Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C69/00—Combinations of shaping techniques not provided for in a single one of main groups B29C39/00 - B29C67/00, e.g. associations of moulding and joining techniques; Apparatus therefore
  • B29C69/001—Combinations of shaping techniques not provided for in a single one of main groups B29C39/00 - B29C67/00, e.g. associations of moulding and joining techniques; Apparatus therefore a shaping technique combined with cutting, e.g. in parts or slices combined with rearranging and joining the cut parts
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
  • B29C48/03—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor characterised by the shape of the extruded material at extrusion
• • 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
  • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
• • 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
  • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
  • C21D1/76—Adjusting the composition of the atmosphere
• • 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
• • 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
  • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
  • B29C48/001—Combinations of extrusion moulding with other shaping operations
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
  • B29C48/03—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor characterised by the shape of the extruded material at extrusion
  • B29C48/07—Flat, e.g. panels

Definitions

• ABSTRACT 0F Til-IE DISCLOSURE A process, applicable to iron or iron-base alloys having a composition in which a gamma phase or face centered cubic lattice structure predominates at elevated temperature, for obtaining a 100) [It/cl] texture in an alloy sheet, which comprises, heating the alloy sheet to convert the alloy to the gamma phase and then cooling the sheet to convert the alloy to the alpha phase.
• This invention relates to magnetic sheet material having an (001) texture and novel processes applicable to iron and ferrous base alloys for developing such texture.
• gamma to alpha phase transforma tion is meant that the alloy when heated to some elevated temperature, 910 C. for iron alone, but depending on the composition for alloys, the crystal structure of the alloy will transform to the gamma phase or face centered cubic lattice, and upon cooling below this temperature the alloy crystal structure will revert to an alpha or body centered cubic lattice structure.
• Many ferrous alloys have no gamma to alpha phase transformation, for example silicon iron alloys having over 2% silicon and carbon below 0.01%.
• the present invention is based on the discovery that members, such as sheets, either hot or cold rolled, of iron or a ferrous base alloy having a gamma to alpha phase transformation can be subjected to a relatively simple annealing process passing from the gamma to alpha region to produce a random cube-on-face or (100) [hkl] grain texture, by suitable control of the composition as to provide a critical dissolved sulfur content therein during the gamma to alpha phase transformation during the anneal.
• the process is not only relatively simple, but is quite economical.
• the resulting product is commercially highly desirable.
• Another object of the invention is to provide a relatively simple process whereby sheets of iron and ferrous base alloys having a gamma to alpha transformation can be given a (100') [hkl] texture by cooling from the gamma to alpha region providing that the dissolved sulfur in the alloy is within a critical range during such phase transformaiton anneal.
• a further object of the invention is to provide a process for producing magnetic sheets of iron and ferrous base alloys having a gamma to alpha phase transformation, such sheets having extremely large (100) [hkl] grains.
• a still further object of the invention is to provide a process for producing magnetic sheets of iron and a ferrous base alloy having gamma to alpha phase transform-ation with a cube texture which comprises initially preparing sheets having a random cube-on-face texture and thereafter cold rolling and annealing to produce a high percentage of (100) [001] grains.
• Another object of the invention is to provide magnetic sheets of iron and ferrous base alloys having a gamma to alpha phase transformation, the sheets having a random (100) [hkl] grain texture.
• strip or sheet or punchings or laminations of iron and ferrous base alloys having a gamma to alpha phase transformation generally in a thickness from less than 1 to mils is heated to above the allotropic transformation temperature to develop the gamma phase therein.
• the metal should have dissolved sulfur in the critical amount of from 0.00003% to 0.0005% at the surface.
• the gamma phase metal is then cooled through the transformation a temperature, or transformation temperature range, to cause a phase change to the alpha phase.
• a high volume of the metal is of cube-nface or (001) [hkl] texture.
• edges are randomly oriented from the [100] to [110] directions. Consequently, improved magnetic properties are available in the resulting members. They are suitable for use in rotating electrical equipment.
• the sheet or strip can be further cold rolled and annealed whereupon it produces cube texture or (100) [001] grains.
• compositions with which the present invention is concerned are binary and multi-element alloys of iron that have a gamma phase at elevated temperature and contain, as alloying constituents, one or more of the following: up to 2.0% of aluminum, up to 12% of chromium, up to 10% of germanium, up to of manganese, up to 5% of molybdenum, up to of nickel, up to 2% of silicon, up to 1% titanium, up to 1% of tantalum, up to 1% of vanadium, up to 6% of tungsten, up to to 50% of cobalt and up to 1% of zirconium.
