Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C1/00—Making non-ferrous alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C1/00—Making non-ferrous alloys
  • C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase

Definitions

• the invention relates to the field of forming metal alloys in the semi-solid state, that is to say at a temperature between the solidus and the liquidus of the alloy, having in this semi-solid state, thixotropic properties. .
• This forming in the semi-solid state can be a “rheofo ⁇ nage”, a process in which a mass of semi-solid metal alloy of any shape, which is immediately formed, is produced by pouring liquid metal under specific conditions. by forging, extrusion or pressure injection, derived from die casting.
• thixoforming a process more widely used industrially, in which a solid semi-finished product is prepared, for example a toilet, which is heated this semi-finished product or a piece from this semi-finished product in the state semi-solid and that it is shaped by spinning, forging or injection under pressure.
• the metal must have solidified with a particular structure, either a globular structure, which can be obtained either by mechanical stirring as in the first patents of Pr FLEMINGS, or by stirring electromagnetic, as for example in the patents ITT-ALUMAX US 4434837 and US 4457355, or the patents ALUMINUM PECHTNEY EP 0351327 and EP 0439981, that is to say a very refined equiaxed dendritic structure, allowing a globalization with reheating in the semi-solid state, which 'is obtained by adding to the alloy a grain refiner and by special casting conditions.
• a globular structure which can be obtained either by mechanical stirring as in the first patents of Pr FLEMINGS, or by stirring electromagnetic, as for example in the patents ITT-ALUMAX US 4434837 and US 4457355, or the patents ALUMINUM PECHTNEY EP 0351327 and EP 0439981, that is to say a very refined equiaxed dendritic
• the level of gassing of the metal can be estimated on the liquid metal by a density measurement called dgo- It consists of taking a small amount of liquid metal using a cup, introducing it under a vacuum bell where it will solidify slowly under a residual pressure of 80 hPa and measure its density using a precision balance. The less gas in the liquid metal, the higher this density.
• the specifications for thixotropic billets recommend minimum values of the density d S o; for example, for an alloy with 7% silicon and 0.6 magnesium, we set d 80 > 2.60 for a theoretical density of 2.67, i.e. a volume porosity rate of the sample solidified under 80 hPa , defined by the ratio (d ⁇ - d 80 ) / dt h ⁇ 2.62%.
• the inventors have found, unexpectedly, that in the case of semi-solid forming, non-compliance with these specifications, that is to say a higher level of gassing, not only does not entail the disadvantages expected on the metallurgical health of the parts produced, but led to a very significant reduction in the apparent viscosity at high shear of the piece heated in the semi-solid state, leading on the contrary to a better quality of the parts forged or injected under pressure, which are free of any porosity, even after subsequent heat treatment.
• the elongation of the finished parts is increased without decreasing the breaking strength and the elastic limit, and the dispersion of the elongations is significantly reduced.
• this metallic mass is poured in the semi-solid state and shaped immediately to obtain the finished part.
• thixoforming it is cast in the solid state in the form of a semi-finished product, for example a forge blank or a spinning billet, or a toilet which will be cut into cylindrical pieces for pressure injection. .
• the invention also relates to a mass of metal alloy for forming in the semi-solid state, having, after being cooled in ambient air from a temperature corresponding to a rate of water fraction between 30 and 70%, up to ambient temperature, a volume porosity rate p, measured by image analysis at mid-distance between the center of the mass and its external surface, between 2 and 20%, and preferably between 3 and 8%.
• the mass is obtained directly in the semi-solid state from the casting.
• the metaUic mass comes from the solid semi-finished product obtained during casting (blank, rod or slug), reheated in the solid-state to a temperature corresponding to a Hquide fraction rate between 30 and 70%.
• t 0.16 D 2
• D being the diameter of the cylinder in cm.
• the invention applies in particular to aluminum alloys and, more particularly to AISi alloys containing from 3 to 30% of Si and, optionally, other addition elements such as copper or magnesium.
• the manufacture of thixotropic metal according to the invention is carried out in the usual manner, for example, for thixoforming bûlettes, by vertical pouring in charge with pseudotoric stirring by means of Three-phase linear motors with sliding fields according to the process described in patents EP 0351327 and EP 0439981.
• the metallic masses can also be produced by mechanical stirring during drying, by using static mixer-coolers or by other methods of electromagnetic stirring as described in US patents 4434837 and US 4457355. They can finally be produced without stirring from a metal containing a grain refiner (for example TiB 2 for aluminum alloys) with special casting conditions , as described for example in patent application WO 96/732519.
• a grain refiner for example TiB 2 for aluminum alloys
• a fixed quantity of a gas soluble in the bath and not capable of reacting with it is introduced into the liquid metal, ensuring a fine and homogeneous dispersion of the gas bubbles.
• the most suitable gas for this purpose is hydrogen, which can optionally be mixed with a neutral gas such as nitrogen or argon. It is also possible to use fluxes based on hydrated salts as a source of hydrogen.
• Another means consists in using to treat the hydrogen the treatment pocket which is generally placed between the holding furnace and the casting site, for example a pocket provided with a gas injector with a rotary nozzle, such as the ALPUR pocket. ® sold by PECHTNEY RHENALU.
• a neutral gas such as argon or nitrogen
• a certain proportion of hydrogen will be mixed with the neutral gas.
• a static gas bubbling device can also be used.
• the gassing of the metal can be facilitated by maintaining during the treatment a pressure higher than atmospheric pressure.
• the injection of the gas or gas mixture is preferably done in continuous mode.
• the level of gassing of the liquid metal can be assessed by the density measurement d 80 described above.
• d 80 the density measurement of an alunrinium alloy with 7% Si and 0.6% Mg
• the theoretical density of which in the absence of porosity is 2.67
• this rate a must be greater than 3%, and preferably 4%, and it is only above 50% that there is a risk of seeing harmful porosities appear in the forged part. or injected under pressure. However, it is best to keep a below 25%.
• the starting semi-finished product is a piece cut from a cylindrical stick of diameter D
• an image analysis method is used which consists of taking samples approximately halfway from the geometric center of the mass of alloy and its external surface, that is to say in the case of a mass of cylindrical shape such as a piece cut from a stick, half-height and half-radius, then to carry out an image analysis on micrographs carried out on a polished face without chemical attack of the sample.
• the white parts represent the globules, the gray parts the eutectic and the black parts the porosities.
• the resolution must be such that the pore size> 10 ⁇ m is taken into account.
• the measurement is repeated on at least 25 fields of the sample distributed over 360 °, until the average of the surface fractions stabilizes.
• viscosity reduction properties appear as soon as the volume porosity rate exceeds 2% and that above 20%, porosities appear in the forged or pressure injected parts. These rates are actual rates of gaseous porosity in the metal at the stage of its industrial use by spinning, forging or die-casting.
• the main result hey to the use of metal according to the invention consists in the spectacular lowering of the apparent viscosity of the metallic mass in the semi-solid state, all the other parameters being similar, in particular the microstructure.
• the rheological test which measures this apparent viscosity is a penetration test consisting in measuring the resistance to deformation F of the metallic mass in the semi-solid state, compressed by a tool at constant speed after a stroke of determined length. .
• F / F s ratio of more than 40%.
• the alloy treated with pure argon had a density d 8 o of 2.64 corresponding to a volume rate of porosity a of 1.2%, while the alloy treated with the argon-hydrogen mixture at the lowest flow rate had a density d 8 o of 2.52, corresponding to a porosity rate a of 5.6%, and that treated with the mixture at a higher flow rate a density d 8 o of 2.23, ie a porosity rate a of 16.5%.
• 10 plots of height 110 mm were taken from an alloy strip treated with pure argon and 10 plots from each of the alloy strips treated with an argon-hydrogen mixture at two flow rates, each plot corresponding to the quantity of metal required. upon pressure injection of a control piece. The plots have been reheated at a temperature of 578 ° C for 9 min in an induction oven to reach a rate of 50% hquide fraction.
• the volume porosity p (in%) was measured by image analysis. The observations were made at mid-height of the plot on areas of 110 mm 2 centered respectively on the plot axis, at mid-radius and 10 mm from the edge. For each zone examined, 3 groups of 8 measurements were made, each offset by an angle of 120 °, so as to eliminate the bias due to possible segregation. The images of the micrographs obtained were analyzed, using the KONTRON BBAS analysis software, with a resolution ⁇ 10 ⁇ m, the porosities corresponding to the black parts. The results were as follows:

