Metal treatment – Process of modifying or maintaining internal physical... – Magnetic materials
Reexamination Certificate
2000-11-07
2003-01-07
Sheehan, John (Department: 1742)
Metal treatment
Process of modifying or maintaining internal physical...
Magnetic materials
C148S111000
Reexamination Certificate
active
06503339
ABSTRACT:
The invention relates to a method for producing non-grain-oriented magnetic steel sheet made of thin-slab or slab casting with low specific total loss and high polarisation and favourable mechanical properties.
The term “non-grain-oriented magnetic sheet steel” is understood herein as being such according to DIN 10106 (fully finished) or 10165 (semi-finished). Moreover, more highly anisotropic types are included as long as they are not regarded as grain-oriented magnetic steel sheet (specific total loss anisotropy up to approx. 30%). This material is mainly used as core material in machines (motors, generators) with a rotating direction of magnetic flux.
For economic and ecological reasons there is a demand for a further reaching improvement of the magnetic properties (polarization J in T, specific total loss P in W/kg). The specific total losses are to be reduced and the polarisation in the respectively used induction range is to be increased. At the same time there are special requirements that are placed on the mechanical-technological properties from the viewpoint of working and processing. Cutting capability has particular relevance in this respect, e.g. during punching.
Non, low and medium silicated low-loss types with high polarisation are to be considered here. Such a strip is particularly suitable as core material for ballasts and high-efficiency motors, for railway engines, industrial drives for pumps and compressors, boosters and drives for household technology.
It is known that by additional processing steps such as hot strip annealing or two-stage cold-rolling with intermediate annealing an improvement of the magnetic properties is achieved.
In WO 96/00306 it is proposed for steels with the main alloying elements of silicon, manganese and aluminium to finish-roll the hot strip for magnetic steel sheet in the austenite range and to perform the coiling at temperatures above the complete conversion into ferrite. Moreover, a direct annealing of the coil from the rolling heat is provided. In this way a final product with favourable magnetic properties is obtained. However, increased costs must be taken into account due to the high energy expenditure during the heating prior to and during the hot rolling and due to the alloying additions.
EP 0 469 980 B1 demands increased coiling temperatures in combination with an additional hot strip annealing. Useful magnetic properties are already set at low alloy contents. An increased coiling temperature and the additional hot strip annealing require an increased energy expenditure and thus cause higher costs.
In EP 0 651 061 B2 the setting of a cubic texture which is twisted by 45° about the normal of the sheet is proposed. Particularly interesting magnetic properties are obtained with respect to polarisation. This requires a complex method, however. In addition to increased final rolling and coiling temperatures it is necessary to perform additional steps during cold rolling such as preheating and intermediate annealing and dressing once or several times.
EP 0 511 601 B1, which is aimed at higher silicon and aluminium contents (Si+2 Al≧2%), provides hot strip annealing at particularly high temperatures above 1000° C. Expensive alloying elements must consequently be used and very high temperatures with additional annealing of the hot strip must be applied.
The invention is now based on the objective of providing a magnetic steel sheet in a cost effective manner with the combination, suitable for many fields of application, of high polarisation, low specific total loss and favourable mechanical properties.
In order to achieve this object it is provided by the generic method in accordance with the invention to hot roll the casting directly from the casting heat or, after a renewed heating to a temperature of T≧900° C., and to perform two or more metal forming passes in the two-phase range austenite/ferrite in the course of finishing rolling in order to set a state of the hot strip which is favourable with respect to the properties of the magnetic steel sheet. In order to fulfil these prerequisites, the steel must be alloyed in such a way that an austenite share of not less than 10% is obtained during the hot rolling temperature. This is to be effected by a respective adjustment of the alloying additions of austenite and ferrite-forming elements at a basic composition of (Si+2 Al)≦3%. The steel melts thus used contain 0.001 to 0.1% C, 0.05 to 3.0% Si, up to 0.85% Al with Si+2 Al≦3.0%, 0.05 to 2.0% Mn, remainder of iron and the usually companion elements and alloying additions of P, Sn, N, Ni, Co, Ti, Nb, Zr, V, B, Sb up to a total of 1.5%.
During slab casting there is usually a renewed heating to at least 900° C. so that austenite is formed and the finishing rolling can be performed in accordance with the invention in the &ggr;/&agr; two phase region. In the production of thin slabs or strip, the material is usually also heated to at least 900° C. prior to finishing rolling by using the casting heat for the reasons as stated above.
Thin slab or strip casting offer the following additional advantages as compared with conventional slab casting: Due to the lower cooling time until the complete solidification, the dendrite arm distances are smaller and there are thus fewer enhancement, thus making the material more homogeneous. Due to the lower thickness of the slabs and the possibility of using the casting heat, the hot strip rolling is shortened and savings in cost are achieved. In the case of a respective design of the thin slab casting and rolling installation, a wider range of final rolling and coiling temperatures and lower hot strip thicknesses can be set. At lower hot strip thicknesses of ≦1.5 mm the hot rolling can occur at final rolling speeds of over 10 m per second in order to obtain a high productivity.
By providing a roller lubrication in at least one of the last three hot rolling passes of the finishing rolling, a more homogeneous structure can be obtained over the cross section due to a lower shear deformation. Since in addition the roll separating force is reduced, a higher thickness reduction to a lower end thickness is possible.
In a further claim the finishing rolling is completed by at least one metal forming pass with a dimensional change &egr;
h
=(h
i
−h
i+1
)/h
i
>10% in the ferrite region. If the hot rolling is completed by one or several metal forming passes in the ferrite region and the hot strip is coiled at temperatures below 650° C., then this leads to a solidified hot strip state and to a suppression or fine dispersion of the precipitations. This can reduce the subsequently necessary degree of cold rolling. The hot strip can principally be cold rolled in one or several stages with intermediate annealing to its end thickness. These measures set a finer structure, thus improving the cutting and punching capabilities of the cold strip.
A limitation of the Si content of the steel to 0.05 to 1.6% Si is appropriate in cases when otherwise no two-phase region is present anymore in case of respective shares of other components of the composition. Because the reheating temperature of the steel slabs lies in the austenite region it is ensured that the required metal forming passes are performed in the two-phase region.
If the steel slab is cooled directly from the casting heat to temperatures below 900° C. and is hot rolled after a reheating up to the austenite region, coarse precipitations are formed. In contrast to finer precipitations, such coarse precipitations can lead to improved magnetic properties of the magnetic steel sheet. The latter applies in particular when the reheating temperature is not more than 1150° C. At such a low chosen temperature, the previously formed coarse precipitations are prevented from dissolving again.
The thus produced hot strip with a thickness of up to 6 mm is coiled at coiling temperatures of either below 650° C. or in the range of 650° C. to Ar1, depending on its intended purpose. If the strips were coiled at high temperatures,
Espenhahn Manfred
Hammer Brigitte
Kawalla Rudolf
Peters Klaus
Pircher Hans
Proskauer Rose LLP
Sheehan John
Thyssen Krupp Stahl AG
LandOfFree
Method for producing non-grain oriented magnetic sheet steel does not yet have a rating. At this time, there are no reviews or comments for this patent.
If you have personal experience with Method for producing non-grain oriented magnetic sheet steel, we encourage you to share that experience with our LandOfFree.com community. Your opinion is very important and Method for producing non-grain oriented magnetic sheet steel will most certainly appreciate the feedback.
Profile ID: LFUS-PAI-O-3050173