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EP0429019A1 - Verfahren zur Herstellung einer Legierung mit hoher Reaktionsfähigkeit - Google Patents

Verfahren zur Herstellung einer Legierung mit hoher Reaktionsfähigkeit Download PDF

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Publication number
EP0429019A1
EP0429019A1 EP90121960A EP90121960A EP0429019A1 EP 0429019 A1 EP0429019 A1 EP 0429019A1 EP 90121960 A EP90121960 A EP 90121960A EP 90121960 A EP90121960 A EP 90121960A EP 0429019 A1 EP0429019 A1 EP 0429019A1
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EP
European Patent Office
Prior art keywords
alloy
melting point
point temperature
granules
ingot
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.)
Withdrawn
Application number
EP90121960A
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English (en)
French (fr)
Inventor
Hideo C/O Patent & License Department Nakamura
Tomoo C/O Patent & License Department Izawa
Naoki C/O Patent & License Department Sakata
Iehisa C/O Patent & License Department Takezawa
Toshio C/O Patent & License Department Nayuki
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.)
JFE Engineering Corp
Original Assignee
NKK Corp
Nippon Kokan 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
Application filed by NKK Corp, Nippon Kokan Ltd filed Critical NKK Corp
Publication of EP0429019A1 publication Critical patent/EP0429019A1/de
Withdrawn legal-status Critical Current

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    • 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
    • C22C1/02—Making non-ferrous alloys by melting

