TW201610187A - Process for producing a component of a metal alloy with an amorphous phase - Google Patents

Abstract

The invention relates to a process for producing a component of an at least partly amorphous a metal alloy comprising the following steps: Providing a powder of an at least partly amorphous metal alloy, the powder consisting of spherical particles having a diameter of less than 125 [mu]m; Pressing the powder into the desired shape of the component to be produced; Compressing and sintering the powder by a heat treatment, during or after the pressing, at a temperature between the transformation temperature and the crystallization temperature of the amorphous phase of the metal alloy, the duration of the heat treatment being selected so that after the heat treatment the component is sintered and has an amorphous proportion of at least 85 percent. The invention also relates to a component made of a pressed, sintered, spherical, amorphous metal alloy powder, the component having an amorphous proportion of at least 85 percent, and the use of such a component as a gear, frictional wheel, wear-resistant component, housing, watch case, part of a transmission, or semi-finished product.

Description

Method of manufacturing an amorphous phase metal alloy component

This invention relates to a method of making at least a portion of an amorphous phase metal alloy component.

The invention further relates to amorphous phase metal alloy components and the use of the components.

Amorphous phase metals and alloys thereof have been known for decades. For example, a thin strip and its manufacture are described in the patent publication DE 35 24 018 A1, which comprises the production of a thin metallic glass by melt quenching on a support. Furthermore, the patent specification EP 2 430 205 B1 describes a composite made of an amorphous phase alloy which requires a quenching rate of 102 K/sec to produce this composite. A disadvantage of this known method is that it can only produce thin layers or very tight components with a section of a few millimeters.

Therefore, manufacturing a large and complicated component having an amorphous phase structure encounters problems. The cooling rate required to manufacture complex components or semi-finished products with large volumes is not technically convenient. WO 2008/039134 A1 describes a method of making larger components from amorphous phase metal powders. This by using The 3D printing type (where the parts of the layer are melted by electron beams) constructs a layered component.

The disadvantage of this method is that its implementation is very labor intensive and costly. Moreover, the components produced by this method fail to have consistent physical properties. The local melting of the powder causes the crystallization temperature of the alloy to be spotted as expected, and if the cooling rate of the melt is too low, the alloy crystallizes. More precisely, the heat input produced by local melting and the re-cooling of the powder close to the surface cause the crystallization temperature of the alloy in the deeper layer (which has been an amorphous phase solid) to exceed as expected, resulting in alloy crystallization. Chemical. This produces an undesired amount of crystalline phase and its irregular distribution in the assembly.

Accordingly, it is an object of the present invention to overcome the disadvantages of the prior art. In particular, it is an object of the present invention to develop a simple and economical method for producing a partially amorphous phase metal alloy component having a volume of 0.1 cubic centimeters or more, preferably 1 cubic centimeter or more, and which can be manufactured in different shapes and Even partially amorphous phase metal alloy components of complex shape. The physical properties of the resulting assembly and the distribution of the amorphous phase therein should also be as uniform as possible. Another object of the invention is also to provide the assembly. This method should be simple to implement and the results should have good remanufacturability. The proportion of the amorphous phase metal phase in the resulting assembly should be as high as possible. It is also desirable to make the assembly as tight as possible and have only a few holes. Another object is to carry out this method with as many alloys as possible with different amorphous phases. It is also advantageous to implement the method in a device and tool that is as simple as possible and generally available in the laboratory.

The object of the invention is achieved by a process for producing at least a portion of an amorphous phase metal alloy component comprising the steps of: A) providing at least a portion of an amorphous phase metal alloy powder having spherical particles having a diameter of less than 125 microns B) pressing the powder into the desired shape of the component to be fabricated; C) pressurizing and sintering the powder by heat treatment, during or after the pressing, in the amorphous phase of the metal alloy The temperature is between the temperature and the crystallization temperature, and the period of the heat treatment is selected such that after the heat treatment, the assembly is sintered and has an amorphous phase of at least 85%.

Preferably, the selected heat treatment is sufficiently long at least after the powder has been subjected to the heat treatment of sintering and is short enough after the heat treatment of the assembly such that the assembly has an amorphous phase of at least 85%.

Preferably, 100% of the particles of the powder have a diameter of less than 125 microns. This particle size or particle distribution is also typically expressed as D100 = 125 microns.

In physics and chemistry, "amorphous phase material" means a substance in which an atom does not form a regular structure, but forms an irregular pattern and has only a short range of regularity rather than a long range of regularity. Unlike amorphous phase materials, regular structured materials are referred to as crystalline phases.

