alloy was welded to ultra-high strength steels under lap joint configuration. Different types of steel surface coatings including uncoated, hot-dipped galvanised and electrogalvanised coating have been studied in order to investigate the influence of zinc on the joint properties. The correlation among welding parameters, microstructures, intermetallic formation and mechanical properties are demonstrated in this thesis.  Results have shown that friction stir welding can deliver fully strong joints between aluminium alloy and ultra-high strength steels. Two intermetallic phases, Al5Fe2 and Al13Fe4, were formed at the interface of Al to Fe regardless of surface coating conditions. The presence of zinc can improve joint strength especially at low heat input welding due to an increased atomic bonding at Al-Fe interface. The formation of intermetallic phases as well as their characteristics has been demonstrated in this thesis. The proposed welding mechanisms are given based on metallography investigations and related literature.

QC 20170519

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Chamisa, Alfonce. "Development of ultra high strength steels for reduced carbon emissions in automotive vehicles." Thesis, University of Sheffield, 2014. http://etheses.whiterose.ac.uk/6274/.

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Automotive steels with enhanced strength and ductility beyond the current bounds can be engineered through microstructural strategies that take into account the benefits brought about by nanoprecipitates formed during the transformation from austenite to ferrite. Three multiphase steel compositions were initially studied. A patented Ti-Al-Mo steel composition was selected as the baseline for comparison with the other two steels. It is claimed that this steel has exceptional mechanical properties. The Ti and V microalloyed steels were selected to check whether interphase precipitates (IP), which can yield a high degree of precipitation strengthening, could be produced. Results showed that Ti-Al-Mo had superior microstructure and properties as compared to the other two. The microstructure was composed of ferrite, martensite, bainite and retained austenite. Unlike the other two steels, IP was also observed and the UTS of 780MPa and uniform elongation of 21% previously reported by other authors were also confirmed. The V microalloyed steel composition was selected for the next part of the project since it would be commercially viable to produce for Tata Steel. The time/temperature/transformation behaviours of the V microalloyed steel were extensively studied. The microstructures developed were analysed and high precipitate number densities averaging 394 particles/m2 were recorded in the sample transformed at 700oC for 1200s. A high uniform elongation of 30.8% and the highest UTS of 627MPa were also reported on the same sample. The UTS value was attributed to the high precipitate number density which made an overall contribution to the yield strength of 270MPa. However, further studies need to be carried out, since the properties were not optimised and were inferior to some of the steels in current use for automotive applications. Questions were asked as to why IP was not observed. The low austenising temperature of 950oC was cited as the possible reason. Thermodynamic calculations using Thermo-Cal software had predicted that the optimum should have been 1050oC. As a result, 950oC was believed to be inadequate to effectively dissolve the carbides present to allow effective formation of interphase precipitates during the temperature hold in the α + γ temperature region. The high N content was cited as another possible reason, but this was not conclusive and shown in itself not to be true by work in the next stage of the project. It has since been established that Mo retards precipitate growth in both Nb and Ti alloyed steels. However, nothing has been reported on the effects of Mo on V microalloyed steels. As a result, the next stage of the project studied the effects of Mo on V microalloyed steels. Predominantly ferritic steels with Nb-V-Mo microalloying additions were produced and coiled at different temperatures. Samples microalloyed with Ti-Mo, Ti, V-Mo, V, Nb-Mo and Nb were also produced for comparison purposes. IP was observed in most of the Nb-V-Mo steels. IP with average interparticle distances of 8 ± 2nm and row spacing of 22 ± 3nm were observed in sample 10-630Nb+VMo. High YS of 925MPa, UTS of 1023MPa and total elongation of 16.8% were recorded for this sample. The exceptional mechanical properties were attributed to high number densities of fine IP averaging 1766 particles/m2. 82% of the precipitates had average sizes below 7nm and these made a contribution to YS of approximately 546MPa. It was then concluded that Mo additions were likely to have influenced the formation of fine precipitates that strengthened the ferritic steels. Hence Mo is likely to influence the high nucleation rate and slow precipitate growth in the same way that it influences Ti and Nb microalloyed steels. Since one of the steels studied at this stage had high N additions, it was also confirmed that the precipitate number densities in the previous V microalloyed steels batch had nothing to do with the N content; instead, it all had to do with the low austenising temperature which failed to put the carbides into solution.
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Ardehali, Barani Araz. "Optimization of the critical content of tramp elements in ultra-high strength silicon chromium spring steels through thermomechanical treatment." Göttingen Cuvillier, 2007. http://d-nb.info/988382563/04.

