US2859143A - Ferritic aluminum-iron base alloys and method of producing same - Google Patents
Ferritic aluminum-iron base alloys and method of producing same Download PDFInfo
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- US2859143A US2859143A US448398A US44839854A US2859143A US 2859143 A US2859143 A US 2859143A US 448398 A US448398 A US 448398A US 44839854 A US44839854 A US 44839854A US 2859143 A US2859143 A US 2859143A
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- 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
-
- 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
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
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- 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
- C21D8/1227—Warm 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
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
Definitions
- the present invention relates to a series of alloys for high temperature and magnetic uses, and more particularly to the method and processing technique essential to produce physically sound high quality materials.
- An object of the present invention is to provide compositions of ferritic alloys having excellent high temperature strength andoxidation resistance.
- Another object of the invention is to provide a new processing aluminum-iron base and oxidation.
- Another object of the e, of aluminum-iron base materials capable of being exing three or more of the aforesaid metals into physically sound flexible sheets of any desired and workable thickness.
- the present invention contemplates the provision of a new series of ferritic high temperature and magnetic alloys containing non-strategic materials, such, for exmaterial characterized by invention is to provide a series "truded by standard hot extrusion methodsinto usable shapes possessing the magnetic and high temperature properties associated with these alloys.
- Still another object of the invention is to provide a series of materials with a very high electrical'resistivity' microohm-Cm] coupled with the excellent'high temperature properties suitable for use in electrical resistance heating applications.
- a further object of the invention is for producing a series of materials exhibiting good. re-' sistance to wet corrosion, at room temperature, when. 'I
- a still further object of the invention is to provide a method for producing a series of magnetic materials high hardness and wear resistance.
- object of the invention is to a series of alloys'in usable form such, for example, as sheets, castings and the like,
- the alloy compositions may consist of 10 to 18% Al, 0 to 5% of to provide a method possessing excellent magnetic properties coupled with 'a provide exhibiting second phase precipitation phenomena to strengthen the materials both any one orany combination of the following elements- Mo, V, Cr, Ti, Ta, Cb, W, and B, the remainder or basic alloy being Fe.
- the high temperatureand rhagnetic alloy ofthe inst'aht 4 sheet material that limit being the composition where difliculties in cold roning ⁇ e alloys by either strengthe'n- Y invention may be made, *for example, by-melting togethera an alloy of 10 to 18% aluminum, up to '5 strengthening element additives, the remainder of the alloy being iron, forminga casting or shape, solution heat treating the casting to a temperature within the single phase solid solution region, 'When this has been done the shape or casting is rapidly cooled to a temperature within the multi-phase region, andthe'castin'gor shape-is maintained at this reduced temperature until at least one other phase has beenprecipitated. ,7
- strengthening element as einployed herein and in the appended claims is' defined as an element such, for example, as M0, V, Ti, Cr, Ta,
- the alloys are composed of basically iron and aluminum with oneor more of the elements Mo, V, Ti, Ta, Cb,-Cr, W, and B present.
- the cold rolled sheet alloys may be recrystallized at about 750 C. for 1 hour. By actual tests it has been found that this recrystallized fine grain size is only possi-- ble from cold worked sheet alloys.
- Material fabrication method Melting and casting
- the melting of the aforesaid alloys may be performed in any suitable type of melting furnace, such for example, asa vacuum or controlled atmosphere induction furnace.
- a suitable type of melting furnace such for example, asa vacuum or controlled atmosphere induction furnace.
- the melting is to melt the iron and molybdenum under vacuum.
- the melting is preferably carried out in a magnesium oxide crucible.
- wet and dry hydrogen gas is passed over the melt. This operation is performed for the purpose of decarburizing and deoxidizing the iron-molybdenum molten solution.
- Helium is now introduced into the tank to displace the hydrogen.
- Hot rolling After melting, casting and conditioning the'slab, the hot rolling operation is in order.
- the slab is hot rolled to about 0.250" in thickness at a temperature of 1050" C.
- the reductions in thickness between reheatings and v the reductions per pass through the mill are based upon the-mill capacity and the rate at which the strip loses heat. Rolling is stopped and reheating is necessary when the strip drops in temperature to a dull red heat.
- the hot rolling is performed at about 950 ,C.
- the cold rolling operation is in order.
- cold rolling denotes cold working the alloy at a temperature below the recrystallitemperature.
- Cold rolling may be performed to reduce the material to -a relatively thin gage, such, for example, as 0.002 of an inch or thinner.
- the hotslab is then placed in a furnace at 1050 C. for about two If it is desired .to. remove this coating for any purpose, lspotwelding';
- the slabs or sheets. produced by the aforesaid method may be of any desired length andwi'dth and characterized by high tensile strength :and high resistance to.
- C. 3 The method of making a high temperature and magnetic sheet alloy containing essentially 16% alurninum and up to 5% molybdenum and remainder iron, which consists of melting the constituents in a suitable. melting apparatus to form a molten alloy, forming. the: molten alloy into an ingot, controlling the solidifiea-Y tion rate of the molten alloy to produce an ingot having a line equiaxed cast grain structure, transferring the in-. got from the melting apparatus while red .hot to a :heatn ing apparatus and heat treating the ingot at a temperatu're of about 1050 'C.
- magnetic sheet alloy containing essentially 16% alumi num, 3.3% molybdenum, and remainder iron, which consists of melting the constituents in a suitable melting.
- apparatus to "form a molten alloy, forming the molten alloy into an ingot, controlling the solidification rate' of the molten alloy to produce an ingot having aIfine' equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a heating apparatus and heat treating the ingot at a temperature
- molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a heating apparatus and heat treating the ingot at a temperature of about 1050 C. for a time sufilcient to uniformly heat the ingot, cooling the ingot slowly to substantially room temperature, removing surface imperfections from the ingot, hot working the ingot above the recrystallization temperature to a sheet of predetermined thickness, and thereafter cold working the sheet below the recrystallization temperature to a reduced thickness.
