Process and apparatus for producing metallic glass

TECHNICAL FIELD

This invention relates to processes and apparatus for producing bulk metallic glasses (bulk amorphous metals) of various desired shapes exhibiting excellent strength properties which are free from the so called cold shuts, which are the amorphous regions formed by meeting of the surfaces of the molten metal.

BACKGROUND ART

Various methods for producing amorphous materials have been proposed. Exemplary such methods include the method wherein a molten metal or alloy in liquid state is solidified by quenching and the resulting quenched metal (alloy) powder is compacted at a temperature below the crystallization temperature to produce a solid of the predetermined configuration having the true density; and the method wherein a molten metal or alloy is solidified by quenching to directly produce an ingot of the amorphous material having the predetermined configuration. Almost all amorphous material produced by such conventional methods had an insufficiently small mass, and it has been impossible to produce a bulk material by such conventional methods. Another attempt for producing a bulk material is solidification of the quenched powder. Such attempt, however, has so far failed to produce a satisfactory bulk material.

For example, the amorphous material produced in small mass have been produced by melt spinning, single roll method, planar flow casting and the like whereby the amorphous material in the form of thin strip (ribbon) in the size of, for example, about 200 mm in the strip width and about 30 μm in the strip thickness are produced. Use of such amorphous materials for such purposes as the core material of a transformer has been attempted, but so far, most amorphous materials produced by such methods are not yet put to industrial use. The techniques that have been used for solidification forming or compaction molding the quenched powder into an amorphous material of a small mass include CIP, HIP, hot press, hot extrusion, electro-discharge plasma sintering, and the like. Such techniques, however, suffered from the problems of poor flow properties due to the minute configuration, and the problem of temperature-dependent properties, namely, incapability of increasing the temperature above the glass transition temperature. In addition, forming process involves many steps, and the solidification formed materials produced suffer from insufficient properties as a bulk material. Therefore, such methods are still insufficient.

Recently, the inventors of the present invention found that a number of ternary amorphous alloys such as Ln-Al-TM, Mg-Ln-TM, Zr-Al-TM, Hf-Al-TM and Ti-Zr-TM (wherein Ln is a lanthanide metal, and TM is a transition metal of the Groups VI to VIII) ternary systems have low critical cooling rates for glass formation of the order of 10

2

K/s, and can be produced in a bulk shape with thickness up to about 9 mm by using a mold casting or a high-pressure die casting method.

It has been, however, impossible to produce a large-sized amorphous alloy material of desired configuration irrespective of the production process. There is a strong needs for the development of a new solidification technique capable of producing a large-sized amorphous alloy material and an amorphous alloy having a still lower critical cooling rate for enabling the production of the amorphous metal material of larger size.

In view of such situation, the inventors of the present invention proceeded with the investigation of the bulk amorphous alloy using the ternary alloy by focusing on the effect of increasing the number of the alloy constituents each having different specific atom size as exemplified by the high glass formation ability of the ternary alloy primarily attributable to the optimal specific size distribution of the constituent atoms that are mutually different in size by more than 10%. As a consequence, the inventors found amorphous alloys of Zr-Al-Co-Ni-Cu alloy systems, Zr-Ti-Al-Ni-Cu alloy systems, Zr-Ti-Nb-Al-Ni-Cu alloy systems, and Zr-Ti-Hf-Al-Co-Ni-Cu alloy systems that have significantly lower critical cooling rates in the range of from 1 to 100 K/s, and disclosed in U.S. Pat. No. 5,740,854 (Unites States Patent corresponding to JP-A 6-249254) that alloys of Zr-Al-Ni-Cu alloy systems may be produced into a bulk amorphous alloy material with a size of up to 16 mm in diameter and 150 mm in length by quenching the melt in a quartz tube in water.

The inventors of the present invention also disclosed in U.S. Pat. No. 5,740,854 and JP-A 6-249254 that the resulting bulk amorphous alloy material has a tensile strength of as high as 1500 MPa comparable to the compressive strength and break (crack) accompanying serrated plastic flow in the tensile stress-strain curves, and that such high tensile strength and serrated plastic flow phenomenon result in excellent malleability despite the large thickness of the bulk amorphous alloy produced by casting.

On the bases of the above-described findings of the bulk amorphous alloy production, the inventors of the present invention have continued an intensive study to thereby develop a method that is capable of producing a glassy metal material of even larger size with various configurations by a simple procedure. As a consequence, the inventors proposed a process for producing metallic glass by suction casting wherein an amorphous material of large size having excellent properties can be readily produced in simple operation by instantaneously casting the molten metal material in a mold cooled with water.

Such process of metallic glass production by suction casting as disclosed in U.S. Pat. No. 5,740,854 and JP-A 6-249254 is capable of producing a columnar bulk amorphous material, and the thus produced columnar bulk amorphous material exhibits good properties. In this prior art process, however, the bottom of the water cooled crucible is moved downward at a high speed and the molten metal is instantaneously cast into a vertically extending water-cooled mold to thereby attain a high moving speed of the molten metal and a high quenching rate.

In such production process, the molten metal is fluidized with the surface of the molten metal becoming wavy, and the surface area of the molten metal is increased with the increased surface area contacting the outer atmosphere. In some extreme cases, the molten metal is fluidized into small separate bulk molten metal droplets before being cast into the vertically extending mold. Therefore, the surfaces of the molten metal often meet with each other upon casting of the molten metal into the vertically extending water-cooled mold, and the so called cold shuts or discontinuities are formed at the interfaces of the thus met interfaces. The resulting bulk amorphous material thus suffered from inferior properties at such cold shuts, and hence, the bulk amorphous material as a whole suffered from poor properties.

In addition, the metal material is melted in a water-cooled hearth, and the part of the metal in contact with the hearth is at a temperature below the melting point of the metal material even if the metal material is in molten state. The part in contact with the hearth, therefore, is likely to induce nonuniform nucleation. In the above-described suction casting, such part of the molten metal which may induce uniform nucleation is also cast into the vertically extending water-cooled mold and there is a fair risk of crystal nucleus formation in the corresponding part.

Furthermore, since the bottom of the water-cooled crucible is moved downward at a high speed, the process suffered from a fair chance of the molten metal entering into the gaps formed between moveable parts and the like to reduce the reproducibility. In some cases, the molten material entered is even caught in such gaps to result in failure, stop, or incapability of operation.

DISCLOSURE OF INVENTION

An object of the present invention is to obviate the drawbacks of the above-described techniques and to provide processes and apparatus for producing a metallic glass which is free from the so called cold shuts which are formed by amorphousizing at the interfaces where the surfaces of the molten metal cooled to a temperature below the melting point by contact with outer atmosphere have met; and which is also free from crystalline part where crystal nuclei have developed through nonuniform nucleation by the molten metal below its melting temperature. In other words, an object of the present invention is to provide a simple process and a simple apparatus for producing a metallic glass which are capable of producing a bulk metallic glass of desired shape exhibiting excellent strength properties in a simple procedure at a high reproducibility by selectively cooling the molten metal above its melting temperature at a rate above the critical cooling rate.