In the context of this invention, the spherical particles do not have to be geometrically perfect spherical, but may also be spherically offset. Preferably, the spherical powder particles have a round shape, at least about a spherical shape, and the ratio of the longest cross section to the shortest cross section thereof is not More than 2:1. Thus, in the context of this invention, "spherical geometry" does not refer to a strict geometric or mathematical sphere. These cross sections refer to the extreme dimensions in the powder particles. Particularly preferred spherical powder particles have a ratio of the longest cross section to the shortest cross section of no more than 1.5:1; very particularly preferably, they may be spherical. In the context of the present invention, "diameter refers to the largest cross section of the powder particles.

The spherical shape of the powder particles has the advantage that the spherical particles form a free-flowing powder, which is helpful, especially when the powder groove and the squeegee are used for layer processing; the high overall density of the powder can be achieved; the powder particles have a curve similar to that of the powder The surface, which is softened under the same conditions (temperature and time, or the same thermal energy output) - or at least close to these conditions. This causes them to contact the adjacent powder particles particularly well, or to sinter, and to sinter in a short time or at previously known time points or previously known time periods. Another advantage of high overall density is that the components do not shrink when sintered. This is made close to the original shape.

In a preferred embodiment of the invention, the assembly is considered to be sintered when the density of the component is at least 97% of the theoretical density of the fully amorphous phase metal alloy.

In the context of the present invention, sintering refers to a process in which the surface of the powder particles softens and contacts each other and remains connected after cooling. This self-made powder makes an adhesive or component.

The transition temperature of the amorphous phase is also commonly referred to as the glass transition temperature or transition point or glass transition point, and it should be explicitly stated herein that these lexical pairs are equal to the transition temperature.

Preferably, the powder is placed in a mold or tool, after which the powder is pressed into a mold or tool, or shaped by application of a tool.

The method of the invention comprises heating to the transition temperature and cooling as quickly as possible, since even if these temperatures are below the transition temperature, it is inevitable that crystallization occurs on the seed crystal before the powder particles soften (which will result in sintering of the powder). . The method of the invention is such that the powder particles undergo a plastic transformation which causes the powder to compact and thus accelerate the sintering of the powder. Try to avoid temperatures above the desired or final temperature.

The powder particle size or distribution can be achieved by the borrowing method and by sieving the starting powder. Thus, the powders obtained by the process of the present invention are prepared by sieving the starting powder which was previously supplied or used in the process of the present invention. That is, the starting powder already has the desired properties unless after the process. In addition, sieving can also reduce or minimize the number of powder particles in which the shape contained in the starting powder is strongly deviated from the spherical shape (as a result of sintering of several powder particles, so-called satellite formation).

The invention also proposes that, as a preferred embodiment of the method, the heat treatment is carried out under vacuum, preferably the powder is compressed by heat treatment at a vacuum of at least 10-3 mbar.

This makes the surface of the powder less reactive with ambient gases. The reason for its importance is that the metal oxides and other reaction products act as nucleating agents for the crystalline phase such that they have a negative impact on the purity of the amorphous phase in the fabricated assembly.

For the same reason, the method of the invention may be further or alternatively proposed to mask gases (especially inert gases such as argon, The heat treatment is preferably carried out with a purity of at least 99.99%, particularly preferably at least 99.999%. This embodiment may preferably provide an atmosphere for performing pressurization and heat treatment or heat treatment only, and the atmosphere is hardly free of residual gas by repeatedly evacuating and scrubbing with an inert gas (particularly argon).

Alternatively, the process of the invention may also be carried out by heat treatment under a reducing gas, in particular a forming gas, such that the amount of interfering metal oxide is as small as possible.

Another way to reduce the metal oxide in the assembly is to use an oxygen getter in the heat treatment and/or manufacture of the powder.

The method of the present invention may also propose a powder which is compressed by hot pressing or hot pressing.

The combination of pressure and heat treatment makes the assembly tighter. In addition, the plastic deformation improves the connection of the powder particles to each other and accelerates the sintering behavior, so that the heat treatment time is short and the proportion of the crystal phase in the assembly is lowered.

Further developments of the invention also suggest that during the selective heat treatment, the amorphous phase of the assembly is at least 90%, preferably more than 95%, particularly preferably more than 98%.

The higher the proportion of the amorphous phase in the assembly, the closer it is to the desired physical properties consisting entirely of the amorphous phase.

Preferred embodiments of the invention also teach that the powder used consists of an amorphous phase metal alloy or at least a portion of an amorphous phase metal alloy comprising at least 50% zirconium.