Definitions

  • the present invention relates to a method for producing a high reactive alloy containing elements having a high melting point temperature.
  • Methods for producing a high reactive alloy containing at least one metallic element having a high melting point temperature are roughly divided into (a) a melting process, and (b) a powder sintering process.
  • the melting process is a process for converting alloy components to an alloy by melting the alloy components.
  • the melting furnace an electron beam melting furnace, plasma melting furnace, vacuum arc melting furance, argon arc melting furnace or the like is used.
  • granules or powders of alloy elements are pressed into a compact, and the compact thus produced is used as a consumable electrode.
  • the consumable electrode is melted and an ingot is produced.
  • the above-mentioned melting process is widly used as a process for producing Ti alloy.
  • this melting process has difficulties in that those alloy elements each having a high melting point temperature remain not melted, which makes it impossible to produce a uniform ingot.
  • the powder sintering process is widely applied to alloys such as alloys of W, Mo and the like which have higher melting point tempertures than those used in the melting process.
  • alloys such as alloys of W, Mo and the like which have higher melting point tempertures than those used in the melting process.
  • the compact is sintered and formed into a compact.
  • This process has disadvantages such that the material powders are expensive and impurities are liable to be included into the compact due to conversion of metals and alloys to powders.
  • the present invention provides a method for producing a high reactive alloy, comprising the steps of: producing an alloy containing a metal having a high melting point temperature and Al, a melting point temperature of said alloy being lowered to less than the melting point temperature of said metal; crushing said alloy to form granules of alloy; mixing said granules of alloy with metallic granules having a high melting point temperature, which has components other than components constituting said alloy, to make a mixture of said granules of alloy and said metallic granules; pressing said mixture into a compact to form the compact; and melting said compact by means of electron beams, Al in said alloy being evaporated and an ingot being produced.
  • the present invention provides another method for producing a high reactive alloy, comprising the steps of: producing an alloy containing a metal having a high melting point temperature and Al, a melting point temperature of said alloy being lowered to less than the melting point temperature of said metal; crushing said alloy to form granules of alloy; mixing said granules of alloy with metallic granules having a high melting point temperature, which has components other than components constituting said alloy, to make a mixture of said granules of alloy and said metallic granules; pressing said mixture into a compact to form the compact; and premelting said compact, a first ingot being produced; and melting said first ingot by means of electron beams , Al in said alloy being evaporated and a second ingot being produced.
  • the present invention provides another method for producing a high reactive alloy, comprising the steps of: producing an alloy containing a metal having a high melting point temperature and Al, a melting point temperature of said alloy being lowered to less than the melting point temperature of said metal; crushing said alloy to form granules of alloy; mixing said granules of alloy with metallic granules having a high melting point temperature, which has components other than components constituting said alloy, to make a mixture of said granules of alloy and said metallic granules; and melting said mixture by means of electron beams, Al in said alloy being evaporated and an ingot being produced.
  • the present invention provides another method for producing a high reactive alloy, comprising the steps of: producing an alloy containing a metal having a high melting point temperature and Al from material ore, metallic granules, reducing agent and thermal booster and casting said alloy into a mold to form a first ingot; and melting said ingot by means of electron beams, Al in said alloy being evaporated and a second ingot being produced.
  • the present invention provides still another method for producing a high reactive alloy, comprising the steps of: producing a metal having a high melting point temperature and Al from material ore, first metallic granules, reducing agent and thermal booster and casting said metal into a mold to form a first ingot; crushing said ingot to form granules of alloy; mixing said granules of alloy with a second metallic granules to produce a mixture of said granules of alloy and said second metallic granules; pressing said mixture into a compact and producing a compact; and melting said compact as a consumable electrode by means of electron beams, Al in said alloy being evaporated and a second ingot being produced.
  • the present invention provides yet another method for producing a high reactive alloy, comprising the steps of: crushing ingots produced by means of the aforementioned methods; mixing granules of said ingot with metallic granules as components of alloy and making a mixture of said granules of said ingot and said metallic granules; pressing said mixture into a compact; and melting said compact in a melting furance.
  • a great amount of molten metal is charged into a crucible made of refractory.
  • a feedstock is added to the molten metal.
  • Said molten metal is sufficiently heated and left for a long time. Since the crucible made of refractory cannot be applied to the case of a high reactive alloy, a water-cooled copper vessel as a reaction vessel for converting metals to alloy is required to be used. However, since the volume of molten metal cannot be increased in the copper vessel, it is difficult to keep the great amount of molten metal, which is disadvatageous from the viewpoint of making an alloy.
