The invention relates to an apparatus (1) for cooling an automobile component (20) by means of a gas, the apparatus comprising a cooling box (11) with a re-closeable opening (12) for receiving an automobile component (20) to be cooled, wherein at least one heat sink (13) is provided inside the cooling box (11) for cooling of the gas, and wherein the apparatus (10) includes at least one infra sound pulsator (2, 3) arranged to provide an infra sound into said cooling box (11) to improve heat exchange of the gas both with a cooling surface of the at least one heat sink (13), and with the automobile component (20). The invention also relates to a process for cooling an automobile component in such an apparatus.

The invention relates to an apparatus (1) for cooling an automobile component (20) by means of a gas, the apparatus comprising a cooling box (11) with a re-closeable opening (12) for receiving an automobile component (20) to be cooled, wherein at least one heat sink (13) is provided inside the cooling box (11) for cooling of the gas, and wherein the apparatus (10) includes at least one infra sound pulsator (2, 3) arranged to provide an infra sound into said cooling box (11) to improve heat exchange of the gas both with a cooling surface of the at least one heat sink (13), and with the automobile component (20). The invention also relates to a process for cooling an automobile component in such an apparatus.

A method of producing a CoFe alloy strip is provided. The method comprises hot rolling a CoFe alloy to form a hot rolled strip, followed by quenching the strip from a temperature above 700° C. to a temperature of 200° C. The CoFe alloy comprises an order/disorder temperature T.sub.o/d and a ferritic/austenitic transformation temperature T.sub.α/γ, wherein T.sub.α/γ>T.sub.o/d. The method further comprises cold rolling the hot rolled strip, after cold rolling, continuous annealing the strip at a maximum temperature T.sub.1, wherein 500° C.<T.sub.1<T.sub.o/d, followed by cooling at a cooling rate R.sub.1 of at least 1 K/s in the temperature range of T.sub.1 to 500° C., and after continuous annealing, magnetic annealing the strip, or parts manufactured from the strip, at a temperature between 730° C. and T.sub.α/γ.

The invention relates generally to structural steel components for automotive vehicles, and methods for manufacturing the structural components. The method includes heating a workpiece to at least 900° C. to form austenite in the steel material, hot forming the workpiece, and quenching the formed workpiece to transform the austenite to martensite. The method next includes tempering at least one portion of the quenched workpiece, wherein the tempering step includes simultaneously applying thermal energy and a magnetic field to the workpiece. During the tempering step, the martensite of the steel material transforms to a mixture of ferrite and cementite precipitates. The portions of the steel material subject to the thermomagnetic tempering are also typically free of pearlite and spheroid particles. The remainder of the workpiece is protected during the tempering step to maintain a hard zone including the martensite.

The invention relates generally to structural steel components for automotive vehicles, and methods for manufacturing the structural components. The method includes heating a workpiece to at least 900° C. to form austenite in the steel material, hot forming the workpiece, and quenching the formed workpiece to transform the austenite to martensite. The method next includes tempering at least one portion of the quenched workpiece, wherein the tempering step includes simultaneously applying thermal energy and a magnetic field to the workpiece. During the tempering step, the martensite of the steel material transforms to a mixture of ferrite and cementite precipitates. The portions of the steel material subject to the thermomagnetic tempering are also typically free of pearlite and spheroid particles. The remainder of the workpiece is protected during the tempering step to maintain a hard zone including the martensite.

Systems and methods of threading a metal substrate on a rolling mill include receiving a coil of the metal substrate. The method also includes uncoiling the metal substrate from the coil while the coil and guiding the metal substrate to a work stand of the rolling mill with a threading system.

Systems and methods of threading a metal substrate on a rolling mill include receiving a coil of the metal substrate. The method also includes uncoiling the metal substrate from the coil while the coil and guiding the metal substrate to a work stand of the rolling mill with a threading system.

The steel material for a soft magnetic part according to the present invention has a chemical composition consisting of, in mass %, C: 0.02 to 0.13%, Si: 0.005 to 0.50%, Mn: 0.10 to 0.70%, P: 0.035% or less, S: 0.050% or less, Al: 0.005 to 1.300%, V: 0.02 to 0.50%, and N: 0.003 to 0.030%, with the balance being Fe and impurities. The average grain diameter of ferrite grains in the steel material for a soft magnetic part ranges from 5 to 200 μm. Further, in the ferrite grains, the number Sv (number/mm.sup.2) of precipitates having a circle-equivalent diameter of 30 nm or more satisfies Formula (1):
Sv≤10V×7.0×10.sup.6  (1) where the V content (mass %) in the steel material for a soft magnetic part is substituted into V in Formula (1).

The steel material for a soft magnetic part according to the present invention has a chemical composition consisting of, in mass %, C: 0.02 to 0.13%, Si: 0.005 to 0.50%, Mn: 0.10 to 0.70%, P: 0.035% or less, S: 0.050% or less, Al: 0.005 to 1.300%, V: 0.02 to 0.50%, and N: 0.003 to 0.030%, with the balance being Fe and impurities. The average grain diameter of ferrite grains in the steel material for a soft magnetic part ranges from 5 to 200 μm. Further, in the ferrite grains, the number Sv (number/mm.sup.2) of precipitates having a circle-equivalent diameter of 30 nm or more satisfies Formula (1):
Sv≤10V×7.0×10.sup.6  (1) where the V content (mass %) in the steel material for a soft magnetic part is substituted into V in Formula (1).

Conventional Fe-based soft magnetic alloy ribbons each containing Co and Ni have a problem that magnetic anisotropy that is neatly arranged in one direction cannot be induced easily even by a magnetic field annealing treatment and, therefore, a wound magnetic cores, a problem that a residual magnetic flux density Br is high, a problem that the hysteresis of the B—H curve becomes large (coercivity Hc becomes large), a problem that the change in incremental permeability relative to superimposed magnetic field becomes large, and others. In order to solve the problems, provided is an Fe-based soft magnetic alloy ribbon including a Cu-concentrated region present directly below a surface of the ribbon, and a Co-concentrated region present directly below the Cu-concentrated region. Also provided is a magnetic core including the Fe-based soft magnetic alloy ribbon.