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Ardehali, Barani Araz. "Optimization of the critical content of tramp elements in ultra-high strength silicon chromium spring steels through thermomechanical treatment /." Göttingen : Cuvillier, 2008. http://bvbr.bib-bvb.de:8991/F?func=service&doc_library=BVB01&doc_number=017079000&line_number=0001&func_code=DB_RECORDS&service_type=MEDIA.

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Books on the topic "Ultra high strenght steels"

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Billur, Eren, ed. Hot Stamping of Ultra High-Strength Steels. Cham: Springer International Publishing, 2019. http://dx.doi.org/10.1007/978-3-319-98870-2.

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Hang kong chao gao qiang du gang de fa zhan: Development of aeronautical ultra-high strength steels. Beijing Shi: Guo fang gong ye chu ban she, 2012.

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Elsudani, Abuagila H. Ali. Development of ultra-high strength in low carbon steel wire. Manchester: UMIST, 1993.

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Billur, Eren. Hot Stamping of Ultra High-Strength Steels: From a Technological and Business Perspective. Springer, 2019.

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Billur, Eren. Hot Stamping of Ultra High-Strength Steels: From a Technological and Business Perspective. Springer, 2018.

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Book chapters on the topic "Ultra high strenght steels"

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Sha, Wei. "Ultra High-Strength Maraging Steel." In Steels, 141–61. London: Springer London, 2013. http://dx.doi.org/10.1007/978-1-4471-4872-2_6.

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Çetin, Barıs, and Halim Meço. "Metallurgy of Steels." In Hot Stamping of Ultra High-Strength Steels, 19–29. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_2.

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Wang, Xinhua. "Extra Low Sulfur and Non-metallic Inclusions Control for Ultra Fine Grain High Strength Steels." In Ultra-Fine Grained Steels, 431–72. Berlin, Heidelberg: Springer Berlin Heidelberg, 2009. http://dx.doi.org/10.1007/978-3-540-77230-9_8.

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Hsu, T. Y., and Xuejun Jin. "Ultra-high Strength Steel Treated by Using Quenching–Partitioning–Tempering Process." In Advanced Steels, 67–73. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-17665-4_8.

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Billur, Eren. "Introduction." In Hot Stamping of Ultra High-Strength Steels, 1–17. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_1.

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Porzner, Harald, and Eren Billur. "Computer Modeling of Hot Stamping." In Hot Stamping of Ultra High-Strength Steels, 203–23. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_10.

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Billur, Eren, Rick Teague, and Barış Çetin. "Economics of Hot Stamping." In Hot Stamping of Ultra High-Strength Steels, 225–45. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_11.

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Billur, Eren, Göran Berglund, and Tord Gustafsson. "History and Future Outlook of Hot Stamping." In Hot Stamping of Ultra High-Strength Steels, 31–44. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_3.

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Billur, Eren, and Hyun-Sung Son. "Blank Materials." In Hot Stamping of Ultra High-Strength Steels, 45–76. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_4.

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Jonasson, Jan, Eren Billur, and Aitor Ormaetxea. "A Hot Stamping Line." In Hot Stamping of Ultra High-Strength Steels, 77–104. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-98870-2_5.

