Deformation behaviour and oxidation resistance of single-phase and two-phase L21-ordered Fe–Al–Ti alloys

Palm, Martin; Sauthoff, Gerhard

doi:10.1016/j.intermet.2004.03.017

Cited by 99 publications

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“…7 Isothermal section of the Fe-Al-Ti system at 1173 K. 10) alloys only at temperatures below 823 K, 12,13) and the Ti addition in the Fe-Al binary alloys would result in a particularly large increase of the D0 3 (L2 1 )!B2 transition temperature about 60 K/at%. [6][7][8][9][10][11] Obviously, the Ti concentration would be the predominant factor for the stabilization of the L2 1 phase at high temperature. In our previous study of the Fe-23 at% Al-8.5 at% Ti alloy aged at 1173 K for 6-24 h, 14) it was found that the Ti concentration in the wellgrown L2 1 domains was up to about 11.1 at%, therefore, the L2 1 phase exhibited more stable and no evidence of the phase separation could be detected.…”

Section: Resultsmentioning

confidence: 99%

“…This feature has never been reported by other workers in the Fe-Al-Ti alloy systems before. Extending the previous work, the purpose of this study is an attempt to examine the microstructural developments of the Fe-24.6 at% Al-7.5 at% Ti alloy aged at 1173 K. It is noted that according to the previously established isothermal sections of Fe-Al-Ti ternary alloys at 1173 K, [6][7][8][9][10][11] the chemical compositions of both the previous alloy and the present alloy are just located in the (B2+L2 1 ) region. However, the chemical composition of the present alloy is much closer to the A2/B2/L2 1 apex than that of the previous alloy.…”

Section: Introductionmentioning

confidence: 92%

“…In previous studies, [1][2][3][4][5][6][7][8][9][10][11] it is seen that the Ti addition in the Fe-Al binary alloys would (1) strongly increase the D0 3 !B2 and B2!A2 transition temperatures, [1][2][3][4][5][6][7][8][9][10] (2) significantly expand the (A2+D0 3 ) phase field, [5][6][7] and (3) cause the D0 3 APBs to exhibit a tendency toward anisotropy. 6) In addition, a (B2+L2 1 ) (L2 1 is the ternary equivalent of the binary D0 3 structure.…”

Section: Introductionmentioning

confidence: 99%

“…3) ) two-phase field was reported to be existent at temperatures ranging from 1073 to 1273 K in the Fe-Al-Ti ternary alloys. [7][8][9][10][11] It is noted that the (B2+D0 3 ) two-phase field has not been found by previous workers in the Fe-Al binary alloys before. 12,13) However, the existence of the (B2+L2 1 ) two-phase field in the Fe-Al-Ti ternary alloys was determined principally by using X-ray diffraction, differential scanning calorimetry, differential thermal analysis and electron-probe microanalysis.…”

Section: Introductionmentioning

confidence: 99%

“…12,13) However, the existence of the (B2+L2 1 ) two-phase field in the Fe-Al-Ti ternary alloys was determined principally by using X-ray diffraction, differential scanning calorimetry, differential thermal analysis and electron-probe microanalysis. [7][8][9][10][11] Recently, we have performed transmission electron microscopy (TEM) investigations on the phase transformations of a Fe-23 at% Al-8.5 at% Ti alloy aged at 1173 K. 14) Consequently, it was found that when the alloy was aged at 1173 K for longer times, the L2 1 domains grew considerably and an A2! (A2+L2 1 )!…”

Section: Introductionmentioning

confidence: 99%

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Phase Separation from L21 to (B2+L21) in Fe-24.6Al-7.5Ti Alloy

Tsay

Tuan

et al. 2010

Mater. Trans.

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As-quenched microstructure of the Fe-24.6 at% Al-7.5 at% Ti alloy was a mixture of (A2+L2 1 ) phases. When the as-quenched alloy was aged at 1173 K for moderate times, the L2 1 domains grew considerably and B2 phase was formed at a/2h100i anti-phase boundaries (APBs) as well as phase separation from well-grown L2 1 to (B2+L2 1 Ã ) occurred basically contiguous to the APBs, where L2 1 Ã is also a L2 1 -type phase. With continued aging at 1173 K, the phase separation would proceed toward the whole well-grown L2 1 domains. This microstructural evolution has not been reported in the Fe-Al-Ti alloy systems before.

