EP0841406A1 - Verfahren zum Formen halbfester Metalle - Google Patents

Verfahren zum Formen halbfester Metalle Download PDF

Info

Publication number
EP0841406A1
EP0841406A1 EP97119554A EP97119554A EP0841406A1 EP 0841406 A1 EP0841406 A1 EP 0841406A1 EP 97119554 A EP97119554 A EP 97119554A EP 97119554 A EP97119554 A EP 97119554A EP 0841406 A1 EP0841406 A1 EP 0841406A1
Authority
EP
European Patent Office
Prior art keywords
alloy
temperature
holding vessel
shaping
less
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP97119554A
Other languages
English (en)
French (fr)
Other versions
EP0841406B1 (de
Inventor
Mitsuru Adachi
Satoru Sato
Yasunori Harada
Hiroto Sasaki
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Ube Corp
Original Assignee
Ube Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=26560669&utm_source=***_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP0841406(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Priority claimed from JP29642096A external-priority patent/JP3246358B2/ja
Priority claimed from JP31731396A external-priority patent/JP3246363B2/ja
Application filed by Ube Industries Ltd filed Critical Ube Industries Ltd
Publication of EP0841406A1 publication Critical patent/EP0841406A1/de
Application granted granted Critical
Publication of EP0841406B1 publication Critical patent/EP0841406B1/de
Anticipated expiration legal-status Critical
Revoked legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
    • B22D17/007—Semi-solid pressure die 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
    • C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase

