WO1990005603A1 - Process and device for producing a laminated material for sliding elements - Google Patents

Abstract

Process and device for producing a laminated material for sliding elements with a sliding layer consisting of an alloy in the form of a metallurgical two- or more component system with immiscibility gaps. The sliding layer is continuously cast from the alloy and cooled immediately after casting in a continuous pass at a cooling rate sufficient to prevent the growth of particles of the immiscible metallurgical components to particle sizes greater than 0.01 to 1 $g(m)m, preferably < 1 $g(m)m. To this end, a film can be cast from an alloy and quenched at a high cooling rate. This film is then joined to the substrate which forms the carrier layer, by means of a joining process, preferably using a laser beam. The sliding layer can also be cast from the alloy onto said substrate in one or more steps. Said substrate itself may consist of a strip consisting of a steel backing and an intermediate layer of a bearing metal with good emergency running properties. The following metallurgical two- or more component systems with immiscibility gaps can be cast to form sliding layers: AlPb, AlSn, AlBi, AlSb, CrPb, CrSn, MnPb, FePb, CoPb, NiPb, CuPb and PbZn.

Description

 Method and device for producing a slit / er-is of es for sliding elements

The invention relates to a method for producing a layer material for sliding elements with a sliding layer of at least one alloy applied to a carrier layer in the form of a metallurgical two- or multi-component system with a miscibility gap (onotectic). The invention further relates to a device for performing this method.

Alloys in the form of metallurgical two-component or multi-component systems with a miscibility gap (monotectic), which are also referred to as dispersion alloys, generally consist of metallic components with widely differing specific weights. The heavy components, e.g. the Pb in AlPb dispersion alloys tend to segregate, i.e. When the alloy solidifies - according to the state diagram - mixed crystals of a different concentration are deposited first than in the later stage of the cooling process, so that the mixed crystals formed from the melt are not homogeneous. The production of AlPb materials for plain bearing purposes under terrestrial conditions by casting technology is therefore carried out by e.g. Gaps in the mixture in the AlPb system made impossible. The fine distribution of the lead in the Al matrix required for use as a plain bearing material is not achieved.

For the production of functional layers from such dispersion alloys, for example from DE-OS 31 37 745, the production of metal powder by atomizing a melt and sintering the same together Known on a carrier layer. However, the method leads to a highly inhomogeneous structure, so that the results obtained on bearing testing machines fluctuate greatly. In addition, it has been found that pores still present in the sintered layer give rise to cracks as a result of internal notching when the sliding element is subjected to an alternating load.

From DE-AS 15 08 856 a method is already known which claims the application of the continuous casting method to aluminum alloys containing high lead. A homogeneous, single-phase melt made of an aluminum-lead alloy with 20 to 50% lead is to be poured onto a metal carrier for the direct production of a composite bearing material. However, this process leads to poor bonding of the AlPb sliding layer (functional layer) to the steel. In addition, despite water cooling, segregation occurs in the mold, i.e. the temperature gradient between the temperature of the homogeneous melt and the mold temperature is too small, the setting of the thermodynamic equilibrium cannot be prevented. Consequently. there is a sliding layer with a homogeneous, segregated structure; a sandwich consisting of two layers that cannot be used tribologically is produced, which also has a poor bond to the carrier.

There are already known from DE-PS 21 30 421 and ^" DE-OS 22 41 628 a method for producing a composite metal strip, in which molten aluminum passes through an opening in the bottom of the crucible and molten lead in a thin, thread-like stream through the molten aluminum also into the Bottom opening of the crucible is guided. The melt mixture of, for example, aluminum and lead formed in the bottom opening of the crucible is then whirled through and mixed by means of gas jets and blown onto the upper surface of the substrate passed by. A functional layer formed in this way is still very inhomogeneous, the lead particles, due to their much greater density, tending to segregate and coagulate to a great extent when the swirling stream of melt mixture hits the surface of the substrate.

In a method known from DE-AS 22 63 268, a molten mixture of lead and aluminum is flung off to the side by means of a rotor in the form of fine particles and is quenched on a baffle wall and solidified to form scale-like material (splat cooling). However, due to its scale-like (flake-like) structure, this material cannot be processed into a material capable of plating by extrusion or by powder rolling. In the production of molded parts under pressure and temperature (by means of isostatic pressing), segregation occurs again, which leads to severe inhomogeneity and thus to the uselessness of the AlPb solid bearings produced in this way.