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Conference papers on the topic "Ultra high strenght steels"

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Heikkala, Jouko A., and Anu J. Väisänen. "Usability Testing of Ultra High-Strength Steels." In ASME 2012 11th Biennial Conference on Engineering Systems Design and Analysis. American Society of Mechanical Engineers, 2012. http://dx.doi.org/10.1115/esda2012-82770.

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New ultra high strength (UHS) steels have been developed in order to get advantages in machine design and construction. Following benefits can be obtained for example: - less material usage due to lighter constructions; - better payload and less fuel consumption in vehicle industry; - energy saving in material production. A rough distinction of structural steels can be defined to ductile steels, with tensile strength less than 300 MPa, and high strength steels, up to 700 Mpa. A steel material can be defined as UHS steel when the tensile strength exceeds 700 MPa. Steels with yield strength of 1500 Mpa have been developed so far. UHS steels can also be divided into structural steels and wear resistant steels. With the tensile strength also the hardness increases and the tensile strain decreases. That causes several difficulties when the material is processed into products. Especially mechanical processing like bending, machining and shearing gets difficult as the material strength increases. That causes problems for the construction material users to find the proper manufacturing methods in production. In Oulu University Production Technology Laboratory material processing tests have been performed during several years in co-operation with the local steel manufacturer. The usability tests comprise mainly of bending and machining tests. Shearing and welding tests have been made to a smaller extent. Also laser treatment has been used for local heat conditioning in order to improve the bending and shearing properties, but these techniques are not yet widely used in production. The bending tests are carried out with standard bending tools and test steel plates with standard dimensions. The plate thickness varies depending on the test material. The target is to determine the reliable minimum bending radiuses whereby the plate can be bent without failure, from both sides and along the rolling direction and orthogonally to that. Also the springback angle is measured and the bent surfaces are evaluated according to several criteria. When necessary, also the mechanical testing of the formed material is carried out. The machining tests are made mainly by drilling. Also some milling tests have been performed. Drilling is a convenient way of machining testing because a substantial amount of holes can be drilled in one test plate. The drilling power can be observed precisely by monitoring the spindle power. Also a variety of different tool types can be used, from uncoated HSS drills to boring tools with indexable inserts. The optimal machining parameters (feed and speed) will be defined according to maximum tool life and minimum machining costs.
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Mendiguren, Joseba, Rafael Ortubay, Xabier Agirretxe, Lander Galdos, and Eneko Sáenz de Argandoña. "Press hardening of alternative high strength aluminium and ultra-high strength steels." In ESAFORM 2016: Proceedings of the 19th International ESAFORM Conference on Material Forming. Author(s), 2016. http://dx.doi.org/10.1063/1.4963434.

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Bilimoria, Yaz F., Bala Subbaraman, and N. Terry Burton. "Galvanized Ultra-High-Strength Sheet Steels for Automotive Applications." In International Congress & Exposition. 400 Commonwealth Drive, Warrendale, PA, United States: SAE International, 1993. http://dx.doi.org/10.4271/930748.

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Lardon, J. M., and T. Poulain. "Advanced High Strength Martensitic Stainless Steels for High Pressure Equipment." In ASME 2018 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2018. http://dx.doi.org/10.1115/pvp2018-84546.

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Maraging stainless steels offer a large panel of high strength materials with good ductility and stress corrosion cracking resistance. Their mechanical properties compared to conventional 15-5 PH and 17-4 PH martensitic stainless steels show much better yield strength / toughness compromise for yield strength exceeding 1300 MPa. In the same time, fatigue resistance is significantly increased at high strength stress levels and material keeps good resistance to stress corrosion. These properties make them particularly suitable for ultra-high pressure equipment or high pressure rotating components submitted to high cyclic stresses. Their application for Pascalisation pressure vessels and ultra-high pressure compressors for ethylene gas is briefly presented.
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Cornette, D., P. Cugy, A. Hildenbrand, M. Bouzekri, and G. Lovato. "Ultra High Strength FeMn TWIP Steels for Automotive Safety Parts." In SAE 2005 World Congress & Exhibition. 400 Commonwealth Drive, Warrendale, PA, United States: SAE International, 2005. http://dx.doi.org/10.4271/2005-01-1327.