Definitions

  • This invention relates to a method of shaping semisolid metals. More particularly, the invention relates to a method of shaping semisolid metals, in which liquid alloy having crystal nuclei and at a temperature not lower than the liquidus temperature or a partially solid, partically liquid alloy having crystal nuclei and at a temperature less than the liquidus temperature but not lower than the molding temperature is poured into a holding vessel, cooled at an average cooling rate in a specified range and held as such until just prior to the start of shaping under pressure, whereby fine primary crystals are generated in the alloy solution and the alloy within said holding vessel is temperature adjusted by induction heating such that the temperatures of various parts of the alloy fall within the desired molding temperature range for the establishment of a specified fraction liquid not later than the start of shaping and the alloy is recovered from the holding vessel, supplied into a forming mold and shaped under pressure.
  • the invention also relates to a method of shaping semisolid metals, in which a molten aluminum or magnesium alloy containing a crystal grain refiner which is held superheated to less than 50°C above the liquidus temperature is poured directly into a holding vessel without using any cooling jig and held for a period from 30 seconds to 30 minutes as the melt is cooled to the molding temperature where a specified fraction liquid is established such that the temperature of the poured alloy which is either liquid and superheated to less than 10°C above the liquidus temperature or which is partially solid, partially liquid and less than 5°C below the liquidus temperature is allowed to decrease from the initial level and pass through a temperature zone 5°C below the liquidus temperature within 10 minutes, whereby fine primary crystals are generated in the alloy solution, and the alloy is recovered from the holding vessel, supplied into a forming mold and shaped under pressure.
  • the first two concern magnesium alloys that will easily produce an equiaxed microstructure and Zr is added to induce the formation of finer crystals [method (B)] or a carbonaceous refiner is added for the same purpose [method (C)];
  • the third approach concerns aluminum alloys and a master alloy comprising an Al-5% Ti-1% B system is added as a refiner in amounts ranging from 2 - 10 times the conventional amount [method (D)].
  • the raw materials prepared by these methods are heated to temperature ranges that produce semisolid metals and the resulting primary crystals are spheroidized before molding.
  • alloys within a solubility limit are heated fairly rapidly up to a temperature near the solidus line and, thereafter, in order to ensure a uniform temperature profile through the raw material while avoiding local melting, the alloy is slowly heated to an appropriate temperature beyond the solidus line so that the material becomes sufficiently soft to be molded [method (E)].
  • a method is also known, in which molten aluminum at about 700°C is cast to flow down an inclined cooling plate to form partialy molten aluminum, which is collectd in a vessel [method (F)].
  • a casting apparatus (I) which produces a partially solidified billet by cooling a metal in a billet case either from the outside of a vessel or with ultrasonic vibrations being applied directly to the interior of the vessel and the billet is taken out of the case and shaped either as such or after reheating with r-f induction heater.
  • Method (A) is cumbersome and the production cost is high irrespective of whether the agitation or recrystallization technique is utilized.
  • method (B) is economically disadvantageous since Zr is an expensive element and speaking of method (C), in order to ensure that carbonaceous refiners will exhibit their function to the fullest extent, the addition of Be as an oxidation control element has to be reduced to a level as low as about 7 ppm but then the alloy is prone to burn by oxidation during the heat treatment just prior to molding and this is inconvenient in operations.
  • Method (E) is a thixo-casting process which is characterized by heating the raw material slowly after the temperature has exceeded the solidus line such that the raw material is uniformly heated and spheroidized.
  • an ordinary dendritic microstructure will not transform to a thixotropic structure (in which the primary dendrites have been spheroidized) upon heating.
  • method (F) partially molten aluminum having spherical particles in the microstructure can be obtained conveniently but no conditions are available that provide for direct shaping.
  • thixo-casting methods (A) - (F) have a common problem in that they are more costly than the existing casting methods because in order to perform molding in the semisolid state, the liquid phase must first be solidified to prepare a billet, which is heated again to a temperature range that produces a semisolid metal.
  • the billets as the starting material are difficult to recycle and the fraction liquid cannot be increased to a very high level because of handling considerations.
  • method (G) which continuously generates and supplies a molten metal containing spherical primary crystals is more advantageous than the thixocasting approach from the viewpoint of cost and energy but, on the other hand, the machine to be installed for producing a metal material consisting of a spherical structure and a liquid phase requires cumbersome procedures to assure effective operative association with the casting machine to yield the final product. Specifically, if the casting machine fails, difficulty arises in the processing of the semisolid metal.
  • Method (H) which holds the chilled metal for a specified time in a temperature range that produces a semisolid metal has the following problem. Unlike the thixocasting approach which is characterized by solidification into billets, reheating and subsequent shaping, the method (H) involves direct shaping of the semisolid metal obtained by holding in the specified temperature range for a specified time and in order to realize industrial continuous operations, it is necessary that an alloy having a good enough temperature profile to establish a specified fraction liquid suitable for shaping should be formed within a short time.
  • the desired rheo-casting semisolid metal which has a fraction liquid and a temperature profile that are suitable for shaping cannot be obtained by merely holding the cooled metal in the specified temperature range for a specified period.
  • the fraction liquid of the billet has dropped below 40%, it could be reheated with a r-f induction heater but is is still difficult to attain a fraction liquid in excess of 50% and special considerations must be made in injection and other shaping conditions.
  • eliminating any significant temperature uneveness that has occurred within the partially solidified billet is a time-consuming practice and it is required, although for only a short time, that the r-f induction heater produce a high power comparable to that required in thixo-casting.
  • Another problem with the industrial practice of shaping semisolid metals in a continuous manner is that if a trouble occurs in the casting machine, the semisolid metal may occasionally be held in a specified temperature range for a period longer than the prescribed time. Unless a certain problem occurs in the metallographic structure, it is desired that the semisolid metal be maintained at a specified temperature; in practice, however, particularly in the thixo-casting process where the semisolid metal is held with its temperature elevated from room temperature, the metallographic structure becomes coarse and the billets are considerably deformed (progressively increase in diameter toward the bottom) and, in addition, such billets are usually discarded, which is simply a waste in resources, unless their temperatures are individually controlled.
  • the present invention has been accomplished under these circumstances of the prior art and its principal object is to provide a method that does not use billets or any cumbersome procedures but which ensures that semisolid metal (including those which have higher values of liquid fracton than what are obtained by the conventional thixo-casting process) which are suitable for subsequent shaping on account of both a uniform structure containing spheroidized primary crystals and uniform temperature profile can be produced in a convenient and easy way with such great rapidity that the power requirement of the r-f induction heater is no more than 50% of what is commonly spent in shaping by the thixo-casting process, said semisolid metals being subsequently shaped under pressure.
