Relevant bibliographies by topics / Fe-Al alloys

Contents

  1. Journal articles
  2. Dissertations / Theses
  3. Books
  4. Book chapters
  5. Conference papers
  6. Reports

Academic literature on the topic 'Fe-Al alloys'

Author: Grafiati
Published: 4 June 2021
Last updated: 1 February 2022

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Journal articles on the topic "Fe-Al alloys"

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Kostov, Ana, B. Friedrich, and D. Zivkovic. "Thermodynamic calculations in alloys Ti-Al, Ti-Fe, Al-Fe and Ti-Al-Fe." Journal of Mining and Metallurgy, Section B: Metallurgy 44, no. 1 (2008): 49–61. http://dx.doi.org/10.2298/jmmb0801049k.

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Thermodynamic calculations of three binary Ti-based alloys: Ti-Al, Ti-Fe, and Al-Fe, as well as ternary alloy Ti-Al-Fe, is shown in this paper. Thermodynamic calculations involved thermodynamic determination of activities, coefficient of activities, partial and integral values for enthalpies and Gibbs energies of mixing and excess energies at different temperatures: 1873K, 2000K and 2073K, as well as calculated phase diagrams for the investigated binary and ternary systems. The FactSage is used for all thermodynamic calculations.
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Srivastava, A. K., and S. Ranganathan. "Microstructural characterization of rapidly solidified Al–Fe–Si, Al–V–Si, and Al–Fe–V–Si alloys." Journal of Materials Research 16, no. 7 (July 2001): 2103–17. http://dx.doi.org/10.1557/jmr.2001.0287.

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The present study of rapidly solidified melt-spun Al80Fe14Si6 Al80V14Si6, and Al80Fe10V4Si6 alloys by electron microscopy techniques, x-ray diffractometry, and differential scanning calorimetry leads to a number of microstructural results. Coexistence of a micro-quasicrystalline state of an icosahedral phase with monoclinic θ–Al13Fe4 and hexagonal β–Al6V in Al–Fe–Si and Al–V–Si alloys, respectively, is reported. Also, the growth morphology of the icosahedral phase surrounded by a crystalline ring was investigated in an Al–Fe–V–Si alloy. The crystalline ring has the particles of the cubic α–Al12(Fe,V)3Si silicide phase. Evidence of irrational twinning of cubic crystals, giving rise to a symmetry not deviating much from icosahedral symmetry was found in this alloy. In all the three alloys crystalline intermetallics were elucidated in the context of rational approximants of an icosahedral quasicrystal. It was noticed that while the icosahedral phase in Al–Fe–Si and Al–V–Si alloys transforms to crystalline intermetallics at about the same temperature (approximately 610 K), the transformation of icosahedral phase in Al–Fe–V–Si alloy occurred at a relatively lower temperature (540 K). The origin of different metastable microstructures and their stability at elevated temperatures, in these alloys, are compared and discussed.
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Novák, Pavel, and Kateřina Nová. "Oxidation Behavior of Fe–Al, Fe–Si and Fe–Al–Si Intermetallics." Materials 12, no. 11 (May 29, 2019): 1748. http://dx.doi.org/10.3390/ma12111748.

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Iron aluminides are still deeply investigated materials for their use in power plants, automotive and chemical industry, and other sectors. This paper shows that it is possible to strongly improve their oxidation behavior by the addition of silicon. The description of the synergic effect of aluminum and silicon on the oxidation behavior of Fe–Al–Si alloys at 800 °C in air is presented. The oxidation rate, microstructure, phase, and chemical composition of these ternary alloys are compared with the binary Fe–Al and Fe–Si alloys. Results showed that the oxidation of Fe–Al–Si ternary alloys provides an oxide layer based on aluminum oxide with a low concentration of iron and silicon. Below this oxide layer, there is a layer of silicides formed as a result of depletion by aluminum, which forms a secondary oxidation protection.
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Bryantsev, Pavel, and Marina Samoshina. "Mechanical Milling of Quasicrystalline Al-Cu-Fe Alloys." Materials Science Forum 794-796 (June 2014): 761–65. http://dx.doi.org/10.4028/www.scientific.net/msf.794-796.761.