  • a great difference of melting point temperatures generally means a great defference of vapor pressures.
  • elements having a higher vapor pressure are preferentially evaporated, which makes it difficult to regulate components in the metals.
  • the present inventors payed attention to the fact that difficulties in conversion of high reactive metals to an alloy as mentioned above were caused by the difference of the melting point temperatures among metals.
  • the Al containing alloy whose melting point temperature is lowered by preliminarily converting the high reactive metals and Al to an alloy is used.
  • the difference of the melting point temperatures is large when a metal having a high melting temperature and a metal having a low melting temperature are used.
  • the Al containing alloy whose melting point temperature is lowered by converting the high reactive metals and Al to an alloy and the metal having a low melting point temperature are used, the difference of the melting point temperatures is decreased. Accordingly, when the Al containing alloy is used, the difference of the melting point tempearatures is decreased, which makes it easy to produce an alloy.
  • the reason for obtaining the feedstock by producing the alloy by adding Al to a metal is that Al can be easily evaporated and removed by means of the vacuum refining after the production of the alloy since the vapor pressure of Al is comparatively high except that the effect of the low melting point temperature of the Al can be expected. Further, since a vacuum degree in the electron beam melting furnace reaches 10 ⁇ 4 Torr, Al can be easily evaporated and removed.
  • the vacuum degree in melting furnaces other than the electron beam melting furnace is about 10 ⁇ 2 Torr even if a pressure in the melting furnaces is lower than the atmospheric pressure. The electron beam melting furnace is superior to the other melting furnaces in the evaporation and removal of Al.
  • the lowest limit of the concentration of Al in the Al containing alloy is determined in consideration for the difference of the melting point temperatures between the Al containing alloy and a mother phase metal. Since the highest limit of the melting point temperatures is determined by individual properties such as the melting rate of an alloy to be the object and the like, the highest limit cannot be unconditionally determined. However, the difference of the melting point temperatures between the above-mentioned alloy and the mother phase metal is desired to be about 600 °C or less. There is a tendency such that the larger the Al content in the Al containing alloy, the lower the melting point temperature of the Al containing alloy. However, when the concentration of Al is high, the amount of evaporating Al is increased in the electron beam melting at the successive step, which can interfere with a normal operation condition. Accordingly, the highest limit of the concentration of Al is determined by the amount of evaporating Al. The amount of evaporating Al is determined by an equipment condition of the electron beam melting furnace.
  • An alloy of Al and at least one sort of metal having a high melting point temperature is produced by means of an aluminium thermite reduction process at low cost.
  • this aluminium thermite reduction process at least one sort of oxide of metal having a high melting point temperature is reduced by excessive Al.
  • the Al content in the alloy is control led by regulating the amount of Al.
  • an appropriate thermal booster is added to the alloy.
  • An alloy ingot produced by means of the aluminium thermite reduction process is used fundamentally as it is as a feedstock for the electron beam melting furnace at the successive step.
  • the alloy ingot can be premelted.
  • the alloy ingot is melted in the melting furnace such as the vacuum arc melting furnace, plasma melting furnace or induction skull crucible melting furnace at atmospheric pressure or at a pressure of 10 ⁇ 2 Torr.
  • the alloy ingot can be melted in the melting furnace of the inert atmosphere.
  • pure Al or metal having a high melting temperature can be added to the alloy ingot to regulate the components in the alloy ingot if necessary.
  • a high reactive metal of the object which contains metals having high melting point temperatures, is produced by evaporating Al in the Al containing alloy in the electron beam melting furnace with the use of the Al containing alloy obtained in such a manner as described above and the mother phase metal.
  • the feedstocks if necessary during the production of the high reactive alloy, a high reactive alloy of multiple components can be produced.
  • the high reactive alloy as described above is an alloy which cannot be melted, reacting with a refractory crucible made mainly of ordinary oxides in the molten state.
  • the metals having high melting point temperatures are Ti, Nb, Mo, W, Sr, Ta, V and the like, and their melting point temperatures are 1650 °C or more.
  • Fig.1 is a vertical sectional view illustrating the electron beam melting furnace used in the method of the present invention.
  • Fig.1 shows the case where all the amount of the feedstock used is a compact.
  • reference numeral 1 denote an airtight vessel, 2 a compact, 5a and 5b electron guns. The ranges shown with dotted lines which are irradiated are various.
  • Reference numeral 3 denotes a hearth which receives molten metal 8 produced by melting the above-mentioned compact and promotes the evaporation of Al and conversion of metals into an alloy.
  • Reference numeral 4 denotes a continuous casting mold, into which the above-mentioned molten metal is cast, and 9 a high reactive alloy produced.
  • the compact is successively melted by the electron beams 7a from the electron guns 5a and a molten metal flows into the hearth 3.
  • the molten metal 8 in the hearth 3 is kept at a predetermined temperature by means of the electron guns 5a and 5b.
  • Al in the molten metal is evaporated and the conversion of the molten metal 8 to an alloy goes on.
