DE1181255B - Process for the production of sheets or plates from an iron-silicon alloy with a crystallographically oriented structure - Google Patents
Process for the production of sheets or plates from an iron-silicon alloy with a crystallographically oriented structureInfo
- Publication number
- DE1181255B DE1181255B DEG30439A DEG0030439A DE1181255B DE 1181255 B DE1181255 B DE 1181255B DE G30439 A DEG30439 A DE G30439A DE G0030439 A DEG0030439 A DE G0030439A DE 1181255 B DE1181255 B DE 1181255B
- Authority
- DE
- Germany
- Prior art keywords
- iron
- cooled
- per minute
- texture
- sheets
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000676 Si alloy Inorganic materials 0.000 title claims description 6
- XWHPIFXRKKHEKR-UHFFFAOYSA-N iron silicon Chemical compound [Si].[Fe] XWHPIFXRKKHEKR-UHFFFAOYSA-N 0.000 title claims description 6
- 238000000034 method Methods 0.000 title claims description 6
- 238000004519 manufacturing process Methods 0.000 title claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 10
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- 239000011593 sulfur Substances 0.000 claims description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 239000011572 manganese Substances 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 claims description 2
- 239000000956 alloy Substances 0.000 claims description 2
- 239000010936 titanium Substances 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 238000005098 hot rolling Methods 0.000 claims 1
- 239000000463 material Substances 0.000 description 12
- 238000001816 cooling Methods 0.000 description 10
- 238000000137 annealing Methods 0.000 description 9
- 229910002804 graphite Inorganic materials 0.000 description 7
- 239000010439 graphite Substances 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- 239000004576 sand Substances 0.000 description 6
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 239000007795 chemical reaction product Substances 0.000 description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000008021 deposition Effects 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/84—Controlled slow cooling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Electromagnetism (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Dispersion Chemistry (AREA)
- Power Engineering (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Continuous Casting (AREA)
- Soft Magnetic Materials (AREA)
Description
BUNDESREPUBLIK DEUTSCHLANDFEDERAL REPUBLIC OF GERMANY
DEUTSCHESGERMAN
PATENTAMTPATENT OFFICE
Internat. Kl.: C21dBoarding school Class: C21d
Nummer:
Aktenzeichen:
Anmeldetag:
Auslegetag:Number:
File number:
Registration date:
Display day:
Deutsche Kl.: 18 c-1/78 German class: 18 c -1/78
G 30439 VI a/18 c
6. September 1960
12. November 1964G 30439 VI a / 18 c
September 6, 1960
November 12, 1964
Das Patent 1159 978 betrifft ein Verfahren zur Herstellung von Blechen oder Platten aus einer Eisen-Silicium-Legierung, in der die meisten Kristallite die (110) [001]-Orientierung aufweisen, bei dem eine Legierung aus 2,5 bis 4% Silicium, höchstens 0,035% Kohlenstoff, 0,015 bis 0,05% Schwefel, höchstens 0,15% Mangan, weniger als 0,1% Titan, Rest im wesentlichen Eisen zu einem brammenartigen Block mit einer Höchstdicke von 50 mm gegossen wird, der in der Blockform auf Zimmertemperatur abgekühlt und zum Wannwalzen wieder auf etwa 1000° C erhitzt wird. Im warmen Zustand wird der Block dann auf Bleche und Bänder von weniger als 4 mm Dicke ausgewalzt, die anschließend im kalten Zustand um mehr als 40% ihrer Dicke heruntergewalzt und dann rekristallisierend geglüht werden.The patent 1159 978 relates to a method for the production of sheets or plates from a Iron-silicon alloy, in which most of the crystallites have the (110) [001] orientation, in which an alloy of 2.5 to 4% silicon, not more than 0.035% carbon, 0.015 to 0.05% sulfur, at most 0.15% manganese, less than 0.1% titanium, the remainder being essentially iron to form a slab-like Block with a maximum thickness of 50 mm is poured in the block mold at room temperature cooled and heated again to about 1000 ° C for rolling. When warm the block is then rolled out onto sheets and strips less than 4 mm thick, which subsequently rolled down by more than 40% of its thickness when cold and then recrystallized to be annealed.