  • the stated object of the invention can be attained by the method of shaping a semisolid metal recited in claim 1, in which liquid alloy having crystal nuclei and being at a temperature not lower than the liquidus temperature or a partially solid, partially liquid alloy having crystal nuclei and being at a temperature less than the liquidus temperature but not lower than the molding temperature is poured into a holding vessel having a thermal conductivity of at least 1 kcal/mh°C, cooled at an average cooling rate of 0.01 °C/s - 3.0 °C/s and held as such until just prior to the start of shaping under pressure, whereby fine primary crystals are generated in said alloy solution and the alloy within said holding vessel is temperature adjusted by induction heating such that the temperatures of various parts of the alloy fall within the desired molding temperature range for the establishment of a specified liquid fraction no later than the start of shaping and the alloy is recovered from said holding vessel, supplied into a forming mold and shaped under pressure.
  • the induction heating mentioned in claim 1 is for effecting thermal adjustment such that a specified amount of electric current is applied for a specified time immediately after the pouring of the molten alloy before the representative temperature of the alloy slowly cooling in the holding vessel has dropped to at least 10°C below the desired molding temperature, so that the temperatures of various areas of the alloy within said holding vessel fall within the limits of ⁇ 5°C of the desired molding temperature.
  • the temperature of said alloy is held until just before the start of the shaping step by induction heating at a frequency comparable to or higher than the frequency used in the induction heating for the preceding temperature adjustment.
  • either the top portion or the bottom portion or both of the holding vessel are heat-retained or heated to a higher temperature than the middle portion or the top and bottom portions of the holding vessel are smaller in wall thickness than the middle portion.
  • the alloy within the holding vessel is cooled by blowing either air or water or both against said holding vessel from its outside.
  • either air or water or both which are at a specified temperature are blown from at least two different, independently operable heights exterior to the holding vessel such that the blowing conditions and times can be varied freely.
  • the alloy to be supplied into the forming mold has a liquid fraction of at least 1.0% but less than 75%.
  • the crystal nuclei are generated by vibrating the alloy which builds up in the holding vessel by pouring in a melt superheated to less than 50°C above the liquidus temperature, the vibration being applied to said alloy either by means of vibrating rod which is submerged in the melt during its pouring so that it has direct contact with the alloy or by vibrating not only the vibrating rod but also the holding vessel as the alloy is poured into said holding vessel.
  • the crystal nuclei are generated by pouring a molten aluminum alloy into the holding vessel, said alloy being held superheated to less than 50°C above the liquidus temperature and containing 0.001% - 0.01% B and 0.005% - 0.3% Ti.
  • the crystal nuclei are generated by pouring a molten magnesium alloy into the holding vessel, said alloy being held superheated to less than 50°C above the liquidus temperature and containing 0.01% - 1.5% Si and 0.005% - 0.1% Sr or 0.05% - 0.30% Ca alone.
  • the stated of the invention can also be attained by the method of shaping a semisolid metal recited in claim 11, in which a molten aluminum or magnesium alloy containing a crystal grain refiner which is held superheated to less than 50°C above the liquidus temperature is poured directly into a holding vessel without using any cooling jig and held for a period from 30 seconds to 30 minutes as the melt is cooled to the molding temperature where a specified liquid fraction is established such that the temperature of the poured alloy which is liquid and superheated to less than 10°C above the liquidus temperature or which is partially solid, partially liquid and less than 5°C below the liquidus temperature is allowed to decrease from the initial level and pass through a temperature zone 5°C below the liquidus temperature within 10 minutes, whereby fine primary crystals are generated in said alloy solution, and the alloy is recovered from the holding vessel, supplied into a forming mold and shaped under pressure.
  • the aluminum alloy mentioned in claim 11 has 0.03% - 0.30% Ti added and superheated to less than 30°C above the liquidus temperature as it is poured into the holding vessel.
  • the aluminum alloy mentioned in claim 11 has 0.005% - 0.30% Ti and 0.001% - 0.01% B added and superheated to less than 50°C above the liquidus temperature as it is poured into the holding vessel.
  • the temperature of the alloy poured into the holding vessel is held by temperature adjustment through induction heating such that the temperatures of various parts of said alloy within said holding vessel are allowed to fall within the desired molding temperature range for the establishment of a specified fraction liquid not later than the start of shaping.
  • liquid alloy having crystal nuclei and at a temperature not lower than the liquidus temperature or a partially solid, partially liquid alloy having crystal nuclei and at a temperature less than the liquidus temperature but not lower than the molding temperature is poured into a holding vessel having a thermal conductivity of at least 1 kcal/mh°C, is cooled at an average cooling rate of 0.01 °C/s - 3.0 °C/s and held as such until just prior to the start of shaping under pressure, whereby fine primary crystals are generated in said alloy solution and the alloy within said holding vessel is temperature adjusted by induction heating such that the temperatures of various parts of the alloy fall within the desired molding temperature range for the establishment of a specified fraction liquid not later than the start of shaping and the alloy is recovered from said holding vessel, supplied into a forming mold and shaped under pressure. Since the temperature control of the alloy prior to the shaping step is performed in the ideal manner, satisfactory shaped parts can be obtained that have a homogeneous structure containing spheroidized primary crystals.
  • a molten aluminum containing Ti either alone or in combination with B or a molten magnesium alloy containing Ca or both Si and Sr, is held superheated to less than 50°C above the liquidus temperature, poured directly into a holding vessel without using any cooling jig and held for a period from 30 seconds to 30 minutes as the melt is cooled to the molding temperature where a specified fraction liquid is established such that the temperature of the poured alloy which is liquid and superheated to less than 10°C above liquidus temperature or which is partially solid, partially liquid and less than 5°C below the liquidus temperature is allowed to decrease from the initial level and pass through a temperature zone 5°C below the liquidus temperature within 10 minutes, whereby fine primary crystals are generated in said alloy solution and the temperatures of various parts of the alloy within said holding vessel are adjusted such that by means of induction heating and local heating or heat retention of the vessel, said temperatures will fall within the desired molding temperature range for the establishment of a specified fraction liquid not later than the start of shaping, and said alloy is
  • Fig. 1 is a diagram showing a process sequence for the semisolid forming of a hypoeutectic aluminum alloy having a composition at or above a maximum solubility limit
  • Fig. 2 is a diagram showing a process sequence for the semisolid forming of a magnesium or aluminum alloy having a composition within a maximum solubility limit
  • Fig. 3 shows a process flow starting with the generation of spherical primary crystals and ending with the molding step
  • Fig. 4 shows diagrammatically the metallographic structures obtained in the respective steps shown in Fig. 3
  • Fig. 5 is an equilibrium phase diagram for an Al-Si alloy as a typical aluminum alloy system
  • Fig. 1 is a diagram showing a process sequence for the semisolid forming of a hypoeutectic aluminum alloy having a composition at or above a maximum solubility limit
  • Fig. 2 is a diagram showing a process sequence for the semisolid forming of a magnesium or aluminum alloy having a composition within a maximum solubility limit
  • FIG. 6 is an equilibrium phase diagram for a Mg-Al alloy as a typical magnesium alloy system
  • Fig. 7 is a diagrammatic representation of a micrograph showing the metallographic structure of a shaped part according to the invention
  • Fig. 8 is a diagrammatic representation of a micrograph showing the metallographic structure of a shaped part according to the prior art
  • Fig. 9 is a graph illustrating the correlationship between the temperature distribution of AC4CH alloy in a holding vessel and its cooling rate:
  • Fig. 10 is a graph showing the effect of r-f induction heating on the temperature distribution of AC4CH alloy in a holding vessel;
  • Fig. 11 is another graph showing the effect of r-f induction heating on the temperature distribution of AC4CH alloy in a holding vessel; and
  • Fig. 12 illustrates how holding by r-f induction heating affects the compositional homogenization of a semisolid metal after the molding temperature was reached.
  • Fig. 13 - 18 relate to Examples 11 - 14 of the invention.