- the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot fromthe melting apparatus while red hot to a heating apparatus and heat treating, the ingot at a temperature of about 1050 C. for a time sufficient to uniformly heat the ingot, slow cooling the ingot at a rate of about 30 C. per hour until theingot is substantially at room temperature, removing surface imperfections from the ingot, hot working the ingot into a sheet substantially 0.250" thick at at temperatures of about 1050 C. followed by hot working the sheet at a temperature of 950 C. from a thickness of 0.250 of an inch thick to a thickness of substantially 0.125 of an inch, and thereafter cold working the sheet to the desired thickness at a temperature of about 575 C.
- said alloy being subjected'to a.
- coolingfat a a high temperature and. comprises producing a aluminum, up the remaihder treating said casting to a temperature within the single phase solid solution region, rapidly cooling the casting to a temperature within taining the casting at said last named temperature for a the multi-phase region, and mainperiod of time sufiicient to precipitate at least one other phase.
- V 23 A high temperature and magnetic ferritic alloy consisting essentially of 10 to 18% elements include 3.3% molybdenum and 0.3%
- a high temperature and magnetic ferritic alloy consisting essentially of 1010 18% aluminum, up to 5% molybdenum, and the remainder essentially iron, said i by a recrystallized fine grain alloy being characterized size with disordered atomic structure.
- a method for making a high temperature magnetic ferritic casting which comprises producing a melt consisting essentially of 10 to 18% aluminum, up to 5% of strengthening element, and the remainder essentially iron, casting said melt and controllably solidifying the same to produce a fine equiaxed cast grain structure, annealing said casting at a temperature of about 1050 C. to eliminate stresses therein, and thereafter slowly cooling the casting while avoiding the occurrence of further stresses therein.
Description
FERRITIC ALUMINUM METHOD OF PRODUCING SAlVIE Nachman and William J. Buehler, Silver Spring,
of one-fourth to EdwardrA. Gaugler,
No Drawing. Application August 6, 1954 Serial No. 448,398
, 27 Claims. (Cl. 1482) (Granted under Tifle, 35, U. S. Code (1952), see. Zoo) The invention described herein maybe manufactured and used by or for the Government of the United States of America for governmental purposes without the payment of any royalties thereon or therefor.
The present invention relates to a series of alloys for high temperature and magnetic uses, and more particularly to the method and processing technique essential to produce physically sound high quality materials.
Heretofore, certain known alloys of aluminum and iron possessed excellent oxidation resistance when heated to a high temperature in air. However, such alloys were weak in structure and lacked high temperature strength, and desired malleable characteristics such that they could be formed into any desired shape. To take advantage of the high temperature oxidation and hightemperature strength possibilities the aluminum content of these alloys must be rather high [minimum of about Al]. Considerable difficulty, however, was encountered in-melting,- casting, rolling, and processing, even binary AlFe alloys, into cold rolled sheet form when the aluminum content exceeded 10%. Moreover, due to the inherent brittle characteristics of the binary Al-'-Fe alloys with the Al content exceeding 10% no successful method has been devised heretofore to produce a usable and workable sheet material from such alloys, having strengthening additives such, for example, as Mo, V, Ti, Ta, Cb, Cr, W, and B. Nor was it possible heretofore to hot and cold roll such materials containto Stephen Girard Lax,
' United Statcs-Patent'O -IRON BASE ALLOYS AND r and improved method of alloys into workable sheet high tensile strength and high resistance to corrosion Patented Nov. 4, 1958 cial ferritic type high temperature materials currently:
being used in high temperature applications.
devised for rolling such component inexcess of 10% into physically sound usablematerial'" and processing the alloys'into various forms, thin cold rolled sheets.
An object of the present invention is to provide compositions of ferritic alloys having excellent high temperature strength andoxidation resistance. P
including Another object of the invention is to provide a new? and improved method of making aluminum-iron base alloys into usable material having improved high temperature and magnetic properties. 7
Another object of the invention is to provide a new processing aluminum-iron base and oxidation.
Another object of the e, of aluminum-iron base materials capable of being exing three or more of the aforesaid metals into physically sound flexible sheets of any desired and workable thickness. I
The present invention contemplates the provision of a new series of ferritic high temperature and magnetic alloys containing non-strategic materials, such, for exmaterial characterized by invention is to provide a series "truded by standard hot extrusion methodsinto usable shapes possessing the magnetic and high temperature properties associated with these alloys.
Still another object of the invention is to provide a series of materials with a very high electrical'resistivity' microohm-Cm] coupled with the excellent'high temperature properties suitable for use in electrical resistance heating applications.
A further object of the invention is for producing a series of materials exhibiting good. re-' sistance to wet corrosion, at room temperature, when. 'I
brought'in contact with common corrosive mediums;
A still further object of the invention is to provide a method for producing a series of magnetic materials high hardness and wear resistance.
A still further. object of the invention is to a series of alloys'in usable form such, for example, as sheets, castings and the like,
at room temperature and at elevated temperatures.
Other objects and many of the attendant advantages of this invention will be readily appreciated as the same becomes better understood by reference to'the' following detailed description. A 1
In accordance with the present invention the alloy compositions may consist of 10 to 18% Al, 0 to 5% of to provide a method possessing excellent magnetic properties coupled with 'a provide exhibiting second phase precipitation phenomena to strengthen the materials both any one orany combination of the following elements- Mo, V, Cr, Ti, Ta, Cb, W, and B, the remainder or basic alloy being Fe.
Using the methods of. limits in accordance with the present invention the lowing stress-rupture results were actually achieved, the 7 results being set forth on the following chart 'Ol'ialfl with the alloy compositions given andv the respective. heat treatments and material form included.
fabrication and composition fol- High temperature stress-rupture data Stress-Rupture Times in Hrs. Sample N 0. Alloy Composition Form of Alloy Heat Treatment Using 25,000
Material p. s. 1. load and tested at 1,200 F.