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Shi, Steve, and Steve Westgate. "Laser welding of ultra-high strength steels for automotive applications." In PICALO 2008: 3rd Pacific International Conference on Laser Materials Processing, Micro, Nano and Ultrafast Fabrication. Laser Institute of America, 2008. http://dx.doi.org/10.2351/1.5056993.

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Walp, Matthew S. "Impact Dependent Properties of Advanced and Ultra High Strength Steels." In SAE World Congress & Exhibition. 400 Commonwealth Drive, Warrendale, PA, United States: SAE International, 2007. http://dx.doi.org/10.4271/2007-01-0342.

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Isaksson, K., M. Jönsson, and D. Berglund. "The Direct Press Hardening Process for Zn-Coated Ultra-High Strength Steels." In The 2nd International Conference on Advanced High Strength Steel and Press Hardening (ICHSU 2015). WORLD SCIENTIFIC, 2016. http://dx.doi.org/10.1142/9789813140622_0089.

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Wallin, Kim, Sakari Pallaspuro, Päivi Karjalainen-Roikonen, and Pasi Suikkanen. "Applicability of the Master Curve Method to Ultra High Strength Steels." In ASME 2015 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2015. http://dx.doi.org/10.1115/pvp2015-45554.

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Although Ultra High Strength Steels (UHSS) with nominal strengths up to 1500 MPa have been available on the market for many years, the use of these steels in the civil engineering industry is still rather uncommon. One critical point limiting the use of UHSS steels lies in their rather poorly documented fracture properties in relation to more conventional steels covered by the codes. The major concept governing the assessment of steels is the Master Curve (MC) methodology. It provides a description for the fracture toughness scatter, size effect and temperature dependence in the ductile to brittle transition region. It enables a complete characterization of brittle fracture toughness of a material based on only a few small size specimens. The method combines a theoretical description of the scatter, a statistical size effect and an empirically found temperature dependence of fracture toughness. The fracture toughness in the brittle fracture regime is thus described with only one parameter, the transition temperature T0. At this temperature the mean fracture toughness for a 25.4 mm thick specimen is 100 MPa√m. The Master Curve method as defined in ASTM E1921-13a is applicable to ferritic structural steels with yield strength between 275 MPa and 825 MPa. Very few studies have been made with respect to the applicability of the Master Curve to Ultra High Strength Steels with yield strengths in the excess of 900 MPa. This is the topic of this work. Focusing on novel directly quenched high performance steels, the applicability of the Master Curve methodology with special emphasis on the temperature dependence will be investigated. Possible improvements to the Master Curve will be proposed for further consideration.
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Carlsson, Björn. "New High-Pressure Hydroform Tool Design Reduces Springback in Ultra-High Strength Steels." In WCX SAE World Congress Experience. 400 Commonwealth Drive, Warrendale, PA, United States: SAE International, 2019. http://dx.doi.org/10.4271/2019-01-1084.

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Reports on the topic "Ultra high strenght steels"

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Garrison, Jr, and W. M. An Investigation of the Role of Second Phase Particles in the Design of Ultra High Strength Steels of Improved Toughness. Fort Belvoir, VA: Defense Technical Information Center, June 1990. http://dx.doi.org/10.21236/ada226056.

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Anthony J. DeArdo and C. Isaac Garcia. Conservation Research and Development/ New Ultra-Low Carbon High Strength Steels with Improved Bake Hardenability for Enhanced Stretch Formability and Dent Resistance. Office of Scientific and Technical Information (OSTI), December 2003. http://dx.doi.org/10.2172/820518.