• carbon When carbon is present, its content generally is in the range of 0.001 to 0.08%.
• the preferred limits for the foregoing alloying elements are: 0.001 to 0.8% of aluminum, up to 2% of chromium, up to 0.5 of germanium, up to 1% of manganese, up to 2% of molybdenum, up to 1% of nickel, up to 2% of silicon, up to 0.5% of titanium up to 0.5% of tantalum, up to 0.5% of vanadium, up to 0.5% of tungsten, to 45% of cobalt and 0.1 to 0.5% of zirconium.
• the invention can also be practiced with unalloyed iron.
• ferrous alloy When two or more alloying elements are present in the ferrous alloy, their total amount preferably does not exceed about 50%.
• ferrous alloy with over 2% silicon may be employed by incorporating substantial amounts of carbon, molybdenum, nickel, or cobalt which extend -the gamma loop.
• Ternary, quaternary and higher alloys may be employed in practicing the invention.
• Illustrative examples are: (1) 1.0% silicon, 0.5% molybdenum, .01% carbon, balance iron; (2) 0.6% silicon, 0.3 manganese, 0.01% carbon, balance iron; (3) 1% chromium, 1% cobalt, 0.2% manganese, balance iron; (4) 0.5% silicon, 0.5% chromium, 0.5% nickel, 0.1% manganese, balance iron and (5) 0.8% silicon, 0.01% carbon, 0.5% molybdenum, 0.5% nickel, 0.2% chromium, balance iron.
• Incidental impurities such as oxygen, nitrogen and traces of various elements may be present.
• the alloy may be extremely pure or clean, or it may be a regular commercial product, and either will be suitable for the practice of the invention.
• Oxygen has been found not to be critical in practicing the invention and relaively large amounts can be present without adverse effects.
• the sulfur content and its precise form and distribution is critically important. Sulfur present as inclusions of relatively stable sulfides, such as manganese sulfide, plays no significant part in effecting the desired results of the invention. Sulfur dissolved in the ferrous phase so that it is present in critical proportions at the surface of the sheet is the indispensable constituent. At the time that the gamma to alpha transformation takes place the dissolved sulfur adjacent or at the surface must be within the range of 0.00003% to 0.0005 by weight. The sulfur content of the sheets should be so analyzed as to exclude sulfur as a relatively stable sulfide.
• a sheet may include a relatively high percentage, say 0.02% of sulfur, which however is nearly all in the form of manganese sulfide, and it will transform to cube-on-face during the gamma to alpha annealing because the dissolved sulfur at the surface is in the critical range.
• the furnace atmosphere may be treated to introduce a small amount of hydrogen sulfide, for example 0.001% by volume of the hydrogen sulfide. This not only prevents evaporation of the dissolved sulfur from the metal but may even introduce enough into the metal to bring it into the desired range if the sulfur content is low.
• carbon is not a 'desirable constituent of magnetic sheets, and every effort is made to reduce the carbon content to less than 0.01%, preferably below 0.005% in the final sheet.
• a decarburization anneal, using wet hydrogen, for example 50 F. dew point, at 800 C. to 900 C. for A1 to 2 hours will reduce the carbon content to a low level. This treatment may precede or follow the gamma to alpha phase transformation of the inven tion.
• Iron and its alloys for use in the present invention generally are in sheet or strip form of about 0.001 to 0.150 inch in thickness, though it has been found that the process is essentially insensitive to the thickness of the material being processed.
• sheet or strip material is produced by forging or hot rolling a slab directly to the desired thickness or to an intermediate thickness on the order of about 0.1 to 0.5 inch. The intermediate thickness is then reduced by cold rolling to the final thickness in one or more stages. Each stage comprises a cold rolling anneal, and pickling if necessary.
• the strip or sheet can be decarburized by annealing in the decarburizing atmosphere, for example wet hydrogen, that is, hydrogen s aturated with water vapor at about 20 to 50 C. When cold rolling is practiced, reduction at each stage on the order of 40 to generally are taken.
