Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
  • B22F3/006—Amorphous articles
  • B22F3/007—Amorphous articles by diffusion starting from non-amorphous articles prepared by powder metallurgy
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C45/00—Amorphous alloys

Definitions

• the invention relates to a method for producing a metallic body using an amorphous alloy, in particular a metallic glass, formed from at least two predetermined starting elements or compounds, in which method a preliminary product with respectively adjacent layers of the starting elements or compounds with the respective layer thickness of at most 0.001 mm is created, then an intermediate with the non-crystalline structure is formed in a rapid diffusion reaction at a predetermined, relatively low temperature from the intermediate and finally the intermediate is further processed to the metallic body.
• metallic glasses Materials referred to as “metallic glasses” are generally known (cf. for example "Zeitschrift für Metallischen”, volume 69, 1978, number 4, pages 212 to 220 or “ Elektrotechnik und Maschinenbau", 97th year, September 1980, number 9, Pages 378 to 385). These materials are generally special alloys, which are made from at least two predetermined starting elements or compounds, also referred to as alloy partners, by means of special Ver drive are manufactured. These special alloys have a glass-like, amorphous structure instead of a crystalline one and therefore have properties or combinations of properties that are superior to those of crystalline metallic materials.
• Metallic glasses can be characterized in particular by high wear and corrosion resistance, great hardness and tensile strength with good ductility as well as special magnetic properties.
• metallic glasses have generally been produced by rapid quenching from the melt.
• this method requires that at least one dimension of the material be less than about 0.1 mm.
• Such a diffusion reaction is generally also referred to as anomalous, rapid diffusion.
• Certain energetic requirements must be met for such a reaction (see, for example, Physical Review Letters ", vol. 51, no. 5, August 1983, pages 415 to 418 or" Journal of Non-Crystalline Solids ", vol. 61 and 62, 1984, pages 817 to 822), in particular an exothermic reaction between the two alloy partners.
• the fast diffusion less than 0.001 mm thick layers of the alloying partners were alternately stacked and the thus formed sandwich-like precursor in the V learn typical temperatures between 100 and 300 ° C heated, whereby an intermediate product is formed as a semi-finished product with a thin layer of the non-crystalline structure of the metallic glass. Then this semi-finished product can be processed from the very thin metallic glass to a metallic body as an end product in a known manner.
• the object of the present invention is to design the method mentioned at the outset in such a way that metallic bodies with a relatively extensive shape and dimension can be produced on an industrial scale using amorphous alloys, in particular metallic glasses.
• this object is achieved in that firstly a starting product from a predetermined number by means of a bundling or layering technique is assembled of mutually adjacent individual parts of the respective starting elements or compounds and that then from this starting product duren least one querroughsvermindernde V ER- forming treatment the preliminary product with the predetermined layer thicknesses of the starting elements or compounds created.
• the metallic glass to be produced should have an average composition A x B y , where A and B denote, for example, metallic starting elements and x and y atomic percentages.
• a and B denote, for example, metallic starting elements and x and y atomic percentages.
• commercially available foils of metals A and B with thicknesses between 0.001 mm and 1 mm, preferably between 0.01 and 0.1 mm are used.
• the later average composition of alloy AB is determined via the ratio of the thickness of foils A and B.
• a foil of metal A or B it is also possible to use a plurality of foils of a metal which are layered one on top of the other in order to set the correct layer thicknesses of the respective metal.
• These films are now, after they have been suitably layered, deformed to thicknesses between 0.00005 and 0.001 mm, preferably between 0.0001 and 0.0005 mm, since the diffusion lengths at the available temperatures, which are known to be below the crystallization temperature of the respective metallic glass AB are very small.
• the degree of deformation required during the deformation corresponds to the ratio of the starting foil thickness to the layer thickness desired for the diffusion annealing.
• the bundling technique then depends on the required degree of deformation and the desired deformation of the starting product. Multiple bundling may be appropriate.
• the first bundling can be carried out either by alternately stacking appropriately cut foils of metals A and B or by coiling the superimposed foils together. In the latter case, the winding can be either oval or circular.
• These film bundles can thus consist of any number of double film layers, taking into account the initial thickness of the films and the desired final thickness of the bundle after the deformation. Typical values are between 50 and 500 layers.
• the film bundles are then advantageously deformed into a suitable envelope, e.g. made of steel or copper.
• Bundling by alternating stacking or oval winding of the foils is particularly suitable for producing a sheet of metallic glass.
• the deformation here is advantageously carried out by rolling.
• the shell of the preliminary product thus produced can be ent mechanically or chemically removed after the deformation.