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Section: Resultsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 92%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

See 3 more Smart Citations

Phase Separation from L21 to (B2+L21) in Fe-24.6Al-7.5Ti Alloy

Tsay

Tuan

et al. 2010

Mater. Trans.

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Intermetallics

Sauthoff

2006

Ullmann's Encyclopedia of Industrial Chemistry

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The article contains sections titled: 1. Introduction 1.1. Definition of Intermetallics 1.2. Historical Remarks 2. General Considerations 2.1. Crystal Structure and Compound Stability 2.2. Basic Properties 2.3. Criteria for Compound Selection 3. Magnetic Materials 3.1. AlNiCo Alloys 3.2. FeCo Alloys 3.3. Sendust Alloy 3.4. Laves Phases 3.5. Rare‐Earth Compounds 4. Superconducting Materials 4.1. Laves Phases 4.2. A15 Compounds 4.2.1. V 3 Si 4.2.2. V 3 Ga 4.2.3. Nb 3 Sn 4.2.4. Nb 3 Al 4.2.5. Nb 3 Si 5. Electronic Materials 5.1. Silicides 5.2. Other Compounds 6. Electric Materials 7. Thermoelectric and Thermomagnetic Materials 7.1. Silicides 7.2. Other Thermoelectric Compounds 7.3. Thermomagnetic Compounds 8. Optical Materials 9. Hydrogen‐Storage Materials 9.1. B2 Compounds 9.2. Laves Phases 9.3. Rare Earth Metal Compounds and Other Phases 10. Electrode Materials 10.1. Mg 2 Ni Alloys 10.2. Laves Phase Alloys 10.3. RNi 5 Alloys 11. Coating Materials 11.1. Aluminides 11.2. Silicides 12. Shape‐Memory Materials 12.1. Cu‐Base Alloys 12.1.1. Cu ‐ Zn ‐ Al Shape Memory Alloys 12.1.2. Cu ‐ Al ‐ Ni Shape‐Memory Alloys 12.2. NiAl Alloys 12.3. NiTi Alloys 13. Medical Biomaterials 14. Dental Materials 14.1. Amalgams 14.2. Cu ‐ Au Alloys 15. Wear‐Resistant Materials 16. Structural High‐Temperature Materials 16.1. Titanium Aluminide Alloys 16.1.1. Ti 3 Al Alloys 16.1.2. TiAl Alloys 16.2. Iron Aluminide Alloys 16.2.1. Fe 3 Al Alloys 16.2.2. FeAl Alloys 16.3. Nickel Aluminide Alloys 16.3.1. Ni 3 Al alloys 16.3.2. NiAl Alloys 16.4. Silicide Alloys

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Recent Developments Toward the Application of Iron Aluminides in Fossil Fuel Technologies

Morris¹,

Muñoz-Morris²

2010

Adv Eng Mater

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Iron aluminides are of interest for applications in power generation from fossil fuels because of excellent high temperature oxidation–corrosion resistance in aggressive environments and are potential replacements for high temperature steels. The Fe‐base composition ensures relative cheapness, while the high Al content leads to significant density reduction over commercial steels. Problems of low ductility/toughness at room temperature and poor high temperature (creep) strength, however, have prevented significant commercial use. After studies led by Oak Ridge National Laboratory (USA) from about 1980 to 2000, research has continued in Europe both as pan‐European efforts and as national efforts in countries such as the Czech Republic, France, Germany and Spain. An overview of such recent activities is presented, indicating the research strategies involved, and the progress toward making iron aluminides useful engineering materials. Recent activities have targeted microstructural refinement through novel processing to improve room temperature ductility or attempted alloying additions to improve high temperature strength. Achieving the required properties remains difficult, and has led to developments of iron aluminides as cast components and as coatings.

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Deformation behaviour and oxidation resistance of single-phase and two-phase L21-ordered Fe–Al–Ti alloys

Cited by 99 publications

References 62 publications

Phase Separation from L2<SUB>1</SUB> to (B2+L2<SUB>1</SUB>) in Fe-24.6Al-7.5Ti Alloy

Phase Separation from L2<SUB>1</SUB> to (B2+L2<SUB>1</SUB>) in Fe-24.6Al-7.5Ti Alloy

Intermetallics

Recent Developments Toward the Application of Iron Aluminides in Fossil Fuel Technologies

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