To attain such object, there is provided by the present invention a process for producing a bulk metallic glass of desired shape comprising the steps of:

filling a metal material in a hearth;

melting said metal material by using a high-energy heat source which is capable of melting said metal material;

pressing a molten metal at a temperature above the melting point of said metal material to deform the molten metal at a temperature above the melting point into the desired shape by at least one of compressive stress and shear stress, while avoiding surfaces of the molten metal cooled to a temperature below the melting point of said metal material from meeting with each other during the pressing; and

cooling said molten metal at a cooling rate higher than the critical cooling rate of the metal material simultaneously with or after said deformation to produce the bulk metallic glass of desired form.

According to the present invention, there is also provided by a process for producing a bulk metallic glass wherein said molten metal at a temperature above the melting point of said metal material is pressed while avoiding not only the meeting of the surfaces of the molten metal cooled to a temperature below the melting point of said metal material with each other but also meeting of such molten metal surface with another surface cooled to a temperature below the melting point of said metal material.

In this process, the pressing and deforming of said molten metal is preferably accomplished by selectively rolling said molten metal at a temperature above the melting point of said metal material into the plate shape or other desired shape with a cooled roll for rolling.

Preferably, after melting said metal material filled in the hearth, the molten metal at a temperature above the melting point rising over the hearth is selectively rolled with simultaneous cooling by rotating said cooled roll and moving the hearth in relation to said high energy heat source and said rotating cooled-roll to thereby produce a metallic glass of plate shape or other desired shape.

It is also preferable to use a hearth of an elongated shape, and the melting, rolling of the molten metal at a temperature above the melting point, and the cooling are continuously conducted by using such hearth of an elongated shape and moving such hearth in relation to said high energy heat source and said rotating cooled roll to thereby continuously produce a metallic glass of elongated shape or other desired shape.

The cooled roll for rolling is preferably provided at the position corresponding the hearth with a molten metal-discharging mechanism for discharging the molten metal at a temperature higher than the melting point from the hearth, said molten metal-discharging mechanism being fabricated from a material of low thermal conductivity.

It is also preferable to accomplish the pressing and deforming of said molten metal by selectively transferring said molten metal at a temperature above the melting point of said metal material into a cavity of the desired shape in the mold provided near said hearth without fluidizing the molten metal, and pressing the molten metal with a cooled upper mold without delay to forge the molten metal into the desired shape together with simultaneous cooling.

In this case, after melting said metal material filled in the hearth, said hearth and said lower mold is preferably moved to right underneath said upper mold and the upper mold is descended toward said lower mold without delay to thereby selectively transfer the molten metal at a temperature above the melting point into said mold where it is pressed and cooled to produce the metallic glass of desired shape by forging.

To attain the above-described object, there is provided by the present invention an apparatus for producing a metallic glass comprising a hearth for accommodating a metal material, a means for melting said metal material in said hearth, a means for pressing a molten metal which has been melted by said metal material-melting means at a temperature higher than the melting temperature to deform the molten metal into the desired shape by at least one of compressive stress and shear stress, while avoiding the surfaces of the molten metal cooled to a temperature below the melting point of said metal material from meeting with each other during the pressing; and a means for cooling said molten metal at a cooling rate higher than the critical cooling rate of the metal material simultaneously with or after said deformation by said pressing means.

In this apparatus, said molten metal is preferably pressed while avoiding not only the meeting of the surfaces of the molten metal cooled to a temperature below the melting point of said metal material with each other but also meeting of such molten metal surface with another surface cooled to a temperature below the melting point of said metal material.

Preferably, said pressing means doubles as said cooling means.

Preferably, said pressing means has a cooled roll for rolling and a mold provided near said hearth.

Preferably, the molten metal at a temperature above the melting point rising over the hearth is cast into said mold by said cooled roll by rotating said cooled roll and moving said hearth and said mold in relation to said cooled roll and said melting means to accomplish the rolling by said cooled roll and said mold.

Preferably, said hearth is of elongated shape, and the rolling and the cooling by said cooled roll and said mold is continuously conducted by moving said hearth and said mold in relation to said cooled roll and said melting means.

Preferably, said cooled roll for rolling is provided at the position corresponding said hearth with a molten metal-discharging mechanism for discharging the molten metal at a temperature higher than the melting point from the hearth, said molten metal-discharging mechanism being fabricated from a material having low thermal conductivity.

Preferably, said pressing means has a lower mold provided near said hearth into which the molten metal discharged from said hearth is filled, and an upper mold which forges the molten metal filled in said lower mold together with said lower mold.

Preferably, after melting said metal material filled in the hearth, said hearth and said lower mold are moved in relation to said melting means and said upper mold until said upper mold is positioned at a position opposing said hearth and said lower mold, and the upper mold is descended or the lower mold is ascended without delay to thereby transfer the molten metal from said hearth into said mold where it is forged.

Preferably, said upper mold is provided at the position corresponding said hearth with a molten metal-discharging mechanism for discharging the molten metal at a temperature higher than the melting point from the hearth, said molten metal-discharging mechanism being fabricated from a material having low thermal conductivity.

The upper mold is preferably provided at the position corresponding the hearth with a molten metal-discharging mechanism for discharging the molten metal at a temperature higher than the melting point from the hearth, said molten metal-discharging mechanism being fabricated from a material of low thermal conductivity.

In the present invention, the phrase “meeting” of “the surfaces cooled” means the “meeting” of “the surfaces of the molten metal cooled to a temperature below the melting point of said metal material” in a narrower sense. In a broader sense, this phrase also include the case wherein “the surfaces of the molten metal cooled to a temperature below the melting point of said metal material” meet with “other surfaces cooled to a temperature below the melting point of said metal material” such as the surface of the hearth cooled by water. It should be noted that the phrase “the surfaces of the molten metal cooled to a temperature below the melting point of said metal material” are the surfaces of the molten metal cooled to a temperature below the melting point by contact with outer atmosphere, mold, hearth or the like.

The phrase “pressing a molten metal at a temperature above the melting point of said metal material to deform the molten metal, while avoiding the surfaces cooled to a temperature below the melting point of said metal material from meeting with each other during the pressing” used herein does not only mean the pouring of the molten metal maintained at a temperature above the melting point from the cooled hearth into the mold followed by pressing, while avoiding the formation of cold shuts which are formed by the meeting of the surfaces cooled to a temperature below the melting point of said metal material caused by fluidization or surface wave-formation. This phrase also includes use of a mold fabricated from a material such as quartz which is not thermally damaged at a temperature above the melting point of the metal material, and heating of the lower mold to a temperature near the melting point, preferably, to a temperature above the melting point, followed by pouring of the metal molten with a high energy source, for example, a radio frequency heat source and maintained at a temperature above the melting point into the preliminarily heated lower mold without forming any surface which is cooled to a temperature below the melting point; and pressing with the cooled upper mold to thereby conduct the pressing and quenching at a rate above the critical cooling rate. Namely, if the metal material used is a material with an extremely low critical cooling rate, the metal molten in a quartz tube may be directly poured and cooled in water while maintaining its shape.