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Weiss, Charles, William McGinley, Bradford Songer, Madeline Kuchinski, and Frank Kuchinski. Performance of active porcelain enamel coated fibers for fiber-reinforced concrete : the performance of active porcelain enamel coatings for fiber-reinforced concrete and fiber tests at the University of Louisville. Engineer Research and Development Center (U.S.), May 2021. http://dx.doi.org/10.21079/11681/40683.

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A patented active porcelain enamel coating improves both the bond between the concrete and steel reinforcement as well as its corrosion resistance. A Small Business Innovation Research (SBIR) program to develop a commercial method for production of porcelain-coated fibers was developed in 2015. Market potential of this technology with its steel/concrete bond improvements and corrosion protection suggests that it can compete with other fiber reinforcing systems, with improvements in performance, durability, and cost, especially as compared to smooth fibers incorporated into concrete slabs and beams. Preliminary testing in a Phase 1 SBIR investigation indicated that active ceramic coatings on small diameter wire significantly improved the bond between the wires and the concrete to the point that the wires achieved yield before pullout without affecting the strength of the wire. As part of an SBIR Phase 2 effort, the University of Louisville under contract for Ceramics, Composites and Coatings Inc., proposed an investigation to evaluate active enamel-coated steel fibers in typical concrete applications and in masonry grouts in both tension and compression. Evaluation of the effect of the incorporation of coated fibers into Ultra-High Performance Concrete (UHPC) was examined using flexural and compressive strength testing as well as through nanoindentation.
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FIRE RESISTANCE OF STEEL TUBULAR COLUMNS INFILLED WITH ULTRA-HIGH STRENGTH CONCRETE. The Hong Kong Institute of Steel Construction, September 2018. http://dx.doi.org/10.18057/ijasc.2018.14.3.8.

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FINITE ELEMENT ANALYSIS OF LOCAL BUCKLING OF STEEL AND COMPOSITE COLUMNS UTILISING HIGH AND ULTRA-HIGH STRENGTH STEEL. The Hong Kong Institute of Steel Construction, December 2018. http://dx.doi.org/10.18057/icass2018.p.017.

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NUMERICAL STUDY ON SHEAR BEHAVIOUR OF ENHANCED C-CHANNELS IN STEEL-UHPC-STEEL SANDWICH STRUCTURES. The Hong Kong Institute of Steel Construction, September 2021. http://dx.doi.org/10.18057/ijasc.2021.17.3.4.

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This paper firstly developed a three-dimensional (3D) finite element model (FEM) for enhanced C-channels (ECs) in steel-UHPC-steel sandwich structures (SUSSSs). The FEM was validated by 12 push-out tests on ECs with UHPC. With the validated FEM, this paper performed in-depth parametric studies on shear behaviours of ECs with ultra-high performance concrete (UHPC). These investigated parameters included bolt-hole gap (a), grade (M) and diameter (d) of bolt, core strength (fc), length of C-channel (Lc), and prestressing force ratio on bolt (ρ) in ECs. Under shear forces, the ECs in UHPC exhibited successive fractures of bolts and C-channels. Increasing the bolt-hole gap within 0-2 mm has no harm on the ultimate shear resistance, but greatly improves the slip capacity of ECs. Increasing grade and diameter of bolts improves the shear resistance and ductility of ECs through increasing the PB/PC (shear strength of bolt to that of C-channel) ratio. Increasing the core strength increased the shear resistance, but reduced the ductility of ECs due to the reduced PB/PC ratio. The ECs with Lc value of 50 mm offer the best ductility. Prestressing force acting on the bolts reduced the shear strength and ductility of ECs with UHPC. Analytical models were proposed to estimate the ultimate shear resistance and shear-slip behaviours of ECs with UHPC. The extensive validations of these models against 12 tests and 31 FEM analysis cases proved their reasonable evaluations on shear behaviours of ECs with UHPC.
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