DE-OS 17 75 322 describes a plain bearing or material for its production which consists of Al alloys (eg dispersion alloys based on AlPb, AlSn), the Al material which is later plated onto steel as a carrier, is produced by a powder rolling process. The AI bearing material made in this way has a line arrangement of the soft minority phase (eg Pb) due to the compression by powder rolling and the subsequent rolling and plating operation. Such banded structure, however, is for stressed ^"Removable load bearings considerable disadvantage, since the formation of the lines due to internal notch effect duration cracks.

PCT WO 87/04377 describes a process with the aid of which a 1 to 5 mm thick AlPb — Ba-.d is produced and plated onto steel as the carrier material. The fine distribution of lead described here is not achieved in practice, however, since the lead plating is scattered in rows and does not become globular even after subsequent heat treatment. In addition, it can be seen that segregation already occurs in strips with a thickness of more than 0.5 mm.

DE-PS 37 30 862.9-16 wants to avoid this disadvantage by using an AlPb film of 0.5 mm maximum thickness with extremely fine, globular Pb distribution when using a melt-spin method similar to WO 87/04377 claimed and applies the same to a carrier while avoiding rolling operations by ultrasonic welding, soldering and gluing.

But it has been shown that the

Ultrasonic welding is, on the one hand, a complex and by no means safe connection process, but the processes of soldering or gluing are not suitable for producing the semi-finished product required for the manufacture of plain bearings by means of a belt process. , The object of the invention is therefore to provide a method and an apparatus for producing a layer material for sliding elements with a sliding layer made of at least one alloy in the form of a metallurgical two- or multi-component system with a mismatch gap (monotectic) applied to a carrier layer, one in the sliding layer globular fine distribution of the dispersed metal component (the minority phase) in a quasi amorphous metallic matrix.

This object is achieved by a method according to the features of claim 1 or by a device according to the features of claim 22. Preferred embodiments are the subject of the dependent claims.

Such a layered material is obtained by a process in which the sliding layer is continuously cast from the alloy and immediately after casting in a continuous pass of cooling with, for the prevention of particle growth of the immiscible metallurgical components over particle dimensions of 0.01 to 1 / µm, preferably ^ .1 um, is subjected to sufficiently high solidification speed. The high cooling rate freezes a uniform globular distribution of the dispersed metal component (minority phase) in the matrix of the melt. The segregation that occurs with alloys of this type is reduced to a minimum.

In this way, a one-layer material is produced, the sliding layer (functional slide) of which is due to the quasi-amorphous state of its matrix material and due to the essentially uniform, globular - o -

Distribution of the minority phase is equipped with significantly improved properties. This significantly increases the strength of the functional layer. Similarly, the ductility and toughness of the functional layer are improved despite extremely high strength.

The alloy or the alloys are preferably produced by means of a melt-metallurgical process and, in the process and when they are ready for casting, are kept at a temperature above the separation temperature corresponding to the system and the composition.

A particularly preferred possibility in the context of the invention to achieve a fine globular distribution of the minority phase in the matrix, which is as uniform as possible, consists in that the alloy or the alloys to be cast have nucleating agents adapted to the respective alloy type, for example P, B , Ti, Si, borides, nitrides and oxides are added in a weight proportion between 0.1 and 3.5%. In this way it can be achieved that a large number of fine particles of the minority phase are formed very quickly, but these mutually prevent each other from growing, so that even with high cooling rates that can still be achieved in practice, a very fine, globular distribution of the matrix solidifying on cooling is achieved. Systems with lead as a minority phase are particularly suitable in the process according to the invention, for example AlPb, FePb, CuPb, MnPb, NiPb, possibly also CrPb and CoPb. There are also similar systems with tin, bismuth or antimony as a minority phase, such as AlSn, AlBi, AlSb, CrSn. The invention offers two basic options:

a) The dispersion alloy is cast in the form of a thin layer or a film on a substrate forming the carrier layer, preferably continuously on a strip-shaped substrate. In this pouring and subsequent rapid cooling, the measures according to the invention mentioned above are used to achieve a fine globular distribution of the minority phase in the metal matrix. The sliding layer can be poured on in one or more stages. A multi-stage pouring would then provide that first a first thin film is poured on and then immediately and quickly cooled effectively. After the first infused film has solidified, a second film is poured over it and also quickly solidified again. Such a construction of the sliding layer can take place in several stages. The individual melted films can have different thicknesses. The films can also have different alloy compositions. By using different alloys and / or different cooling conditions, thin layers of different structures can also be formed within the sliding layer.

b) Another possibility for the formation of the sliding layer is that first the sliding layer in the form of a tape or a film is poured free of the carrier layer and after cooling with the aid of a joining process with the help of a laser beam, for example, is continuously applied to the carrier layer.