Zirconium-containing amorphous phase metal alloys are particularly useful for carrying out the process of the present invention, since the difference between the transition temperature and the crystallization temperature of many of these alloys is large, making the process easier to perform.

A very particularly preferred embodiment of the invention also provides that the powder used is an amorphous phase metal alloy powder or an at least partially amorphous phase metal alloy powder comprising a) from 58 to 77% by weight of zirconium; b) from 0 to 3% by weight铪; c) 20 to 30% by weight of copper; d) 2 to 6% by weight of aluminum; and e) 1 to 3% by weight of bismuth

Of these alloys, the remaining ratio of 100% by weight is zirconium. This alloy may contain general impurities. These zirconium-containing amorphous phase metal alloys are highly suitable for carrying out the process of the present invention.

Further, the method of the present invention proposes a spherical amorphous phase metal alloy powder which is preferably atomized, preferably in an inert gas, particularly argon, particularly preferably in an inert gas having a purity of 99.99%, 99.999% or higher. Made in China. In the context of this invention, "amorphous phase metal alloy" also refers to a metal alloy having at least 85% by volume of amorphous phase.

Of course, the powder is made before it is supplied. The atomization method can produce spherical powder particles in a simple and economical manner. The use of an inert gas (especially argon or highly purified argon) during atomization has the effect of minimizing interference impurities (such as metal oxides) contained in the powder.

Further developments of the invention may also provide a powder which is less than 1 The weight percent of the particles are less than 5 microns in diameter, or the powder is sieved or classified by air such that less than 1% by weight of the particles are less than 5 microns in diameter.

In the method of the present invention, preferably, the powder particles having a diameter of less than 5 μm are removed by air sorting treatment, or more precisely, the proportion of powder particles having a diameter of less than 5 μm is reduced by air classification treatment.

A small proportion of powder particles having a diameter below 5 microns limits the surface of the powder (the total surface of all powder particles) that is sensitive to the oxidation reaction or another chemical reaction of the powder particles with the ambient gas. In addition, the particle size of the powder is limited, ensuring that the powder particles soften under similar conditions (with respect to temperature and time or energy input), which is similar to the volume of the powder particles, which allows the powder to be tightly packed by pressurization. Therefore. A small proportion of fine powder particles (less than 5 microns) does not have an adverse effect, so that the powder particles can be embedded in the void spaces between the larger particles and thus increase the density of the unsintered powder. However, excessive amounts of fine powder particles have a negative influence on the fluidity of the powder, so it is preferable to remove them. Fine (small) powder particles will agglomerate with larger particles.

A further development of the method of the present invention provides that the heat treatment of the powder occurs at a transition temperature between the amorphous phase of the metal alloy and a temperature difference (transition temperature (T _T ) and a transition temperature (T _T ) of 30% exceeding the transition temperature (T _T ). The temperature (T) between the highest temperatures of the crystallization temperatures (T _C ) (preferably exceeding 20% or 10% of this temperature difference).

If the heat treatment is performed at or just above the transition temperature, the formation and growth of the crystal phase will be relatively small, and therefore, the purity of the amorphous phase (the ratio of the amorphous phase) of the components in the module will be high. It is expressed by the formula that the temperature at which the powder is heat-treated should meet the following conditions regarding the transition temperature T _T and the crystallization temperature T _C of the amorphous phase of the metal alloy: T _T <T<T _T + (30/100)*(T _C -T _T ) or preferably T _T <T<T _T +(20/100)*(T _C -T _T ) or better T _T <T<T _T +(10/100)*(T _C -T _T ).

The temperature range for heat treatment indicated in the previous mathematical formula will reach sintering and the crystal phase formed in the assembly is extremely small.

A particularly advantageous embodiment of the method of the invention proposes that the geometry of the component to be fabricated, in particular the thickness, preferably the period of heat treatment, is selected depending on the maximum relevant diameter of the component to be fabricated.

The geometry or thickness of the component to be fabricated is taken into account to ensure that the heat transfer of the shaped powder or component to be molded is sufficient to cause the interior of the powder or component inside the assembly to be heated or above the transition temperature such that the powder inside the assembly is also sintered.

The maximum relevant diameter of the component can be geometrically determined as the [in diameter] of the largest inscribed ball. When the maximum correlation diameter is determined, it is possible to ignore channels or gaps in the body that do not affect the heat input or have a small degree of influence (eg, less than 5% in total) via the surrounding gas and/or another heat source.

Preferably, it is proposed that the time period during the heat treatment is from 3 to 900 seconds per millimeter of the thickness of the component or the thickness or wall thickness or maximum relevant diameter of the component to be produced, preferably in the time range of 5 to 600 seconds.