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Ingots of alloys Al-Cu-Fe were obtained by casting in a graphite mold. Mechanical milling of alloy particles in the as-cast state and after homogenization annealing was carried out in planetary ball mill Retsch PM400 in an argon atmosphere. As a result of mechanical milling granules with an average size of 35-40 μm and fine internal microstructure are formed. The size of coherent scattering regions in quasicrystalline phase after mechanical milling was about 10-15 nm. Mechanical milling after homogenization heat treatment allows much refines the quasicrystalline phase than in the case of mechanical milling of cast alloy.
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Weinhagen, M., B. Köhler, J. Wolff, and Theodor Hehenkamp. "Interdiffusion in Fe-Al Alloys." Defect and Diffusion Forum 143-147 (January 1997): 449–54. http://dx.doi.org/10.4028/www.scientific.net/ddf.143-147.449.

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Cullen, J. R., A. E. Clark, M. Wun-Fogle, J. B. Restorff, and T. A. Lograsso. "Magnetoelasticity of Fe–Ga and Fe–Al alloys." Journal of Magnetism and Magnetic Materials 226-230 (May 2001): 948–49. http://dx.doi.org/10.1016/s0304-8853(00)00612-0.

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Tsubakino, Harushige, Atsushi Yamamoto, Takeshi Kato, and Akira Suehiro. "Precipitation in Deformed Al-Fe and Al-Fe-Si Dilute Alloys." Materials Science Forum 331-337 (May 2000): 951–56. http://dx.doi.org/10.4028/www.scientific.net/msf.331-337.951.

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Yang, Shui Yuan, Cui Ping Wang, Yu Su, and Xing Jun Liu. "Evolutions of Microstructure and Phase Transformation in Cu-Al-Fe-Nb/Ta High-Temperature Shape Memory Alloys." Materials Science Forum 833 (November 2015): 67–70. http://dx.doi.org/10.4028/www.scientific.net/msf.833.67.

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The evolutions of microstructure and phase transformation behavior of Cu-Al-Fe-Nb/Ta high-temperature shape memory alloys under the quenched and aged states were investigated in this study, including Cu-10wt.% Al-6wt.% Fe, Cu-10wt.% Al-4wt.% Fe-2wt.% Nb and Cu-10wt.% Al-4wt.% Fe-2wt.% Ta three types alloys. The obtained results show that after quenching, Cu-10wt.% Al-6wt.% Fe alloy exhibits two-phase microstructure of β′1 martensite + Fe (Al,Cu) phase; Cu-10wt.% Al-4wt.% Fe-2wt.% Nb alloy also has two-phase microstructure of (β′1 + γ′1 martensites) + Nb (Fe,Al,Cu)2 phase; Cu-10wt.% Al-4wt.% Fe-2wt.% Ta alloy is consisted of three-phase of (β′1 + γ′1 martensites) + Fe (Al,Cu,Ta) + Ta2(Al,Cu,Fe)3 phases. However, α (Cu) phase precipitates after aging for three alloys; and Fe (Al,Cu,Nb) phase is also present in Cu-10wt.% Al-4wt.% Fe-2wt.% Nb alloy. All the studied alloys exhibit complicated martensitic transformation behaviors resulted from the existence of two types martensites (β′1 and γ′1).
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Nguyen, Viet H., Oanh T. H. Nguyen, Dina V. Dudina, Vinh V. Le, and Ji-Soon Kim. "Crystallization Kinetics of Al-Fe and Al-Fe-Y Amorphous Alloys Produced by Mechanical Milling." Journal of Nanomaterials 2016 (2016): 1–9. http://dx.doi.org/10.1155/2016/1909108.

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In this work, the effect of a slight change in the composition of the Al-Fe amorphous alloys (from Al84Fe16to Al82Fe18) and the substitution of Y for Al (2 at.%) on their crystallization kinetics was studied. According to the X-ray diffraction analysis, powders of the Al84Fe16, Al82Fe18, and Al82Fe16Y2alloys with a fully amorphous structure were formed after 100 h of mechanical milling of the mixtures of the elemental powders. The crystallization behavior of the alloys was also studied by transmission electron microscopy. Upon heating up to a temperature of the first exothermic peak,α-Al crystals precipitated from the amorphous Al84Fe16matrix. During crystallization of the Al82Fe18alloy, crystals of the Al6Fe intermetallic compound formed along withα-Al crystals. Substitution of Y for 2 at.% of Al in the Al82Fe16Y2alloy made crystallization of the alloy more complicated:α-Al, Al6Fe, and Fe4Y crystals coexisted with an amorphous phase. The activation energies corresponding to the first crystallization event of the alloys were calculated using the Kissinger and Ozawa methods. The values obtained by these two methods were in good agreement with each other and the same trends of changing with the alloy composition were observed. The Avrami exponentnwas determined from the Johnson-Mehl-Avrami equation and showed that crystallization at the first stage is interface-controlled growth for all the three powder alloys studied.
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Chisholm, M. F., G. Duscher, Lixin Pang, and K. S. Kumar. "Nu-Phase in Fe-Al-B Alloys." Microscopy and Microanalysis 6, S2 (August 2000): 148–49. http://dx.doi.org/10.1017/s1431927600033237.