In other words, the cold shuts are formed when the pressing, deformation, compression, shearing of the molten metal are not conducted at a rate higher than the critical cooling rate and meeting of the cooled surface are not avoided. When a metal having a certain critical cooling rate, for example, 10° C./sec is used, an amorphous bulk material without cold shuts can be produced only when the time between the molten state and the deformation and the decrease in temperature attain the predetermined critical cooling rate (higher than 10° C./sec in this case); and the meeting of the cooled surface is avoided.

The term “desired shape” used herein is not limited to any particular shape as long as the metallic glass material is formed through pressing or forging by using an upper press roll or forging mold of various contour and a lower press surface or forging mold of various contour which are controlled and cooled in synchronism. Exemplary shapes include, a plate, an unspecified profile plate, a cylindrical rod, a rectangular rod, and an unspecified profile rod.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1

is a flow sheet schematically showing an embodiment of the metallic glass production apparatus of rolling type used in carrying out the metallic glass production process according to the present invention.

FIG. 2

is a top view of water-cooled hearth and mold used in the metallic glass production apparatus of rolling type shown in FIG.

1

.

FIG. 3

schematically show an embodiment of the production of a plate-shaped amorphous bulk material in the metallic glass production apparatus of rolling type wherein an arc electrode is used for the heat source.

FIG. 3

a

is a schematic view of the process wherein the metal material is melted, and

FIG. 3

b

is a schematic view of the process wherein the molten metal is rolled and cooled.

FIGS. 4

a

and

4

b

are partial cross-sectional view and partial top view of essential parts of another embodiment of the metallic glass production apparatus of rolling type according to the present invention.

FIG. 5

is a flow sheet schematically showing an embodiment of the metallic glass production apparatus of forging type used in carrying out the metallic glass production process according to the present invention.

FIG. 6

schematically show an embodiment of the production of a plate-shaped amorphous bulk material in the metallic glass production apparatus of forging type wherein an arc electrode is used for the heat source.

FIG. 6

a

is a schematic view of the process wherein the metal material is melted, and

FIG. 6

b

is a schematic view of the process wherein the molten metal is forged and cooled.

FIG. 7

is X-ray diffraction pattern for the piece taken from the central region of the transverse section of the Zr

55

Al

10

Cu

30

Ni

5

alloy material produced in Example

14

of the present invention.

FIG. 8

is differential scanning calorimetry curve for the piece taken from the central region of the transverse section of the Zr

55

Al

10

CU

30

Ni

5

alloy material produced in Example 14 of the present invention.

FIG. 9

is a photomicrograph showing the metal structure in the central region of the transverse section of the Zr

55

Al

10

Cu

30

Ni

5

alloy material produced in Example 14 of the present invention.

BEST MODE FOR CARRYING OUT THE INVENTION

The processes and the apparatus for producing metallic glass of the present invention are described in detail by referring to the preferred embodiments shown in the attached drawings.

In the metallic glass production process of the present invention, a hearth, for example, a water-cooled copper hearth in the form of a recess is filled with a metal material which is preferably a mixture of a powder or pellets of metals having high amorphousizing properties. Next, the metal material is melted by means of a high energy heat source, for example, by an arc heat source after evacuating the chamber and maintaining the vacuum, or under reduced pressure, or after substituting the chamber with an inert gas with or without forced cooling of the hearth. (Melting in vacuum has the merit of retarded cooling of the molten metal due to the absence of convection compared to the casting at atmospheric pressure. The metal may be melted, for example, by means of electron beam.)

Next, the molten metal at a temperature above the melting point of the metal material is transferred into the cavity of the mold. More illustratively, in the case of the water-cooled hearth, the molten metal at a temperature above the melting point is selectively transferred into the mold cavity by directly pressing the molten metal in the hearth with a new mold or by transferring the molten metal mass into the mold cavity followed by pressing. In such transfer of the molten metal onto the mold cavity, the surfaces of the molten metal in contact with the atmosphere should be avoided from meeting with each other, and fluidization or surface weaving of the molten metal should be avoided. When the molten metal is pressed in the mold cavity, at least one of compression stress and shear stress is applied to the molten metal at a temperature higher than the melting temperature for deformation of the molten metal into the desired shape, and the molten metal at a temperature higher than the melting temperature is cooled at a rate higher than the critical cooling rate of the metal material after the deformation or simultaneously with the deformation.

For example, in an embodiment, the molten metal at a temperature above the melting point rising over the hearth is selectively rolled simultaneously with cooling into an ingot of plate shape or other desired shape by means of a cooled (water-cooled) roll for (metal) rolling disposed on the hearth (this process is referred to as (metal) rolling process). In this process, the hearth is moved in relation to the cooled roll for rolling which is rotated. When a hearth of an elongated shape is used, the metal material in the hearth may be melted in continuity by the high energy heat source in correspondence with the relative movement of the hearth, and the continuously melted metal at a temperature higher than the melting point is continuously rolled and cooled by the continuously rotating cooled roll for rolling to produce an ingot of plate shape or other desired shape. It should be noted that the cooled roll for rolling is preferably provided with a molten metal-discharging mechanism fabricated from a material of low thermal conductivity at the position corresponding the hearth to thereby discharge the molten metal at a temperature higher than the melting point from the hearth into the new mold surface (rolling surface).

In another embodiment, the molten metal in the hearth at a temperature higher than the melting point of the metal material is selectively transferred into the lower half of the mold having a cavity of desired shape provided near the hearth without causing fluidization or surface weaving of the molten metal, and the molten metal is immediately pressed with the cooled upper half of the mold which mates with the cavity of the lower mold for press forging of the molten metal, or alternatively, the mold may be cooled. simultaneously with the forging (this process is hereinafter referred to as forging process). In this process, the hearth and the lower mold are moved in relation to the high energy heat source and the upper mold to align the lower and the upper molds, and the lower and the upper molds are mated by either descending the upper mold or ascending the lower mold to press forge the molten metal in the lower mold at a temperature above the melting point simultaneously with the rapid cooling of the mold. It should be noted that the upper mold is preferably provided with a molten metal-discharging mechanism fabricated from a material of low thermal conductivity at the position corresponding the hearth to thereby discharge the molten metal at a temperature higher than the melting point from the hearth into the cavity of the lower mold.

As mentioned above, the first object of the present invention is to produce a bulk amorphous material of the desired final shape which is free from cold shuts, and hence, which is free from casting defects; and the second object is, in addition to the fist object, to produce a bulk amorphous material which is free from crystal nuclei resulting from the nonuniform nucleation. Therefore, the means for attaining such objects are not limited to the above-described processes, and any means can be adopted as long as the molten metal as a mass at a temperature above the melting point can be selectively formed into the final desired shape by directing compression stress and/or shear stress to the molten metal by pressing the molten metal while avoiding the meeting of the surfaces of the molten metal which had been in contact with the atmosphere by fluidization or surface weaving of the molten metal or the meeting of the preceding molten metal stream with the subsequent molten metal stream.