Taking into account the shape, thickness, and wall thickness of the component and/or its maximum relevant diameter, while selecting the heat treatment period, the powder is fully charged. Sintering, but at the same time making the formation of the crystal phase in the assembly as small as possible, ideally minimal. For some components and for some applications, it is sufficient if the component is only completely sintered on the edge and if the unsintered powder is present inside the component. Preferably, however, the assembly is completely sintered (even inside).

The object of the invention is also achieved by means of a pressurized, sintered, spherical, amorphous phase metal alloy powder assembly having at least 85% amorphous phase.

This assembly can be made using one of the methods of the present invention. The method of the present invention is described above.

The object of the invention is also achieved by the use of such components (such as gears, friction wheels, wear components, hoods, cases, parts of transmissions, or semi-finished products).

The present invention is based on the surprising discovery that a high proportion (at least 85% by volume) of an amorphous phase can be produced from an amorphous phase metal alloy powder using appropriately sized spherical powder particles and heat treatment at a suitable temperature for a short period of time and thus Larger and/or more complex components exhibiting advantageous physical properties of the amorphous phase metal alloy. Accordingly, the present invention first describes a method of fabricating a component from an amorphous phase alloy or from a metal alloy having at least 85% amorphous phase by sintering the powder while retaining a high proportion of the amorphous phase. Preferably, when the powder is sintered, a heat treatment period is employed depending on the size of the component to be fabricated to obtain the highest possible proportion of the amorphous phase, or the crystal phase ratio in the metal alloy is as low as possible. For the same reason, it is advantageous to carry out a heat treatment under masking gas or under vacuum to maintain the proportion of metal oxides or other air reaction products in the powder and thus to cause metal oxides in the assembly. Or the proportion of other air reaction products is as low as possible. The ratio of this metal oxide or other air reaction product is particularly useful as a nucleus and reduces the amorphous ratio in the assembly.

Here, importantly, when the amorphous phase powder is not heated to or above the crystallization temperature, the amorphous phase of the alloy disappears due to crystallization. On the other hand, the material must be heated to at least the transition temperature, i.e., when it is cooled, the amorphous phase of the metal alloy changes from the plasticity range to the temperature of the rigid state. Within this temperature range, the powder particles are connected but not crystallized. The transition temperature is also referred to as the glass transition temperature and is often referred to as this.

In the context of the present invention, it has been found that if the amorphous phase metal powder used to make the module is produced by an atomization process and the powder is an X-ray amorphous phase, the particles of which are preferably less than 125 microns, the method of the invention has Very good results. In the atomization treatment, the obtained molten alloy is cooled extremely rapidly by the process gas (argon) flow, which promotes the presence of the amorphous phase powder portion. A further development of the method of the invention is that fine (particles less than 5 microns) and coarse particles larger than 125 microns are mostly separated from this powder, for example by sieving removal and/or air classification of the powder. This powder portion is the most suitable starting material (powder provided) for the manufacture of complex amorphous phase components by pressurization and heat treatment; the pressurization and temperature steps here have very good amorphous behavior associated with the assembly. The results, whether in succession or in combination, are all possible. Using the powder produced in this way, a component having a particularly high proportion of an amorphous metal phase is obtained. At the same time, the assembly made in this way and from this powder has a high proportion of sintered powder particles and low porosity, preferably with a lower porosity 5%. The upper limit of the particle size is such that the particle has no more cross-section than the layer produced; the particle can then be removed by a doctor blade leaving a layer of incompleteness.

Importantly, this method does not heat the amorphous phase powder up to or above the crystallization temperature, otherwise crystallization will occur and the amorphous phase nature of the alloy will be lost. On the other hand, the material must be heated to at least the transition temperature, i.e., when it is cooled, the amorphous phase of the metal alloy changes from the plasticity range to the temperature of the rigid state. Within this temperature range, the powder particles will join but will not crystallize. This transition temperature is also referred to as the glass transition temperature and is often referred to as this.

However, since it is technically difficult and uneconomical to be absolutely free of impurities and particularly oxygen-free, it is unavoidable to include a microcrystalline phase. A small proportion of oxygen in the range of 10-99 ppm causes a corresponding oxidation reaction of the oxophilic alloy component. These are then present as small crystal nuclei, and as a result, the grains contain small oxides, which are confirmed by a magnification of 1,000 times the photomicrograph or the peak in the X-ray diffraction spectrum. Further or other impurities in the starting material and other elements (eg, nitrogen) can also have similar effects.

