Interaction of hydrogen-absorbing intermetallic compound tife with hydrogen IV. Mechanism of oxidation of TiFe

1996 ◽  
Vol 35 (5-6) ◽  
pp. 290-295 ◽  
Author(s):  
V. G. Chuprina
Keyword(s):  
Intermetallic Compound ◽  
Mechanism Of Oxidation ◽  
Compound Tife ◽  
Intermetallic Compound Tife

Mechanical alloying of nanocrystalline intermetallic compound TiFe doped with sulfur and magnesium

2014 ◽  
Vol 615 ◽  
pp. S569-S572 ◽  
Author(s):  
V. Yu. Zadorozhnyy ◽  
S.N. Klyamkin ◽  
M. Yu. Zadorozhnyy ◽  
M.V. Gorshenkov ◽  
S.D. Kaloshkin
Keyword(s):  
Intermetallic Compound ◽  
Mechanical Alloying ◽  
Compound Tife ◽  
Intermetallic Compound Tife

Hydriding of powder alloys based on the intermetallic compound TiFe

1993 ◽  
Vol 32 (4) ◽  
pp. 330-334 ◽  
Author(s):  
V. D. Dobrovol'skii ◽  
S. N. Endrzheevskaya ◽  
L. I. Kopylova ◽  
V. V. Skorokhod ◽  
L. V. Strashinskaya ◽  
...  
Keyword(s):  
Intermetallic Compound ◽  
Powder Alloys ◽  
Compound Tife ◽  
Intermetallic Compound Tife

Mechanical alloying of nanocrystalline intermetallic compound TiFe doped by aluminum and chromium

2014 ◽  
Vol 586 ◽  
pp. S56-S60 ◽  
Author(s):  
V.Yu. Zadorozhnyy ◽  
S.N. Klyamkin ◽  
M.Yu. Zadorozhnyy ◽  
O.V. Bermesheva ◽  
S.D. Kaloshkin
Keyword(s):  
Intermetallic Compound ◽  
Mechanical Alloying ◽  
Compound Tife ◽  
Intermetallic Compound Tife

Investigation of the structure and properties of hypereutectic Ti-based bulk alloys

2004 ◽  
Vol 842 ◽  
Author(s):  
Dmitri V. Louzguine-Luzgin ◽  
Larissa V. Louzguina-Luzgina ◽  
Akihisa Inoue
Keyword(s):  
Mechanical Properties ◽  
Solid Solution ◽  
Intermetallic Compound ◽  
Deformation Behaviour ◽  
High Strength ◽  
Solid Solution Phase ◽  
Mn Additions ◽  
Bulk Alloys ◽  
Compound Tife ◽  
Intermetallic Compound Tife

ABSTRACTStructure and mechanical properties of binary Ti-TM (TM-other transition metals) and ternary Ti-Fe-(TM, B or Si) alloys produced in the shape of the arc-melted ingots of about 25 mm diameter and 10 mm height are studied. The formation of high-strength and ductile hypereutectic alloys was achieved in the Ti-Fe, Ti-Fe-Cu and Ti-Fe-B systems. The structures of the high-strength and ductile hypereutectic alloys studied by X-ray diffractometry and scanning electron microscopy were found to consist of the primary cubic Pm3 m intermetallic compound (TiFe-phase or a solid solution on its base) and a dispersed eutectic consisting of this Pm3m intermetallic compound + BCC Im 3 m β-Ti supersaturated solid solution phase. The hypereutectic Ti-Fe alloy showed excellent compressive mechanical properties. The addition of Cu improves its ductility. B addition increased mechanical strength. Ni, Cr and Mn additions caused embrittlement owing to the formation of alternative intermetallic compounds. The deformation behaviour and the fractography of the Ti-based alloys were studied in details. The reasons for the high strength and good ductility of the hypereutectic alloys are discussed.

Dislocation Substructures Produced During Tensile, Creep, and Fatigue Deformation of Ti3Al at 700°C

1977 ◽  
Vol 35 ◽  
pp. 272-273
Author(s):  
S. M. L. Sastry
Keyword(s):  
Intermetallic Compound ◽  
Strain Rate ◽  
Tensile Creep ◽  
Slip Systems ◽  
Slip Vector ◽  
Superlattice Structure ◽  
Slip Activity ◽  
Dislocation Arrangement ◽  
Ordered Intermetallic ◽  
Tangled Dislocation

Ti3Al is an ordered intermetallic compound having the DO19-type superlattice structure. The compound exhibits very limited ductility in tension below 700°C because of a pronounced planarity of slip and the absence of a sufficient number of independent slip systems. Significant differences in slip behavior in the compound as a result of differences in strain rate and mode of deformation are reported here.Figure 1 is a comparison of dislocation substructures in polycrystalline Ti3Al specimens deformed in tension, creep, and fatigue. Slip activity on both the basal and prism planes is observed for each mode of deformation. The dominant slip vector in unidirectional deformation is the a-type (b) = <1120>) (Fig. la). The dislocations are straight, occur for the most part in a screw orientation, and are arranged in planar bands. In contrast, the dislocation distribution in specimens crept at 700°C (Fig. lb) is characterized by a much reduced planarity of slip, a tangled dislocation arrangement instead of planar bands, and an increased incidence of nonbasal slip vectors.

Sign in / Sign up

Export Citation Format

Share Document