Microstructure and Hydrogenation Behaviour of （Ti₆₅Fe₃₅）_100-xV_x Ternary Alloy AITranslate

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Basic Information:

DOI：10.13373/j.cnki.cjrm.XY22120020

Chinese Library Classification Number:TG146

Citation Information:

Group 5B metals （Nb，V and Ta） and related alloys are considered as promising hydrogen permeation membranes to replace commercial Pd and its alloys. Vanadium-based alloys，as a new substitute for Pd membranes，not only have lower cost but also higher hydrogen permeability. Despite all this，huge challenges remain-especially the poor mechanical stability and high susceptibility to hydrogen embrittlement （HE） which is closely related to high absorbed hydrogen concentration of vanadium. Among group 5B alloys，hydrogenation （thermal-hydrogen treatment technology） has obvious advantages in improving the properties of V-based alloys.However，no relevant research has been carried out on V-TiFe alloys so far. Based on this，the hydrogenation behavior of （Ti₆₅Fe₃₅）_100-xV_x （x=0，2.5，5，10，15，25），x is the percentage of atoms of V） alloys with low cost and high hydrogen permeability were explored. In the solid state，two operating processes of static hydrogenation and dynamic hydrogenation were used，besides，the effects of hydrogen flow，hydrogenation time and hydrogenation temperature （350 and 450 ℃） on the hydrogenation behavior of the above alloys with different V content were systematically studied by the control variable method. The solidification path，microstructure evolution and mechanical properties of the alloy were analyzed by thermodynamic calculation software （Thermo-Calc），scanning electron microscope （SEM），energy spectrometer （EDS），X-ray diffraction meter （XRD），and Vickers hardness tester. First，the composition-temperature curve obtained from the thermodynamic solidification data of Thermo-Calc using the origin software found that： when 0<x<8，the primary phase was TiFe；when x=8，the alloy appeared fully eutectic；and when 8<x<25，the primary phase was body-centered cubic （bcc）-V.With the decrease of solidification temperature，binary and ternary eutectic reactions occurred successively until the end of solidification. Subsequently，the phase analysis of （Ti₆₅Fe₃₅）_100-xV_x cast alloys by XRD，SEM and EDS showed that： when 0<x<10，the alloy was composed of the primary TiFe phase and {bcc-（V，Ti）+TiFe} phase；when x=10，the alloy consisted of a divorced eutectic {β-Ti+TiFe}；when x>10，the alloy consistd of a primary bcc-（V，Ti） solid solution phase and a small amount of TiFe phase. In addition，exploring the changes of hydrogenation amount of （Ti₆₅Fe₃₅）_100-xV_x alloys caused by the difference in hydrogen flow，hydrogenation time and hydrogenation temperature，it was found that： when V content was constant，the hydrogenation effect of alloys was proportional to the variable parameters under any single variable parameter such as hydrogen flow，hydrogenation time and hydrogenation temperature，in other words，when the hydrogenation temperature and hydrogen flow kept a constant，the hydrogenation amounts of the alloy grew with the increase of hydrogenation time. After the hydrogenation time reached a certain level，the hydrogenation amount reached the maximum and tends to be stable，the alloy composition also had a decisive influence on the hydrogenation amount of the alloy besides，that was to say，it would cause an increase in hydrogenation with the increase of V content. Finally，the mechanical properties of all alloys of the system were studied，and the hardness of the cast microstructure of （Ti₆₅Fe₃₅）_100-xV_x cast alloys and the hardness after hydrogenation at 350 and 450 ℃ were measured using Vickers hardness tester. The hardness of the alloy of the hydrogenated V-TiFe system was significantly enhanced compared with the alloy sample before hydrogenation，that was，Vickers hardness of （Ti₆₅Fe₃₅）₈₅V₁₅ alloy after hydrogenation at 450 ℃ was HV_0.3 720.4，which was equivalent to 1.12 times before hydrogenation，and the hardness increased with the increase of hydrogenation temperature，which could be attributed to the solid solution strengthening of H atom inside the alloy and the precipitation of hydrides.