Dieses Verfahren ermöglicht die Herstellung von Gußblöcken, die zur Lagerung abgekühlt und jederzeit wieder erwärmt werden können, ohne daß dadurch das kristallographische Gefüge des ausgewalzten Endproduktes darunter leidet.This process enables the manufacture of ingots that are cooled for storage and at any time can be reheated without affecting the crystallographic structure of the rolled End product suffers.
In der Zusatzpatentanmeldung G 25589 VI/18 c (deutsche Auslegeschrift 1176164) ist offenbart, daß eine Beziehung zwischen der Geschwindigkeit des sich unmittelbar an das Erstarren des Gußblockes anschließenden Abkühlens des Gußblockes von etwa 1400 auf etwa 800° C und dem Grad der kristallographischen Orientierung besteht, die sich in dem gewalzten Band oder Blech ergibt, wenn man den Gußblock gemäß dem Hauptpatent 1159 978 auf Zimmertemperatur abkühlen läßt und ihn dann wieder erwärmt und zu dem Band oder Blech auswalzt. In the additional patent application G 25589 VI / 18 c (German Auslegeschrift 1176164) it is disclosed that there is a relationship between the speed of the ingot directly involved in the solidification of the ingot subsequent cooling of the ingot from about 1400 to about 800 ° C and the degree of crystallographic orientation that results in the rolled strip or sheet when one the ingot according to the main patent 1159 978 allowed to cool to room temperature and then it reheated and rolled out to form the strip or sheet.
Wenn man nach der durch diese Zusatzpatentanmeldung gegebenen Anweisung einen erstarrten Gußblock zwischen ungefähr 1400 und ungefähr 800° C mit einer Geschwindigkeit von mindestens 130° C pro Minute abkühlt, läßt sich der Block entsprechend dem Patent 1159 978 auf Zimmertemperatur abkühlen und anschließend zu einer scharfen (110) [001]-Textur verarbeiten, indem man ihn, wie es nach dem Patent 1159 978 erwähntermaßen geschieht, wieder auf etwa 1000° C erwärmt, zu einem Band auswalzt und dieses mit entsprechender Wärmebehandlung zum Endprodukt kaltwalzt.If you froze after the instructions given by this additional patent application Ingot between about 1400 and about 800 ° C at a rate of at least 130 ° C per minute cools, the block can be according to patent 1159 978 to room temperature cool and then process to a sharp (110) [001] texture by manipulating it like it happens as mentioned in the patent 1159 978, heated again to about 1000 ° C, rolled out into a strip and this with the appropriate Heat treatment cold rolled to the end product.
Es hat sich nun herausgestellt, daß in einem aus der angegebenen Eisen-Silicium-Legierung bestehenden
und eine bestimmte Menge von Mangan und Schwefel enthaltenden Gußblock eine feine Verteilung
von Mangansulfid erreicht werden kann, wenn man den Gußblock von Temperaturen, bei
Verfahren zum Herstellen von Blechen oder
Platten aus einer Eisen-Silicium-Legierung mit
kristallographisch orientiertem Gefüge
nach Patent 1159 978It has now been found that a fine distribution of manganese sulfide can be achieved in an ingot consisting of the iron-silicon alloy specified and containing a certain amount of manganese and sulfur if the ingot is subjected to temperatures in processes for producing sheet metal or
Iron-silicon alloy plates with
crystallographically oriented structure
according to patent 1159 978
Zusatz zum Patent: 1159 978Addendum to the patent: 1159 978
Anmelder:Applicant:
General Electric Company, Schenectady, N. Y.General Electric Company, Schenectady, N.Y.
(V. St. A.)(V. St. A.)
Vertreter:Representative:
Dipl.-Ing. M. Licht,Dipl.-Ing. M. light,
München 2, Sendlinger Str. 55Munich 2, Sendlinger Str. 55
und Dr. R. Schmidt, Oppenau (Renchtal),and Dr. R. Schmidt, Oppenau (Renchtal),
PatentanwältePatent attorneys
Als Erfinder benannt:Named as inventor:
Howard Charles Fiedler, Schenectady, N. Y.Howard Charles Fiedler, Schenectady, N.Y.
(V. St. A.)(V. St. A.)
