The influence of machining time, ultrasonic amplitude, spindle speed and machining gap on surface roughness and material removal rate were studied and analysed through the experiment of UAMAF of titanium alloy. The results show that the surface roughness decreases rapidly in the beginning and then gradually stabilizes as the machining time increases. The surface roughness reduces from the original Ra0.94μm to Ra0.10μm, when the machining time reaches 30min that is optimum machining time. The material removal rate drops approximately linearly with the increase of machining time. The surface roughness decreases significantly and the material removal rate increases rapidly as the ultrasonic amplitude rises. The surface roughness reduces to Ra0.12μm and the material removal rate increases to 30.5mg/h, when the ultrasonic amplitude is up to 14μm. The surface roughness decreases in the beginning and then increases, and the material removal rate rises in the beginning and then falls, as the spindle speed increases. The surface roughness achieves a minimum of Ra0.11μm and the material removal rate reaches a maximum of 22.74mg/h, when the spindle speed is 1400r/min. The surface roughness drops in the beginning and then rises, and the material removal rate increases in the beginning and then decreases, as the machining gap enlarges. The optimum machining gap is about 1.25mm. In this case, the surface roughness achieves a minimum of Ra0.16μm, and the material removal rate reaches a maximum of 17.7mg/h.
The non-oriented Fe-6.5wt.%Si alloy cast strip with a width of 100 mm and a thickness of 1.7 mm was prepared by the top side-pouring twin-roll casting (TSTRC) process. The surface quality of the air-cooled and water-cooled cast strip was good. Compared with the Fe-6.5wt.%Si alloy ingot, the Fe-6.5wt.%Si alloy cast strip has a relatively ne solidi cation structure and exhibits certain plasticity at room temperature.Microhardness, XRD, and TEM investigated the ordered structure and degree of Fe-6.5wt.%Si alloys prepared by three different cooling methods. The results show that the Fe-6.5wt.%Si alloy ingot prepared by the standard method has many B 2 ordered phases and DO 3 ordered phases, and the order degree is high. The Fe-6.5wt.%Si alloy cast strip prepared by the TSTRC process has a low degree of order and only contains a small B 2 ordered phase. The faster cooling rate effectively inhibits the formation of the DO 3 ordered phase and B 2 ordered phase. The growth of the ordered phase also reduces the reverse domain boundary energy, reduces the motion resistance of superdislocations, and increases its mobility, thereby improving the room temperature plasticity of Fe-6.5wt.%Si alloy cast strips.
The non-oriented Fe-6.5wt.%Si alloy cast strip with a width of 100 mm and a thickness of 1.7 mm was prepared by the top side-pouring twin-roll casting (TSTRC) process. The surface quality of the air-cooled and water-cooled cast strip was good. Compared with the Fe-6.5wt.%Si alloy ingot, the Fe-6.5wt.%Si alloy cast strip has a relatively fine solidification structure and exhibits certain plasticity at room temperature. Microhardness, XRD, and TEM investigated the ordered structure and degree of Fe-6.5wt.%Si alloys prepared by three different cooling methods. The results show that the Fe-6.5wt.%Si alloy ingot prepared by the standard method has many B2 ordered phases and DO3 ordered phases, and the order degree is high. The Fe-6.5wt.%Si alloy cast strip prepared by the TSTRC process has a low degree of order and only contains a small B2 ordered phase. The faster cooling rate effectively inhibits the formation of the DO3 ordered phase and B2 ordered phase. The growth of the ordered phase also reduces the reverse domain boundary energy, reduces the motion resistance of superdislocations, and increases its mobility, thereby improving the room temperature plasticity of Fe-6.5wt.%Si alloy cast strips.
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