  • Fig. 13 shows a process flow starting with the generation of spherical primary crystals and ending with the molding step;
  • Fig. 14 is a graph showing how the B content and the degree of superheating of a melt during pouring affect the size and morphology of the primary crystals of AC4CH alloy (Al-7% Si-0.3% Mg-0.15% Ti);
  • Fig. 15 is a graph showing how the B content and the degree of superheating of a melt during pouring affect the size and morphology of the primary crystals of 7075 alloy (Al-5.5% Zn-2.5% Mg-1.6% Cu-0.15% Ti);
  • Fig. 16 - 18 are diagrammatic representation of a micrographs showing the metallographic structures of shaped parts within the scope of the invention.
  • Fig. 19 - 22 are diagrammatic representation of a micrographs showing the metallographic structures of a shaped parts.
  • the first step of the process according to the invention comprises superheating the melt of a hypoeutectic aluminum alloy of a composition at or above a maximum solubility or a magnesium or aluminum alloy of a composition within a maximum solubility limit, holding the melt superheated to less than sot above the liquidus temperature as it is poured into a holding vessel, with a vibrating rod being submerged within the melt in the holding vessel and vibrated in direct contact with the melt so as to vibrate the latter and, after the end of the pouring, immediately pulling up said vibrating rod so that it disengages from the melt.
  • the liquid alloy having crystal nuclei and at a temperature not lower than the liquidus temperature or the partially solid, partially liquid alloy having crystal nuclei and at a temperature less than the liquidus temperature but not lower than the holding temperature is cooled to the molding temperature, where a specified fraction liquid is established, at an average cooling rate of 0.01 - 3.0 °C/s with a cooling medium such as air at room temperature being blown against said holding vessel from the outside and the alloy is held as such until just prior to the start of shaping under pressure, whereby fine primary crystals are generated in said alloy solution and the alloy within said holding vessel is temperature adjusted by induction heating such that the temperatures of various parts of the alloy fall within the desired molding temperature range for establishment of a specified fraction liquid not later than the start of shaping and said alloy is recovered from said holding vessel, supplied into a forming mold and shaped under pressure.
  • the first step comprises superheating the melt of a hypoeutectic aluminum alloy of a composition at or above a maximum solubility or a magnesium or aluminum alloy of a composition within a maximum solubility limit, both alloys containing a crystal grain refiner (which is hereunder referred to as "refiner"), holding the melt superheated to less than 50°C above the liquidus temperature as it is poured into a holding vessel 30.
  • a crystal grain refiner which is hereunder referred to as "refiner”
  • the alloy is held for a period from 30 seconds to 30 minutes as the melt is cooled to the molding temperature whereas specified fraction liquid is established such that the temperature of either the poured liquid alloy superheated to less than 10°C above the liquidus temperature or the poured partially solid, partially liquid alloy which is less than 5°C below the liquidus temperature is allowed to decrease from the initial level and pass through a temperature range 5°C below the liquidus temperature within 10 minutes, whereby fine primary crystals are generated in said alloy solution, and the alloy is recovered from the holding vessel 30, supplied into a forming mold 60 and shaped under pressure.
  • a molten alloy which has been poured into the holding vessel is cooled by blowing air or water from the outside of the vessel until the melt reaches the predetermined temperature which is set above the temperature of shaping, while the temperature of the upper and the lower portions of the vessel is being maintained constant. Further, the temperature of various portions of the melt in the holding vessel is adjusted by induction heating so that the melt may have a temperature within the desired molding temperature range to establish a specified fraction of liquid before the start of shaping at latest.
  • a specified liquid fraction means a relative proportion of the liquid phase which is suitable for pressure forming.
  • the liquid fraction is less than 75%, preferably in the range of 40% - 65%. If the liquid fraction is less than 40%, not only is it difficult to recover the alloy from the holding vessel 30 but also the formability of the raw material is poor. If the liquid fraction exceeds 75%, the raw material is so soft that it is not only difficult to handle but also less likely to produce a homogeneous microstructure because the molten metal will entrap the surrounding air when it is inserted into the sleeve for injection into a mold on a die-casting machine or segregation develops in the metallographic structure of the casting. For these reasons, the liquid fraction for high-pressure casting operations should not be more than 75%, preferably not more than 65%.
  • the liquid fraction ranges from 1.0% to 70%, preferably from 10% to 65%. Beyond 70%, an uneven structure can potentially occur. Therefore, the liquid fraction should not be higher than 70%, preferably 65% or less. Below 1.0%, the resistance to deformation is unduly high; therefore, the liquid fraction should be at least 1.0%. If extruding or forging operations are to be performed with an alloy having a liquid fraction of less than 40%, the alloy is first adjusted to a liquid fraction of 40% and more before it is taken out of the holding vessel and thereafter the liquid fraction is lowered to less than 40%.
  • the "holding vessel” as used in the invention is metallic nonmetallic vessel (including a ceramic vessel), or a metallic vessel having a surface coated with nonmetallic materials, or a metallic vessel composited with nonmetallic materials. Coating the surface of a metallic vessel with nonmetallic materials is effective in preventing the sticking of the metal.
  • the holding vessel may be heated either internally or externally by means of a heater; alternatively, a r-f induction heater may be employed.
  • the representative temperature refers to the center temperature of the alloy charged into holding vessel. More specifically, it means the temperature at the center of the alloy in the holding vessel in both the height and radial directions. In practical operations, however, it is difficult to measure the temperature of the alloy center in both directions and, instead, the temperature in a position a specified depth (say, 1 cm) below the surface of a semisolid metal is measured. From this temperature, the representative temperature is estimated on the basis of the preliminarily established relationship between the representative temperature and the temperatures of various parts of the alloy.
  • the crystal nuclei are generated "by vibrating the alloy which builds up in the holding vessel by pouring in a melt, the vibration being applied to said alloy by means of a vibrating rod which is submerged in the melt during its pouring so that it has direct contact with the alloy".
  • vibration is in no way limited in terms of the type of the vibrator used and the vibrating conditions (frequency and amplitude) and any commercial pneumatic and electric vibrators may be employed.
  • the frequency typically ranges from 10 Hz to 50 kHz, preferably from 50 Hz to 1 kHz, and the amplitude ranges from 1 mm to 0.1 ⁇ m, preferably from 500 ⁇ m to 10 ⁇ m, per side.
  • the method of pouring the refiner-containing low-temperature melt into the holding vessel 30 should be such that crystal nuclei (fine crystals) can be generated in the poured melt.
  • the melt In order to ensure that the refiner which works as a foreign nucleus or as an element to accelerate the liberation of crystals will manifest its effect, the melt must be poured in at a specified rate and, in addition, it must be superheated to a temperature that is above the liquidus temperature by a specified degree.
  • the degree of superheating varies with the kind of the refiner to be added and the amount of its addition (the criticality of the degree of superheating will be described later in this specification).
  • the metal be poured in at an appropriate rate within the range that does not cause entrapping of the surrounding air.
  • Titanium (Ti) may be added to the aluminum alloy as a refiner either alone or in combination with boron (B) in order to produce fine spherical crystal grains. If Ti is to be added alone, its refining effect is small if the addition is less than 0.03%. Beyond 0.30%, coarse Ti compounds well develop to reduce the ductility. Hence, Ti is added in an amount of 0.03% - 0.30%.
  • Ti and B are to be added, the effect of Ti is small if its addition is less than 0.005%. Beyond 0.30%, coarse Ti compounds will develop to reduce the ductility. Hence, Ti is added in an amount of 0.005% - 0.30% in combination with B. Boron (B), when added in combination with Ti, promotes the refining process. However, if its addition is less than 0.001%, only a small refining effect occurs. The effect of B is saturated if it is added in excess of 0.01%. Therefore, the addition of B should range from 0.001% to 0.01%.