Beanspruchte Priorität:Claimed priority:
V. St. v. Amerika vom 16. September 1959V. St. v. America September 16, 1959
(840290)(840290)
denen das Mangan und der Schwefel in Lösung sind, beispielsweise von 1300 bis 1400° C oder höher, auf ungefähr 1000° C mit einer Geschwindigkeit zwischen 50 bis 130° C pro Minute abkühlt. Das feinverteilte Mangansulfid hemmt das Kornwachstum während der Schlußglühung und ermöglicht dadurch, daß ein entsprechender Grad von Kristallorientierung erreicht wird. Das Metall kann entweder unmittelbar vom flüssigen Zustand, in dem es sich nach dem Eingießen in die Gußform befindet, aus oder von einer Temperatur abgekühlt werden, die oberhalb der Temperatur liegt, bei der sich Mangan und Schwefel normalerweise in Lösung befinden. Die zuletzt genannte Temperatur liegt normalerweise im Bereich von 1300 bis 1400° C. Wird die Eisen-Silicium-Legierung von diesem oder von Temperaturen oberhalb dieser Spanne mit genügender Geschwindigkeit abgekühlt, so wird das Mangansulfidwhere the manganese and sulfur are in solution, for example from 1300 to 1400 ° C or higher cools about 1000 ° C at a rate between 50 to 130 ° C per minute. The finely divided Manganese sulfide inhibits grain growth during the final annealing and thus enables that a corresponding degree of crystal orientation is achieved. The metal can either be immediate from the liquid state in which it is after pouring into the mold, or be cooled from a temperature which is above the temperature at which manganese and Sulfur is usually in solution. The latter temperature is usually in Range from 1300 to 1400 ° C. Is the iron-silicon alloy from this or from temperatures above this range with sufficient speed cooled, so the manganese sulfide
409 727/294409 727/294
im Gußblock so verteilt, daß keine weitere Wärmebehandlung mehr durchgeführt zu werden braucht. Der Gußblock kann dann anschließend ausgewalzt werden, um die erwünschte Textur zu erzeugen.Distributed in the cast block in such a way that no further heat treatment needs to be carried out. The ingot can then subsequently be rolled out to produce the desired texture.
In der Zeichnung zeigtIn the drawing shows
F i g. 1 eine graphische Darstellung, in welcher die Abhängigkeit der (110) [001]-Orientierung (in °/o) von der Temperatur (in 0C) der Schlußglühung an zwei Körpern gezeigt ist, von denen der eine aus einem in einer Graphitform gegossenen Block und der andere aus einem in einer Sandform gegossenen Block hergestellt worden ist,F i g. 1 shows a graphical representation in which the dependence of the (110) [001] orientation (in ° / o) on the temperature (in 0 C) of the final annealing is shown on two bodies, one of which is cast from a graphite mold Block and the other is made from a block cast in a sand mold,
F i g. 2 eine graphische Darstellung ähnlich wie Fig. 1, wobei der eine Körper mit einer Geschwindigkeit von 50° C pro Minute und der andere mit einer Geschwindigkeit von 130° C pro Minute abgekühlt worden ist.F i g. FIG. 2 is a graph similar to FIG. 1, one body having a velocity of 50 ° C per minute and the other is cooled at a rate of 130 ° C per minute has been.
Zur Erörterung des Einflusses der Temperatur auf den (110) [001]-Orientierungsgrad wurden von derselben Metallschmelze zwei 22,5 kg schwere Blöcke gegossen. Der eine Metallblock wurde in eine Graphitform und der andere in eine Sandform gegossen. Die Zusammensetzung des Metalls war 3,27% Silicium, 0,026% Schwefel, 0,057% Mangan, 0,004% Kohlenstoff, 0,009% Sauerstoff, 0,002% Stickstoff und der Rest im wesentlichen Eisen.To discuss the influence of temperature on the (110) [001] degree of orientation, the same Molten metal poured two blocks weighing 22.5 kg. One block of metal was turned into one Graphite mold and the other poured into a sand mold. The composition of the metal was 3.27% silicon, 0.026% sulfur, 0.057% manganese, 0.004% carbon, 0.009% oxygen, 0.002% Nitrogen and the remainder essentially iron.