• a critical step of the present invention involves annealing the material at a temperature, for a period ranging from about 10 minutes, though it may be 30 hours or more, such temperature being in the gamma region for the material being treated. Generally, for purposes of insuring this, annealing is conducted at about 10 to 300 C. above the temperature at which the transition starts but clearly in the gamma region in all events.
• the material is cooled, preferably, though not necessarily slowly cooled, through the allotropic transformation temperature, suitably to about 10 to C. below it.
• Slow cooling at a rate below about C. per hour and suitably in the range of about 4 to 12 C. per hour results in very large grain growth of the (100) [hkl] grains.
• the treated material can be cooled as desired to room temperature and used. Also cooling the sheets rapidly to a temperature of about 10 to 200 C. below the temperature at which the transformation occurs and holding the sheets at this temperature for about 2 to 50 hours tends to convert the grain structure from one containing a substructure to one free from substructure, through selective growth of the (100) grains to a very large size and thereby further improve the magnetic properties.
• the material containing the (100) [hkl] texture can be further cold rolled, i.e. at about a 60 to 80% reduction, and again be given a heat treatment to produce oriented material having a cube or'(100) [001] texture.
• the development of the (100) [hkl] texture of the present invention is critically influenced by employing a selective driving force for (100) grain growth during the allotropic transformation.
• the driving force is provided by the presence of the critical amounts of sulfur during the gamma to alpha transformation.
• the sulfur can be present as an alloying constituent in the metal being treated or it can be supplied in part or entirely by an addition of a sulfur material to the atmosphere in which the process is carried out.
• Sulfur has also been supplied by treating material, that may be present during the annealing, wit-h H 8, for example an A1 sheet separator material which evolves the sulfur by appropriate vapor pressure development.
• Sufiicient sulfur is present for driving purposes when the alloy contains dissolved sulfur to an extent of 0.00003 to 0.0005% of the alloy or the atmosphere is provided with a sulfur-containing compound, preferably hydrogen sulfide, in an amount to provide a partial pressure of sulfur which would produce or maintain an equilibrium condition at least at the surface of the sheet in this range.
• a sulfur-containing compound preferably hydrogen sulfide
• the metal In annealing the metal sheets, strip or punchings or the like in stack or coiled form, the metal must contain dissolved sulfur in essentially the critical proportions of 0.00003% to 0.0005% at the time of the phase transformation. A slight excess of dissolved sulfur may be present in the metal since a small portion of the sulfur is evolved during the anneal, so that the dissolved sulfur content at the sheet surface will be in the proper range at the time the metal is in the gamma to alpha transformation temperature range whereby cube grain growth takes place.
• an atmosphere containing hydrogen sulfide in amounts from 2 to 30 parts per million by volume may be flowed past the laminations in order to maintain or increase the dissolved sulfur in the ferrous metal into the critical range of from 0.00003% to 0.0005%.
• additions of up to 0.5% by weight of elements which have a high aifinity for sulfur may be made.
• Such additions to the alloys of this invention which have bulk sulfur concentrations above the critical range will aid in obtaining the cube grain texture by reducing the amount of sulfur in solution by reason of the formation of very stable sulfides.
• Such elements, in addition to manganese, are barium, calcium, cerium, strontium and the rare earth elements such as lanthanum which forms stable sulfides.
• the transformation can be carried out in a neutral or nonoxidizing atmosphere or in a reducing atmosphere that tends to produce a bright surface on the metal being treated at the time of transformation.
• the transformation can be carried out in a vacuum of at least as low as 10* mm. of Hg or in a reducing gas such as dry hydrogen, or in argon, helium, nitrogen or mixtures of gases, as for example, nitrogen and hydrogen.
• a reducing gas such as dry hydrogen, or in argon, helium, nitrogen or mixtures of gases, as for example, nitrogen and hydrogen.
• the atmosphere can contain water vapor as would for example, be present in wet hydrogen (20 to 50 C. dew point) for pure iron for example and this in some cases tends to benefit the surface energy relationship that functions as a driving force.
• wet hydrogen (20 to 50 C. dew point
• pure iron for example and this in some cases tends to benefit the surface energy relationship that functions as a driving force.
• the atmosphere should be relatively dry, for instance of a dew point
• the metal treated whether in strip, sheet, or other form such as Epstein strips or stator punchings or the like, has a (100) [hkl] texture ranging from about 50 to 98% of its crystal volume or surface area. This proportion is based on counting grains whose cube faces are parallel within 12 to the surface of the sheet. Usually 40 to 50% of the grains have faces within 2 of the surface, and another to within 2 to 6. The magnetic properties are outstanding.