• Bundling by circular winding is suitable for producing a wire or rod-shaped intermediate body from the metallic glass.
• the bundle of films with the casing, which forms the starting product is deformed by hammering, wire drawing or profile rolling to the desired diameter of the preliminary product to be produced.
• Non-circular profiles can also be produced in this way.
• a second bundling step may follow, with which the desired shape of the intermediate product can then also be produced leaves.
• Wires or rods can be in two th bundling step either according to the above-mentioned technique by circular winding or aeer by bundling the wires produced in the first bundling step in a sheath and suitable deformation.
• the film bundle produced in a first bundling step is placed on a thin pipe, e.g. made of steel, wound up and then inserted into a second tube as a sleeve.
• the deformation to the preliminary product is then carried out by tube drawing or tube hammers.
• the cladding tubes can be removed mechanically or chemically after completion of the deformation.
• the conversion of this preliminary product to the intermediate product takes place in a known manner by means of a suitable temperature treatment using the anomalous, rapid diffusion (cf. the cited references “Phys. Rev. Lat. "Or” J.Non-Cryst.Sol. "). It should be noted that the finer the structure, the lower temperatures or the shorter glow times are sufficient for the complete conversion.
• the annealing temperature must in any case be below the crystallization temperature of the metallic glass in a known manner.
• one or both partners can also consist of a connection, in particular an alloy of several elements.
• B is listed in FeNi.
• the above method can be modified so that the non-deformable partner is added in powder form.
• the powder is applied to the film of the deformable partner, for example sprinkled on or sprayed on, inserted or rolled between two corresponding films.
• a corresponding example is FeNi-B, where the boron is not deformable.
• Ni and Zr foils are placed on top of one another and rolled up into an oval bundle, which is then deformed in a steel jacket by rolling.
• the total The thickness is reduced from 10 mm to 0.5 mm.
• the thickness of the individual foils is reduced to approx. 0.0012 mm.
• N ow is the steel casing removed by chemical etching, for example with HC1.
• the Ni-Zr composite sheets are then bundled in a steel jacket 19-fold in a second bundling step and are also deformed in this by rolling.
• the overall thickness is again reduced from 10 mm to 0.5 mm.
• the resulting film package which serves as a preliminary product, is then 0.25 mm thick, 10 mm wide and approx.
• the individual foils are between 0.0001 and 0.0005 mm thick. Annealing this intermediate to form the intermediate at temperatures between 180 ° C and 400 ° C, preferably between 250 ° C and 350 ° C for times between 2 to 100 hours then leads to the formation of the amorphous Ni-Zr. The formation of this amorphous state can be followed by X-ray examinations.
• the double layer of Ni and Zr is rolled up according to the embodiment I to a spiral with about 200 turns, which is then deformed in a round steel jacket by hammering and wire drawing.
• the overall diameter is reduced from 15 mm to 0.6 mm.
• the steel jacket is then removed by etching with HC1.
• the thickness of the individual foils has been reduced to approx. 0.001 mm.
• 91 of the resulting composite film wires are bundled in a steel jacket with an outer diameter of 8 mm and deformed again to 1.2 mm by hammering and wire drawing. After the steel sheath has been removed, 0.8 mm thick Ni-Zr wires from preliminary products remain. These wires can then react to the metallic glass in an annealing treatment corresponding to exemplary embodiment I.
• the metallic body to be produced in the end product was an amorphous, i.e. non-crystalline structure, in particular that of a metallic glass.
• the method according to the invention can also be particularly advantageously provided for the production of microcrystalline materials by way of the amorphous state. Accordingly, intermediates from e.g. Nd-Fe-B alloys are first produced in amorphous form according to the invention. This alloy is then crystallized in a subsequent annealing treatment. The resulting microcrystalline structure has excellent hard magnetic properties (see, for example, "Applied Physics Letters", vol. 44, no. 1, Jan. 1984, pages 148 and 149).
• the starting product can also be formed by bundling rods or wires of the two starting elements or connections.
• the other starting element or the other starting alloy can - in solid form as a wire or rod or also in Powder form available.
• a wire-shaped or rod-shaped output element or a corresponding connection can also be assumed, which is provided with a jacket-shaped layer made of the at least one further element or the at least one further connection.
• Corresponding bundling techniques suitable for these methods are generally known, for example, from superconductor technology.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Mechanical Engineering (AREA)
• Materials Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Manufacturing & Machinery (AREA)
• Pressure Welding/Diffusion-Bonding (AREA)
• Metal Rolling (AREA)
• Wire Processing (AREA)
• Powder Metallurgy (AREA)

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• 1984
  • 1984-05-16 DE DE19843418209 patent/DE3418209A1/de not_active Withdrawn
  • 1984-12-17 EP EP84115569A patent/EP0162143B1/fr not_active Expired - Lifetime
  • 1984-12-17 DE DE8484115569T patent/DE3482046D1/de not_active Expired - Lifetime
• 1985
  • 1985-05-07 US US06/731,507 patent/US4578123A/en not_active Expired - Fee Related
  • 1985-05-15 JP JP60103631A patent/JPS619535A/ja active Granted

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