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FeAl alloys with 40 to 50 at % Al have an impressive combination of oxidation and sulfidation resistance, low density, and low cost and are thus considered as possible substitutes for stainless steels. However, before these materials can be used in structural applications, the fracture characteristics of the alloy's grain boundaries need to be improved. Small additions of carbon and boron have been considered and the resulting properties have been reported. Boron is found to prevent intergranular fracture in iron-rich alloys and to mitigate environmental embrittlement although the improvement is not as dramatic as is seen with Ni3Al alloyed with boron. Boron segregates to the grain boundaries in Fe-Al alloys and boride precipitates at the boundaries and within the grains have been observed.In this paper, we report the composition and atomic arrangement in a recently discovered phase (designated v phase) found in Fe-Al alloys containing small boron additions using a combination of Z-contrast imaging and electron energy-loss spectroscopy.
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Dissertations / Theses on the topic "Fe-Al alloys"

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Wang, Yun. "Solidification microstructure selection and coupled eutectic growth in Al-Fe and Al-Fe-Mn alloys." Thesis, University of Sheffield, 2000. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.324449.

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Conrod, Kevin. "The hot working characteristics of Al-0.65% Fe, and Al-0.5% Fe-0.5% Co conductor alloys." Thesis, National Library of Canada = Bibliothèque nationale du Canada, 2000. http://www.collectionscanada.ca/obj/s4/f2/dsk1/tape4/PQDD_0021/MQ54324.pdf.

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Ranganathan, Sathees. "Rapid solidification behaviour of Fe and Al based alloys." Doctoral thesis, KTH, Materialvetenskap, 2009. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-11325.

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Rapid solidification experiment on Fe-Cr-Mo-Mn-Si-C alloy was performed to investigate metastable phases formed during the solidification. A wide range of cooling rate was used to analyse the sample from melt spinning technique (~107 K/s) to water quenching method (~102 K/s). A single phase featureless structure was obtaind initially in the melt spinning experiment for 77Fe-8Cr-6Mn-5Si-4C alloy. Reduction of C and addition of Mo led to form a complete featureless structure for 2.85 mm rod for 72.8Fe-8Cr-5Mo-6Mn-5Si-3.2C. Subsequent investigation of influence of Mo, Cr and Mn on the single phase featureless structure concludes that 7.5 mm thick complete featureless phase could be formed at 63.8Fe-15Cr-7Mo-6Mn-5Si-3.2C alloy composition. In a separate attempt, powder samples of 40 μm dia. size complete featureless powders were produced for three slightly different compostions for the same alloy system. Characterisation of the featureless phases reveals that it could be a single phase metastable structure of ε phase or austenitic solid solution with high amount of alloying element dissolved in it. Subsequent heat treatment of this featureless phase of the rod and the powder at different temperatures formed bainitic ferrite with fine carbides dispersed in the austenitic matrix. Hardness values measured on featureless phase found to have influenced by the alloying element specially Mo, Cr and Mn. In an attempet to improve clean melting condition to extend the featureless phase and to form amorphous, an elliptic short arc lamp vaccum furnace was designed with 10 kW lamp power. Around 30 g of iron based alloy system was melted and cast as a 7 mm rod sample in a copper mould. Design details of new mirror and the lamp furnace are presented. In a separate study, influence of the melt temperature on Al-Y and Al-Si alloys were investigated by levitaion casting in a silver mould at around 2000 K/s cooling rate. Plate like structure of Al8Y3 primary phase was observed at low melt temperature with small percentage of peritectic transformation of Al8Y3 and liquid melt into Al9Y2. A pre-dentritic star like crystal of Al3Y was observed in a fine eutectic matrix at very high melt temperature. Amount and number of primary Si crystals formed in a unit area during the solidification increases as the melt temperature increases.
QC 20100805
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Stephen, Gail. "Al-Fe-Si intermetallics in 1000 series aluminum alloys." Thesis, McGill University, 1994. http://digitool.Library.McGill.CA:80/R/?func=dbin-jump-full&object_id=26424.