• the (100) [hkl] texture produced in accordance with this invention be present to an extent of about 70% and preferably 80% and higher of the surface of the sheets.
• the allotropic transformation temperature for example at 800 C. to 900 C. there is obtained cube texture material, that is (100) [001] orientation.
• this latter orientation is meant to indicate that at least 80% of the surface area is occupied by (100) grains at least 75% of which have their [001] directions aligned within 15 of the rolling direction.
• the anneal below the allotropic transformation temperature secures secondary recrystallization of the (100) grains which grow to an average diameter which is many times the sheet thickness averaging well above 10 times the said thickness. This last anneal extends for about 10 to 100 hours or more and is carried out in the same conditions of atmosphere, and therefore driving force, as that indicated hereinbefore with respect to producing (100) [hkl] texture.
• Material for the following examples generally was prepared by melting, usually in a vacuum furnace, the appropriate charge contained in a magnesia crucible and then pouring the melt into a stainless steel mold. Purified iron, where its use is indicated, was obtained for this purpose by annealing electrolytic iron one hour at 760 C. in wet hydrogen followed by one hour at 1200 C. in dry hydrogen. Further, the annealing referred to in the examples was, unless otherwise stated, stack annealing using alumina as a separator and a hydrogen atmosphere of a dew point of less than C.
• the sulfur content values given are the total sulfur in the ferrous metal prior to annealing. A substantial or even a major proportion of the sulfur is bound as stable sulfides and plays little part in the cube grain growth process. Also some of the sulfur may be removed during annealing if the atmosphere is below the equilibrium sulfur content whereby a sulfur gradient exists between the center of each sheet and its surface. In each example where or more of cube grain growth occurred, the dissolved sulfur at the surface was in the range of 0.00003% to 0.0005%.
• Example I A sheet of 12 mil thick commercial iron was used having the following composition by weight: 0.003% aluminum present as A1 0 0.002% N, 0.39% Mn, 0.017% Cu, 0.11% P, 0.030% C, 0.022% S and the remainder iron.
• the sample was annealed in dry hydrogen -35 C. dew point for one hour at about 1210 C. (about 300 C. above the gamma to alpha transition temperature) and then slowly cooled, about 110 C. per hour, to a temperature of about 860 C., which is about 50 C. below the alpha to gamma transition temperature, and then cooled to room temperature.
• Example 11 An iron base alloy containing about 1.11% of silicon was prepared by vacuum melting purified electrolytic iron and commercial grade silicon. This alloy was melted in a magnesia crucible and poured into a stainless steel mold. The analysis, by weight, was 0.0013% of oxygen, 0.0009% of nitrogen, 0.0015% of carbon, 0.0013% of sulfur, 1.11% of silicon and the remainder iron.
• the alloy was hot rolled to sheet at a temperature in the range of 800 to 1050 C. to a thickness of 0.100 inch, pickled in a 25% sulfuric acid solution, and then cold rolled to a sheet thickness of 0.018 inch.
• Epstein strips (1 7 x 12") were sheared from the sheet and annealed in a stack with dry alumina as a separator. All annealing as hereinafter indicated was done in an Inconel tube in an atmosphere of dry hydrogen (50 C. dew point).
• Example 111 A series of tests were made on iron-oxygen alloy sheets containing 0.0010 to 0.0023% sulfur and in which the oxygen was varied from 0.0010 to 0.0335 specimens of each composition was annealed at 1050 C. for 12 to 16 hours and then cooled at 4 to 10 C. per hour to the alpha region, and other specimens were annealed for the same period but at the higher temperature of 1200 C. and then cooled at 4 to 10 C. per hour to the alpha region. It was found that changes of the oxygen concentration did not appreciably influence the amount of (001) [hkl] resulting. However, the annealing temperature did influence the results, with the lower (1050 C.) temperature being the better, resulting in a smaller grain size and a larger amount of (100) [hkl] texture which varied from 51 to 80% of the surface.
• Example IV A similar series of tests were made on iron-manganesesulfur alloys containing about 0.093% of manganese in all instances, with the sulfur ranging from 0.0015 to 0.022%.