  • Calcium (Ca) or the combination of Sr and Si may be added to the magnesium alloy as a refiner. If Ca is to be added, its refining effect is small if the addition is less than 0.05%. Beyond 0.30%, the effect of Ca is saturated. Therefore, the addition of Ca should range from 0.05% to 0.30%. In the case of combined addition of Sr and Si, only a small refining effect occurs if Sr is added in an amount of less than 0.005%. The effect of Sr is saturated if it is added in excess of 0.1%. Therefore, the addition of Sr should range from 0.005% to 0.1%. Silicon (Si), when added in combination with Sr, promotes the refining process.
  • Si Silicon
  • step (1) of the process shown in Figs. 3 and 4 a complete liquid form of metal M1 is contained in a ladle 10.
  • step (2) the alloy M1 is poured into a holding vessel 30 (which is either a ceramic or a ceramic-coated metallic vessel) as a vibrating rod 20 submerged in the alloy to have direct contact with it is vibrated to impart vibrations to the alloy, with the holding vessel 30 being vibrated with a vibrator 40 as required during the pouring of the melt.
  • the vibrating rod 20 is immediately pulled up so that crystal nuclei are generated in the alloy which is either liquid or partially liquid at a temperature near the liquidus temperature.
  • step (3) the alloy is cooled at an average cooling rate of 0.01 °C/s - 3.0 °C/s and held as such within the holding vessel 30 until just prior to the start of shaping under pressure so that fine primary crystals are generated in said alloy solution; at the same time, induction heating (i.e., energization of a heating coil 80 around the holding vessel 30) is performed to effect temperature adjustment right after the pouring of the melt such that the temperatures of various parts of the alloy in the vessel will fall within the desired molding temperature range for establishment of a specified fraction liquid not later than the start of the molding step.
  • air (or water) 90 is blown against the holding vessel from its outside.
  • both the tip and bottom portions of the holding vessel 30 may be heat-retained with a heat insulator or heated so that the alloy is held partially molten to generate fine spherical (non-dendritic) primary crystals from the introduced crystal nuclei.
  • Metal M2 thus obtained at a specified fraction liquid is inserted from the inverted holding vessel 30 [see step (3)-d] into a die casting injection sleeve 50 and thereafter pressure formed within an mold cavity 60a on a die casting machine to produce a shaped part [step (4)].
  • step (1) of the process shown in Figs. 3 and 4 a complete liquid form of metal M1 containing a refiner is charged into a pouring ladle 10 (which is hereunder sometimes referred to simply as "ladle").
  • step (2) the melt is gently but rapidly poured into a holding vessel 30 (which is either a ceramic coated or a ceramic vessel), thereby forming either a liquid or a partially solid, partially liquid alloy that contain crystal nuclei (fine crystal grains) and which are at a temperature near the liquidus temperature.
  • step (3) the temperature of the poured alloy which is either liquid and superheated to less than 10°C above the liquidus temperature of which is partially solid, partially liquid and less than 5°C below the liquidus temperature is allowed to decrease from the initial level and pass through a temperature zone 5°C below the liquidus temperature within 10 minutes, whereby fine primary crystals are generated in said alloy solution; at the same time, induction heating (i.e., energization of a heating coil 80 around the holding vessel 30) is performed to effect temperature adjustment such that the temperatures of various parts of the alloy in the vessel 30 will fall within the desired molding temperature range for the establishment of a specified fraction liquid not later than the start of the molding step.
  • induction heating i.e., energization of a heating coil 80 around the holding vessel 30
  • Fig. 9 is a graph illustrating the correlationship between the temperature distribution of AC4CH alloy in the holding vessel and its cooling rate.
  • Fig. 9 shows the effect of cooling rate (for cooling from 615°C to 585°C) on the temperature distribution of AC4CH alloy in the holding vessel 30; obviously, the temperature distribution becomes wider as the cooling rate increases.
  • Fig. 9a shows the case where the cooling rate was 0.3 °C /s; in this case, the alloy was cooled with air being blown from the outside of the holding vessel, the tip portion of which was heat-retained with a heat insulator which was also provided on the underside of the vessel.
  • Fig. 9b shows the case where the cooling rate was 0.2 °C/s; in this case, both the top and bottom portions of the vessel were heat-retained with a heat insulator and the alloy was cooled in the atmosphere.
  • Fig. 10 is a graph showing the effect of r-f induction heating on the temperature distribution of AC4CH alloy in the holding vessel. According to the invention when the representative temperature of the alloy (its center temperature as it is in the holding vessel) has reached +3°C above the desired molding temperature the blowing of air is stopped and r-f induction heating is started when the desired temperature is reached.
  • Fig. 11 is another graph showing the effect of r-f induction heating on the temperature distribution of AC4CH alloy in the holding vessel. According to the invention, when the representative temperature of the alloy (its center temperature as it is within the holding vessel) has reached a temperature 11°C below the desired molding temperature, the blowing of air is stopped and r-f induction heating is started.
  • the induction heating should comprise at least one application of electric current in a specified amount for specified period of time before the representative temperature of the alloy slowly cooling in the holding vessel 30 has dropped to at least 10°C below the desired molding temperature.
  • Fig. 12 illustrates how holding by r-f induction heating affects the compositional homogenization of a semisolid metal after the molding temperature has been reached.
  • Each of the diagrams in Fig. 12 is a vertical section of the alloy in the holding vessel 30;
  • Fig. 12a shows the state of the alloy which has attained the molding temperature;
  • Fig. 12b shows the state of the alloy which was held for 20 minutes by heating with the r-f indication heater at a frequency of 8 kHz;
  • 12c shows the state of the alloy which was held for 20 minutes by heating with the r-f induction heater at a frequency of 40 kHz.
  • the operating frequency of the r-f induction heater is 8 kHz before the alloy's temperature is adjusted to the molding temperature.
  • a peculiar phenomenon which does not occur at the time the molding temperature has been reached (Fig. 12a) is observed if the alloy is held for a prolonged time; that is the uneven occurrence of the liquid phase in the top peripheral portion of the semisolid metal which is inherently a uniform mixture of the liquid and solid phases (the concentrated liquid phase is shown shaded in Fig. 12b).
  • the metal in the holding vessel 30 forms "mushrooms" during the induction heating and the liquid phase of the semisolid metal floats in the top portion of the vessel mainly due to the agitating force.
  • induction heating is performed at a higher frequency after the semisolid metal in the holding vessel has been adjusted to the molding temperature; consequently, the degree of the uneven occurrence of the liquid phase can be reduced.
  • the same alloy is held within the stated range until just prior to the start of the molding step by continuing the induction heating at a frequency either comparable to or higher than the frequency used in the preceding induction heating.
  • the semisolid metal forming process of the invention shown in Figs. 1, 2, 3, 4 and 11 has the following differences from the conventional thixocasting and rheocasting methods.
  • the dendritic primary crystals that have been generated within a temperature range of from the semisolid state are not ground into spherical grains by mechanical or electromagnetic agitation as in the prior art but the large number of primary crystals that have been generated and grown from the introduced crystal nuclei with the decreasing temperature in the range for the semisolid state are spheroidized continuously by the heat of the alloy itself (which may optionally by supplied with external heat hand held at a desired temperature).
  • the semisolid metal forming method of the invention is characterized by the production of a uniform microstructure and temperature distribution by r-f induction heating with lower output and it is a very convenient and economical process since it does not involve the step of partially melting billets by reheating in the thixo-casting process.