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Iron and silicon are the major impurities in the 1000 series of wrought aluminum alloys. As the aluminum is recycled, it picks up more and more of these impurities which cannot economically be refined out of the aluminum. When the concentration of these impurities reaches a certain limit (maximum limit in 1000 series is 1 weight percent (Fe+Si)), the aluminum must be downgraded. The Fe and Si form brittle intermetallic phases in these alloys. The two main phases are the plate-like $ beta$-AlFeSi (Al$ sb5$FeSi) and $ alpha$-AlFeSi (Al$ sb8$Fe$ sb2$Si) which has a Chinese Script morphology. The mechanical properties of these alloys are believed to depend largely on the nature of these intermetallics.
In the first part of this study, the conditions at which the intermetallics form, along with the ability of strontium to modify them were investigated. The second part consisted of determining how the morphology of the Al-Fe-Si phases affects the mechanical properties of the worked product. It was found that the formation of the Chinese Script morphology is promoted with increasing cooling rates, Fe/Si ratios and additions of strontium. However, the relative amount of Chinese Script was found to decrease with increasing (Fe+Si) levels. Tensile testing and formability testing (Erichsen ball punch deformation test) revealed that the presence of a Chinese Script morphology of Al-Fe-Si intermetallics (as opposed to the plate-like morphology) imparts no significant beneficial effect on the formability of the final rolled sheet.
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Maggs, Steven James. "Intermetallic phase selection in dilute Al-Fe-Si alloys." Thesis, University of Leeds, 1996. http://etheses.whiterose.ac.uk/4711/.

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The DC casting of 1000 series AI-Fe-Si alloys often results in the formation of a defect known as the Fir Tree Zone (FI'Z) caused by variations in the type of binary AI-Fe eutectic intennetallic phase. These include AI3Fe, which is the equilibrium phase, and ~Fe, AImFe and AlxFe which are all common metastable phases found in DC cast ingots. Variation in the solidification conditions across a DC cast ingot.in particular, the cooling rate and local solidification velocity, bring about transitions from one intennetallic phase to another. The composition of the alloy, especially the presence of minor trace elements is also known to affect the transitions, but its effect has been less well studied. Equipment was constructed which reliably simulated DC casting conditions and enabled the FfZ to be reproduced. Experiments were conducted to examine the effect of the concentration of Fe, Si (and Fe:Si ratio) and of low levels «0.04 wt %) of Mg, Ti, Ti-B, V and Mn on the occurrence of phases causing the defect. Intennetallic phases extracted from the matrix by dissolution in hot butanol were identified by XRD. It was found that presence of Ti-B grain refmer had a large effect on the intennetallic phase selection, whilst the other trace element additions had lesser effects. In order to understand the way in which each element was affecting phase selection, experiments were conducted using DSC and a Bridgman furnace to isolate the variables of cooling rate and growth velocity respectively. A curve fitting technique was used to obtain values of eutectic nucleation onset temperature from DSC data where the primary aluminium and eutectic peaks overlapped. A technique was developed to extract intennetallic particles from DSC samples for examination in the TEM. It was found that the addition Ti-B grain refmer affected the phase selection by altering the nucleation temperature. The addition of Mg was found to stabilise the equilibrium phase by its affect on both growth temperature an nucleation temperature The effect of Ti was less clear in that it stabilised the equilibrium phase in the DSC experiments but tended to stabilise the metastable phase in the Bridgman experiments.
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Kangouei, Navid. "Study of Equilibrium State in Fe-Mn-Al-C Alloys." Thesis, KTH, Termodynamisk modellering, 2014. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-148223.