• the best results were achieved in the heat treating schedule that included the anneal at 1050 C., with the amount of (100) [hkl] texture ranging from 83.3 to 90.2% of the surface area. It was also discovered that the presence of manganese, along with the necessary dissolved sulfur had a beneficial influence on (100) grain growth.
• Example V An alloy slab containing, by weight, 27% of cobalt, 0.01% manganese, about 0.02% sulfur and the remainder essentially iron was hot rolled at 1000 C. to a band 100 mils thick. The hot rolled band was pickled to remove scale, and it was then cold rolled to 14 mil strip. That strip was placed in a furnace at 800 C. and heated Within the furnace to 1150 C. After 16 hours the strip was furnace cooled (below 12 C. per hour) to 800 C. It is to be noted that the alpha to gamma transformation temperature for this composition is approximately 950 C.
• Example VI Strip of a thickness of 18 mils of cold rolled iron-molybdenum having an analysis, by weight, of 0.0112% of oxygen, 0.0027% of carbon, about 0.0005 of sulfur, 0.99% of molybdenum and the remainder iron was annealed in the gamma range and then slowly cooled through the transition in the same manner and under the conditions set forth in Example III above.
• the treatment including the anneal at 1050 C. was superior, and indeed resulted in one of the highest value of (100) [hkl] texture achieved in any of these tests, 93.5%.
• Example VII Single strips of the iron-molybdenum alloy analysis set forth in Example VI were inserted into a tube furnace at 1140 C. and positioned with one end of each strip in the hot zone and the other in the cold zone. The strips were held in this position for about 1 or 2 hours and then pulled at different rates into a cooling chamber. A portion of each strip that was at a temperature in the gamma temperature region was found to have developed (100) [hkl] texture in inverse proportion to the rate of withdrawal, and therefore the rate of cooling through the transition temperature.
• alloy strip as described was annealed at 1000 to 1300 C., slowly cooled through the transition temperature and then further annealed below the transition temperature, i.e. at 800 C., for about 5 to 120 hours in the sulfur-containing, nonoxidizing atmosphere suitable to the growth of (100) grains. This latter procedure tends to remove substructure thereby contributing to improved magnetic qualities.
• material having a 100) [hkl] texture can be further treated, inaccordance with my discoveries, to develop (100) [001] orientation.
• the following is an example thereof which also demonstrates the desirability of the requirement of starting with at least 80% (100) [hkl] texture for this particular discovery.
• These alloys were prepared 10 by vacuum induction melting, and sheet was obtained therefrom by hot rolling at 1050 C., pickling, and then cold rolling to 0.012 inch for alloy A and cold rolling to 0.018 inch for alloy B.
• Alloy A was annealed in the gamma phase by heating at 1050 C. for 8 hours followed by cooling at 8 C. per hour through the allotropic transformation temperature to 880 C.
• Alloy B was annealed in the gamma phase by heating at 1050 C. for 12 hours followed by cooling through the allotropic transformation temperature at 4 C. per hour to 880 C.
• the anneals for both alloys were conducted in dry hydrogen (below C. dew point) containing traces of sulfur.
• a study of the grains in the resulting product showed that those in alloy A contained 51 to 71.6% of (100) grains within 12 of the rolling plane while alloy B contained 89.7 to 93.9% of its (100) grains within 12 of the rolling plane.
• the annealing indicated in the foregoing examples was conducted in dry hydrogen (50 C. dew point). In other tests, the procedure was changed to substitute +20 C. dew point hydrogen. For those alloys that were insensitive to water vapor, e.g. iron-molybdenum and the like, the desired (100) [hkl] texture was still achieved. However, for alloys that thereby developed a heavy oxide surface film, e.g. iron-silicon alloys, a low value of the desired texture resulted thereby indicating the need to anneal at conditions that result in a bright surface during the phase change.