The heat treatment is mainly dependent on the volume of the component and should generally not be too long, since each nucleus (although small) acts as a seed, and thus can grow crystallites, which are crystalline phases not desired in the field of assembly. Experiments conducted on zirconium-based alloys have shown that the maximum period of the 400 second/1 mm component cross section of the heat treatment in the temperature range of the present invention provides particularly good results. The heating phase should be as fast as possible, as the unwanted crystal growth sometimes occurs at a temperature 50K below the transition temperature.

Other specific embodiments of the invention are explained below using a schematic flow chart, but this flow chart does not limit the invention.

In this flow chart, T represents the operating temperature, the transition temperature of the T _T amorphous phase metal alloy, and the crystallization temperature of the amorphous phase of the T _C metal alloy.

An amorphous phase metal powder is prepared from a metal alloy whose composition is suitable for forming an amorphous phase or which has been composed of an amorphous phase. Thereafter, the powder is classified, wherein too small or too large powder particles are removed, in particular by sieving and air classification. Thereafter, the powder is pressed into a desired shape by heat or without heat. If the powder is not pressure-formed by heat, it is subsequently subjected to a heat treatment (in the context of the present invention, referred to as sintering or initiating sintering). The maximum period of heat treatment during or after pressurization is a 900 sec / 1 mm module cross section which is higher than the transition temperature T _T of the amorphous phase of the metal alloy used and lower than the crystallization temperature T _C .

In the specific embodiments below, the results of the methods of the invention and methods of evaluation are described.

Example 1:

70.5 wt% zirconium (Haines & Maassen Metallhandelsgesellschaft mbH Bonn, Zr-201-Zirkon Crystalbar), 0.2% by weight 铪 (Alpha Aesar GmbH & Co KG Karlsruhe, 铪 crystal bar milled sheet, 99.7%, article number 10204), 23.9 weight % copper (Alpha Aesar GmbH & Co KG Karlsruhe, Copper plate, anaerobic, high conductivity (OFCH), article number 45210), 3.6 wt% aluminum (Alpha Aesar GmbH & Co KG Karlsruhe, aluminum ingot 99.999%, article number 10571) and 1.8 wt% 铌 (Alpha Aesar GmbH & Co KG Karlsruhe, 99 foil 99.97%, part number 00238) alloy melted in induction melting system (VSG, induction heating vacuum, melting, and casting system, Nürmont, Freiberg), this is 800 mbar argon (Argon 6.0, Linde) Under AG, Pullach, it is poured into a water-cooled copper mold. The alloy prepared in this manner was finely powdered by argon atomization in a Nanoval atomization apparatus (Nanoval GmbH & Co. KG, Berlin) using, for example, the method disclosed in WO 99/30858 A1.

The fines were removed by air classification using a Condux fine particle sorter CFS (Netzsch-Feinmahltechnik GmbH Selb Deutschland) such that less than 0.1% of the particles have a size of less than 5 microns, ie at least 99.9% of the particles have a size of 5 microns or more The diameter or size was sieved through a test sieve having a mesh size of 125 microns (Retsch GmbH, Haan-Deutschland, article number 60.131.000125) to remove all powder particles larger than 125 microns. The powder prepared in this way was studied by X-ray diffraction, and its amorphous phase ratio was greater than 95%.

The 5.0 g powder portion obtained in this way was pressurized in a laboratory press machine 54MP250D (mssiencetific Chromatographie-Handel GmbH, Berlin), where a press mold (32 mm, P0764, mssiencetific Chromatographie-Handel GmbH, Berlin) and 15 tons of pressure. The pressed parts were then compressed in a vacuum sintering (Gero high temperature vacuum tempering furnace LHTW 100-200/22, Neuhausen) at 410 ° C and a pressure of about 10 ^-5 mbar for 120 seconds. Thereafter, the pressurized parts were finally compressed at a temperature of 400 ° C for 90 seconds in highly purified argon (Argon 6.0, Linde AG, Pullach) under a pressure of 200 MPa by a heat equalization pressure.

The 15 components produced in this manner were studied by metallographic micrographs to determine the amorphous phase of the surface of the structure. This study shows that an average of 92% of the surface is amorphous.