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We are living in a world of steel. Although there are a lot of other material in use, our most used material is steel. From building industry to transportation and even mother industries like mining, we use steel in different grades and amounts. There is always need for different grades of steel, and there is always interest in better properties and lower costs. Fe-Mn-Al-C steel group is one of the grades of steel is from the TWIP family. Beside its interesting mechanical properties, its corrosion resistance and cryogenic properties makes it very desirable to substitute more expensive current classes of the steel used in the industry. The automobile industry is also looking forward to implement this family of the steel in their products. This group of steel based on their chemical content can created a carbide ordered phase called κ which is one of the reasons of its interesting mechanical properties beside the TWIP properties. While κ may give more hardness due to precipitation hardening, it will make the steel brittle. Thus we need an understanding of the phase diagram of this group of the steels in order to choose our material and process accordingly. Phase diagrams are material engineers’ road maps for the processes and material choice as the initial steps, since we can predict the processes results and stable phases based on the equilibrium state from the diagrams. As the number of components gets more than three the phase diagram calculations and determination gets harder. For the ternary alloying systems we can only show sections of the phase diagrams as isothermal sections, or consider an element constant and depict the diagram as a “binary” system for the other two alloying elements at the other element concentration. In this work, we tried to experiment on the experimental data for equilibrium phases of Fe-Mn-Al-C alloying system based on the Equilibrated Alloys for alloys containing 20, 30 and 40 weight percent Manganese. The results were compared to the current database of the Thermo-Calc software for this family and we found some inconsistencies between the experimental data and the calculations which shows that the calculated results for this alloying system with its high Mn-content, is not reliable and that the thermodynamic descriptions must be adjusted.
PrecHiMn (RFSR-CT-2010-00018)
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Humphreys, Elen Siobhain. "Production and characterisation of rapidly solidified Al-V-Fe alloys." Thesis, University of Oxford, 1999. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.302070.

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Park, Woonsup. "Migration kinetics of antiphase boundaries in Fe-Al ordered alloys." Thesis, Massachusetts Institute of Technology, 1988. http://hdl.handle.net/1721.1/54326.

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Li, Xiaolin [Verfasser], Gerhard [Gutachter] Dehm, and Easo P. [Gutachter] George. "Al-rich Fe-Al based alloys / Xiaolin Li ; Gutachter: Gerhard Dehm, Easo P. George." Bochum : Ruhr-Universität Bochum, 2017. http://d-nb.info/1129452034/34.

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Clauß, Arno Rainer. "Nitriding of Fe-Cr-Al alloys nitride precipitation and phase transformations /." Stuttgart : Max-Planck-Inst. für Metallforschung, 2008. http://d-nb.info/995395918/34.

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Books on the topic "Fe-Al alloys"

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Wysłocki, Jerzy J. Mechanizm koercji magnetycznie twardego anizotropowego stopu Fe-Al-C. Częstochowa: Wydawn. Politechgniki Częstochowskiej, 1996.

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Bi, Yunjie. Microstructural studies of RSP AL/V and AL/MO/Fe alloys. Birmingham: University of Birmingham, 1988.

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Ferguson, David Bruce. Characterization of high damping Fe-Cr-Mo and Fe-Cr-Al alloys for naval ships application. Monterey, California: Naval Postgraduate School, 1988.

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Dunning, J. S. Effects of Al additions on sulfidation resistance of some Fe-Cr-Ni alloys. Washington, D.C: Bureau of Mines, U.S. Dept. of the Interior, 1989.

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HabibollahZadeh, Ali. Fluidity of Al-and Fe- based eutectic alloys at high velocity in thin sections: Ey Ali HabibollahZadeh. Birmingham: University of Birmingham, 2001.

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Bray, D. J. The fatigue crack growth properties of vapour deposited Al-Cr-Fe alloy sheet. London: HMSO, 1985.

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United States. National Aeronautics and Space Administration., ed. Thermodynamic analysis of chemical compatability of several compounds with Fe-Cr-Al alloys. [Washington, DC]: NASA National Aeronautics and Space Administration, 1993.

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United States. National Aeronautics and Space Administration., ed. Thermodynamic analysis of chemical compatability of several compounds with Fe-Cr-Al alloys. [Washington, DC]: NASA National Aeronautics and Space Administration, 1993.

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Hecht, Ulrike, Mark L. Weaver, and Sheng Guo, eds. Dual-phase Materials in the Medium and High Entropy Alloy Systems Al-Cr-Fe-Ni and Al-Co-Cr-Fe-Ni. Frontiers Media SA, 2021. http://dx.doi.org/10.3389/978-2-88971-225-0.