  • nucleating, spheroidizing and molding conditions that are respectively set for the steps shown in Fig. 3, namely, the step of pouring the metal into the holding vessel 30, the step of generating and spheroidizing primary crystals and the forming step, are set forth below more specifically. Also discussed below is the criticality of the numerical limitations the invention should have.
  • crystal nuclei are to be generated by (1) applying vibrations to the melt in the holding vessel 30 or (2) pouring a Ti- and B-containing aluminum alloy or a Si and Sr-containing magnesium alloy or a Ca-containing magnesium alloy directly into the holding vessel, the melt should be superheated to less than 50°C, preferably less than 30°C, above the liquidus temperature. If crystal nuclei are to be generated by pouring a Ti-containing aluminum alloy into the holding vessel, the melt should be superheated to less than 30°C above the liquidus temperature.
  • the temperature of the melt being poured into he holding vessel is higher than these limits, the following phenomena will occur; (1) only a few crystal nuclei are generated; (2) the temperature of the alloy as poured into the vessel is higher than the liquidus temperature and, hence, the number of residual crystal nuclei is small and the size of primary crystals is large enough to produce amorphous dendrites.
  • the upper or lower portion of the holding vessel 30 is not heated or heat-retained while the alloy M1 poured into the vessel is cooled to establish a fraction liquid suitable for molding, dendritic primary crystals are generated in the skin of the alloy M1 in the tip and/or bottom portion of the vessel or a solidified layer will grow to cause nonuniformity in the temperature distribution of the metal in the holding vessel 30; as a result, even if r-f induction heating is performed, the alloy having the specified fraction liquid cannot be discharged from the inverted vessel 30 or the remaining solidified layer within the holding vessel 30 either introduces difficulty into the practice of continued shaping operation or prevents the temperature distribution of the alloy from being improved in the desired way.
  • the top and/or bottom portion of the holding vessel is heated or heat-retained at a higher temperature than the middle portion in the cooling process; if necessary, both the top and bottom portions of the holding vessel 30 may be heated not only in the cooling process but also before the pouring step.
  • the wall thickness of the holding vessel 30 is reduced, the formation of a solidified layer can be suppressed; hence, the wall of the holding vessel is made smaller in the top and bottom portions than in the middle to thereby facilitate the discharge of the alloy from the holding vessel 30.
  • the holding vessel 30 is made of a material having a thermal conductivity of less than 1.0 kcal/mh°C, the cooling time is prolonged to a practically undesirable level; hence, the holding vessel 30 should have a thermal conductivity of at least 1.0 kcal/mh°C.
  • the holding vessel 30 is made of a metal, its surface is preferably coated with a nonmetallic material (e.g. BN or graphite). the coating method may be either mechanical or chemical or physical.
  • Both the magnesium and aluminum alloys are highly oxidizable metals, so if the holding vessel 30 is made of an air-permeable material or if the alloy is to be held for a long time in the vessel, the exterior to the vessel is preferably filled with a specified atmosphere (e.g. an inert or vacuum atmosphere). Even in the case of using the metallic vessel, the magnesium alloy which is highly oxidizable is desirably isolated by an inert of CO 2 atmosphere.
  • an oxidation control element may be preliminarily added to the molten metal, as exemplified by Be and Ca in the case of the magnesium alloy and Be for the aluminum alloy.
  • the shape of the vessel 30 is by no means limited to a tubular form and any other shapes that are suitable for the subsequent forming process may be adopted.
  • the average rate of cooling in the holding vessel 30 should range preferably from 0.01 °C/s to 3.0 °C/s, more preferably from 0.05 °C/s to 1 °C/s.
  • Crystal nuclei can also be generated by pouring a refiner containing molten alloy directly into the holding vessel 30.
  • the as-poured metal should be superheated to less than 10°C above the liquidus temperature. If the temperature of the alloy which is either liquid and superheated to less than 10°C above the liquidus temperature or partially solid, partially liquid alloy and less than 5°C below the liquidus temperature is allowed to decrease from the initial level and pass through a temperature zone 5°C below the liquidus temperature taking a time longer than 10 minutes, it is impossible to produce a fine spherical microstructure.
  • the temperature of the alloy is allowed to decrease from the initial level and pass through the temperature zone 5°C below the liquidus temperature within 10 minutes, preferably within 5 minutes, to thereby generate fine primary crystals in the solution of the alloy, which is taken out of the holding vessel 30, supplied into the forming mold 60 and shaped under pressure.
  • the cooling medium may be blown from at least two different, independently operable heights exterior to the holding vessel such that the blowing conditions and times can be varied freely.
  • the cooling medium to be blown, the amount of blow, its velocity, speed, position and timing are variable with the alloy in the holding vessel 30, the material of which the vessel is made, its wall thickness, etc.
  • the temperature of the yet to be shaped alloy in the holding vessel exceeds the limits of ⁇ 5°C of the desired molding temperature, a shaped part of uniform microstructure cannot be produced by casting. Hence, the temperature of the alloy in the holding vessel should be adjusted by induction heating to fall within the limits of ⁇ 5°C of the desired molding temperature.
  • the vibrating rod 20 is to be used for the purpose of creating crystal nuclei in the alloy being poured into the holding vessel, it preferably satisfied the following two requirements: it should be coolable either internally or externally in order to provide for its continued use and generate many crystal; the surface of the vibrating rod 20 should be coated with a nonmetallic material. It should be noted that the use of rod that can be cooled internally but which is nonvibrating has the following disadvantage even if it is coated with a nonmetallic material: when the rod is pulled up from the poured alloy, a solidified layer will stick extensively to the surface of the rod or many dendrites will form in the alloy in the holding vessel. To avoid this problem, the coolable rod must be vibrated when it is placed in contact with the molten metal.
  • the use of the vibrating rod 20 is effective in generating fine primary crystals in the alloy in the holding vessel but, at the same time, dendrites may occasionally form in those parts of the alloy which contact the inner surface of the holding vessel 30.
  • the holding vessel 30 is preferably vibrated during pouring of the metal.
  • Table 1 sets forth the conditions for the preparation of semisolid metal samples to be shaped
  • Table 2 sets forth the temperature distribution of yet to be shaped metal samples in the holding vessel, as well as the quality of shaped parts.
  • the forming step consisted of inserting the semisolid metal into the sleeve 50 and subsequent treatment with a squeeze casting machine.
  • the forming conditions were as followed: pressure, 950 kgf/cm 2 ; injection rate, 0.5 m/s; casting weight (inclusive of biscuits), 1.5 kg; mold temperature, 230°C. Temperature of Semisolid Metals and Microstructure of Shaped Parts No.
  • Fig. 14 is a graph showing how the B content and the degree of superheating of a melt during pouring affect the size and morphology of the primary crystals of AC4CH alloy (Al-7% Si-0.3% Mg-0.15% Ti). Unlike in the case of combined addition of Ti and B, no spherical crystals can be obtained at temperatures more than 30°C above the liquidus temperature when only Ti was added as a refiner.
  • Fig. 15 is a graph showing how the B content and the degree of superheating of a melt during pouring affect the size and morphology of the primary crystals of 7075 alloy (Al-5.5% Zn-2.5% Mg-1.6% Cu-0.15% Ti).
  • the 7075 alloy was in contrast with the AC4CH alloy in that fine spherical crystals are obtained with high degree of superheating even when only Ti is used as a refiner.
  • Table 3 sets forth the conditions for the preparation of semisolid metal samples and the results of examination of the microstructure of shaped parts.
  • the forming step consisted of inserting the semisolid metal into the injection sleeve 170 and subsequent treatment with a squeeze casting machine.
  • the forming conditions were as follows: pressure, 950 kgf/cm 2 ; injection rate, 0.5 m/s; casting weight (inclusive of biscuits), 1.5 kg; mold temperature, 230°C.
  • shaped parts having fine and spherical microstructures can be produced in a convenient, easy and inexpensive manner without relying upon agitation by the conventional mechanical and electromagnetic methods.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Continuous Casting (AREA)
EP97119554A 1996-11-08 1997-11-07 Verfahren zum Formen halbfester Metalle Revoked EP0841406B1 (de)

