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Method for producing grain-oriented magnetic steel strip or steel sheet for electrical purposes

A grain-oriented, magnetic steel plate technology, applied in the direction of magnetic materials, magnetic objects, circuits, etc., can solve the problem of not achieving magnetic properties

Inactive Publication Date: 2016-10-12
THYSSENKRUPP STEEL EURO AG +1
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  • Summary
  • Abstract
  • Description
  • Claims
  • Application Information

AI Technical Summary

Problems solved by technology

However, it must be accepted that the resulting, grain-oriented steel sheet products often do not achieve the expected magnetic properties of HGO materials.

Method used

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  • Method for producing grain-oriented magnetic steel strip or steel sheet for electrical purposes
  • Method for producing grain-oriented magnetic steel strip or steel sheet for electrical purposes
  • Method for producing grain-oriented magnetic steel strip or steel sheet for electrical purposes

Examples

Experimental program
Comparison scheme
Effect test

example 1

[0069] A slab was cast from a melt which, in addition to iron and unavoidable impurities, had (shown in % by weight) 3.05% Si, 0.045% C, 0.052% Mn, 0.010 % of P, 0.030% of S, 0.206% of Cu, 0.067% of Cr, 0.030% of Al, 0.001% of Ti, 0.003% of N, 0.011% of Sn, 0.016% of Ni, divided by the continuous casting slab into a thin steel ingot having a thickness of 63 mm and a width of 1100 mm. After free, uncontrolled cooling to about 900° C., a homogenization annealing is carried out in which the thin steel ingot is completely heated to 1050° C. The thin steel ingot was then hot-rolled in a hot-rolling train comprising seven successive hot-rolling stands one behind the other to form a hot-rolled strip having a hot-rolled strip thickness of 2.30 mm. The temperature of the rolled stock was in the range of 960-980° C. in the first rolling pass and 930-950° C. in the second rolling pass. The final temperature of hot rolling is 840°C.

[0070] The hot-rolled steel strip thus obtained was...

example 2

[0074] Melt A according to the invention and melt B not according to the invention were melted, Table 1 gives the composition of these two melts.

[0075] These melts were cast into thin steel ingots having a thin steel ingot thickness of 63 mm in a continuous casting method. The superheat temperature of the melt in the tundish is 25-45K. The casting rate during continuous casting was in the range of 3.5-4.2 m / min. The slab is then cooled to about 900°C before entering the roller hearth furnace.

[0076] The thin ingots divided from the continuous cast slabs are reheated for 20 minutes in the leveling furnace to a temperature between 1030 and 1070° C. and then transported to the hot rolling station. Table 2 gives the reheating temperature SRT for specific settings, and the ratios of %Mn / %S and %Cu / %S in the alloys of melts A and B.

[0077] On the way from the leveling furnace to the first hot deformation pass, the temperature of the thin steel slab drops to a value of appr...

example 3

[0083] Like melts A and B, melts C formed according to the invention and melts not formed according to the invention having the compositions given in Table 4 were cast in the same manner as described above and processed into hot strip. This is followed by annealing and rapid cooling of the hot strip in the same manner as described above for the production of hot strip from steels A and B.

[0084] The following process is carried out by cold rolling to the nominal thickness of the finished steel strip of 0.23mm in one step and then performing an annealing treatment capable of recrystallization and decarburization, wherein during the decarburization process by adding 15% NH 3 Used as an annealing gas while performing nitriding treatment. Then an annealing separator consisting essentially of MgO is applied as a bond protector and annealed in a high-temperature bell annealing furnace for secondary recrystallization. An insulating layer is then applied and a stress-relieving stra...

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Abstract

The present invention relates to a method for producing a grain-oriented magnetic steel strip or steel sheet, in which a magnetic steel sheet having (in % by weight) Si: 2-6.5%, C: 0.02-0.15%, S: 0.01‑0.1%, cu: 0.1‑0.5%, the ratio of Cu content to S content is %Cu / %S>4, Mn: not higher than 0.1%, and the ratio of Mn content to S content is %Mn / % S<2.5, and optional N, Al, Ni, Cr, Mo, Sn, V, Nb content of the thin steel ingot steel ingot temperature homogenization to 1000‑1200 ° C, in this method at the beginning of hot rolling When the temperature is ≤1030°C and the hot rolling final temperature is ≥710°C, the thin steel ingot is hot-rolled into a hot-rolled steel strip with a thickness of 0.5-4.0mm and the thickness is reduced in the first heat deformation pass and the second heat deformation pass, respectively ≥ 40% of the thickness of the hot-rolled steel strip, which is cooled and wound into coils, in which process the hot-rolled steel strip is cold-rolled to a cold-rolled steel strip with a final thickness of 0.15-0.50 mm , in which an annealing separator is applied to the annealed cold-rolled steel strip and in which the cold-rolled steel strip with the annealing separator is finally annealed to cast a Goss texture.

Description

technical field [0001] The invention relates to a method for producing grain-oriented magnetic steel strip or steel sheet for electrical applications. Such a magnetic steel strip or steel sheet has a particularly clearly defined {110}<001> texture with a slight direction of magnetization parallel to the rolling direction. Named after the discoverer of this texture, this texture is called a "Gaussian texture". Background technique [0002] The Gaussian texture is formed by selective, abnormal grain growth, which is also called secondary recrystallization. For this purpose, the natural tendency of the metal base layer towards grain growth is suppressed by the presence of a grain growth inhibitor, which is also referred to simply as "inhibitor" or "inhibitor phase". [0003] The inhibitor phase consists of very fine and as uniformly distributed particles of one or more impurity phases as possible. The relevant particles already have a natural interfacial energy at thei...

Claims

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Application Information

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Patent Type & Authority Patents(China)
IPC IPC(8): C21D8/02C22C38/02C22C38/04C22C38/16C21D8/12
CPCC21D8/0284C21D8/1255C21D8/1283C22C38/001C22C38/008C22C38/02C22C38/04C22C38/06C22C38/16C22C38/34C22C38/42C21D8/02C21D8/12C21D8/0226C21D8/0247H01F1/14775
Inventor 安德烈亚斯·波切尔卢德格尔·拉恩格哈德·因顿埃伯哈德·索卡
Owner THYSSENKRUPP STEEL EURO AG
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