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Ternary Alloy Systems, Phase Diagrams, Crystallographic and Thermodynamic Data: Iron Systems, Part 1: Selected Systems from Al-B-Fe to C-Co-Fe. Berlin, Heidelberg: Springer Berlin Heidelberg, 2008.

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Book chapters on the topic "Fe-Al alloys"

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Fe-Nd." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 211–16. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_64.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Fe-Pr." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 222–23. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_67.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Fe-Sm." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 227. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_69.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Fe-Y." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 230–31. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_71.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-B-Fe (012)." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 79–80. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_19.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Ca-Fe (017)." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 86–87. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_24.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Co-Fe (030)." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 128. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_37.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Cu-Fe (041)." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 155–57. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_50.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Fe-Gd (051)." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 207–8. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_61.

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Carow-Watamura, U., D. V. Louzguine, and A. Takeuchi. "Al-Fe-Ge (052)." In Physical Properties of Ternary Amorphous Alloys. Part 1: Systems from Ag-Al-Ca to Au-Pd-Si, 209. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-03481-7_62.

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Conference papers on the topic "Fe-Al alloys"

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"The Structural Phase Diagrams of Fe-Y (Y = Ga, Ge, Al) Alloys." In Shape Memory Alloys 2018. Materials Research Forum LLC, 2018. http://dx.doi.org/10.21741/9781644900017-31.

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"Thermomechanical and Magnetic Properties of Fe-Ni-Co-Al-Ta-B Superelastic Alloy." In Shape Memory Alloys 2018. Materials Research Forum LLC, 2018. http://dx.doi.org/10.21741/9781644900017-7.

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Zhou, Z. C., Z. C. Shen, Z. Jiang, and F. S. Han. "Magnetomechanical hysteresis damping in Fe-Al alloys." In SPIE Proceedings, edited by Jose F. Lopez, Chenggen Quan, Fook Siong Chau, Francisco V. Fernandez, Jose Maria Lopez-Villegas, Anand Asundi, Brian Stephen Wong, Jose M. de la Rosa, and Chwee Teck Lim. SPIE, 2005. http://dx.doi.org/10.1117/12.621903.

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Wun-Fogle, M., J. B. Restorff, and A. E. Clark. "Magnetomechanical Coupling in Stress Annealed Fe-Ga and Fe-Al Alloys." In INTERMAG 2006 - IEEE International Magnetics Conference. IEEE, 2006. http://dx.doi.org/10.1109/intmag.2006.376403.

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Bendjeddou, L., M. Y. Debili, A. Fekrache, and S. Boulkhessaim. "Structural features of ternary Al-Fe-Ti alloys." In 2008 2nd ICTON Mediterranean Winter (ICTON-MW). IEEE, 2008. http://dx.doi.org/10.1109/ictonmw.2008.4773105.

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Guanabara, Paulo, Levi de O. Bueno, Gilmar Ferreira Batalha, Francisco Chinesta, Yvan Chastel, and Mohamed El Mansori. "Towards a Superplastic Forming of Fe-Mn-Al Alloys." In INTERNATIONAL CONFERENCE ON ADVANCES IN MATERIALS AND PROCESSING TECHNOLOGIES (AMPT2010). AIP, 2011. http://dx.doi.org/10.1063/1.3552435.

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Rodríguez, D. Martín. "Magnetic Evolution with Composition on Fe-rich Fe-Al Alloys by Mössbauer spectroscopy." In INDUSTRIAL APPLICATIONS OF THE MOSSBAUER EFFECT: International Symposium on the Industrial Applications of the Mossbauer Effect. AIP, 2005. http://dx.doi.org/10.1063/1.1923660.

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Sporer, Dieter R., and Ingo Reinkensmeier. "High Vacuum Brazing of Fe-Cr-Al-Y Honeycomb." In ASME Turbo Expo 2004: Power for Land, Sea, and Air. ASMEDC, 2004. http://dx.doi.org/10.1115/gt2004-53407.