For example, most preferable means are use of a levitation device or the like wherein the metal material is melted and maintained at a temperature above the melting point in non-contacted state, and the use of cold crucible (skull melting) device or the like wherein the metal material is melted and maintained at a temperature above the melting point in a state resembling the non-contacted state. Sections of a sectional die, for example, two sections of a mold are moved toward the molten metal maintained at a temperature above the melting point in non-contacted state or in a state resembling the non-contacted state to thereby sandwich and press the molten metal into the desired final shape. In an alternative process, a material which does not melt at a temperature higher than the melting point of the metal material, which does not react with the molten metal, and which has excellent mechanical strength or a material which is not damaged by high temperature heating and rapid cooling is chosen in accordance with the type of the molten metal from such materials as carbon, nickel, tungsten, ceramics, and the like, and the lower half of the mold is fabricated from the thus selected material. The metal material is filled in the lower mold, melted, and pressed with the upper mold immediately after the melting of the metal material for press forming. Simultaneously with the pressing, the upper and lower molds may be cooled with a coolant such as a gas or water to produce the bulk amorphous material of desired final shape. In such a case, it is preferable that the lower mold is not cooled during the melting of the metal and the cooling of the lower mold is preferably started after the completion of the melting, and in such a case, the lower mold may be fabricated from any material as long as the lower mold can maintain the temperature near the melting point. For example, the lower mold may be fabricated from either a material of high conductivity or a material of low conductivity.

It should also be noted that, in the metal rolling process as described above, the metal rolling may be conducted by two-roll metal rolling process which is capable of producing a bulk amorphous material having desired surface pattern. In a single roll metal rolling process, the rolling and the cooling by the cooled roll for metal rolling may be accomplished not only by the reciprocal movement of the hearth in one direction but the hearth may be rotated within the horizontal plane so that the roll may be moved in different directions. In the forging process, the hearth and the lower mold may be rotated within the horizontal plane in addition to their reciprocal movement in one direction.

A bulk amorphous material of plate shape or other shape, namely, a large sized metallic glass bulk material is thus produced. The large sized metallic glass bulk material thus produced which has not experienced nonuniform solidification is a high density bulk amorphous material which is free from cold shuts and other casting defects, which is free from crystal nuclei resulting from nonuniform nucleation, and which has uniform strength properties, in particular, impact strength. Furthermore, the large sized metallic glass bulk material thus produced has been produced at once into the final desired shape adapted for its use, and no further processing is required.

When a metal material is melted in a metallic hearth, in particular, in a water-cooled copper hearth to obtain the molten metal at a temperature above the melting point of the metal material, the part of the molten metal in contact with the hearth is inevitably cooled to a temperature below the melting temperature, and nonuniform nucleation is induced by this part of the molten metal where crystal nuclei are present. The resulting bulk material, therefore, is likely to be a bulk amorphous material wherein crystalline phase is present. Even if the crystalline phase were present in the bulk amorphous material, the material can be used as a functional material having both the functionality of the amorphous phase and the functionality of the crystalline phase, namely, as a functionally gradient material as long as the material is sufficiently functional and free from cold shuts and other casting defects. Such functionally gradient material is also within the scope of the amorphous bulk material produced by the present invention.

The present invention may be applied for the alloys of almost Many combination of the elements including the above mentioned ternary alloys, Zr based alloys such as Zr-Al-Ni-Cu, Zr-Ti-Al-Ni-Cu, Zr-Nb-Al-Ni-Cu, and Zr-Al-Ni-Cu-Pd alloys and other multi-component alloys comprising four or more components to form the amorphous phase, as long as these alloys can be melted using high energy heat source such as the arc heat source. When such alloys are used for the metal material of the invention, it would be preferable to use the alloy in powder or pellet form to facilitate rapid melting of the alloy by high energy heat source. The form of the alloy, however, is not limited to such forms, and the metal material used maybe in any form as long as rapid melting is possible. Exemplary forms other than powder and pellets include wire, ribbon, rod, and ingot, and a metal material of any desired form may be adequately selected depending on the hearth, particularly the water-cooled hearth and the high-energy heat source employed.

The high-energy heat source used in the present invention is not limited to any particular type, and any heat source may be employed so long as it is capable of melting the metal material filled in the hearth or the water-cooled hearth. Typical high-energy heat sources include arc heat source, plasma heat source, electron beam, and laser. When such heat source is employed, either single heat source or multiple heat sources may be provided per one hearth or one water-cooled hearth.

The basic constitutions of the process and the apparatus for producing a metallic glass of the present invention are as described above. Next, the apparatus for producing metallic glass of the present invention embodying the present process are described.

FIG. 1

is a flow sheet schematically showing an embodiment of the metallic glass production apparatus of metal rolling type used in carrying out the metallic glass production process according to the present invention.

As shown in

FIG. 1

, the metallic glass production apparatus of rolling type

10

comprises a water-cooled copper hearth (hereafter referred to as a water-cooled hearth)

12

having a recess of predetermined configuration into which the metal material, for example, a metal material in powder or pellet form is to be filled; a roll casting section

13

extending from the periphery of the water-cooled hearth

12

; a water-cooled electrode (tungsten electrode)

14

for arc melting the metal material in the water-cooled hearth

12

; and a water-cooled roll for rolling

16

for rolling the molten metal arc-melted at a temperature higher than the melting point rising from the water-cooled hearth

12

onto the roll casting section

13

to form an ingot of plate shape, and which rapidly cools the metal material at a rate higher than the critical cooling rate intrinsic to the metal material (molten metal) simultaneously with the rolling; a cooling water supplier

18

for supplying a cooling water to the water-cooled hearth

12

, the water-cooled electrodes

14

, and the water-cooled roll for rolling

16

by water circulation; a vacuum chamber

20

for accommodating the water-cooled hearth

12

, the water-cooled electrodes

14

, and the water-cooled roll for rolling

16

; and a hearth-moving mechanism

22

for moving the water cooled hearth

12

provided with the roll casting section

13

in vacuum chamber

20

in the direction of arrow b (in horizontal direction) in synchronism with the rotation of the water-cooled roll for rolling

16

in the direction of arrow a.

The water-cooled roll for rolling

16

is rotated by a drive motor

17

to selectively roll and rapidly cool the molten metal at a temperature higher than the melting point rising from the water-cooled hearth

12

between the roll casting section

13

and the water-cooled roll for rolling

16

, and the hearth-moving mechanism

22

is constructed so as to be driven by a drive motor

23

to horizontally move the water-cooled hearth

12

in synchronism with the rotation of the water-cooled roll for rolling

16

. Although the water-cooled roll for rolling

16

is rotated by drive motor

17

in the embodiment of

FIG. 1

, the embodiment shown in

FIG. 1

is not a sole case and the present invention may be rotated by a mechanism other than such mechanism. For example, the water-cooled roll for rolling

16

may be kept in pressure contact with the water-cooled hearth

12

by means of a biasing means (not shown) such as a spring which can control the pressure, and the water-cooled roll for rolling

16

may be rotated by means of the friction between the water-cooled roll for rolling

16

and the water-cooled hearth

12

in correspondence to the horizontal movement of the water-cooled hearth

12

by the hearth-moving mechanism

22

. The water-cooled electrodes

14

is connected to an arc power source

24

. The water-cooled electrodes

14

is arranged at a slight angle from the direction of the depth of the recess

12

a

of the water-cooled hearth

12

, and the electrodes

14

is arranged to enable its control in X, Y and Z directions by a stepping motor

15

. In order to keep the gap (in Z direction) between the metal material in the water-cooled hearth

12

and the water-cooled electrodes

14

at a constant distance, the position of the metal material may be detected by a semiconductor laser sensor

26

to automatically control the movement of the water-cooled electrodes

14

by the motor

15

. When the gap between the arc electrodes

14

and the metal material is inconsistent, the arc established would be unstable, leading to inconsistency in the melt temperature. A nozzle for discharging a cooling gas (for example, argon gas) may be provided near the arc generation site of the water-cooled electrode

14

to discharge the cooling gas supplied from a gas source (a steel gas cylinder)

28

to thereby promote rapid cooling of the molten metal after the heat melting.