  • the aforementioned Al is evaporated in the form of a pure Al or a suboxide of Al, for example, Al2O, and discharged out of the airtight vessel 1.
  • the electron beams from the electron gun 5b keep the molten metal 8 at a predetermined temperature and prevent the molten metal 8 from being solidified by irradiating the upper portion of the mold and a portion at the vicinity of an outflow portion in the hearth 3, through which the molten metal 8 flows out.
  • the mold 4 is a continuous casting mold.
  • the airtight vessel 1 is used to cause the atmosphere inside the electron beam melting furnace to be highly vacuous.
  • a well-known vacuum device (not specifically shown ) is used in this Preferred Embodiment.
  • the vacuum degree is determined to be about 10 ⁇ 4 Torr.
  • the elements having high vapor pressures evaporate together with Al, which decreases the yield of the elements.
  • the difference of the vapor pressures among the constiutent elements is large, the temperature of the molten metal produced by the electron beam melting or the melting time is controlled.
  • the yield of the elements can be increased without excessively evaporating the elements by controlling the temperature or the melting time of the molten metal produced by the electron beam melting, by which the yield of the elements is stabilized
  • Fig.2 is a graphical representation designating the relationship between the melting time and the content of the components in the electron beam melting. The result obtained at the time when a Nb-45 wt.% Ti-10 wt.% Al alloy was melted and the temperature of the molten alloy was kept at 2200°C is shown. The abscissa denotes the time, during which the molten metal was kept as it was, and the ordinate the amount of Al and Ti contained in the produced alloy. Fig.2 shows the result obtained by sampling the molten metal with the lapse of time in a batch melting in the test. In the case of the continuous melting, time on the ordinate corresponds to the melting rate.
  • Fig.2 initially, Al is evaporated and the concentration of Al is lowered under the condition of a predetermined melting temperature. After the concentration of Al has decreased to zero, Ti begins to be evaporated. When the molten metal further continues to be irradiated by the electron beams, Ti is evaporated excessively. Accordingly, to obtain a Nb-Ti alloy having a predetermined concentration of the elements, it is good to stop melting at the moment when the concentration of Al comes to zero, that is, at "A" point as shown in Fig. 2. The moment when the concentration of Al reaches substantially zero is deterimined by the temperature of the molten metal and the melting time, that is, by the reaction time.
  • a drip melting process can be used.
  • the hearth 3 is not arranged, but drops of the molten metal produced by melting the compact 2 by means of the electron guns 5 directly flow into the mold 9.
  • the components are easily regulated by charging components into the hearth 2, but the hearth 3 is required to be arranged and the power of the electron guns 5a and 5b is required to be increased.
  • the components are hard to regulate, but it is advantageous that an equipment cost is low. It can be determined in response to the purpose of melting which process is used.
  • the above mentioned two melting processes are processes wherein a compact is used as a feedstock. It is unncessary, however, to use the compact, but crushed materials or granular materials can be directly added to the molten metal or directly charged into the hearth in the electron beam melting furnace. Further, to regulate the amount of evaporating Al in the alloy produced in the electron beam melting furnace and the concentration of the components in the ingot, there are cases where the electron beam melting is carried out more than twice.
  • the electron beam melting furnace As the melting furnace for regulating the final components, the electron beam melting furnace, vacuum arc melting furnace, plasma melting furnace or induction skull crucible melting furance can be used.
  • Those furnaces are furnaces, to which refractory as a material for a crucible is not applied, and in which the high reactive alloy can be produced smoothly.
  • the high reactive alloy containing multiple components can be produced. Since the concentrations of many components are required to be regulated when the high reactive alloy of multiple components is produced, a separate melting step as the final step is desired to be arranged.
  • the melting furance wherein the final components are regulated is desired to be a melting furance wherein refractory is not applied to the crucible.
  • the vacuum arc melting furnace, plasma melting furnace, induction skull crucible melting furnace, electron beam melting furnace or the like is pointed out.
  • the difference of the melting point temperatures among the feedstocks at the final step is desired to be as small as possible. Since the melting point temperature of the high reactive alloy produced in this process is lowered compared with that of pure metal, the high reactive alloy is fit to use for a master alloy.
  • the master alloy is referred to as an alloy, which is produced in the electron beam melting furnace and which contains metals having high melting point temperatures.
  • the concentration of metal having a high melting point temperature in the master alloy is determined by how to set the melting point temperature of the master alloy. This is determined by a method of melting at the melting step wherein the master alloy is used as a material. For example, in the case of using a melting furnace wherein a high energy density is obtained as in the electron beam melting furnace or plasma melting furnace, the melting point temperature of the aforementioned master alloy can be higher than that in the case of using the vacuum arc melting furnace. In the case of using the electron beam melting furnace or plasma melting furnace, the melting point temperature of the aforementioned master alloy is desired to be 2300 °C or less. In the case of using the vacuum arc melting furance, the melting point temperature of the aforementioned master alloy is desired to be 2100 °C or less.