15.6% A1, Remainder Fe 0.020 thick cold None 0.5
rolled sheet. 15% A1, 3.3% Mo, Remaindo 1,050 O.fr2hrs.iol1owed 47. 6
der Fe. by an air cool. 175%?1, 3.3% Mo, Remaindo o 69 er e. 17.2% A1, 3.3% Mo, Redo 900 C. for 2 hrs. followed 24 in der Fe. by an air cool. A1, 3.3% Mo, Remain- --do 1,050 C.ior2hrs.iollowed 0.25
der Fe. by an air cool. 13.8% Al, 4% Mo, Remaind0 d0 54.4
der Fe. r 16% a1, 3.3% M0, 0.05% 0, -do d0 19.3 14 r rii 2f i' it iiav v V d 7 a 17 2 x .1, y "1 ,0 O 155,311,573 Mo, R'einamder ..-do do e1 '6. w I mg ai, 1.68% M0, 0.3% Ti, ..-do do 73. 2 e. a 167311, 1% Ti, .Bal. Fer; do do 9. 9
From the foregoing table of stressqupture data the following conclusions are obvious:
(I) The basic binary alloy containing about 16% Al, the remainder iron, -in the cold rolled sheet form, with no heat treatment has a very 'low high temperature strength.
'(2) The addition of elements such as M0, V, and Ti definitely improve the-high temperature strength.
(3) Coupled with the aforesaid additives, 'maximum high temperature strengths are attained by -a heat treatment of about I050 C. for about 2 hours followed by a still air cool. The effectiveness 'of this'heat treatment can be seen try-comparin samples 3 and 4 in the table.
(4) The percentage of aluminum 'and 'iron present 'in the alloy as shown inth table, in combination with the other elements greatly improves the high temperature strength. This can be shown by comparing samples 2 and 5 in the table.
(5) Higher percentages of elements, siic-h'a's -Mo, increase the high temperature strength. However, the'reis a "practical limit on cold rolled areencountered.
(6) The addition of the etements such'as-Mo, V, and Ti -is for the purpose of increasing the -high temperature strength of the basic Al ing the existingferritic solid 'solutiono'r by precipitating a. strengthening second phase. These element additions appear to have very little'efle'ct upon the grain size or oxidation resistance of'the resultant alloys.
These sample data given in the table further illustrate the nature of this inventiomhowever, it should be understood that the-invention is not res'trictedto these specific examples.
The high temperatureand rhagnetic alloy ofthe inst'aht 4 sheet materialthat limit being the composition where difliculties in cold roning} e alloys by either strengthe'n- Y invention may be made, *for example, by-melting togethera an alloy of 10 to 18% aluminum, up to '5 strengthening element additives, the remainder of the alloy being iron, forminga casting or shape, solution heat treating the casting to a temperature within the single phase solid solution region, 'When this has been done the shape or casting is rapidly cooled to a temperature within the multi-phase region, andthe'castin'gor shape-is maintained at this reduced temperature until at least one other phase has beenprecipitated. ,7 The term strengthening element? as einployed herein and in the appended claims is' defined as an element such, for example, as M0, V, Ti, Cr, Ta,
ande, or any combination thereof.
Cb, W, Ni,
W .heat treatment eonsists of=heating the alloy to a'tem'pera-. V
'ture of about -0 -C. 'for Magnetic data Nominal alloy composition 6% A1, 3.3% Mo, re
mainder -Fe. 1050 C. for one hour,
Heat treatment furnace cool to 600 oersteds.
Based '-'-1ipon actual tests and data '-'obtain'eii on these unique alloys fabricated in accordance-with the teaching of the present invention, there areeeitainfcoinbinations and qiiantities of metallic elements th'zit'rnu's't-be alloyed to produce high temperature materials with suitable strength and oxidation resistance.
be 'from "about-l0 to 18% Added to the Al'i's 'a'nother'type-el'ement or elementsfsuch in the alloyeither as a siiigle' element added to the Al and Fe, tor in combinations of two, or more of these elements.
the alloys however, are composed of basically iron and aluminum with oneor more of the elements Mo, V, Ti, Ta, Cb,-Cr, W, and B present.
In addition to-the optimum alloy compositions, and
alloy fabrication IhBthOdSftO'Obtfiill the maximum high temperaturestress-rupture.strength in these materials it is essential to :perform certain heat treating operations upon thefabricated-material as hereinbefore set forth "in greater detail. By actual tests, the most satisfactory about two hours followed by a still-air cool. This=heat-treatment cyclewas'applied to 0.020 thick Sheet material, however, ifthicker'secr [at ;H =-30. -oerstedsl The's'e quantities may be summarized iris-follows: Thehliiniinuih 'eon'tent s'liould 'of total alloy by weight;
' The amountfofany one or more but not all of the elements Mc, V, Ti, Ta, Cb, 'Cr, W, and B, present amo tions or sheets are heat treated, longer times of holding at 1050 C. and more rapid cooling means may be needed to elfect the same heat treating cycle.
Moreover, when a fine grained sheet material is desired the cold rolled sheet alloys may be recrystallized at about 750 C. for 1 hour. By actual tests it has been found that this recrystallized fine grain size is only possi-- ble from cold worked sheet alloys.
Material fabrication method Melting and casting The melting of the aforesaid alloys may be performed in any suitable type of melting furnace, such for example, asa vacuum or controlled atmosphere induction furnace. For the purpose of clarity in describing the operations, an example melt of 16% All, 3.3% Mo, 80.7% Fe will be described. The is to melt the iron and molybdenum under vacuum. The melting is preferably carried out in a magnesium oxide crucible. After the elements are completely melted, wet and dry hydrogen gas is passed over the melt. This operation is performed for the purpose of decarburizing and deoxidizing the iron-molybdenum molten solution. Helium is now introduced into the tank to displace the hydrogen. When the gaseous mixture in the furnace chamber no longer supports a combustion, it will be understood that such action removes most all of the hydrogen that may have been dissolved in the molten alloy. Helium is introduced again into the furnace chamber until one atmosphere of helium is present. At this time the 16% of aluminum is added to the melt and the furnace chamber is again evacuated [using a vacuum pump] to a pressure of 5 millimeters of helium. When this pressure is attained, and the optimum pouring temperature reached, the melt into a suitable mold for shaping the material into a final cast shape or it may be poured into aningot or slabtype mold, forming an ingot or slab for subsequent roll ing, swaging or extrusion into strips, sheets, rods, wire or other shapes.