Example 2:

70.5 wt% zirconium (Haines & Maassen Metallhandelsgesellschaft mbH Bonn, Zr-201-Zirkon Crystalbar), 0.2% by weight 铪 (Alpha Aesar GmbH & Co KG Karlsruhe, 铪 crystal bar milled sheet, 99.7%, article number 10204), 23.9 weight % copper (Alpha Aesar GmbH & Co KG Karlsruhe, copper plate, anaerobic, high conductivity (OFCH), article number 45210), 3.6 wt% aluminum (Alpha Aesar GmbH & Co KG Karlsruhe, aluminum ingot 99.999%, article number 10571) And an alloy made of 1.8% by weight Al (Alpha Aesar GmbH & Co KG Karlsruhe, 铌 foil 99.97%, part number 00238) was melted in an induction melting system (VSG, induction heating vacuum, melting, and casting system, Nürmont, Freiberg). This was carried out at 800 mbar argon (Argon 6.0, Linde AG, Pullach) and poured into a water-cooled copper mold. The alloy prepared in this manner was finely powdered by argon atomization in a Nanoval atomization apparatus (Nanoval GmbH & Co. KG, Berlin) using, for example, the method disclosed in WO 99/30858 A1.

By air classification, use Condux fine particle sorter CFS (Netzsch-Feinmahltechnik GmbH Selb Deutschland) Separation and removal of fines such that less than 0.1% of the particles are less than 5 microns in size and sieved through a test sieve having a mesh size of 125 microns (Retsch GmbH, Haan-Deutschland, article number 60.131. 000125) Remove all powder particles larger than 125 microns. The powder prepared in this way was studied by X-ray diffraction, and its amorphous phase ratio was greater than 95%.

In each case, 15.0 g of the powder obtained in this manner was partially sintered by hot pressing, which was carried out at a temperature of 400 MPa for 3 minutes at a pressure of 200 MPa.

The 15 components produced in this manner were studied by metallographic micrographs to determine the amorphous phase of the surface of the structure. This study shows that an average of 85% of the surface is amorphous.

Example 3:

70.6 wt% zirconium (Haines & Maassen Metallhandelsgesellschaft mbH Bonn, Zr-201-Zirkon Crystalbar), 23.9% by weight copper (Alpha Aesar GmbH & Co KG Karlsruhe, copper plate, anaerobic, high conductivity (OFCH), article number 45210), 3.7 wt% aluminum (Alpha Aesar GmbH & Co KG Karlsruhe, aluminum ingot 99.999%, article number 10571), and 1.8 wt% niobium (Alpha Aesar GmbH & Co KG Karlsruhe, niobium foil 99.97%, article number 00238) alloy melting In an induction melting system (VSG, induction heating vacuum, melting, and casting system, Nürmont, Freiberg), this was carried out under 800 mbar argon (Argon 6.0, Linde AG, Pullach) and poured into a water-cooled copper mold. Use, for example, WO 99/30858 A1 The method disclosed herein, the alloy obtained in this manner, was obtained by atomization of argon in a Nanoval atomization apparatus (Nanoval GmbH & Co. KG, Berlin).

By air classification, the fine particles were removed using a Condux fine particle sorter CFS (Netzsch-Feinmahltechnik GmbH Selb Deutschland), such that less than 0.1% of the particles were less than 5 microns in size and sieved through a test sieve having a mesh size of 125 microns ( Retsch GmbH, Haan-Deutschland, article number 60.131.000125) removes all powder particles larger than 125 microns. The powder prepared in this way was studied by X-ray diffraction, and its amorphous phase ratio was greater than 95%.

In each case, 15.0 g of the powder obtained in this manner was partially sintered by hot pressing, which was carried out at a temperature of 400 MPa for 3 minutes at a pressure of 200 MPa.

The 15 components produced in this manner were studied by metallographic micrographs to determine the amorphous phase of the surface of the structure. This study shows that an average of 87% of the surface is amorphous.

Example 4:

70.6 wt% zirconium (Haines & Maassen Metallhandelsgesellschaft mbH Bonn, Zr-201-Zirkon Crystalbar), 23.9% by weight copper (Alpha Aesar GmbH & Co KG Karlsruhe, copper plate, anaerobic, high conductivity (OFCH), article number 45210), 3.7 wt% aluminum (Alpha Aesar GmbH & Co KG Karlsruhe, aluminum ingot 99.999%, article number 10571), and 1.8 wt% niobium (Alpha Aesar GmbH & Co KG Karlsruhe, niobium foil 99.97%, Alloy No. 00238) is melted in an induction melting system (VSG, induction heating vacuum, melting, and casting system, Nürmont, Freiberg) under 800 mbar argon (Argon 6.0, Linde AG, Pullach) and Pour into a water-cooled copper mold. The alloy prepared in this manner was finely powdered by argon atomization in a Nanoval atomization apparatus (Nanoval GmbH & Co. KG, Berlin) using, for example, the method disclosed in WO 99/30858 A1.