Die Formen hatten einen Querschnitt von 67 · 127 mm. Von den Blöcken wurden Scheiben mit einer Dicke von 25 mm abgeschnitten, auf 1000° C erwärmt und ohne Wiedererwärmen zu einem Band von 2 mm Stärke ausgewalzt. Das Band wurde gebeizt, in einem Sandstrahlgebläse behandelt und 5 Minuten lang bei 900° C wärmebehandelt. Anschließend wurde es auf 0,6 mm Dicke kaltgewalzt, 1 bis 5 Minuten lang bei 860° C wärmebehandelt und auf 0,3 mm kaltgewalzt.The molds were 67 x 127 mm in cross section. The blocks became slices cut to a thickness of 25 mm, heated to 1000 ° C and closed without reheating rolled into a strip of 2 mm thickness. The tape was pickled, sandblasted and heat-treated at 900 ° C for 5 minutes. It was then cold rolled to a thickness of 0.6 mm, Heat treated at 860 ° C for 1 to 5 minutes and cold rolled to 0.3 mm.
Je höher die Abkühlgeschwindigkeit ist, mit der ein Gußblock von der Lösungstemperatur des Mangansulfids oder von einer Temperatur oberhalb dieser Lösungstemperatur abgekühlt wird, desto kleiner sind die Mangansulfidteilchen und desto wirksamer verhindern sie normales Kornwachstum im Endprodukt. Beispielsweise hat ein Material, das in einer Sandform gegossen, auf die Enddicke verarbeitet und 10 Minuten lang bei 950° C wärmebehandelt worden ist, eine Korngröße von ungefähr 0,038 mm, während ein in einer Graphitform gegossenes Material eine Korngröße von ungefähr 0,030 mm hat. Zur Feststellung der Abkühlgeschwindigkeiten wurden von dem in einer Graphitform gegossenen Block und von dem in einer Sandform gegossenen Block 25 mm dicke Probescheiben hergestellt, die über die Lösungstemperatur von Mangan und Schwefel (1300 bis 1400° C) erwärmt und dann mit Geschwindigkeiten von 50° C pro Minute bis 130° C pro Minute abgekühlt wurden. Das Endprodukt der mit 130° C pro Minute abgekühlten Probe hatte eine durchschnittliche Korngröße von ungefähr 0,020 mm, während das von einer mit 50° C pro Minute abgekühlten Probe eine durchschnittliche Korngröße von ungefähr 0,028 mm hatte. Das Endprodukt aus dem mit 500C pro Minute abgekühlten Material hat also im wesentlichen dieselbe Korngröße wie das aus dem in Graphitformen hergestellte Produkt. Daraus ergibt sich, daß das in einer Graphitform gegossene Material eine Abkühlgeschwindigkeit in der Größenordnung von 50° C pro Minute zeigt, während das in Sand gegossene Material eine beträchtlich niedrigere Kühlgeschwindigkeit hat.The faster the cooling rate at which an ingot is cooled from the solution temperature of the manganese sulfide or from a temperature above this solution temperature, the smaller the manganese sulfide particles and the more effectively they prevent normal grain growth in the end product. For example, a material cast in a sand mold, processed to final thickness and heat treated at 950 ° C for 10 minutes has a grain size of approximately 0.038 mm, while a material cast in a graphite mold has a grain size of approximately 0.030 mm. To determine the cooling rates, 25 mm thick test disks were produced from the block cast in a graphite mold and from the block cast in a sand mold, which were heated above the solution temperature of manganese and sulfur (1300 to 1400 ° C) and then at speeds of 50 ° C per minute to 130 ° C per minute were cooled. The final product of the sample cooled at 130 ° C per minute had an average grain size of approximately 0.020 mm, while that of a sample cooled at 50 ° C per minute had an average grain size of approximately 0.028 mm. The end product made from the material cooled at 50 ° C. per minute thus has essentially the same grain size as the product made from the graphite molds. It follows that the material cast in a graphite mold exhibits a cooling rate of the order of 50 ° C. per minute, while the material cast in sand has a considerably slower cooling rate.
