In the AleSneCu ternary system, for compositions where themiscibility gap is stabilized, one of the main challenges in themanufacturing process is to cross the large liquidus-solidus temperature range. This characteristic can lead to an inhomogeneousdistribution of b-Sn particles. The liquid immiscibility causes severesegregation mainly due to the large density difference between theAl-rich and Sn-rich liquids. It was reported that the monotecticreaction is very sensitive to the level of gravity and the undercooling condition prior to crystallization, [23,24]. Even undermicrogravity conditions, a coarse phase separation occurs due tothe Marangoni motion [25]. However, the use of rapid solidificationcan allow obtaining an homogeneous refined microstructure evenwhen the solidification pathway involve a stable or metastablemiscibility gap [10,19,22,23,26e28].The traditional plain bearing manufacturing process uses beltcasting of thick Al20Sn1Cu strips followed by several rolling passesto reduce the thickness and join the “antifriction” material to an Alinterlayer and this to the steel of the bearing back. In this work, theAl20Sn1Cu alloy was produced by rapid solidification which allowsa solidification pathway throughout the metastable miscibility gap.Also, the effect of the Mn addition on the microstructure andproperties was studied. The melt-spinning technique was used toobtain thin ribbons with a refined microstructure and improvedmechanical and surface properties. It is expected to reduce rollingpasses needed to manufacture plain bearings and to obtain a material with higher strength and wear resistance that improve theperformance of the Al20Sn1Cu alloy currently used in plainbearings.2. Experimental methodsSamples of Al20Sn1Cu and Al20Sn1Cu0.5Mn (wt.%) were produced by Belt Casting (BC), Twin Roller (TR) and Single Roller MeltSpinning (SR) techniques. Master alloys, BC and TR samples wereprepared in air by Sintermetal S.A., meanwhile SR melt-spunsamples were prepared at laboratory scale in a reduced heliumatmosphere with a previous vacuum of 106 Torr using quartznozzles with a closed-loop controlled ejection temperature at~800 C and with two different wheel speed, 1.5 m/s and 7 m/s.Table 1 shows the samples code and the alloy nominal chemicalcompositions.
In the AleSneCu ternary system, for compositions where themiscibility gap is stabilized, one of the main challenges in themanufacturing process is to cross the large liquidus-solidus temperature range. This characteristic can lead to an inhomogeneousdistribution of b-Sn particles. The liquid immiscibility causes severesegregation mainly due to the large density difference between theAl-rich and Sn-rich liquids. It was reported that the monotecticreaction is very sensitive to the level of gravity and the undercooling condition prior to crystallization, [23,24]. Even undermicrogravity conditions, a coarse phase separation occurs due tothe Marangoni motion [25]. However, the use of rapid solidificationcan allow obtaining an homogeneous refined microstructure evenwhen the solidification pathway involve a stable or metastablemiscibility gap [10,19,22,23,26e28].The traditional plain bearing manufacturing process uses beltcasting of thick Al20Sn1Cu strips followed by several rolling passesto reduce the thickness and join the “antifriction” material to an Alinterlayer and this to the steel of the bearing back. In this work, theAl20Sn1Cu alloy was produced by rapid solidification which allowsa solidification pathway throughout the metastable miscibility gap.Also, the effect of the Mn addition on the microstructure andproperties was studied. The melt-spinning technique was used toobtain thin ribbons with a refined microstructure and improvedmechanical and surface properties. It is expected to reduce rollingpasses needed to manufacture plain bearings and to obtain a material with higher strength and wear resistance that improve theperformance of the Al20Sn1Cu alloy currently used in plainbearings.2. Experimental methodsSamples of Al20Sn1Cu and Al20Sn1Cu0.5Mn (wt.%) were produced by Belt Casting (BC), Twin Roller (TR) and Single Roller MeltSpinning (SR) techniques. Master alloys, BC and TR samples wereprepared in air by Sintermetal S.A., meanwhile SR melt-spunsamples were prepared at laboratory scale in a reduced heliumatmosphere with a previous vacuum of 106 Torr using quartznozzles with a closed-loop controlled ejection temperature at~800 C and with two different wheel speed, 1.5 m/s and 7 m/s.Table 1 shows the samples code and the alloy nominal chemicalcompositions.<br>
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