The operation of pumping down to 5 millimeters of helium pressure after the aluminum addition and prior to Pouring is an important and essential step in the process. First, it removes the hydrogen from the molten alloy, thus producing sound castings. Secondly, coupled with the mold design it promotes a more desirable solidification rate for the molten alloy thus producing a highly desirable fine and equiaxed cast grain size. If thesame melt is poured at one atmosphere of helium, using the same mold, a large grained columnar cast structure would result. When the same melt is poured at one atmosphere of helium into a ceramic mold an equiaxed structure results and a much larger grain size is evident. Thus by the aforesaid treatments it is apparent that it is possible to produce the type of cast grain formation and size of cast grain by varying the rate of solidification of the alloy.
By actual test it has been found that casting such alloys in a steel slab mold under a vacuum of 5 mm. of helium and containing 16% A1, 3.3% Mo, and 80.7% Fe produced a desirable fine equiaxed cast grain structure, the casting in a steel slab mold under one atmosphere of helium produced a less desirable large columnar cast grain structure and the casting in a ceramic mold under one atmosphere of helium produced a large and equiaxed cast grain structure.
It will be understood that the formation ot a fine equifirst step in the melting operation is poured. Pouring may be either axed cast grainstructure is an important step in the production'of good quality material. Large columnar cast.
grain structure causes hottearing 'or crackingduring fabrication. Hot tearing or cracking is practically nonexistent in slabs with a fine equiaxed cast grain structure;
Conditioning cast slabs Immediately following the pouring, the cast slab hours and allowed to cool with the furnace, about 30 C.
drop'in temperature per hour. This operation prevents u the cast slab from cracking during rapid cooling'following solidification after the heat treatment, if desired, the" slab may be machined free of surface imperfections be fore beginning the hot rolling-operations. 'Machined to crack severely during hot-working.
Hot rolling After melting, casting and conditioning the'slab, the hot rolling operation is in order. The slab is hot rolled to about 0.250" in thickness at a temperature of 1050" C. The reductions in thickness between reheatings and v the reductions per pass through the mill are based upon the-mill capacity and the rate at which the strip loses heat. Rolling is stopped and reheating is necessary when the strip drops in temperature to a dull red heat. At a thickness of about 0.250", the hot rolling is performed at about 950 ,C. When the strip has been finished to about 0.125 or preferably 0.1", the cold rolling operation is in order.
It has been found during the rolling operation that some of the aforesaid materials can be successfully hot.
rolled in the Sendzimir Hot Mill reducing a 1.0" slab to about 0.1" thick in one pass.
Conditioning'prior to cold rolling Any surface imperfections present on the hot rolled strip may be removed prior to thebeginning of the cold rolling operation in the aforesaid manner. The removal of the imperfections will not effect the material. In 7 reality this operation improves the surface of the material for the final cold rolling operation.
Cold rolling This rolling operation is performed at about 575 C.,
and may be considered cold rolling for the reasons that the temperature is below the recrystallization temperature.
It will be understood that cold rolling denotes cold working the alloy at a temperature below the recrystallitemperature.
rolling process, the crystal structure remains unrecrystallized and the crystals are'elongated. Rolling at about 7 575 C. gives the material a regular cold worked appearance and elongates the grains into long'fibered structure. The greater the percentage of cold work, the higher the mechanical properties of the alloy .[tensile strength,
yield trength, hardness, impact strength, etc.]. Cold rolling may be performed to reduce the material to -a relatively thin gage, such, for example, as 0.002 of an inch or thinner.
Removal of oxide coating After rolling the material into strip form of a suitable thickness, it has a naturally formed coating of aluminum and iron oxides upon the surface.
should be stripped from the mold while'still red hot. The hotslab is then placed in a furnace at 1050 C. for about two If it is desired .to. remove this coating for any purpose, lspotwelding';
Cold rolled strip "of a reasonable thickness may ,be formed' and shearejd if warmed. The. exact temperature of warming is dependent. upon the forming configuration and material thickness of the alloy; V
The slabs or sheets. produced by the aforesaid method may be of any desired length andwi'dth and characterized by high tensile strength :and high resistance to.
corrosion .and oxidation at elevated temperatures. This material is. suffi'cientl'y ductile to be readily"worked' or. shape without damage or formed into any desired breakage thereof. Furthermore, it has been found by actual test that the metallic sheets produced in accordance with the present invention are about lighter than stainless steel alloys 'and the physical and chemical characteristics thereof include high tensile strength and high resistance to corrosion and oxidation. .Moreover, creep-rupture tests have proven that the aforesaid ma terial is far superior to some forms of the critical stainless steel alloys now being "widely used. It has been further found that because'of the high electrical resistivity of the aforesaid material, the material is admirably suited for use in heater elements, low temperature furnaces, and other numerous electrical appliances. It has also been found that due to the electrical resistivity and excellent magnetic characteristics of these cold rolled almay be removedby the folsolution by loys, these alloys are well. suited for magnetic applications.
From the foregoing, it will be apparent that 'new and improved ferritic materials and the method of making same has been invented, wherein such materials are characterized by high tensile strength and high resistance to corrosion and oxidation at elevated temperatures, high electrical resistivity, ductile to be readily formed into various forms including thin tape-like strips or sheets and which is well adapted to extrusion.
Obviously many modifications and variations of the present invention are possible in the light of the above teachings. .It is therefore to be understood that Within the scope'of the appended claims the invention may be practiced otherwise than as specifically described.