Der Einfluß der Kühlgeschwindigkeiten ist aus den Fig. 1 und 2 klar ersichtlich, in denen der Texturgrad eingetragen ist, der bei der dargestellten Temperatur nach 2 Stunden erhalten wurde. Die Kurve 10 bezieht sich auf das in einer Graphitform gegossene Material. In diesem Falle werden Texturgrade von über 80% erreicht, wenn das Material im Bereich von ungefähr 925 bis 975° C wärmebehandelt wird. Andererseits zeigt das Material, das aus einem in einer Sandform gegossenen Block hergestellt und daher mit einer Geschwindigkeit von weniger als 50° C pro Minute abgekühlt wurde, nach Kurve 11 nur einen Texturgrad von höchstens 40%, wenn es bei 925 bis 975° C wärmebehandelt wird.The influence of the cooling speeds can be clearly seen from FIGS. 1 and 2, in which the The degree of texture is entered, which was obtained at the temperature shown after 2 hours. the Curve 10 relates to the material cast in a graphite mold. In this case, texture grades of over 80% when the material is heat treated in the range of approximately 925 to 975 ° C will. On the other hand, it shows the material made from a block cast in a sand mold and therefore cooled at a rate of less than 50 ° C per minute after Curve 11 only has a texture level of at most 40% when it is heat treated at 925 to 975 ° C.
In Fig. 2 bezieht sich die Kurve 15 auf ein Blech, das aus einem mit 130° C pro Minute abgekühlten Material hergestellt ist, während sich die Kurve 16 auf ein Blech bezieht, das aus einem mit einer Geschwindigkeit von ungefähr 50° C pro Minute abgekühlten Material hergestellt ist. Der Texturgrad des mit 50° C pro Minute abgekühlten Materials entspricht im wesentlichen dem in Kurve 10 von F i g. 1 angegebenen Texturgrad. Der Höchstwert des erreichten Texturgrades liegt in der Größenordnung von 80%, und der Texturgrad fällt schnell ab, wenn höhere Temperaturen bei der Schlußglühung angewendet werden. Es ist wichtig, daß der Orientierungsgrad mit ansteigenden Glühtemperaturen absinkt, da es dadurch möglich wird, beim Glühen zum Erzeugen der Textur verhältnismäßig niedrige Heizgeschwindigkeiten anzuwenden. In der Tabelle ist der entwickelte Texturgrad in Abhängigkeit der Heizgeschwindigkeit beim Schlußglühen gezeigt.In FIG. 2, curve 15 relates to a sheet which has been cooled from a sheet at 130.degree. C. per minute Material is made, while the curve 16 relates to a sheet metal made of a with material cooled at a rate of about 50 ° C per minute. Of the The degree of texture of the material cooled at 50 ° C. per minute essentially corresponds to that in the curve 10 of FIG. 1 specified degree of texture. The maximum value of the degree of texture achieved is in On the order of 80%, and the degree of texture drops quickly when higher temperatures occur at the Final annealing can be applied. It is important that the degree of orientation increases with increasing annealing temperatures drops, as this makes it possible to produce the texture in proportion to the annealing use low heating speeds. In the table, the developed degree of texture is in Dependency of the heating rate during final annealing shown.
Abkühlgeschwindigkeit
des Blockes
(°C/min)Cooling rate
of the block
(° C / min)
50
13050
130
Texturgrad in Prozent HeizgeschwindigkeitDegree of texture in percent heating speed
25° C/Stundell00°C/Stunde 200°C/Stunde25 ° C / hour or 00 ° C / hour 200 ° C / hour
82 8882 88
70 8570 85
71 8471 84
Bei 9500C dauert die Entwicklung der Textur wesentlich langer als bei einer etwas höheren Temperatur, beispielsweise bei einer Temperatur im Bereich von 1050 bis 1100° C. Mit einer Geschwindigkeit von 130° C pro Minute abgekühltes Material entwickelt normalerweise einen Texturgrad von annähernd 90% und einen Texturgrad von über 80%, wenn die Glühtemperatur auf 1100° C erhöht wird. Wenn also die Abkühlgeschwindigkeit zur Abscheidung einer feinen, das Kornwachstum anhaltenden zweiten Phase, d. h. zur Abscheidung von Mangansulfid oder eines anderen derartigen Einschlusses, auf einem hohen Wert gehalten wird, kann eine hochgradige Orientierung durch Anwendung von höheren Temperaturen leicht und schnell entwickelt werden. Es hat sich herausgestellt, daß bei Temperaturen um 950° C zur Entwicklung einer angemessenen Textur Glühzeiten in der Größenordnung von einer halben Stunde erforderlich sind, während bei Glühtemperaturen in der Größenordnung von 1050 bis 1100° C oder möglicherweise etwas höher die Texturentwicklung schon ungefähr nach 5 Minuten abgeschlossen ist. Mit einer Abkühl-At 950 0 C, the development of the texture takes much longer than at a slightly higher temperature, for example at a temperature in the range of 1050 to 1100 ° C. at a rate of 130 ° C per minute cooled material usually develops a texture level of approximately 90% and a texture level of over 80% when the annealing temperature is increased to 1100 ° C. Thus, if the cooling rate for the deposition of a fine, grain growth-sustaining second phase, ie, for the deposition of manganese sulfide or other such inclusion, is kept high, a high degree of orientation can be easily and quickly developed by using higher temperatures. It has been found that at temperatures around 950 ° C, annealing times of the order of half an hour are required to develop an adequate texture, while at annealing temperatures of the order of 1050 to 1100 ° C or possibly a little higher, the texture development already after about 5 Minutes is complete. With a cooling
geschwindigkeit von 50° C pro Minute kann man also gute (110) [001]-Texturen erreichen, jedoch können mit noch höheren, bis zu 130° C pro Minute gesteigerten Abkühlgeschwindigkeiten noch weitere Vorteile erzielt werden.speed of 50 ° C per minute one can therefore achieve good (110) [001] textures, however can do even more with even higher cooling speeds of up to 130 ° C per minute Benefits can be achieved.