  • the content of Mo is 70 wt.% at its maximum. In the case of setting the melting point temperature for 2100°C , the content of Mo is 55 wt.% at its maximum.
  • a Ti alloy ingot is produced by using a master alloy as follows: The master alloy is crushed. Powder of the master alloy, a Ti source such as sponge Ti and other alloy elements are well mixed with each other. The mixture thereof is pressed into a compact and an consumable electrode is prepared. Melting processes are carried out more than twice in the vacuum arc melting furnace, and a Ti alloy ingot to be the object is produced.
  • Fig.3 is a schematic illustration showing a vacuum arc melting process of the present invention.
  • the vacuum arc melting process is carried out in a vacuum, but an airtight vessel is omitted in Fig. 3.
  • reference numeral 11 denotes a consumable electrode produced by pressing the sponge Ti, master alloy and other alloy elements into a compact.
  • the consumable electrode 11 is melted from the bottom portion thereof by means of an arc 14, and molten metal produced in this way forms a pool 15 of the molten metal in a water-cooled copper mold 13.
  • the surface of the pool 15 of the molten metal rises as the melting goes on, and the molten metal is successively solidified, by which a Ti alloy ingot 12 to be the object which has a high melting point temperature is produced.
  • This Nb-Ti ingot was remelted in the plasma hearth melting furance to regulate the components in this alloy , and an Nb-47 wt.% Ti alloy of 74 kg was produced by adding 1.8 kg of Ti to the Nb-Ti alloy.
  • This ingot was melted under the condition of the power of the electron beam of 190 kW, the melting rate of 60 kg/Hr and the operational vacuum degree of 10 ⁇ 4 Torr, and an ingot of an Nb-49 wt.% Ti alloy of 83 kg and 136 mm in diameter was produced.
  • the compact was used as the feedstock in the Examples 1 to 4, but granular melting materials were used in this Example 5.
  • 50 kg of granular Nb-20 wt.% Al produced by means of the aluminium thermite process was well mixed with 37 kg of scrap titanium to make the feedstock.
  • This feedstock was charged into a hearth from a material feeder (not shown in Fig.1 ).
  • the feedstock was melted under the condition of the power of the electron beam of 200 kW, the melting rate of 60 kg/Hr and the operational vacuum degree of 10 ⁇ 4 Torr.
  • An ingot of Nb-47 wt.% Ti alloy of 75 kg and 136 mm in diameter was produced.
  • Nb ore 65 kg of Nb ore, 95 kg of Ti ore ( rutile ) and 69 kg of powdery aluminium together with thermal booster were mixed with each other, and the mixture thereof was melted by means of the aluminium thermite process, by which a Nb-Ti-Al alloy of 87 kg was produced.
  • This alloy was cast into a mold of 100 mm in diameter to make a compact.
  • the composition of the alloy on this occasion was Nb-43 wt.% Ti -11 wt.% Al.
  • the compact was melted under the condition of the power of the electron beam of 200 kW, the melting rate of 60 kg/Hr and the operational vacuum degree of 10 ⁇ 4 Torr, by which an ingot of Nb-47 wt.% Ti alloy of 75 kg and 136 mm in diameter was produced.
  • Nb ore 64 kg of Nb ore, 18 kg of Ti ore ( rutile ) 40 kg of sponge titanium and 34 kg of powdery aluminium together with thermal booster were mixed with each other , and the mixture thereof was melted by means of the aluminium thermite process, by which a Nb-Ti-Al alloy of 87 kg was produced.
  • This alloy was cast into a mold of 100 mm in diameter to make a compact 2.
  • the composition of the alloy on this occasion was Nb-43 wt.%Ti-11 wt.% Al.
  • the compact was melted under the condition of the power of the electron beam of 200 kW, the melting rate of 60 kg and the operational vacuum degree of 10 ⁇ 4 Torr, by which an ingot of Nb-46 wt.% Ti alloy of 75kg and 136 mm in diameter was produced.
  • This consumable electode as the compact was melted under the condition of the power of the electron beam of 200 kW, the melting rate of 60 kg/Hr and the operationalloy vacuum degree of 10 ⁇ 4 Torr, by which an ingot of Nb-47 wt.% Ti alloy of 75 kg and 136 mm in diameter was produced.
  • the compact was twice melted in the electron beam melting furnace under the condition of the power of the electron beam of 230 kW, the melting rate of 40 kg/Hr and the operational vacuum degree of 10 ⁇ 4 Torr, and Al was evaporated and removed from the alloy, by which an ingot of Nb-43 wt.% Ti-25 wt.% Ta alloy of 102kg and 136 mm in diameter was produced.
  • Nb-14 wt.% Al alloy produced by means of the aluminium thermite process was well mixed with 12 kg of sponge titanium, and the mixture thereof was pressed into a compact of 71 kg and 100 mm in diameter.
  • the composition of the compact was Nb-12 wt.% Al-17 wt.% Zr.
  • the compact was melted under the condition of the power of the electron beam of 190 kW, the melting rate of 50 kg/Hr and the operational vacuum degree of 10 ⁇ 4 Torr, by which an ingot of Nb-15 wt.% Zr alloy of 59 kg and 136 mm in diameter was produced.
  • the alloy as the compact 2 was melted by means of the hearth melting process in the electron beam melting furance, and Al was evaporated and removed from the alloy, by which an ingot of Ti-29 wt.% Mo alloy of 200 mm in diameter was produced.
  • the melting point of the Ti-29 wt.% Mo alloy was about 1900°C.
  • This master alloy ingot was crushed and granulated. The particle size of the granulated alloy was made uniform.
  • An ingot of Ti-18 wt.% V-18 wt.% Mo alloy of 125 kg and 200 mm in diameter was produced by melting the compact in the electron beam melting furnace and evaporating and removing Al. This master alloy was crushed and the crushed master alloy was granulated. The particle size of the granulated alloy was made uniform.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)
EP90121960A 1989-11-20 1990-11-16 Verfahren zur Herstellung einer Legierung mit hoher Reaktionsfähigkeit Withdrawn EP0429019A1 (de)