What is'elaimed as new anddesired to be secured by Letters Parent of the UnitedState's is:
l. The method of making a high temperature and magnetic alloy containing from 10 'to 18% aluminum, up to 5% 'o 'fa'strengthening element and the remainder iron, which consists 'of'meltingthe constituents in a suitable melting apparatus to -form a molten alloy, forming the moltenalloy intoan ingot, controlling the solidification'rateof the molten 'alloy'to produce an ingothaving a fine equiaxed cast grain structure, transferring the ingot from the 'melting apparatus while red hot to a heating apparatus andheat'treating the ingot at a*ternperature of about 1050" C. for a time sufii'cient to uniformly heat the ingot, slow cooling theingot ata rate of about C. per hou r until theingot is substantially at room temperature, removing surface imperfections from the 'ingot, hot Working the ingot into a sheet substantially .250 of an inch thick at a temperature-of about 1050 C. followed by hot working the sheet at a temperature and whichis sufiiciently tough and of 350 C. from a thickness of 0.250 of an inch thick to 'a (thickness of substantially 0.125 of an inch, and thereafter cold working the sheet 'to 'a "predetermined thickness at a temperature of "575 C.
asuitable melting apparatus to jform a molten array, T
fomfring use molten :alloy into an. ingot, controlling the sdlidifica'tionrateof the molten alloy to produce anfin;
got having a fine equiaxed cast grain structure, trans fern'ng the ingot from :the melting apparatus while red hot to a heatingapparatus and .heattreating the ingot 1 at a temperature of about 1050 C. for a time sutficient; to uniformly heat'theingogjs'low cooling the ingot'ajt r t of. about 30, C. Per hour until .the ingot is sub'-.; stantiaIly-jatflrfoom(temperature, removing snrfacei impeifectio' ns from the ingot,- hot working the mgot mtoj."
a sheetfsubstantially "0.25.0" thick at a temperature; of about'l050 C. followed by hot working ,the'sheetlat; a,
temperature of 950 C. from a thickness of 0.250 of I an inch thick to a thickness of substantially 0.125-of an inch,..and thereafter cold working the sheet to..;the
desired thickness at a temperature of about 575. C. 3. The method of making a high temperature and magnetic sheet alloy containing essentially 16% alurninum and up to 5% molybdenum and remainder iron, which consists of melting the constituents in a suitable. melting apparatus to form a molten alloy, forming. the: molten alloy into an ingot, controlling the solidifiea-Y tion rate of the molten alloy to produce an ingot having a line equiaxed cast grain structure, transferring the in-. got from the melting apparatus while red .hot to a :heatn ing apparatus and heat treating the ingot at a temperatu're of about 1050 'C. 'for a time sufiicient to uniformly heat the ingot, slow cooling the ingot at a rate of about 30 C. per hour until the ingot is substantially atroom temperature, removing surface imperfections from .the ingot, hot working the ingot into sheet substantially 0.250 thick at a temperature of ab0ut.l050 C. followed by hot working .the sheet at a temperature of 950 C.
from a thickness of 0.250 of an inch thick to a thickness.
of substantially 0.125 of an inch, and thereafter cold working the sheet to a desired thickness at a temperature of about 575 C. V 4. The method of making a high temperature and."
magnetic sheet alloy containing essentially 16% alumi num, 3.3% molybdenum, and remainder iron, which consists of melting the constituents in a suitable melting. apparatus to "form a molten alloy, forming the molten alloy into an ingot, controlling the solidification rate' of the molten alloy to produce an ingot having aIfine' equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a heating apparatus and heat treating the ingot at a temperature,
of about 1050 C. for a time suflicient to uniformly heat the ingot, slow cooling the ingot at a rate of about 30 C. per hour until the ingot is substantially at'room temperature, removing surface imperfections from the ingot, hot working the ingot into a sheet substantially, 0.250" thick at a temperature of about 1050 C. followed by hot working 'the sheet at a temperature of 950 C. from a thickness of 0.250 of an inch thick tea I thickness of substantially 0.125 of an inch, and thereafter cold working the sheet to a desired thickness at 1 a temperature of about 575 C.
5.1'I'he'method of making a high temperature and magnetic sheet alloy containing essentially .l6% alumi-' num, essentially 2% Mo, essentially 0.3% Ti, andthe remainder iron, which consists of melting the constituents together to form a molten into an ingot, controlling the solidification rate of the molten'alloy to produce aningot having a fine equiaxed 7 cast grain structure, uniformly heating the ingot while the ingot is still red hot toa temperature of 1050 C., j slow cooling the ingot at a rate of about "30 "C. per hour until the ingot is substantially at room temperature, machine working'theingot free of surface imperfections,
alloy, forming the molten alloy I hot working the ingot above the recrystallization temessentially 2% Mo, essentially 0.3% Ti, and the remainder iron, which consists of melting the constituents in a suitable melting apparatus to form a molten alloy, forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a heating apparatus and treating the ingot at a temperature of about 1050 C. for a time sufficient to uniformly heat the ingot, slow cooling the ingot at a rate of about 30 C. per hour until the ingot is substantially at room ternperature, removing surface imperfections from the ingot, hot working the ingot into a sheet substantially 0.250 thick at a temperature of about 1050 C. followed by hot working the sheet at a temperature of 950 C. from a. thickness of 0.250 of an inch thick to a thickness of substantially 0.125 of an inch, and thereafter cold working the sheet to a desired thickness at a temperature of about 575 C.
7. The method of making a high temperature and magnetic sheet alloy containing essentially 16% aluminum, essentially 2% Mo, essentially 0.3% Ti, and the re mainder iron, which consists of melting the constituents in a suitable melting apparatus to form a molten alloy,
forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a heating apparatus and heat treating the ingot at a temperature of about 1050 C. for a time sufilcient to uniformly heat the ingot, cooling the ingot slowly to substantially room temperature, removing surface imperfections from the ingot, hot working the ingot above the recrystallization temperature to a sheet of predetermined thickness, and thereafter cold working the sheet below the recrystallization temperature to a reduced thickness.
8. The method of making a high temperature and magnetic sheet alloy containing essentially 16% aluminum, essentially 2% molybdenum, essentially 0.3% vanadium, and the remainder iron, which consists of melting the constituents together to form a molten alloy, forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, uniformly heating the ingot while the ingot is still red hot to a temperature of 1050" C., slow cooling the ingot at a rate of about 30 C. per hour until the ingot is substantially at room femperature, machine working the ingot free of surface imperfections, hot Workingthe ingot above the recrystallization temperature into a sheet substantially 0.125" thick, and cold working the sheet below the recrystallization temperature to the desired thickness.