Claims (1)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US832438XA | 1956-12-31 | 1956-12-31 | |
US845167XA | 1957-10-29 | 1957-10-29 | |
US840290A US3069299A (en) | 1956-12-31 | 1959-09-16 | Process for producing magnetic material |
Publications (1)
Publication Number | Publication Date |
---|---|
DE1181255B true DE1181255B (en) | 1964-11-12 |
Family
ID=27374494
Family Applications (3)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
DEG23613A Pending DE1159978B (en) | 1956-12-31 | 1957-12-24 | Process for the production of sheets or plates from an iron-silicon alloy with a crystallographically oriented structure |
DEG25589A Pending DE1176164B (en) | 1956-12-31 | 1958-10-28 | Process for the production of sheets and plates from an iron-silicon alloy with (110) [001] orientation of the crystallites |
DEG30439A Pending DE1181255B (en) | 1956-12-31 | 1960-09-06 | Process for the production of sheets or plates from an iron-silicon alloy with a crystallographically oriented structure |
Family Applications Before (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
DEG23613A Pending DE1159978B (en) | 1956-12-31 | 1957-12-24 | Process for the production of sheets or plates from an iron-silicon alloy with a crystallographically oriented structure |
DEG25589A Pending DE1176164B (en) | 1956-12-31 | 1958-10-28 | Process for the production of sheets and plates from an iron-silicon alloy with (110) [001] orientation of the crystallites |
Country Status (5)
Country | Link |
---|---|
US (1) | US3069299A (en) |
BE (2) | BE571059A (en) |
DE (3) | DE1159978B (en) |
FR (2) | FR1197045A (en) |
GB (3) | GB832438A (en) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB933873A (en) * | 1959-07-09 | 1963-08-14 | United States Steel Corp | Method of producing grain oriented electrical steel |
US3147158A (en) * | 1961-11-22 | 1964-09-01 | Gen Electric | Process for producing cube-on-edge oriented silicon iron |
US3438820A (en) * | 1965-04-02 | 1969-04-15 | Dominion Foundries & Steel | Silicon steel process |
US3636579A (en) * | 1968-04-24 | 1972-01-25 | Nippon Steel Corp | Process for heat-treating electromagnetic steel sheets having a high magnetic induction |
FR2007129A1 (en) * | 1968-04-27 | 1970-01-02 | Yawata Iron & Steel Co | |
JPS5018445B1 (en) * | 1970-03-30 | 1975-06-28 | ||
JPS5032059B2 (en) * | 1971-12-24 | 1975-10-17 | ||
JPS5339852B2 (en) * | 1973-05-09 | 1978-10-24 | ||
JPS5168422A (en) * | 1974-12-11 | 1976-06-14 | Nippon Steel Corp | Kyojinkono seizoho |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2534141A (en) * | 1948-01-14 | 1950-12-12 | Gen Electric | Heat-treatment of cold rolled silicon steel strip |
US2618843A (en) * | 1949-11-21 | 1952-11-25 | United States Steel Corp | Preventing cracking of silicon steel during hot rolling |
BE563546A (en) * | 1956-12-31 |
-
0
- BE BE563542D patent/BE563542A/xx unknown
- BE BE571059D patent/BE571059A/xx unknown
-
1957
- 1957-12-23 FR FR1197045D patent/FR1197045A/en not_active Expired
- 1957-12-23 GB GB39883/57A patent/GB832438A/en not_active Expired
- 1957-12-24 DE DEG23613A patent/DE1159978B/en active Pending
-
1958
- 1958-08-26 GB GB27326/58A patent/GB845167A/en not_active Expired