The vacuum chamber

20

has the structure of water-cooling jacket made from an SUS stainless steel, and is connected to an oil diffusion vacuum pump (diffusion pump)

30

and oil rotary vacuum pump (rotary pump)

32

by means of the exhaust port for evacuation. The vacuum chamber

20

has an argon gas inlet port in communication with a gas source (a steel gas cylinder)

34

to enable purging of the atmosphere with the inert gas after drawing a vacuum. The cooling water supplier

18

cools the cooling water that has circulated back by means of a coolant, and then send the thus cooled cooling water to the water-cooled hearth

12

, the water-cooled electrode

14

, and the water-cooled roll for rolling

16

.

The hearth-moving mechanism

22

which moves the water-cooled hearth

12

in the (horizontal) direction shown by arrow b in

FIG. 1

is not limited to any particular mechanism, and any mechanism known in the art for translational or reciprocal movement may be employed, for example, a drive screw and a traveling nut using a ball thread, pneumatic mechanism such as air cylinder, and hydraulic mechanism such as hydraulic cylinder.

Next, the process for producing a metallic glass by the rolling system according to the present invention is described by referring to

FIGS. 1

,

2

and

3

.

FIG. 2

is a schematic top view of the water-cooled hearth and the roll casting mold section (the mold for rolling)

13

shown in FIG.

1

.

FIG. 3

a

is a schematic cross sectional view of the metal material-melting step in the production process of a plate shaped amorphous bulk material in the metallic glass production apparatus of rolling type wherein arc melting is employed.

FIG. 3

b

is a schematic cross-sectional view of the step wherein the molten metal is rolled and cooled by the water-cooled roll for rolling

16

and the roll casting mold section

13

of water-cooled hearth

12

.

First, the water-cooled roll for rolling

16

is rotated by the drive motor

17

, and the hearth-moving mechanism

22

is driven by the drive motor

23

in synchronism with the rotation of the water-cooled roll for rolling

16

to move the water-cooled hearth

12

to the initial position where it is set as shown in

FIG. 3

a

. The metal material (powder, pellets, crystals) is then filled in the recess

12

a

of the water-cooled hearth

12

. In the meanwhile, the position of the water-cooled electrode

14

is adjusted in X, Y and Z directions by means of the sensor

26

and the motor

15

via an adapter

14

a

(see

FIGS. 3

a

and

3

b

) and the distance between the water-cooled electrode

14

and the metal material (in Z direction) is adjusted to a predetermined distance.

The chamber

20

is then evacuated by the diffusion pump

30

and the rotary pump

32

to a high vacuum of, for example, 5×10 Pa (using liquid nitrogen trap), and argon gas is supplied to the chamber

20

from the argon gas source

34

to purge the chamber

20

with argon gas. In the meanwhile, the water-cooled hearth

12

, the water-cooled electrode

14

, and the water-cooled roll for rolling

16

are cooled by the cooling water supplied from the cooling water supplier

18

.

When the preparation as described above is completed, the arc power source

24

is turned on to generate a plasma arc

36

between the tip of the water-cooled electrode

14

and the metal material to completely melt the metal material to form the molten alloy

38

(see

FIG. 3

a

). The arc power source

22

is then turned off to extinguish the plasma arc

36

. Simultaneously, the drive motors

17

and

23

are turned on to horizontally move the water-cooled hearth

12

by the hearth-moving mechanism

22

in the direction of the arrow b as shown in

FIG. 3

b

at the predetermined rate, and rotate the water-cooled roll for rolling

16

at a constant rotation rate in synchronism with the horizontal movement of the water-cooled hearth

12

in the direction of the arrow a. The molten metal at a temperature above the melting point rising over the water-cooled hearth

12

is thus selectively transferred into the cavity (recess)

13

a

in the roll casting mold section

13

of the water-cooled hearth

12

by the water-cooled roll for rolling

16

, and the thus transferred metal in the mold cavity

13

a

is rolled and pressed by sandwiching and pressing the molten metal between the roll casting section

13

and the water-cooled roll for rolling

16

at a predetermined pressure with simultaneous cooling. The metal liquid (molten metal)

38

is thus rolled by the water-cooled roll for rolling

16

into a thin plate simultaneously with the cooling, and therefore, the molten metal is cooled at a high cooling rate. Since the molten metal

38

is cooled at a rate higher than the critical cooling rate while it is rolled into its final plate-like shape, the molten metal undergoes a rapid solidification to become the amorphous bulk material

39

of the final desired plate shape in the roll casting mold section

13

.

The thus obtained amorphous bulk material

39

in the form of a plate is the one which has been selectively formed from the molten metal at a temperature above the melting point of the metal material (preferably, the molten metal of the part of the molten metal rising over the water-cooled hearth

12

which is at a temperature above the melting point) which is completely free from the portion

37

of the molten metal in the vicinity of the bottom of the water-cooled hearth

12

whose temperature is lower than the melting point of the metal material and which is likely to invite nonuniform nucleation, and hence formation of the crystalline phase. In addition, the plate shaped amorphous bulk material

39

is the one formed from the molten metal at once into the final plate form with simultaneous cooling, without causing any fluidization or surface weaving. Therefore, the molten metal is uniformly cooled and solidified, and the resulting bulk material

39

is free from the crystalline phase resulting from the nonuniform solidification or nonuniform nucleation as well as the casting defects such as cold shuts.

In the embodiment shown in

FIGS. 3

a

and

3

b

, the portion

37

of the molten metal in the vicinity of the bottom of the water-cooled hearth

12

whose temperature is lower than the melting point is avoided from entering into the final product, and a plate-shaped amorphous bulk material

39

of high strength is reliably produced.

In this embodiment, however, some of the molten metal

38

whose temperature is above the melting temperature of the metal material remains within the recess

12

a

of the water-cooled hearth

12

, and such molten metal

38

is not used in the production of the plate-shaped amorphous bulk material

39

, detracting from efficiency. Therefore, in an alternate embodiment of the present invention, as shown in

FIG. 4

a

the water-cooled roll for rolling

16

is provided with a molten metal-discharging mechanism

16

a

in the form of a protrusion fabricated from a material of low thermal conductivity at the position corresponding the recess

12

a

of the water-cooled hearth

12

to thereby selectively discharge the molten metal at a temperature higher than the melting point from the recess

12

a

and prevent nonuniform nucleation. The molten metal

38

in the water-cooled hearth

12

at a temperature above the melting point is thereby efficiently utilized. In such embodiment, the protrusion constituting the molten metal-discharging mechanism

16

a

is preliminarily heated to a temperature near the melting temperature of the molten metal.

