| The Fe83.3Si4B8P4Cu0.7(added Nb), Fe85Si2B8P4Cu1(added Nb), Fe84.3Si4B8P3Cu0.7(P replaced by B), Fe85Si2B8P4Cu1(added Hf) and Fe88Si22:Fe83B17:Fe83P17serie alloys’ ribbons were formed by melt spinning technology with the industry raw material such as iron, sillion, copper, niobium, hafnium, FeP compound, FeB compound and so on. The glass forming ability (GFA), the precipitated phases and magnetic properties after heat treatment were researched by X-ray diffraction (XRD), differential sacnning calorimeter (DSC) and vibrating specimen magnetometer (VSM). The main results were as follows:1) GFA of Fe83.3Si4B8P4Cuo.7and Fe85Si2B8P4Cu1series alloys was reduced after addition Nb. A nano structural a-Fe phase with a perferred orientation in (200) lattice plane was observed in the samples, and then the amorphou/crystalline structure was formed. The first and second initial crystallization temperatures(Tx1and Tx2) were improved.2) The saturation magnetic density (Bs) could reach to the maximum as the samples were annealed near Tx1. After annealed at400℃and450℃for10min, Fe83Si4B8P4Cuo.5Nbo.5and Fe85Si2B8P4Cu1alloys showed their maximum Bs at2.14T and2.16T, respectively.3) Fe84.3Si4B8P3Cuo.7alloy would precipitate Fe(B,P) compound as P was replaced by B, and Tx1nearly kept the same, while its Bs and Tx2would decrease, which meant the thermostability decreased.4) After annealed, Fe(B,P) compound or Fe2B compound would precipitate in Fe84.3Si2B10P3Cu0.7, Fe84.3Si2B11P2Cu0.7, Fe84.3Si2B12P1Cu0.7and Fe84.3Si2B13Cu0.7alloys. Fe84.3Si4B8P3Cu0.7and Fe84.3Si2B11P2Cu0.7alloys annealed at400℃and450℃for10min showed the maximum Bs2.14T and1.94T, respecrtively.5) GFA and thermostability were improved by adding Hf in Fe85Si2B8P4Cu1alloy. Fe85Si2B8P4Cuo.5Hfo.5and (Fe85Si2B8P4Cu1)0.99Hf0.01alloys could form a full amorphous structure.6) After annealed near Tx1, Fe85Si2B8P4Cu0.5Hf0.5and (Fe85Si2B8P4Cu1)0.99Hf0.01alloys showed the maximum Bs. The two samples after heat treatment at450℃for lOmin showed the maximum Bs2.00T and1.90T, respectively.7) Fe84.7Si4B5.7P5.6, Fe84.3Si3B43P8.4, Fe84.3Si3B8.5P4.2and Feg5.5Si6B4.3P4.2alloy ribbons showed an a-Fe (200) perferred orientation except Fe85.5Si6B4.3P42alloy, which appeared a partial of a-Fe (100) plane diffraction.8) Bs value of Fe84.3Si3B8.5P4.2and Fe85.5Si6B4.3P4.2alloys was nearly stable when the Bs value of Fe84.7Si4B5.7P5.6and Fe84.3Si3B4.3P8.4had been improved after heat treatment, which improved from0.58T to1.64T and0.57T to1.66T when the samples were annealed at500℃and450℃, respectively. |
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