- 1958-10-23 FR FR1213741D patent/FR1213741A/en not_active Expired
- 1958-10-28 DE DEG25589A patent/DE1176164B/en active Pending
-
1959
- 1959-09-16 US US840290A patent/US3069299A/en not_active Expired - Lifetime
-
1960
- 1960-08-09 GB GB27546/60A patent/GB919206A/en not_active Expired
- 1960-09-06 DE DEG30439A patent/DE1181255B/en active Pending
Also Published As
Publication number | Publication date |
---|---|
DE1159978B (en) | 1963-12-27 |
FR1213741A (en) | 1960-04-04 |
BE563542A (en) | |
DE1176164B (en) | 1964-08-20 |
GB832438A (en) | 1960-04-13 |
BE571059A (en) | |
FR1197045A (en) | 1959-11-27 |
GB919206A (en) | 1963-02-20 |
US3069299A (en) | 1962-12-18 |
GB845167A (en) | 1960-08-17 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
DE3885584T2 (en) | Process for the production of austenitic stainless steel with excellent seawater resistance. | |
DE2252784C3 (en) | Process for the production of a silicon iron sheet material with a cube-edged texture with a silicon content of 2 to 4% | |
DE112010004925T5 (en) | Carbon-rich, martensitic stainless steel and its production process | |
DE3812624A1 (en) | BALL GRAPHITE CAST IRON AND METHOD FOR PRODUCING IT | |
DE1181255B (en) | Process for the production of sheets or plates from an iron-silicon alloy with a crystallographically oriented structure | |
DE69738447T2 (en) | Method for producing grain-oriented silicon-chromium electrical steel | |
DE3330814A1 (en) | METHOD FOR PRODUCING FINE-GRINED ALUMINUM ROLLING PRODUCTS | |
DE1533381B1 (en) | Use of a steel for the manufacture of razor blades | |
EP1441041A1 (en) | Aluminium alloy with high strength and low quenching sensitivity | |
DE1954168A1 (en) | Secondary recrystallization of silicon iron with nitrogen | |
DE68908301T2 (en) | METHOD FOR PRODUCING NON-ORIENTED ELECTROFINE SHEETS. | |
DE2751577A1 (en) | PROCESS FOR MANUFACTURING FOLD-HARDENED COPPER ALLOYS AND THEIR USE FOR CONTACT SPRINGS | |
DE2647874A1 (en) | PROCESS FOR THE MANUFACTURING OF INTENSIVE (70 TO 99% IGES) COLD FORMS WORKABLE ISOTROPIC MECHANICAL PROPERTIES STRIPS OR PLATES MADE OF COPPER OR COPPER ALLOYS | |
DE2531536A1 (en) | METHOD OF MANUFACTURING SHEET FROM SILICON IRON WITH ADDED BORON | |
DE3927310A1 (en) | Etch stripe-resistant iron-nickel alloy prodn. - by continuous casting and heat treatment | |
AT277300B (en) | Steel that can be hardened in the martensitic state | |
AT204064B (en) | Process for the production of an aluminum-containing protective coating for ingots, metal pins, blanks and billets | |
DE971310C (en) | Process for the production of aluminum sheets which, when deformed into hollow bodies, only cause weak ear formation | |
DE1227490B (en) | Process for the production of magnetic iron-aluminum sheet | |
AT142545B (en) | Chromium-cobalt-iron alloys with a low coefficient of thermal expansion. | |
DE1258884B (en) | Process for the production of silicon iron sheet with (110) [001] orientation | |
DE1274603B (en) | Process for the production of magnetic sheet with cube texture | |
DE1117624B (en) | Process for the production of strips with a high grain orientation from an iron-silicon alloy | |
DE704928C (en) | Bearing shell | |
DE587392C (en) | Process for the production of fine-grained magnetizable powder |