• alloys having an oriented texture from ferrous-base alloys having a gamma to alpha phase transformation
• such alloys containing, by weight, at least one element selected from the group consisting of up to 2% of aluminum, up to 12% of chromium, up to 10% of germanium, up to 5% of manganese, up to 5% of molybdenum, up to of nickel, up to 2% of silicon, up to 1% of titanium, up to 1% of tantalum, up to 1% of vanadium, up to 6% of tungsten, up to 50% of cobalt, up to 1% of zirconium and from 0.001 to 0.08% of carbon, the total amount of such elements not exceeding 50%, by weight, of the alloy when more than one of said elements is present, the steps comprising heating a sheet of such alloy to a temperature sufficient to convert the alloy to the gamma phase, then cooling the alloy to the alpha phase, the alloy having from 0.00003 to 0.0005%, by weight, of dissolved sulfur
• a method of producing ferrous-base alloy sheets having an oriented texture comprising rolling a ferrousbase alloy body containing as alloying constituents at least one member selected from the group consisting of up to 2% aluminum, up to 2% chromium, up to 10% germanium, up to 5% of manganese, up to 5% of molybdenum, up to 10% of nickel, up to 2% of silicon, up to 1% of titanium, up to 1% of tantalum, up to 1% of vanadium, up to 6% of tungsten, up to 20 to of cobalt, up to 1% 0f zirconium, up to 0.08% of carbon, to a thickness of from less than 1 to 150 mils, heating the resulting sheet to a temperature within the range of about 900 to 1300 C.
• the alloy sheet at which the alloy is in the gamma phase, then cooling the heated sheet at a rate below about 175 C. per hour through its allotropic transformation temperature to a temperature at which the alloy is in the alpha phase, the alloy sheet having therein from 0.00003 to 0.0005%, by weight, of dissolved sulfur at the surface during the transformation to the alpha phase, cold reducing the sheet about to then heating the cold reduced sheet at a temperature just below the allotropic transformation temperature for a period to produce a major proportion of grains having a [001] orientation, said process being carried out in an atmosphere which is nonoxidizing to the surface of the alloy being treated.
• a method of producing alloy sheets having an oriented texture from ferrous-base alloys having a gamma to alpha phase transformation such alloys containing, by weight, at least one element selected from the group consisting of up to 2% of aluminum, up to 12% of chromium, up to 10% of germanium, up to 5% of manganese, up to 5% of molybdenum, up to 10% of nickel, up to 2% of silicon, up to 1% of titanium, up to 1% of tantalum, up to 1% of vanadium, up to 6% of tungsten, up to from 20 to 50% of cobalt, up to 1% of zirconium and from 0.001 to 0.08% of carbon, the total amount of such elements not exceeding 50%, by weight, of the alloy when more than one of said elements is present, the method comprising heating a sheet of such alloy to a temperature sufficient to convert the alloy to the gamma phase, then cooling the alloy to the alpha phase, the alloy having from 0.00003 to 0.0005 by weight, of
• a method of making sheets of iron-cobalt alloy having a (100) [hkl] texture comprising heating a sheet of such alloy to a temperature to convert the 13 metal to the gamma phase, then cooling the alloy sheet to the alpha phase, the alloy sheet having from 0.00003 to 0.0005%, by weight, of dissolved sulfur at the surface thereof during the phase transformation.
• the steps comprising heating a single strip of iron or ferrous-base alloy having a gamma to alpha phase transformation to a temperature in the gamma region, cooling the strip to the alpha region, the heating and cooling steps being carried out in a nonoxidizing atmosphere comprising from 2 to 30 parts per million of hydrogen sulfide, conducive to the development of grains having the (100) [hkl] orientation whereby the surface of the strip has from 0.00003% to 0.0005% of sulfur during the phase transformation so that cube grains nucleate on the surface and grow therefrom.
• a method of making sheets of oriented iron, the iron having only small amounts of additives and impurities therein comprising heating a sheet of said iron to a temperature above 910 C. to convert the iron sheet to the gamma phase, then cooling the iron sheet to the alpha phase, the iron sheet having from 0.00003% to 0.0005 by Weight, of dissolved sulfur at the surface thereof during the phase transformation whereby grains occupying at least 80% of the surface of the iron sheet are oriented to a (100) [hkl] texture.

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Citations (3)

• 1964
  • 1964-06-04 US US372693A patent/US3351501A/en not_active Expired - Lifetime
• 1965
  • 1965-05-12 DE DE1965W0039135 patent/DE1483514A1/de active Pending
  • 1965-05-18 GB GB21000/65A patent/GB1080578A/en not_active Expired
  • 1965-06-03 FR FR19433A patent/FR1443470A/fr not_active Expired
  • 1965-06-04 SE SE7415/65A patent/SE318900B/xx unknown
  • 1965-06-04 BE BE664974A patent/BE664974A/xx unknown

Patent Citations (3)

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