Applications Claiming Priority (8)

Application Number Priority Date Filing Date Title
JP30116489 1989-11-20
JP301164/89 1989-11-20
JP31879/90 1990-02-13
JP3187990 1990-02-13
JP12495490 1990-05-15
JP124954/90 1990-05-15
JP12495190 1990-05-15
JP124951/90 1990-05-15

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EP90121960A Withdrawn EP0429019A1 (de) 1989-11-20 1990-11-16 Verfahren zur Herstellung einer Legierung mit hoher Reaktionsfähigkeit

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CA (1) CA2030274A1 (de)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108070724A (zh) * 2016-11-18 2018-05-25 宁波创润新材料有限公司 混料方法以及铸锭的熔炼方法
EP3572539A1 (de) * 2018-05-22 2019-11-27 Bernd Spaniol Verfahren zur herstellung einer nbti-legierung
CN114908261A (zh) * 2022-05-20 2022-08-16 西北有色金属研究院 一种铌锆碳合金铸锭的制备方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR1458238A (fr) * 1965-07-13 1966-03-04 Commissariat Energie Atomique Procédé de préparation d'alliage germanium-silicium
US3342250A (en) * 1963-11-08 1967-09-19 Suedwestfalen Ag Stahlwerke Method of and apparatus for vacuum melting and teeming steel and steellike alloys
US3700428A (en) * 1969-05-30 1972-10-24 Anvar Method of preparation of alloys of refractory metals
FR2231768A1 (en) * 1973-05-29 1974-12-27 Zaboronok Georgy Electron beam melting of refractory metals - using low-density briquettes in a channel
EP0073585A1 (de) * 1981-08-26 1983-03-09 Special Metals Corporation Umschmelzverfahren für Legierungen
GB2160224A (en) * 1984-05-29 1985-12-18 Toho Titanium Co Ltd Consumable electrode of high-melting point alloys
EP0259856A2 (de) * 1986-09-09 1988-03-16 Nippon Kokan Kabushiki Kaisha Verfahren zur Herstellung von Legierungen

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3342250A (en) * 1963-11-08 1967-09-19 Suedwestfalen Ag Stahlwerke Method of and apparatus for vacuum melting and teeming steel and steellike alloys
FR1458238A (fr) * 1965-07-13 1966-03-04 Commissariat Energie Atomique Procédé de préparation d'alliage germanium-silicium
US3700428A (en) * 1969-05-30 1972-10-24 Anvar Method of preparation of alloys of refractory metals
FR2231768A1 (en) * 1973-05-29 1974-12-27 Zaboronok Georgy Electron beam melting of refractory metals - using low-density briquettes in a channel
EP0073585A1 (de) * 1981-08-26 1983-03-09 Special Metals Corporation Umschmelzverfahren für Legierungen
GB2160224A (en) * 1984-05-29 1985-12-18 Toho Titanium Co Ltd Consumable electrode of high-melting point alloys
EP0259856A2 (de) * 1986-09-09 1988-03-16 Nippon Kokan Kabushiki Kaisha Verfahren zur Herstellung von Legierungen

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108070724A (zh) * 2016-11-18 2018-05-25 宁波创润新材料有限公司 混料方法以及铸锭的熔炼方法
EP3572539A1 (de) * 2018-05-22 2019-11-27 Bernd Spaniol Verfahren zur herstellung einer nbti-legierung
CN114908261A (zh) * 2022-05-20 2022-08-16 西北有色金属研究院 一种铌锆碳合金铸锭的制备方法

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Withdrawal date: 19921215