9. The method of making a high temperature andmagnetic sheetalloycontaining essentially 16% aluminum, essentially 2% .rnolybdenum, essentially 0.3% vanadium, and, the remainder iron which consists of melting the. constituents in a suitable melting apparatus to form a'molten alloy, formingthe molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a heating apparatus'and heat treating the ingot at a temperature of. about-1050 C. for a time sufficient to uniformly heat the ingot, slow cooling the ingot at a rateof about 30 C. per hour until the ingot is substantially at room temperature, removing surface imperfections from the ingot, hot-working the ingot into 3 :sheet "substantially 0.250" 'thick' at a temperature of recrystallization temperature '75 working the ingot into a sheet substantially 0.250'.-'
10 about 1050" C. followed'by hot working the sheet at a temperature of 950 an inch thick to a thickness of substantially 0.125 of an inch, and thereafter cold Working the sheet to a desired thickness at a temperature of about 575 C.
10. The method of making a magnetic sheet alloy containing essentially 16% aluminum, essentially 2% molybdenum, essentially 0.3% vanadium, and the remainder iron, which consists of melting the constituents in a suitable melting apparatus to form a molten alloy, forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus while red hot to a the ingot at a temperature of about1050 C. for a time sufficient to uniformly heat the ingot, cooling the ingot slowly to substantially room temperature, removing surface imperfections above the recrystallization temperature to a predetermined thickness, and thereafter cold working the.
the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot fromthe melting apparatus while red hot to a heating apparatus and heat treating, the ingot at a temperature of about 1050 C. for a time sufficient to uniformly heat the ingot, slow cooling the ingot at a rate of about 30 C. per hour until theingot is substantially at room temperature, removing surface imperfections from the ingot, hot working the ingot into a sheet substantially 0.250" thick at at temperatures of about 1050 C. followed by hot working the sheet at a temperature of 950 C. from a thickness of 0.250 of an inch thick to a thickness of substantially 0.125 of an inch, and thereafter cold working the sheet to the desired thickness at a temperature of about 575 C.
12. The method of making a high temperature and magnetic sheet alloy containing essentially 16% aluminum, essentially 1% titanium, and the remainder iron, for solid solution strength at high elevated temperatures,
which consists of ,melting the constituents together to' forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy form a molten alloy,
above the recrystallization temperature into a sheet substantially 0.125. thick, and cold working the sheet below the recrystallization temperature to a desired thickness.
13. The method of making a high temperature and magnetic sheet alloy containing essentially 16% aluminum, essentially 1% titanium, and the remainder iron for solid solution'streng'th at high elevated temperatures, 1
which consists of melting the constituents in a suitable melting apparatus to form a molten alloy, forming the molten alloy into aningot, controlling the-solidification rateof the molten alloy. to produce an ingot having a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus While red hot to a heating apparatus and heat treating the ingot at a temperature of about 1050 C. for a time suflicient to uniformly heat theingot, 'slow cooling the ingot at a rate of about 30 C. per hour until the ingot is substantially at room temperature, removing surface imperfections from the ingot, hot
C. from a thickness'of 0.250 of high temperature and heating apparatus and heat treating from the ingot, hot working the ingot thick at a temperature of about -1050 working the sheet at a temperature thickness of 0.250 of anjnch thickto stantially 0.125 of an inch, and thereafter cold working the sheet to'a desired thickness 'ata temperature ofa'bout 575 C. V 4
"142The method of making a hightemperature and magnetic sheet alloy containing essentially 16% aluminum, essentially 1% for solid solution strengthening at high elevated temperatures, which consists ofme'lting the constituents in a suitable melting apparatus to form a molten alloy, forming the molten alloy into an ingot, controlling .the solidification rate of the molten alloy to produce aningot'hav'ing a fine equiaxed cast grain structure, transferring the ingot from the melting apparatus while'red hot to a heating apparatus and heat treating the ingot at a temperature of about 1050 C. for a time sutlicient to uniformly heat the ingot, cooling the ingot slowly to substantially ro'omtemperature, removing surface imperfections from the ingot, hot working the ingot ture to a sheet of predetermined thickness, and thereafter cold working the sheet below the recrystallization temperaturetoareduced-thickness..
15. The method of making a ferritic high temperature and magnetic alloy containing from 10 to 18%. aluminum," up to 5% of a strengthening element and the remainder'iro'n, which consists of melting and refining the C. followed by hot iron ina magnesium oxide crucible usinga vacuumor controlled atmosphere, charging the melt with said element' and aluminum, allowing suflicient time to cause thorough mixing, pouring the melt into a mold and allowing it to solidify underhelium or suitable inert atmosphere at a pressure of 5 mm. into a slab substantially one inch thick, stripping "the slab from said mold while the slab is substantially red hot, heat treating the slab at 1050 C. for about two hours, cooling slab to about room temperature at-a rate of substantially 30 C. per hour, machine working the slab to remove surface imperfections, hot working the. slab into a sheet substantially 0.250 thick at a temperature of about I050 C. followed by hot working the sheet at about 950 C. to a thicknessv of 0.125", and thereafter cold working the sheet to a desired thickness at about 575C. I
'16. The method 'o'fmaking a high temperaturea'lumihum-iron base alloy containing to 18% aluminum and up to 5% of a strengthening element and the remainder iron, which consists of melting the constituents together to form a' molten alloy, forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy guniforml y'heating the ingotto a temperature of 105%)"0, siow 'cooling the ingot at a rate of about 30'- C.
perhour until the ingot is substantially at room temperaj ture, removing surface imperfectionslfrom the ingot, hot
of predetermined thickness Working the ingot into a sheet at atemperature-of about 950 at a temperature of about 575 'C., cold wor'kingithesheet C. to' a reduced thickness,
immersing the cold worked sheet into a hot agitated 20% solution of-NaOH by weight, washing the sheet in water, immersing the sheet in an agitated HNO solution by volume at room temperature, and thereafter washing the sheetin clear water to remove all and-theoxidecoa'ting formed during .rolling.