With the method according to the invention, three-component plain bearings can also be easily produced. This can be done with both basic ones

Achieve job opportunities by pouring the sliding layer directly onto a pre-coated tape. If the sliding layer is to be cast free from the T-layer and added to it, a pre-coated tape can also be used as a carrier material for the cast sliding layer film in this case.

In the context of the method according to the invention, such strips can have a steel backing and an intermediate layer made of one of the following alloys:

Copper-lead alloys, for example Pb 9 to 25%, Sn 1 to 11%, Fe, Ni, M less than or equal to 0.7%, the rest Cu;

- Copper-aluminum alloys, for example Al 5 to 8%, balance Cu;

- Aluminum-tin alloys, for example

Cu 0.5 to 1.5%, Sn 5 to 23%, Ni 0.5 to 1.5%, balance AI;

- Aluminum-nickel alloys, for example Ni 1 to 5%, Mn 0.5 to 2%, Cu less than or equal to 1%, balance AI;

- Aluminum-zinc alloys, for example

Zn 4 to 6%, Si 0.5 to 3%, Cu to 2%, Mg to 1%, balance Al. It has been found that a layer material made of steel / intermediate layer with a functional layer cast on or applied with another joining method can be produced safely and continuously, preferably in the desired thickness of the functional layer.

Additional elements can be added to the melts to increase the strength of the matrix materials and increase the wear resistance. It has thus been shown that an AIPb dispersion alloy can also be added with about 1 to 4% by weight of silicon, 0.2 to 1% by weight of Mg and 0.1 to 1.5% by weight of Co in order to achieve a to get wear-resistant functional layer. To improve the corrosion resistance of the lead minority phase, it is also advisable to add 0.5 to 3% by weight of tin. For copper-based alloys such as CuPb22, 0.5 to 2% by weight of Sn and 0.2 to 1% by weight of Fe are usually added.

To improve the bond strength between the sliding layer and the intermediate layer, a binding or diffusion barrier layer between the sliding layer and the intermediate layer, for example, made of Ni, Zn, Fe, Co (especially copper-based alloys) as well as NiSn, CuZn, Co, CuSn (especially with aluminum alloys) may be useful.

To carry out the method, it is preferable to start with a device which is equipped with a crucible for melting and / or keeping an alloy ready for casting in the form of a metallic two-component or one with a miscibility gap - 'i -

Multi-component system, with a casting device connected to the crucible for pouring a strip from the alloy, also with devices for collecting the poured strip and for discharging it from the casting point, and with cooling devices for the cast alloy strip leaving the casting point. According to the invention, the pouring device for forming a film or sheet-shaped thin strip should be free or designed as a support on a substrate and the cooling device should be a forced-cooled collecting surface for the film to be cast or a forced-cooled abutment surface for the substrate to be poured and on the free surface contain the directional, highly effective cooling units of the cast film or film.

In particularly advantageous embodiments, the device is equipped with strongly forced-cooled rollers, in particular a strongly forced-cooled roller as a ^' hanger' for the cast film or carrier for the substrate to be cast. In another embodiment of the device according to the invention, a flat-guided guide or transport path can be provided A casting flow device for the molten alloy is arranged across this guide or transport track, the distance between which can be adjusted above the guide track or above a substrate placed on the guide track a sliding layer in a multi-stage construction can be poured onto a substrate in a particularly favorable manner. For this purpose, a plurality of such ^" pouring-flow devices ^{" are} arranged one behind the other in the direction of transport and between the pouring-flow device and behind the last one n pouring and flow bars onto the free surface of the use cast film or cooling units that act on the free surface of the cast film.

Embodiments of the invention are explained in more detail below with reference to the drawing. Show it:

Figure 1 is a greatly enlarged partial section of a layer material with a poured sliding layer made of dispersion alloy.