As shown in FIG.

4

(

b

), when the water-cooled hearth

12

(namely, the recess

12

a

) comprises an elongated recess

12

a

(of semicylindrical configuration), and the roll casting mold section

13

having the cavity

13

a

is provided on either side or both sides of the hearth

12

, the metal material in the water-cooled hearth

12

may be continuously melted by the water-cooled electrode

14

, and the molten metal at a temperature above the melting point may be selectively transferred by the water-cooled roll for rolling

16

into the cavity

13

a

of the roll casting mold section

13

of the water-cooled hearth

12

for continuous rolling with simultaneous cooling. As in the case of FIG.

4

(

a

), the water-cooled roll for rolling

16

of this embodiment may be provided with a molten metal-discharging mechanism

16

a

, for instance, on its periphery with a molten metal-discharging mechanism

16

a

in the form of a ridge of a predetermined length to selectively and effectively discharge the molten metal at a temperature higher than the melting point in the water-cooled hearth

12

to the cavity

13

a

and prevent nonuniform nucleation. As described above, the molten metal-discharging mechanism

16

a

in the form of a ridge is preferably fabricated from a material of low thermal conductivity, and more preferably, the molten metal-discharging mechanism

16

a

is preliminarily heated to a temperature near the melting temperature of the molten metal.

In the metallic glass production process of the rolling type according to the present invention, the roll casting mold section

13

is formed integrally with the water-cooled hearth

12

. Instead of the roll casting mold section

13

integrally formed with the water-cooled hearth

12

, another roll for rolling may be provided underneath the water-cooled roll for rolling

16

to constitute a twin-roll rolling system. In such a case, the cross section of the plate-shaped amorphous bulk material produced by the rolling may be changed by changing the contour of the lower roll, for example, the contour of the cavity, into various shape not restricted to the rectangle shape.

In the embodiment as described above, the water-cooled roll for rolling

16

rotates with its axis of rotation remaining in the same position, and the position in the horizontal plane of the water-cooled electrode

14

is also substantially fixed. It is the water-cooled hearth

12

that is moved within its horizontal plane.

The present invention is not limited to such an embodiment, and alternatively, the rotating water-cooled roll for rolling

16

and the water-cooled electrode

14

may be moved in parallel with each other in horizontal direction, and the water-cooled hearth

12

may be the fixed at one position.

Although the roll casting mold section

13

integrally formed with the water-cooled hearth

12

may be formed with a cavity

13

a

as shown in the drawing, and the lower roller of the twin-roll system may be also formed with the cavity

13

a

, the present invention is not limited to such types and the provision of the cavity is not always necessary as long as the molten metal

38

is adequately rolled.

In the embodiments as described above, the water-cooled roll for rolling

16

is strongly water cooled, and the roll casting mold section

13

and the lower roller of the twin-rolling system are not forcedly cooled. It is of course possible to forcedly cool the roll casting mold section

13

and the lower roller of the twin-rolling system. In addition, the water-cooled hearth

12

, the water-cooled electrode

14

and the water-cooled roll for rolling

16

are forcedly cooled by cooling water. The present invention is not limited to such embodiment, and other cooling media (coolant) such as a coolant gas may be used.

The metallic glass production process of rolling type and the apparatus used therefor of the present invention are basically as described above.

Next, the process for producing a metallic glass by the forging type as well as the apparatus used therefor according to the present invention is described in detail.

FIG. 5

is a flow sheet schematically showing an embodiment of the metallic glass production apparatus of forging type used in carrying out the metallic glass production process according to the present invention.

As shown in

FIG. 5

, the metallic glass production apparatus of forging type

50

is similar to the metallic glass production apparatus of rolling type

10

in

FIG. 1

except that the molten metal at a temperature above the melting point is press formed (forged, or cast forged) between the lower mold

52

provided near the water cooled hearth

12

and the rapidly cooled upper mold

54

instead of the roll casting mold section

13

integrally formed with the water cooled hearth

12

and the water-cooled roll for rolling

16

. Same reference numerals are used for the elements common to the apparatus

50

and the apparatus

10

, and the explanation is omitted.

As shown in

FIG. 5

, the metallic glass production apparatus of forging type

50

comprises a water-cooled hearth

12

; a water-cooled electrode

14

; a lower mold

52

having a cavity

52

a

having the desired final configuration provided near the water-cooled hearth

12

; a molten metal-discharging mechanism

54

for discharging the molten metal at a temperature higher than the melting point from the water-cooled hearth

12

into the cavity

52

a

of the lower mold

52

, while avoiding nonuniform nucleation; an upper mold

54

which mates with the cavity

52

a

of the lower mold

52

to press mold (forge) the molten metal in the cavity

52

a

at a temperature above the melting point with simultaneous quenching of the molten metal at a rate higher than the critical cooling rate intrinsic to the metal material (molten metal); a cooling water supplier

18

for supplying a cooling water to the water-cooled hearth

12

, the water-cooled electrodes

14

, and the upper mold

54

by water circulation; a vacuum chamber

20

for accommodating the water-cooled hearth

12

, the water-cooled electrodes

14

, and the upper mold

54

; a hearth-moving mechanism

22

for moving the water cooled hearth

12

integrally formed with the lower mold

52

in vacuum chamber

20

in the direction of arrow b (in horizontal direction) in order that the position of the lower mold

52

is set just below the upper mold

54

; and an upper mold-moving mechanism

56

for moving the upper mold

54

in the direction of arrow c (in vertical direction) in the vacuum chamber

20

to thereby selectively discharge the molten metal at a temperature above the melting point in the water-cooled hearth

12

(integrally formed with the lower mold

52

which has been moved to the position of press molding) into the cavity

52

a

of the lower mold

52

by means of the molten metal-discharging mechanism

54

a

provided with the upper mold

54

, and selectively press mold (forge) the molten metal at a temperature above the melting point in the cavity

52

a

simultaneously with quenching. The upper mold-moving mechanism

56

for vertical movement of the upper mold

54

is driven by the drive motor

57

.

Next, the process for producing a metallic glass by the forging type according to the present invention is described by referring to

FIGS. 5 and 6

.

FIG. 6

a

is a schematic cross sectional view of the metal material-melting step wherein in the process wherein an amorphous bulk material of the desired final shape is produced in the metallic glass production apparatus of forging type wherein arc melting is employed.

FIG. 6

b

is a schematic cross-sectional view of the step wherein the molten metal is forged and cooled between the upper mold

54

and the lower mold

52

integrally formed with the water-cooled hearth

12

.

In the metallic glass production apparatus of forging type

50

, the upper mold-moving mechanism

56

and the hearth-moving mechanism

22

are respectively driven by the drive motors

57

and

23

to move the water-cooled hearth

12

integrally formed with the lower mold

52

and the upper mold

54

to the initial position where there are set as shown in

FIG. 6

a

. As in the case of the metallic glass production apparatus of rolling type

10

, the metal material is then filled in the recess

12

a

of the water-cooled hearth

12

, whereby the preparation for the metallic glass production by forging is completed.