By air classification, the fine particles were removed using a Condux fine particle sorter CFS (Netzsch-Feinmahltechnik GmbH Selb Deutschland), such that less than 0.1% of the particles were less than 5 microns in size and sieved through a test sieve having a mesh size of 125 microns ( Retsch GmbH, Haan-Deutschland, article number 60.131.000125) removes all powder particles larger than 125 microns. The powder prepared in this way was studied by X-ray diffraction, and its amorphous phase ratio was greater than 95%.

The 50 g powder portion obtained in this way was pressurized in a laboratory press machine 54MP250D (mssiencetific Chromatographie-Handel GmbH, Berlin), where a press mold (32 mm, P0764, mssiencetific Chromatographie-Handel GmbH, Berlin) and 25 tons maximum pressure and sintered in highly purified argon (Argon 6.0, Linde AG, Pullach) at 410 ° C for 5 minutes.

The components produced in this manner were studied by means of a number of metallographic micrographs to determine the amorphous phase of the surface of the structure. This study shows that an average of 90% of the surface is amorphous.

The table below lists the results of the tests of Examples 1 to 4 and the control measurements:

Testing and testing methods

1) Method for determining the particle size of a metal alloy powder:

The particle size of the inorganic powder was determined by laser light scattering using a Sympatec Helos BR/R3 (Sympatec GmbH) equipped with a RODOS/M anhydrous disperser and a VIBRI vibrating feeder (Sympatec GmbH). At least 10 grams of the sample was fed in anhydrous, main pressure dispersion at 1 bar and assayed. The initial standard is an optical concentration of 1.9% to 2.1%. The measurement time is 10 seconds. The results were evaluated by MIE theory and d50 was used to indicate particle size.

2) Test method for measuring density:

For determining the density, a geometrically indeed rectangular parallelepiped is produced by grinding the surface so that it can be accurately determined by a digital micrometer (PR1367, Mitutoyo Messgeräte Leonberg GmbH, Leonberg). The volume is now determined mathematically. After that, the balance in the analysis The exact weight was determined on a balance (XPE analytical scale, Mettler-Toledo GmbH). The measured weight is divided by the calculated volume to obtain the density.

The theoretical density of the amorphous phase alloy corresponds to the density of the melting point.

3) Test method for determining the amorphous surface in the assembly:

In this case, in each case, as described in DIN EN ISO 1463, 15 metallographic parts were produced, each being polished with SiC paper 1200 (Struers GmbH, Willich), followed by 6 microns in the following polishing step. , 3 micron and 1 micron diamond products (Struers GmbH, Willich), and finally polished with OP-S chemical mechanical oxide polishing suspension (Struers GmbH, Willich). The ground surface prepared in this manner was examined by an optical microscope (Leica DM 4000M, Leica DM 6000 M) at 1,000 magnification to determine the crystal phase ratio of the surface in the photomicrograph. This includes the use of the software Leica Phase Expert to evaluate the crystal phase surface ratio, which is expressed as a percentage of the total area of the cross section, with the dark region being considered as the crystalline phase and the bright region being considered as the amorphous phase. Here, the amorphous phase matrix is defined as a photo and is expressed as a percentage of the total measured area. In each case, 10 different sample surfaces were measured and averaged.

4) Test method for determining the transition temperature:

This is carried out using the Netzsch 404 F1 Pegasus® Differential Scanning Card (Erich NETZSCH GmbH & Co. Holding KG) equipped with a high temperature tube furnace and resistance change heater, integrated control thermocouple type S, DSC404F1A72 sample carrier system, attached lid Al ₂ O ₃ crucible, OTS ^TM system to remove residual oxygen in the measurement period (which includes three oxygen ring), and a pumping system for a two-stage rotary pump automatic operation. All assays were carried out under a blanket gas (Argon 6.0 Linde AG) at a flow rate of 50 ml/min. The results were evaluated using the software Proteus® 6.1. The transition temperature was determined using a tangent method (glass transition) in the range of 380 ° C and 420 ° C (initial, intermediate, recurved, final). Using complex peak evaluation, the crystallization temperature (area, peak, start, end, width, height) is determined over a temperature range of 450-500 ° C and is evaluated using a complex peak at a temperature range of 875-930 ° C. Tm (area, peak, start, end, width, height). For this assay, a 25 mg ± 0.5 mg sample was weighed into a crucible and the assay was performed at the following heating rates and temperature ranges.

20-375 ° C: heating rate 20K / min

375-500 ° C: heating rate 1K / min

500-850 ° C: heating rate 20K / min

Above 850 ° C: heating rate 10K / min

The amorphous phase of the module was determined by measuring the crystallization effect by a complex peak method using an amorphous phase sample (obtained by melt spinning) having a 100% crystallization of -47.0 Joules/gram as a control.