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Abstract:
M-Cr-Al-Y and in particular Fe-Cr-Al-Y alloys with high aluminium matrix content have a tendency to form thin, stable and tightly adherent alumina scales even at low oxygen partial pressures. This forms the basis of their superior hot gas oxidation, carburization and sulfidation resistance when used at high temperatures. However, the same tendency makes the alloys more difficult to braze because the easily formed and highly stable ceramic surface layers significantly reduce wettability and hence braze flow. Fe-Cr-Al-Y alloys have recently been suggested as promising alloys for use in gas turbine engines as abradable honeycomb gas path seals. This paper reviews the vacuum brazing of honeycombs made from highly alloyed Fe-Cr-Al-Y foils to metal backing members. Most suitable Fe-Cr-Al-Y materials, commercial braze filler alloys and braze cycles are presented. Emphasis is placed on industrial equipment rather than laboratory vacuum furnaces. Brazing under high vacuum conditions in all-metal furnaces is recommended as a brazing procedure for honeycomb made from MI 2100, which is high in aluminium content, to various commonly used carrier structure alloys.
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Zhou, Z. C., J. Du, Y. K. Zhang, Y. P. Zhang, and S. Y. Gu. "The Vacancy-hardening Properties in Water-quenched Fe-Al Alloys." In 2015 International Conference on Material Science and Applications (icmsa-15). Paris, France: Atlantis Press, 2015. http://dx.doi.org/10.2991/icmsa-15.2015.7.

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LATUCH, J., A. KOKOSZKIEWICZ, and H. MATYJA. "NANOCRYSTALLINE Al-Y-Ni-Fe ALLOYS PREPARED BY RAPID QUENCHING." In Proceedings of the Fifth International Workshop on Non-Crystalline Solids. WORLD SCIENTIFIC, 1998. http://dx.doi.org/10.1142/9789814447225_0068.

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Reports on the topic "Fe-Al alloys"

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Wright, I. G., B. A. Pint, P. F. Tortorelli, and C. G. McKamey. Development of ODS-Fe{sub 3}Al alloys. Office of Scientific and Technical Information (OSTI), December 1997. http://dx.doi.org/10.2172/330684.

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Prichard, Paul D. The structure-property relationships of powder processed Fe-Al-Si alloys. Office of Scientific and Technical Information (OSTI), February 1998. http://dx.doi.org/10.2172/654137.

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Field, Kevin G., Richard H. Howard, and Yukinori Yamamoto. Design of Experiment for Irradiation of Welded Candidate Fe-Cr-Al Alloys. Office of Scientific and Technical Information (OSTI), July 2015. http://dx.doi.org/10.2172/1209215.

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Joslin, D. L., D. S. Easton, C. T. Liu, and S. A. David. The effects of processing variables on reaction synthesis of Fe-Al alloys. Office of Scientific and Technical Information (OSTI), December 1994. http://dx.doi.org/10.2172/28365.

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Briggs, Samuel A. Correlative Microscopy of Alpha Prime Precipitation in Neutron-Irradiated Fe-Cr-Al Alloys. Office of Scientific and Technical Information (OSTI), December 2016. http://dx.doi.org/10.2172/1376614.

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Field, Kevin G., Xunxiang Hu, Ken Littrell, Yukinori Yamamoto, Richard H. Howard, and Lance Lewis Snead. Stability of Model Fe-Cr-Al Alloys Under The Presence of Neutron Radiation. Office of Scientific and Technical Information (OSTI), September 2014. http://dx.doi.org/10.2172/1157142.

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Alven, D. A., and N. S. Stoloff. The effects of composition on the environmental embrittlement of Fe{sub 3}Al alloys. Office of Scientific and Technical Information (OSTI), December 1997. http://dx.doi.org/10.2172/330673.

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Tortorelli, P. F., B. A. Pint, and I. G. Wright. High-temperature corrosion behavior of coatings and ODS alloys based on Fe{sub 3}Al. Office of Scientific and Technical Information (OSTI), June 1996. http://dx.doi.org/10.2172/450765.

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Banovic, S. W., J. N. DuPont, and A. R. Marder. Processing and structure of in situ Fe-Al alloys produced by gas tungsten arc welding. Office of Scientific and Technical Information (OSTI), February 1997. http://dx.doi.org/10.2172/672118.

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Patra, Anirban, Wei Wen, Enrique Martinez Saez, and Carlos Tome. A defect density-based constitutive crystal plasticity framework for modeling the plastic deformation of Fe-Cr-Al cladding alloys subsequent to irradiation. Office of Scientific and Technical Information (OSTI), February 2016. http://dx.doi.org/10.2172/1237412.

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