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP29642096 1996-11-08
JP29642096A JP3246358B2 (ja) 1996-11-08 1996-11-08 半溶融金属の成形方法
JP296420/96 1996-11-08
JP317313/96 1996-11-28
JP31731396A JP3246363B2 (ja) 1996-11-28 1996-11-28 半溶融金属の成形方法
JP31731396 1996-11-28

Publications (2)

Publication Number Publication Date
EP0841406A1 true EP0841406A1 (de) 1998-05-13
EP0841406B1 EP0841406B1 (de) 2001-08-01

Family

ID=26560669

Family Applications (1)

Application Number Title Priority Date Filing Date
EP97119554A Revoked EP0841406B1 (de) 1996-11-08 1997-11-07 Verfahren zum Formen halbfester Metalle

Country Status (3)

Country Link
EP (1) EP0841406B1 (de)
CA (1) CA2220357A1 (de)
DE (1) DE69705917T2 (de)

Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6079477A (en) * 1998-01-26 2000-06-27 Amcan Castings Limited Semi-solid metal forming process
DE19926653A1 (de) * 1999-06-11 2000-12-21 Audi Ag Verfahren zum Durchführen von Thixoforming sowie Thixoforming-Vorrichtung zur Durchführung des Verfahrens
EP1110643A1 (de) * 1999-12-22 2001-06-27 Alusuisse Technology & Management AG Vorbehandlung eines thixotropen Metallbolzens
EP1120471A1 (de) * 2000-01-24 2001-08-01 Ritter Aluminium Giesserei Gmbh Druckgiessverfahren und Vorrichtung zu seiner Durchführung
US6399017B1 (en) 2000-06-01 2002-06-04 Aemp Corporation Method and apparatus for containing and ejecting a thixotropic metal slurry
US6402367B1 (en) 2000-06-01 2002-06-11 Aemp Corporation Method and apparatus for magnetically stirring a thixotropic metal slurry
US6428636B2 (en) 1999-07-26 2002-08-06 Alcan International, Ltd. Semi-solid concentration processing of metallic alloys
US6432160B1 (en) 2000-06-01 2002-08-13 Aemp Corporation Method and apparatus for making a thixotropic metal slurry
WO2003015959A1 (en) * 2001-08-17 2003-02-27 Innovative Products Group, Llc Apparatus for and method of producing slurry material without stirring for application in semi-solid forming
EP1292411A1 (de) * 2000-06-01 2003-03-19 AEMP Corporation Produktion von bedarfsabhängigem halbfesten material für giesslinge
US6611736B1 (en) 2000-07-01 2003-08-26 Aemp Corporation Equal order method for fluid flow simulation
WO2004031423A2 (en) * 2002-09-23 2004-04-15 Worcester Polytechnic Institute Method for making an alloy and alloy
US6796362B2 (en) 2000-06-01 2004-09-28 Brunswick Corporation Apparatus for producing a metallic slurry material for use in semi-solid forming of shaped parts
EP1601481A2 (de) * 2003-03-04 2005-12-07 Idraprince Inc. Verfahren und vorrichtung zur herstellung einer metalllegierung
US7024342B1 (en) 2000-07-01 2006-04-04 Mercury Marine Thermal flow simulation for casting/molding processes
CN102172771A (zh) * 2011-03-25 2011-09-07 天津福来明思铝业有限公司 铝合金半固态触变加工中的重熔加热工艺
RU2509623C1 (ru) * 2012-12-03 2014-03-20 Российская Федерация, От Имени Которой Выступает Министерство Промышленности И Торговли Российской Федерации Устройство для получения тиксозаготовок с глобулярной структурой
RU2590432C2 (ru) * 2014-11-18 2016-07-10 Российская Федерация от имени которой выступает Министерство промышленности и торговли Российской Федерации Способ и устройство для изготовления тиксозаготовок
CN110029259A (zh) * 2019-05-17 2019-07-19 重庆大学 一种镁-稀土系合金光谱标样的制备方法
CN113493876A (zh) * 2021-07-07 2021-10-12 重庆大学 一种铁基非晶改性镁合金表面的方法
US20220017993A1 (en) * 2020-07-17 2022-01-20 Qingyou Han Method and apparatus for processing a liquid alloy

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109759555B (zh) * 2019-01-28 2021-03-30 深圳市银宝山新压铸科技有限公司 一种复合场制备半固态浆料的方法
CN112517872B (zh) * 2020-11-01 2021-12-24 广州德珐麒自动化技术有限公司 一种基于电磁搅拌的半固态铝合金压铸件的生产装置和生产工艺
CN112961997B (zh) * 2021-02-02 2022-03-04 邱从章 一种高熔点差合金及其固液混合成型制备方法

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0701002A1 (de) * 1994-09-09 1996-03-13 Ube Industries, Ltd. Verfahren zur Verarbeitung halbfester Aluminium- oder Magnesiumlegierungen
EP0745694A1 (de) * 1995-05-29 1996-12-04 Ube Industries, Ltd. Verfahren und Vorrichtung zum Formen halbfester Metalle

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0701002A1 (de) * 1994-09-09 1996-03-13 Ube Industries, Ltd. Verfahren zur Verarbeitung halbfester Aluminium- oder Magnesiumlegierungen
EP0745694A1 (de) * 1995-05-29 1996-12-04 Ube Industries, Ltd. Verfahren und Vorrichtung zum Formen halbfester Metalle