After the completion of such preparation, the arc power source

24

is turned on as in the case of the metallic glass production apparatus of rolling type

10

to generate a plasma arc

36

between the tip of the water-cooled electrode

14

and the metal material to completely melt the metal material to form the molten alloy

38

(see

FIG. 6

a

). The arc power source

24

is then turned off to extinguish the plasma arc

36

. Simultaneously, the drive motor

23

is turned on to horizontally move the water-cooled hearth

12

at a constant speed by the hearth-moving mechanism

22

in the direction of arrow b to the position just below the upper mold

54

shown in

FIG. 6

b

. In the meanwhile, the dive motor

57

is turned on to descend the upper mold

54

in the direction of the arrow c by the upper mold-driving mechanism

56

.

As the upper mold

54

descends, the molten metal-discharging mechanism

54

a

selectively discharges the molten metal at a temperature above the melting point from the water-cooled hearth

12

and the thus discharged molten metal is forcedly pressed into the cavity

52

a

of the desired final shape in the lower mold

52

integrally formed with the water-cooled hearth

12

. The molten metal discharged by the molten metal-discharging mechanism

54

a

from the water-cooled hearth

12

and forcedly pressed into the cavity

52

a

is completely free from the portion

37

of the molten metal in the vicinity of the bottom of the water-cooled hearth

12

whose temperature is lower than the melting point of the metal material and which is likely to invite nonuniform nucleation, and hence, formation of the crystalline phase, and the defect such as nonuniform nucleation of the amorphous bulk material can be prevented. It should be noted that the molten metal-discharging mechanism

54

a

in the form of a protrusion or ridge is preferably fabricated from a material of low thermal conductivity, and more preferably, the molten metal-discharging mechanism

54

a

is preliminarily heated to a temperature near the melting temperature of the molten metal.

The upper mold

54

continues to descend and meets with the lower mold

52

, and the upper mold

54

mates with the cavity

52

a

of the lower mold

52

. The molten metal at a temperature above the melting point in the cavity

52

a

is thereby press molded as it is sandwiched between the upper and lower molds

54

and

52

at a predetermined pressure. In other words, the molten metal is forged by compression stress simultaneously with the rapid cooling by the water-cooled upper mold

54

. The metal liquid (molten metal)

38

is thus press molded (forged) into the desired final shape by the upper and lower molds

54

and

52

together with the cooling, and a high cooling rate of the molten metal is thereby realized. Since the molten metal

38

is cooled at a rate higher than the critical cooling rate while it is press molded (forged) into its final plate shape, the molten metal undergoes rapid solidification to become the amorphous bulk material

39

of the final desired thin plate shape.

The thus obtained amorphous bulk material

39

in the form of a plate is the one which has been selectively formed from the molten metal at a temperature above the melting point of the metal material which is completely free from the portion

37

of the molten metal in the vicinity of the bottom of the water-cooled hearth

12

whose temperature is lower than the melting point of the metal material, and which is likely to invite nonuniform nucleation, and hence formation of the crystalline phase. In addition, the plate shaped amorphous bulk material

39

is the one formed from the molten metal at once into the final plate form with simultaneous cooling, without causing any fluidization or surface weaving. Therefore, the molten metal is uniformly cooled and solidified, and the resulting bulk material

39

is free from the crystalline phase resulting from the nonuniform solidification or nonuniform nucleation as well as the casting defects such as cold shuts.

In the embodiment as described above, the position in the horizontal plane of the water-cooled electrode

14

and the upper mold

54

are substantially fixed, and it is the water-cooled hearth

12

that is moved within its horizontal plane. The present invention is not limited to such an embodiment, and alternatively, the water-cooled electrode

14

and the upper mold

54

may be moved in parallel with each other in horizontal direction, and the water-cooled hearth

12

may be the fixed at one position. In the embodiment as described above, the horizontally moved water-cooled hearth

12

is provided with only one pair of the water-cooled hearth

12

and the lower mold

52

. The present invention is not limited to such an embodiment, and two or more pairs of the hearth

12

and the lower mold

52

may be radially arranged at a predetermined interval on a rotatable disk so that the rotatable disk may be incrementally rotated. A continuous forging system of rotatable disk type is thereby constituted to enable successive forging one after another by incremental rotation of the rotatable disk. Of cause, the rotatable disk may be provided with only one pair of the water-cooled hearth

12

and the lower mold

52

, and the one or more pair of the water-cooled hearth

12

and the lower mold

52

may be provided not only on the rotatable disc but also on a plate of other configuration such as a rectangular plate as long as the pairs of the water-cooled hearth

12

and the lower mold

52

can be arranged on the plate and the plate is rotatable.

In the embodiments as described above, the upper mold

54

is strongly water cooled, and the lower mold

52

and the like are not forcedly cooled. It is of course possible to forcedly cool the lower mold

52

and the like. In addition, the water-cooled hearth

12

, the water-cooled electrode

14

and the upper mold

54

are forcedly cooled by cooling water. The present invention is not limited to such embodiment, and other cooling media (coolant) such as a coolant gas may be used.

The upper mold-moving mechanism

56

which presses the upper mold

54

onto the lower mold

52

is not limited to any particular mechanism, and any mechanism known in the art, for example, a hydraulic or pneumatic mechanism may be employed.

The metallic glass production process of forging type and the apparatus used therefor of the present invention are basically constructed as described above.

Industrial Applicability

As described above, the present invention has enabled production of a bulk amorphous material which is free from Casting defects such as cold shuts and which has excellent strength properties. This production processes and apparatus are highly reproducible, and are capable of producing a bulk amorphous material of desired final shape in simple steps. The product produced by the present invention is also free from crystalline phase formed by the development of the crystal nuclei through nonuniform nucleation. Accordingly, the process and the apparatus of the present invention, wherein the molten metal at a temperature above the melting point is selectively cooled at a rate higher than the critical cooling rate, are capable of producing the bulk amorphous mate rial of desired shape comprising single amorphous phase having excellent strength properties in simple steps at a high reproducibility.

Next, the metallic glass production process and apparatus according to the present invention are described in greater detail by referring to the Examples.

EXAMPLES

Examples 1 to 14

The metallic glass production apparatus of forging type

50

shown in

FIGS. 5 and 6

was used to produce amorphous bulk material alloys of rectangular plate with various dimensions in the range of 100 mm (length)×30 mm (width)×2 to 20 mm (thickness) from the 14 alloys shown in Table 1.

In the Examples, the water-cooled copper hearth

12

was a semispherical recess with a dimension of 30 mm (diam.)×4 mm (depth), and the cavity

52

a

of the lower mold

52

was a rectangular recess with a dimension of 210 mm (length)×30 mm (width)×2 mm (depth).

The water-cooled electrode

14

used was the one which is capable of fully utilizing the arc heat source of 3,000 ° C. and controlling the temperature by means of an IC cylister. The argon gas for cooling was injected from a cooling gas-injection port (not shown) provided on the adapter

14

a

. The water-cooled electrode

14

had an arc generating site comprising thorium-containing tungsten, and therefore, electrode consumption and contamination was minimized. The electrode

14

also had a water-cooled structure which mechanically and thermally enabled stable, continuous operation at a high thermal efficiency.