2 shows a greatly enlarged partial section made of a layer material according to another embodiment;

Fig. 3 is a schematic representation of a manufacturing device;

FIG. 4 shows a schematic illustration of a manufacturing device modified compared to FIG. 3;

Fig. 5 is a schematic representation of another embodiment of the manufacturing device;

FIG. 6 shows a schematic illustration of a manufacturing device modified compared to FIG. 5;

Fig. 7 shows another embodiment of the

Manufacturing device in a schematic representation and

Fig. 8 is a greatly enlarged partial section of a with a manufacturing device 7 produced with a soldered sliding layer of dispersion alloy.

FIG. 1 shows a greatly enlarged partial section made of a layer material 10, with a poured-on sliding layer 13 made of AlPb8Si4SnCu dispersion alloy and an intermediate layer 12 made of AlZn5SiCuPbMg with a carrier material 11 made of steel. The functional layer 13 contains a quasi-amorphous aluminum matrix and globular finely distributed lead particles, of which only the larger lead particles 14 in the illustration in FIG. 1 in

Appearance and dimensions in the

-2

Order of 10 to have. The large amount of lead particles is smaller and is not visible at the magnification chosen in FIG. 1. The large amount of lead particles is not least caused by the fact that a nucleating agent adapted to the alloy type, for example P, B, Ti, Si, boride, nitride or oxide, has been added to the dispersion alloy in a proportion by weight of, for example, 2%. As a result, the nucleating agent was immediately generated a very large amount of very fine lead particles in the dispersion alloy, but they prevented each other from growing during the casting and cooling of the sliding layer 13, so that cooling or quenching at a cooling rate in very rapid

2 6 of the order of 10 to 10 K / s. The size

Keep the amount of lead particles so fine that theirs

-2

Dimensions below 10 µm. Both in the case of the larger lead particles 14 and in the case of the smaller lead particles which are not visible, the segregation of the lead particles could be greatly reduced by the very rapid cooling or quenching of the cast sliding layer 13. In the Aluminum matrix of the sliding layer 13 is due to the influence of crystallization inhibitors (glass formers) for which, for example, Si, B, P, Fe, Co or Ti come into consideration individually or in mixtures with a weight fraction of 0.2 to 2%, and due to the very rapid cooling the cast sliding layer 13, the crystallization of aluminum that has been typical for aluminum alloys has been considerably reduced.

In contrast to the sliding layer 13, the intermediate layer 12 has a structure typical of cast aluminum alloys.

The example in FIG. 2 is a layer material 10 with a support layer 11 made of steel and a sliding layer 13 as a functional layer made of aluminum / lead dispersion alloy AlPblOSi.7SnCu, ie with a lead content of 10% by weight and a content of 7% by weight. % of silicon, which in this case acts both as a nucleating agent for the minority phase lead as well ^'as a crystallization inhibitor in aluminum. As can be seen from FIG. 2, lead particles dispersed in the quasi-amorphous aluminum matrix of the functional layer 13 are globularly finer

Distribution, again only the larger ones

-2

Lead particles with size at 10 to be seen. The silicon is mostly dissolved as a glass former in the quasi-amorphous aluminum matrix and partly as a nucleating agent in the lead minority phase. The tin is essentially incorporated into the lead as corrosion protection.

In this example, the intermediate layer 16 consists of a CuPb22Sn dispersion alloy and, in the example shown, has the distribution of the typical of this dispersion alloy Lead particles 17 on.

One embodiment of the device for carrying out the method for producing a layer material described above with a sliding layer 13 made of alloys with a miscibility gap is shown in two variants in FIGS. 3 and 4.

The alloy or the dispersion alloy is melted and introduced into a titanium 21 which has an outlet 22 at its lower end for a fine jet 23 of the melt. As indicated by arrow 24, the crucible 21 is supplied with a pressurized gas from the top, which is inert to the melt and also dissolves as little as possible in the melt. The crucible 21 is surrounded in the examples shown by an induction coil 25, with which the melt is kept at a predetermined temperature at which it is sufficiently liquid to be pressed through the outlet and form a fine jet 23. If a dispersion alloy is to be processed, the crucible 21 can additionally have stirring devices or vibrating devices which continuously mix the melt mixture of the dispersion alloy intensively and keep it in a fine distribution of its mixture components. These mixing devices or vibration devices are not shown in FIGS. 3 and 4 for the sake of simplicity.