Cited By (37)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6079477A (en) * 1998-01-26 2000-06-27 Amcan Castings Limited Semi-solid metal forming process
US6845809B1 (en) 1999-02-17 2005-01-25 Aemp Corporation Apparatus for and method of producing on-demand semi-solid material for castings
DE19926653A1 (de) * 1999-06-11 2000-12-21 Audi Ag Verfahren zum Durchführen von Thixoforming sowie Thixoforming-Vorrichtung zur Durchführung des Verfahrens
DE19926653B4 (de) * 1999-06-11 2005-12-15 Audi Ag Verfahren zum Durchführen von Thixoforming sowie Thixoforming-Vorrichtung zur Durchführung des Verfahrens
US7140419B2 (en) 1999-07-26 2006-11-28 Alcan Internatinoal Limited Semi-solid concentration processing of metallic alloys
US6428636B2 (en) 1999-07-26 2002-08-06 Alcan International, Ltd. Semi-solid concentration processing of metallic alloys
EP1110643A1 (de) * 1999-12-22 2001-06-27 Alusuisse Technology & Management AG Vorbehandlung eines thixotropen Metallbolzens
WO2001045880A1 (de) * 1999-12-22 2001-06-28 Alcan Technology & Management Ltd Vorbehandlung eines thixotropen metallbolzens
EP1120471A1 (de) * 2000-01-24 2001-08-01 Ritter Aluminium Giesserei Gmbh Druckgiessverfahren und Vorrichtung zu seiner Durchführung
WO2001055464A1 (de) * 2000-01-24 2001-08-02 Ritter Aluminium Giesserei Gmbh Druckgiessverfahren und vorrichtung zu seiner durchführung
US6432160B1 (en) 2000-06-01 2002-08-13 Aemp Corporation Method and apparatus for making a thixotropic metal slurry
EP1292411A1 (de) * 2000-06-01 2003-03-19 AEMP Corporation Produktion von bedarfsabhängigem halbfesten material für giesslinge
US6991670B2 (en) 2000-06-01 2006-01-31 Brunswick Corporation Method and apparatus for making a thixotropic metal slurry
US6637927B2 (en) 2000-06-01 2003-10-28 Innovative Products Group, Llc Method and apparatus for magnetically stirring a thixotropic metal slurry
US6399017B1 (en) 2000-06-01 2002-06-04 Aemp Corporation Method and apparatus for containing and ejecting a thixotropic metal slurry
US6402367B1 (en) 2000-06-01 2002-06-11 Aemp Corporation Method and apparatus for magnetically stirring a thixotropic metal slurry
EP1292411A4 (de) * 2000-06-01 2004-06-23 Aemp Corp Produktion von bedarfsabhängigem halbfesten material für giesslinge
AU2001264711B2 (en) * 2000-06-01 2006-04-27 Brunswick Corporation Method and apparatus for magnetically stirring a thixotropic metal slurry
US6796362B2 (en) 2000-06-01 2004-09-28 Brunswick Corporation Apparatus for producing a metallic slurry material for use in semi-solid forming of shaped parts
AU2001264711B9 (en) * 2000-06-01 2006-10-05 Brunswick Corporation Method and apparatus for magnetically stirring a thixotropic metal slurry
US6932938B2 (en) 2000-06-01 2005-08-23 Mercury Marine Method and apparatus for containing and ejecting a thixotropic metal slurry
US6611736B1 (en) 2000-07-01 2003-08-26 Aemp Corporation Equal order method for fluid flow simulation
US7024342B1 (en) 2000-07-01 2006-04-04 Mercury Marine Thermal flow simulation for casting/molding processes
WO2003015959A1 (en) * 2001-08-17 2003-02-27 Innovative Products Group, Llc Apparatus for and method of producing slurry material without stirring for application in semi-solid forming
US6742567B2 (en) 2001-08-17 2004-06-01 Brunswick Corporation Apparatus for and method of producing slurry material without stirring for application in semi-solid forming
WO2004031423A3 (en) * 2002-09-23 2004-07-01 Worcester Polytech Inst Method for making an alloy and alloy
WO2004031423A2 (en) * 2002-09-23 2004-04-15 Worcester Polytechnic Institute Method for making an alloy and alloy
US7513962B2 (en) 2002-09-23 2009-04-07 Worcester Polytechnic Institute Alloy substantially free of dendrites and method of forming the same
EP1601481A2 (de) * 2003-03-04 2005-12-07 Idraprince Inc. Verfahren und vorrichtung zur herstellung einer metalllegierung
EP1601481A4 (de) * 2003-03-04 2007-02-21 Idraprince Inc Verfahren und vorrichtung zur herstellung einer metalllegierung
CN102172771A (zh) * 2011-03-25 2011-09-07 天津福来明思铝业有限公司 铝合金半固态触变加工中的重熔加热工艺
RU2509623C1 (ru) * 2012-12-03 2014-03-20 Российская Федерация, От Имени Которой Выступает Министерство Промышленности И Торговли Российской Федерации Устройство для получения тиксозаготовок с глобулярной структурой
RU2590432C2 (ru) * 2014-11-18 2016-07-10 Российская Федерация от имени которой выступает Министерство промышленности и торговли Российской Федерации Способ и устройство для изготовления тиксозаготовок
CN110029259A (zh) * 2019-05-17 2019-07-19 重庆大学 一种镁-稀土系合金光谱标样的制备方法
CN110029259B (zh) * 2019-05-17 2021-05-04 重庆大学 一种镁-稀土系合金光谱标样的制备方法
US20220017993A1 (en) * 2020-07-17 2022-01-20 Qingyou Han Method and apparatus for processing a liquid alloy
CN113493876A (zh) * 2021-07-07 2021-10-12 重庆大学 一种铁基非晶改性镁合金表面的方法

Also Published As

Publication number Publication date
EP0841406B1 (de) 2001-08-01
DE69705917T2 (de) 2002-04-04
DE69705917D1 (de) 2001-09-06
CA2220357A1 (en) 1998-05-08

Similar Documents

Publication Publication Date Title
EP0841406A1 (de) Verfahren zum Formen halbfester Metalle
US6769473B1 (en) Method of shaping semisolid metals
JP3211754B2 (ja) 半溶融成形用金属の製造装置
US5186236A (en) Process for producing a liquid-solid metal alloy phase for further processing as material in the thixotropic state
CA2177455C (en) Method and apparatus for shaping semisolid metals
CA2379809C (en) Semi-solid concentration processing of metallic alloys
US6918427B2 (en) Process and apparatus for preparing a metal alloy
JP3246296B2 (ja) 半溶融金属の成形方法
JP3246363B2 (ja) 半溶融金属の成形方法
JP3246358B2 (ja) 半溶融金属の成形方法
JP3491468B2 (ja) 半溶融金属の成形方法
JP3246273B2 (ja) 半溶融金属の成形方法
JP3536559B2 (ja) 半溶融金属の成形方法
US20040050523A1 (en) Process for transforming a metal alloy into a partially-solid/partially-liquid shaped body
JP3783275B2 (ja) 半溶融金属の成形方法
JP2003126950A (ja) 半溶融金属の成形方法
JP3473214B2 (ja) 半溶融金属の成形方法
JPH0987773A (ja) 半溶融金属の成形方法
JPH07185770A (ja) アルミニウム合金の加圧鋳造方法および加圧鋳造装置
JP3473216B2 (ja) 半溶融金属の成形方法
Borisov Process for production of aluminum-alloy ingots with non-dendritic thixotropic structure.
JPH0987770A (ja) 半溶融金属の成形方法
JPH07148551A (ja) 半凝固Ａｌ合金の連続鋳造方法
RU99116105A (ru) Способ получения изделий из пеноалюминия
JPH0987767A (ja) 半溶融亜鉛合金の成形方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): DE FR IT

AX Request for extension of the european patent

Free format text: AL;LT;LV;MK;RO;SI

17P Request for examination filed

Effective date: 19981021

17Q First examination report despatched

Effective date: 19981209

AKX Designation fees paid

Free format text: DE FR IT

RBV Designated contracting states (corrected)

Designated state(s): DE FR IT

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE FR IT

ITF It: translation for a ep patent filed

Owner name: STUDIO GLP S.R.L.

REF Corresponds to:

Ref document number: 69705917

Country of ref document: DE

Date of ref document: 20010906

ET Fr: translation filed
PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

PLBQ Unpublished change to opponent data

Free format text: ORIGINAL CODE: EPIDOS OPPO

PLBF Reply of patent proprietor to notice(s) of opposition

Free format text: ORIGINAL CODE: EPIDOS OBSO

26 Opposition filed

Opponent name: ALCAN INTERNATIONAL LIMITED

Effective date: 20020502

PLBF Reply of patent proprietor to notice(s) of opposition

Free format text: ORIGINAL CODE: EPIDOS OBSO

PLBF Reply of patent proprietor to notice(s) of opposition

Free format text: ORIGINAL CODE: EPIDOS OBSO

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20041122

Year of fee payment: 8

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20050117

Year of fee payment: 8

RDAF Communication despatched that patent is revoked

Free format text: ORIGINAL CODE: EPIDOSNREV1

RDAG Patent revoked

Free format text: ORIGINAL CODE: 0009271

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: PATENT REVOKED

27W Patent revoked

Effective date: 20050315