In these Examples, the metallic glass production apparatus of forging type

50

was operated by the conditions as described below. The electric current and the voltage employed for the arc melting were 250 A and 20 V, respectively. The gap between the water-cooled electrode

14

and the metal material in the form of a powder or pellets was adjusted to 0.7 mm. The pressure applied to the upper mold

54

for the press molding was in the range of 5 M to 20 Mpa and changed in accordance with the thickness of the rectangular amorphous alloy plates.

The rectangular amorphous alloy plates produced by the forging process as described above were examined for their structure by X-ray diffractometry, optical microscopy (OM), scanning electron microscopy combined with energy diffusion X-ray spectroscopy (EDX). The samples for use in the optical microscopy (OM) were subjected to an etching treatment in 30% hydrofluoric acid solution at 303 K for 1.8 ks. The samples were also evaluated for their structural relaxation, glass transition temperature (Tg), crystallization temperature (Tx), and heat of crystallization (ΔHx: temperature range of the supercooled liquid region) by differential scanning calorimetry (DSC) at a heating rate of 0.67 K/s. The rectangular amorphous alloy plate samples were also evaluated for mechanical properties. The mechanical properties evaluated were tear energy (Es), Vickers hardness (Hv), tensile strength (σf) (tensile strength could not be measured for the Examples 4, 5, 10 and 11, and compression strength was measured), elongation (εf), and Young's modulus (E). The Vickers hardness (Hv) was measured by Vickers microhardness tester at a load of 100

The alloy composition of the 14 alloys used for the production of the rectangular amorphous alloy plates are shown in Table 1 together with the properties of the rectangular amorphous alloy plates. It should be noted that “t” in Table 1 stands for the thickness of the rectangular amorphous alloy plates.

TABLE 1

Example

Alloy

Es

t

Tg

TX

ΔTX

δf

εf

E

No.

Composition

(kJ/m

2

)

(mm)

(K)

(K)

(K)

Hv

(MPa)

(%)

(GPa)

1

Zr

62.5

Al

7.5

Cu

20

66

8

623

750

127

510

1730

2.0

86

2

Zr

57

Ti

3

Al

10

Ni

10

Cu

20

59

5

655

740

85

540

1800

1.8

88

3

Zr

60

Al

10

Cu

30

67

5

620

708

88

490

1650

3.1

77

4

Fe

56

Cu

7

Ni

7

Zr

10

B

20

—

4

810

883

73

1250

*3560

1.8

160

5

Fe

56

Cu

7

Ni

7

Zr

2

Nb

8

B

20

—

3

805

892

87

1290

*3630

2.0

167

6

Mg

75

Cu

15

Y

10

—

5

424

471

47

250

880

1.9

47

7

Mg

70

Ni

20

La

10

—

5

470

503

33

300

900

2.1

50

8

La

65

Al

15

Ni

20

—

5

180

240

60

370

1210

2.0

58

9

La

65

Al

15

Cu

20

—

5

175

233

58

355

1120

2.2

56

10

Co

56

Fe

14

Zr

10

B

20

—

2

810

838

28

1050

*2850

1.7

150

11

Co

51

Fe

21

Zr

8

B

20

—

2

800

884

84

1080

*3010

1.8

153

12

La

55

Al

15

Ni

10

Cu

20

72

7

210

288

78

360

1150

2.2

56

13

Pd

40

Cu

30

Ni

10

P

20

70

15

580

678

98

550

1760

2.1

78

14

Zr

55

Al

10

Cu

30

Ni

5

68

20

680

760

80

540

1680

2.2

85

*Compaction strength

The results of the X-ray diffractometry, measurements of heat of crystallization, photomicrograph (×500) for the Zr

55

Al

10

CU

30

Ni

15

alloy material produced in Example 14 are shown in

FIGS. 7

,

8

and

9

, respectively.

FIG. 7

represents X-ray diffraction patterns of the Zr

55

Al

10

CU

30

Ni

15

alloy material produced in Example 14 for the central part of the transverse section taken from substantially intermediate portion of the material. The alloy material was of rectangular shape with a size of 30 mm (length)×40 mm (width)×20 mm (thickness). The X-ray diffraction pattern of the material only had a broad halo peak, indicating the single phase constitution of the amorphous phase. The optical micrograph of the central part of the transverse cross section also showed no contrast indicative of the precipitation of the crystal phase to confirm the results of the X-ray diffractometry. These results indicate that the alloy material was formed from the molten metal which was completely free from the molten metal of the region in contact with or in the vicinity of the copper hearth (copper crucible bed) at a temperature below the melting point which invites co-presence of the amorphous and crystal phases, and that nonuniform nucleation due to the contact of the molten metal in the copper hearth with the copper crucible bed is prevented by the present method.

FIG. 8

represents a DSC curve of the Zr

55

Al

10

CU

30

Ni

15

alloy material produced in Example

14

for the central amorphous part of the section taken from substantially intermediate portion of the material. The initiation of endothermic reaction by glass transition and the initiation of the exothermic reaction by crystallization are found at 680° C. and 760° C., respectively, and the supercooled liquid state is found over a considerably wide temperature range of 80° C. The results as described above demonstrate the capability of the forging process to produce a really glassy metal, and in addition, capability of the forging process to produce a large-sized bulk alloy material solely comprising the amorphous phase by suppressing the occurrence of the nonuniform nucleation. The Vickers hardness (Hv) of the large-sized amorphous bulk alloy material produced in Example 14 was measured to be 540, which is a value equivalent with the value (550) measured for the corresponding sampling in the form of a ribbon.

FIG. 9

is a photomicrograph (×500) showing the metal texture of the Zr

55

Al

10

CU

30

Ni

15

alloy material produced in Example 14 for the central amorphous part of the transverse section taken from substantially intermediate portion of the material. This photomicrograph demonstrates that the bulk amorphous alloy material of rectangular shape produced is an amorphous single phase alloy material substantially free from crystalline phase which has been produced by avoiding the nonuniform nucleation.

As demonstrated in Table 1, all of the samples of Examples 1 to 14 exhibited excellent mechanical strength, and the bulk amorphous alloy of rectangular shape produced by the cast forging process of the present invention is a bulk amorphous alloy which is free from casting defects such as cold shuts and which has excellent strength properties. The analysis of the sample obtained in Example 14 reveals that the bulk amorphous alloys of rectangular shape produced in the Examples are amorphous single phase alloys substantially free from crystalline phase which have been produced by avoiding the nonuniform nucleation.

The metallic glass production process and apparatus of the present invention have been described in detail by referring to various embodiments. The present invention, however, is not limited to such embodiments, and various modifications and design changes within the scope of the present invention should occur to those skilled in the art.

Number	Name	Date	Kind
5711363	Scruggs et al.	Jan 1998	A
5740854	Inoue et al.	Apr 1998	A
6267171	Onuki et al.	Jul 2001	B1

Number	Date	Country
32 15 263	Nov 1982	DE
0 577 050	Jan 1994	EP
2 272 451	May 1994	GB

Process and apparatus for producing metallic glass

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