of 950. C. from aj a thickness of sub-v titanium, and the remainder iron t to above the recrystallization tempera- '50 a fine equiaxed .grains'tructraces of thejHNO;
17. method'ofmaking high temperature and mag 3 netic aluminumeiron base alloys containing 10 to 18% aluminum, 3.3% {molybdenum and the balance essentially iron into sheet materiaL-which consists of melting 1 the-eonstituentsin a melting apparatus to form an alloy melt, 'forming the melt into. a slab substantially 1' inch thijckjn a cera mi'c mold, stripping .the mold while the-slab :is, red hot, heat treating the, slab at a temperature of; 1050? C. for about 2 hours, slow cooiing "the slab "to substantially room temperature (at .a C. per hour, removing surface imperfection rate of 30 slab from the from, the slab, hot reducing th e slab "at a temperature, of 1050? C into sheet m terial substantially 0 .250'ofah9 inch thick, hot reducing the sheet material .to a thickness of substantially 0.125 of an inch thicka't'a temperature 6595-0 0;, and thereafter coldreducingthe sheet a't al temperature of about 575 C. to a desired thickness...
18. The method of making 'a high temperature, and,
magnetic alloy containing from 10 to 18% aluminum, up to 5% of a strengthening element and 'the remainder,
iron, which consists of melting the constituents togethen thereafter.
said alloy being subjected'to a.
0. followed by coolingfat a a high temperature and. comprises producing a aluminum, up the remaihder treating said casting to a temperature within the single phase solid solution region, rapidly cooling the casting to a temperature within taining the casting at said last named temperature for a the multi-phase region, and mainperiod of time sufiicient to precipitate at least one other phase.
20. The method of making a high temperature and magnetic .multi-phase alloy which comprises producing .a melt consisting essentially of 10 to 18% to 5% of a strengthening element, and iron, casting said melt and solidifying the the remainder aluminum, up
same to ,pro-. duce a fine-equiaxed cast grain structure, hot working the casting above the recrystallization temperature'to a. desired shape, solution heat treating said shape to a temperature Within the single phase multi-phase region,
precipitate at least one other phase.
21. The method of making -a high temperature and melt consisting'essential'ly of 10 to 18% and solidifying the same to produce a fin grain structure, solution heat treating said multi-phase region, and maintaining the, casting at said' cipitate at least'one other phase.
22. The method of claim 21 wherein the strengthening titanium." V 23. A high temperature and magnetic ferritic alloy consisting essentially of 10 to 18% elements include 3.3% molybdenum and 0.3%
strengthening element, iron, said alloy being fine grain size with disordered atomic structure.
24. A high temperature and magnetic ferritic alloy consisting essentially of 1010 18% aluminum, up to 5% molybdenum, and the remainder essentially iron, said i by a recrystallized fine grain alloy being characterized size with disordered atomic structure.
25. A hightempera'ture and magnetic ferritic alloy aluminum, up to 5% r titanium, and the remainder essentially iron, said alloy being characterized by a recrystallized fine grain size consisting essentially of 10 to 18% with disordered atomic structure.
26. The method of making a high temperature and from 10 to 18% aluminum, element, and the remainder essentially iron, which consists of melting the constituents ,1
magnetic alloy containing up to 5% of strengthening together in a suitable melting apparatus to form a molten solid solution region,fl rapidly cooling the shape to a temperature within the. 1
and maintaining the shape atxsaidfi' last named temperature fora period of time sufiicient to.
e-equiaxed cast 1 casting to a-f. temperature Within the single phase solid solution region, 1 rapidly cooling the casting .to a temperature within the f aluminum, up to 5% and the remainder essentially characterized by a recrystallized. V
alloy, forming the molten alloy into an ingot, controlling the solidification rate of the molten alloy to produce a fine equiaxed cast grain structure, annealing the solidified ingot at a temperature of about 1050 C. to eliminate stresses therein, cooling the ingot slowly to substantially room temperature 'to prevent occurrence of further stresses therein, hot working the ingot above the recrystallization temperature to a sheet of predetermined thickness, and thereafter cold working the sheet below the recrystallization temperature to a desired thickness.
27. A method for making a high temperature magnetic ferritic casting which comprises producing a melt consisting essentially of 10 to 18% aluminum, up to 5% of strengthening element, and the remainder essentially iron, casting said melt and controllably solidifying the same to produce a fine equiaxed cast grain structure, annealing said casting at a temperature of about 1050 C. to eliminate stresses therein, and thereafter slowly cooling the casting while avoiding the occurrence of further stresses therein.
References Cited in the file of this patent UNITED STATES PATENTS 1,915,158 Fahrenwald June 20, 1933 1,972,248 Smith Sept. 4, 1934 2,230,531 Digby Feb. 4, 1941 2,339,842 Digby Jan. 25, 1944 2,523,917 Payson Sept. 26, 1950 2,624,669 Crafts Jan. 6, 1953 FOREIGN PATENTS 370,012 Great Britain Apr. 1, 1932 409,355 Great Britain Apr. 30, 1954 OTHER REFERENCES Metal Progress, vol. 35, No. 6 (1939), G. I. Comstock, page 576.