The crystallization of the assembly is diminished by the quotient obtained from the ruthenium of the control.

5) Determine the elemental composition by emission spectroscopy (inductively coupled plasma):

This system uses the Varian Vista-MPX emission spectrometer (Varian Inc.). For each metal, two calibration samples were prepared from a standard solution having a known metal content (e.g., 1,000 mg/liter) in an aqua regia base (concentrated hydrochloric acid and concentrated nitric acid, 3:1) and assayed. The parameters of the ICP instrument are: Power: 1.25 kW

Plasma gas: 15.0 liters / minute (argon)

Carrier gas: 1.50 liters / minute (argon)

Atomizing gas pressure: 220kPa (argon)

Repeat: 20 seconds

Stability time: 45 seconds

Observation height: 10 mm

Traction in the sample: 45 seconds

Cleaning time: 10 seconds

Pump rate: 20rpm

Repeat: 3

To determine the sample: 0.10 g ± 0.02 g of the sample was placed in a container, to which 3 ml of nitric acid and 9 ml of hydrochloric acid were added, as shown above, and placed in a microwave oven (company: Anton Paar, equipment: Multiwave 3000) at 800 -1,200 watts dissolved for 60 minutes. The dissolved sample was transferred to a 100 ml bottle with 50% by volume hydrochloric acid and measured.

The features of the present invention are disclosed in the foregoing description and claims. The specific embodiments of the flow and the examples can be used in various embodiments to practice the invention; this applies to both individual features and combinations of features.

Claims (15)

A method of making at least a portion of an amorphous phase metal alloy component, comprising the steps of: providing at least a portion of an amorphous phase metal alloy powder consisting of spherical particles having a diameter of less than 125 microns; pressing the powder into The desired shape of the component to be fabricated; pressurizing and sintering the powder by heat treatment, during or after the pressing, at a temperature between the transition temperature of the amorphous phase of the metal alloy and the crystallization temperature, and selecting the heat treatment The period is such that after heat treatment, the assembly is sintered and has an amorphous phase of at least 85%. The method of claim 1, wherein the heat treatment is carried out under vacuum, preferably the powder is compressed by heat treatment under a vacuum of at least 10 ^-3 mbar. The method of claim 1 or 2, wherein the powder is compressed by hot pressing or hot pressing. The method of claim 1 or 2, wherein the heat treatment period is selected such that the amorphous phase of the assembly is at least 90%, preferably more than 95%, particularly preferably more than 98%. The method of claim 1 or 2, wherein the powder for producing the amorphous phase metal alloy comprises at least 50% by weight of zirconium. The method of claim 1 or 2, wherein a) 58 to 77% by weight of zirconium; b) 0 to 3% by weight of cerium; c) 20 to 30% by weight of copper; d) 2 to 6 wt% of aluminum; and e) 1 to 3 wt% of an amorphous phase metal alloy powder of ruthenium. The method of claim 1 or 2, wherein the spherical amorphous phase metal alloy powder is obtained by an atomization method, preferably in an inert gas (particularly argon), particularly preferably in a purity of 99.99%, Manufactured in an inert gas of 99.999% or higher. The method of claim 1 or 2, wherein less than 1% by weight of the powder has a diameter of less than 5 microns, or the powder is sieved or classified by air to make the particles less than 1% by weight. The diameter is less than 5 microns. The method of claim 1 or 2, wherein the heat treatment of the powder occurs at a transition temperature between the amorphous phase of the metal alloy and a temperature between the transition temperature (T _T ) and the crystallization temperature (T _C ) The temperature (T) between the highest temperatures of 30% difference (preferably 20% or 10% of this temperature difference). The method of claim 1 or 2, wherein the heat treatment period is selected depending on the geometry (particularly the thickness) of the component to be manufactured, preferably depending on the maximum relevant diameter of the component to be manufactured. The method of claim 1 or 2, wherein the heat treatment is in a time range of 3 to 900 seconds/mm thickness or a maximum relevant diameter of the component to be produced, preferably in a time range of 5 to 600 seconds Inside. The method of claim 1 or 2, wherein the powder The particles are plastically transformed by this heat treatment. A component of a pressurized, sintered, spherical, amorphous phase metal alloy powder having at least 85% amorphous phase. The component of claim 13 of the patent application is produced by the method of any one of claims 1 to 12. The use of the components of claim 13 or 14 for use as gears, friction wheels, wear components, hoods, cases, parts of transmissions, or semi-finished products.