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• Engineering & Computer Science (AREA)
• Mechanical Engineering (AREA)
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• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Manufacture Of Alloys Or Alloy Compounds (AREA)
• Superconductors And Manufacturing Methods Therefor (AREA)
• Inorganic Compounds Of Heavy Metals (AREA)
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• Battery Electrode And Active Subsutance (AREA)
• Credit Cards Or The Like (AREA)
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• Treatment Of Steel In Its Molten State (AREA)
• Compositions Of Oxide Ceramics (AREA)
• Sampling And Sample Adjustment (AREA)
• Moulds For Moulding Plastics Or The Like (AREA)
• Investigating And Analyzing Materials By Characteristic Methods (AREA)
• Inks, Pencil-Leads, Or Crayons (AREA)
• Pens And Brushes (AREA)
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• 1996
  • 1996-02-01 FR FR9601442A patent/FR2744384B1/fr not_active Expired - Fee Related
• 1997
  • 1997-01-28 EP EP97901684A patent/EP0877658B1/de not_active Expired - Lifetime
  • 1997-01-28 PL PL97327973A patent/PL182441B1/pl unknown
  • 1997-01-28 HU HU9901125A patent/HUP9901125A3/hu unknown
  • 1997-01-28 AT AT97901684T patent/ATE183418T1/de not_active IP Right Cessation
  • 1997-01-28 SK SK1031-98A patent/SK103198A3/sk unknown
  • 1997-01-28 CA CA002244145A patent/CA2244145C/fr not_active Expired - Fee Related
  • 1997-01-28 KR KR1019980705793A patent/KR19990082071A/ko not_active Withdrawn
  • 1997-01-28 CZ CZ982422A patent/CZ242298A3/cs unknown
  • 1997-01-28 DE DE69700431T patent/DE69700431T2/de not_active Expired - Fee Related
  • 1997-01-28 NZ NZ326832A patent/NZ326832A/xx unknown
  • 1997-01-28 ES ES97901684T patent/ES2137775T3/es not_active Expired - Lifetime
  • 1997-01-28 BR BR9707338A patent/BR9707338A/pt not_active IP Right Cessation
  • 1997-01-28 WO PCT/FR1997/000163 patent/WO1997027963A1/fr not_active Ceased
  • 1997-01-28 DE DE0877658T patent/DE877658T1/de active Pending
  • 1997-01-28 AU AU15500/97A patent/AU712356B2/en not_active Ceased
  • 1997-01-28 JP JP9527353A patent/JPH11504682A/ja active Pending
  • 1997-01-28 IL IL12478397A patent/IL124783A/xx not_active IP Right Cessation
  • 1997-02-03 US US08/792,300 patent/US5980660A/en not_active Expired - Fee Related
  • 1997-03-03 TW TW086102700A patent/TW326007B/zh active
• 1998
  • 1998-07-31 NO NO983538A patent/NO983538L/no not_active Application Discontinuation
  • 1998-07-31 IS IS4816A patent/IS4816A/is unknown

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