Claims (1)
1. THE METHOD OF MAKING A HIGH TEMPERATURE AND MAGNETIC ALLOY CONTAINING FROM 10 TO 18% ALUMINUM, UP TO 5% OF A STRENGTHENING ELEMENT AND THE REMAINDER IRON, WHICH CONSISTS OF MELTING THE CONSTITUENTS IN A SUITABLE MELTING APPARATUS TO FORM A MOLTEN ALLOY, FORMING THE MOLTEN ALLOY INTO AN INGOT, CONTROLLING THE SOLIDIFICATION RATE OF THE MOLTEN ALLOY TO PRODUCE AN INGOT HAVING A FINE EQUIAXED CAST GRAIN STRUCTURE, TRANSFERRING THE INGOT FROM THE MELTING APPARATUS WHILE RED HOT TO A HEATING APPARATUS AND HEAT TREATING THE INGOT AT A TEMPERATURE OF ABOUT 1050*C. FOR A TIME SUFFICIENT TO UNIFORMLY HEAT THE INGOT, SLOW COOLING THE INGOT AT A RATE OF ABOUT 30* C. PER HOUR UNTIL THE INGOT IS SUBSTANTIALLY AT ROOM TEMPERATURE, REMOVING SURFACE IMPERFECTIONS FROM THE INGOT, HOT WORKING THE INGOT INTO A SHEET SUBSTANTIALLY 0.250 OF AN INCH THICK AT A TEMPERATURE OF ABOUT 1050* C. FOLLOWED BY HOT WORKING THE SHEET AT A TEMPERATURE OF 950*C. FROM A THICKNESS OF 0.250 OF AN INCH THICK TO A THICKNESS OF SUBSTANTIALLY 0.125 OF AN INCH, AND THEREAFTER COLD WORKING THE SHEET OF A PREDETERMINED THICKNESS AT A TEMPERTURE OF 575*C.
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|---|---|---|---|
| US448398A US2859143A (en) | 1954-08-06 | 1954-08-06 | Ferritic aluminum-iron base alloys and method of producing same |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US448398A US2859143A (en) | 1954-08-06 | 1954-08-06 | Ferritic aluminum-iron base alloys and method of producing same |
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| US2859143A true US2859143A (en) | 1958-11-04 |
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|---|---|---|---|
| US448398A Expired - Lifetime US2859143A (en) | 1954-08-06 | 1954-08-06 | Ferritic aluminum-iron base alloys and method of producing same |
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| US (1) | US2859143A (en) |
Cited By (12)
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|---|---|---|---|---|
| US2960401A (en) * | 1958-12-30 | 1960-11-15 | William J Buehler | Precipitation-hardenable, aluminum-containing iron base alloy |
| US2961360A (en) * | 1958-12-01 | 1960-11-22 | Gen Electric | Magnets having one easy direction of magnetization |
| US2987394A (en) * | 1959-03-25 | 1961-06-06 | John J Mueller | Iron-aluminum base alloys |
| US3210221A (en) * | 1961-05-29 | 1965-10-05 | Lasalle Steel Co | Steel products and method for producing same |
| US3303561A (en) * | 1962-03-02 | 1967-02-14 | Cabane Gerard | Process for the preparation of an ironaluminum alloy |
| US4033791A (en) * | 1975-01-22 | 1977-07-05 | Polska Akademia Nauk, Instytut Fizyki | Magnetostrictive alloy |
| US4130448A (en) * | 1975-06-12 | 1978-12-19 | Inoue-Japax Research Incorporated | High-permeability magnetic alloy |
| US4146391A (en) * | 1976-10-07 | 1979-03-27 | Inoue-Japax Research Inc. | High-permeability magnetic material |
| US4316743A (en) * | 1973-10-29 | 1982-02-23 | Tokyo Shibaura Electric Co., Ltd. | High damping Fe-Cr-Al alloy |
| US4419130A (en) * | 1979-09-12 | 1983-12-06 | United Technologies Corporation | Titanium-diboride dispersion strengthened iron materials |
| CN104264068A (en) * | 2014-09-09 | 2015-01-07 | 董春年 | Method for processing mining drill |
| CN104313496A (en) * | 2014-09-09 | 2015-01-28 | 董春年 | Drilling head for mining |
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| US1915158A (en) * | 1929-07-06 | 1933-06-20 | Southern Wheel Company | Car wheel |
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| US2230531A (en) * | 1936-07-03 | 1941-02-04 | Everard Tuxford Digby | Heat treatment of copper-chromium alloy steels |
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| US1915158A (en) * | 1929-07-06 | 1933-06-20 | Southern Wheel Company | Car wheel |
| GB370012A (en) * | 1931-01-01 | 1932-04-01 | British & Dominions Feralloy L | Manufacture of alloys of iron and aluminium |
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Cited By (13)
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|---|---|---|---|---|
| US2961360A (en) * | 1958-12-01 | 1960-11-22 | Gen Electric | Magnets having one easy direction of magnetization |
| US2960401A (en) * | 1958-12-30 | 1960-11-15 | William J Buehler | Precipitation-hardenable, aluminum-containing iron base alloy |
| US2987394A (en) * | 1959-03-25 | 1961-06-06 | John J Mueller | Iron-aluminum base alloys |
| US3210221A (en) * | 1961-05-29 | 1965-10-05 | Lasalle Steel Co | Steel products and method for producing same |
| US3303561A (en) * | 1962-03-02 | 1967-02-14 | Cabane Gerard | Process for the preparation of an ironaluminum alloy |
| US3386819A (en) * | 1962-03-02 | 1968-06-04 | Commissariat Energie Atomique | Iron-aluminum alloys containing less than 84% by weight iron and an additive and process for preparing the same |
| US4316743A (en) * | 1973-10-29 | 1982-02-23 | Tokyo Shibaura Electric Co., Ltd. | High damping Fe-Cr-Al alloy |
| US4033791A (en) * | 1975-01-22 | 1977-07-05 | Polska Akademia Nauk, Instytut Fizyki | Magnetostrictive alloy |
| US4130448A (en) * | 1975-06-12 | 1978-12-19 | Inoue-Japax Research Incorporated | High-permeability magnetic alloy |
| US4146391A (en) * | 1976-10-07 | 1979-03-27 | Inoue-Japax Research Inc. | High-permeability magnetic material |
| US4419130A (en) * | 1979-09-12 | 1983-12-06 | United Technologies Corporation | Titanium-diboride dispersion strengthened iron materials |
| CN104264068A (en) * | 2014-09-09 | 2015-01-07 | 董春年 | Method for processing mining drill |
| CN104313496A (en) * | 2014-09-09 | 2015-01-28 | 董春年 | Drilling head for mining |
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