Abstract
The Fe-B-Al alloy containing 0 to 10.0 wt.-% Al was melted in a vacuum induction furnace. Effects of the aluminum addition on the microstructure and properties of Fe-B-Al alloys were studied by means of optical microscopy (OM), scanning electron microscopy (SEM), X-ray diffraction (XRD), energy dispersive spectroscopy (EDS), hardness testing and MMG-500 type pin-on-disk high temperature vacuum wear testing. The results showed that the as-casted microstructure of the aluminum-free Fe-B alloy consisted of α-Fe, Fe2(B,C), and Fe23(B,C)6 type borocarbides. However, the as-casted microstructure of the Fe-B-Al alloy consists of a Fe3Al type intermetallic compound when the aluminum content is more than 6.0 wt.-%. Compared with the aluminum-free Fe-B alloy, parts of the borocarbide networks are broken, and the fracture tendency became more obvious with the increase of the aluminum content. Boron is mainly distributed over the borocarbide. Aluminum is mainly distributed over the matrix and Fe3Al type intermetallic compound. Compared with the aluminum-free Fe-B alloy, the addition of a small amount of aluminum reduces slightly the hardness. The hardness gradually increased with the further increasing of the aluminum content. The hardness reached 48.1 HRC when aluminum content was 10.0 wt.-%. The high temperature wear resistance of Fe-B-Al alloy gradually increased with the increase of the aluminum content. When the aluminum content reached 10.0 wt.-%, the high temperature wear resistance of the alloy was the best.
Kurzfassung
Eine Fe-B-Al-Legierung mit 0 bis 10 wt.-% Al wurde in einem Vakuuminduktionsofen verschmolzen. Danach wurden die Auswirkungen der Aluminiumzugabe auf die Mikrostruktur und die Eigenschaften der Legierung mittels Lichtmikroskopie, Rasterelektronenmikroskopie, Röntgendiffraktometrie, EDS, Härtetests und einem Stift-Scheibe-Reibtest der Typs MMG-500 bei hohen Temperaturen und im Vakuum untersucht. Die Ergebnisse zeigen, dass die Mikrostruktur der Aluminium-freien Legierung im Gusszustand aus α-Fe sowie Borcarbiden des Typs Fe2(B,C) und Fe23(B,C)6 bestand. Dem gegenüber bestand die Mikrostruktur im Gusszustand der Fe-B-Al-Legierung aus einer intermetallischen Verbindung des Typs Fe3Al, wenn der Alumniumgehalt mehr als 6 wt.-% betrug. Im Vergleich mit der Aluminium-freien Fe-B-Legierung waren Teile des Borcarbid-Netzwerkes gebrochen und die Bruchtendenz war mit Zunahme des Aluminiumgehalts stärker ausgeprägt. Bor ist hauptsächlich über die Borcarbide verteilt. Aluminium ist hauptsächlich in der Matrix und den intermetallischen Verbindungen des Typs Fe3Al verteilt. Im Vergleich mit der Aluminium-freien Legierung reduziert eine Aluminium-Zugabe in kleinen Mengen geringfügig die Härte. Die Härte nimmt graduell zu mit einer weiteren Aluminium-Zugabe. Die Härte erreicht einen Wert von 48.1 HRC, wenn der Aluminium-Gehalt 10 wt.-% beträgt. Der Hochtemperatur-Verschleißwiderstand der Fe-B-Al-Legierung nimmt graduell mit steigendem Aluminiumgehalt zu. Bei einem Alumniumgehalt von 10 wt.-% war der Hochtemperatur-Verschleißwiderstand am besten.
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