The carrier layer 11 is unwound in the form of a metal strip 40 from a reel and wrapped around a strongly forced-cooled cylinder 26. Before the metal strip 40 reaches the cylinder 26, it undergoes a surface cleaning and deoxidation Device 41, for example a brush device, to ensure that the surface of the metal strip 40 to be coated is free of oxides. For further preparation for the casting, the metal strip 40 runs through a temperature control device in order to ensure the immediate bonding of the cast alloy to the surface of the metal strip 40. In order to maintain the state set in this way until it is poured on, the metal strip 40 is guided under an inert gas atmosphere, which is indicated by the inert gas bell 42, until the crucible 21 emerges. The watering itself and the subsequent cooling also take place under the protective gas bell 42 in this example.

The thin, band-shaped or sheet-like jet 23 of molten alloy or melt mixture of a dispersion alloy pressed out of the crucible strikes the surface of the metal strip 40 at an acute angle * _* in the example of FIG. 3. The angle Λ_T "is chosen so that that the jet 23 is immediately distributed on the surface of the metal strip 40 in the manner of a thin film 20 without lateral spraying or splashing back. Cooling takes place primarily from the cylinder 26. However, the exposed, coated side of the layer material 10 is also intense to cool, it is provided in the example of FIG. 3 that 27 jets 28 of cold gas or cold liquid are directed onto the layer 20 by means of a nozzle arrangement.

The cooling rate of the layer 20 on the cooled roller 26 in opposition to the cooling jets

2 28 is above 10 K / s up to about 10 K / s.

Accordingly, a real alloy that the - Λ ic r- -

Film 20 forms, kept in a quasi-amorphous state, especially when the alloy

Crystallization inhibitors (glass formers) are added. If a dispersion alloy with a mixture gap of its components is processed, a film 20 results, in which the component of the dispersion alloy forming the matrix is in a quasi-amorphous state, while the component (minority phase) dispersed in this matrix is globally finely distributed in the matrix .

In the mode of operation according to FIG. 4, the melt mixture of a dispersion alloy is placed in a crucible 21 and pressurized in this in accordance with arrow 24 by means of a gaseous medium. The crucible 21 at its lower end 22 allows the melt or the melt mixture to enter in a jet "into the gap 30 which is formed between the metal strip 40 guided over a roller 31 and an opposite roller 32. Both rollers 31 and 32 are strong The width of the roller gap 30 is set according to the desired thickness of the layer 20 to be produced, as indicated in Figure 4, a small accumulation of melt or melt mixture forms in front of the gap 30 without any significant delay in the transfer at this point the melt or the melt mixture is to enter the gap 30 from the outlet 22 of the crucible 21. The two rollers 31 and 32 thus do not exert any appreciable pressure effect on the layer material to be formed, but only a certain smoothing effect on the surface of the layer 20 being formed Furthermore, due to the small accumulation of material at the gap 30, a distribution d he melt or the melt mixture in the axial direction of the rollers 31 and 32, so that tapes of greater width than in the example according to FIG. 3 can also be produced. In order to facilitate this axial distribution of the melt or the melt mixture along the gap 30, the crucible 21 is arranged in an inclined position with the angle θ, in order in this way the melt or the melt mixture pressurized in the crucible 21 directly into the gap 30 to inject.

The surface of roller 32 is designed to have virtually no bond with the molten alloy or any of the components of a dispersion alloy to be processed. In order to keep the film 20 formed in the gap 30 on the surface of the metal strip 40, the upper roller 32 is equipped with a strip remover 33. In order to cool the film 20 formed at the exit of the gap 30 on the exposed surface, a cooling nozzle 34 is first provided which directs a jet of cold gaseous or liquid medium against the exit of the gap 30.

The metal strip 40 is further cooled by the cooling roller 31 in order to bring about additional cooling of the film 20 from the metal strip 40 or to avoid reheating the film 20 from the metal strip 40.

The cooling roller 31 is juxtaposed with a third cooling roller 35, which is strongly forced-cooled in order to further cool the film 20 on the side quenched by the roller 32 and the coolant jet from the nozzle 34. A fourth cooling roller 36 is provided behind the third cooling roller 35 and takes over the metal strip with the film 20 from the roller 31. For an effective edition of the film 20 on the To force the surface of the fourth cooling roller 36, a likewise cooled deflection roller 38 is juxtaposed with the fourth cooling roller 36. The strip of layer material 10 is then removed from the fourth cooling roller 36 by means of a strip remover 39. Compared to the procedure according to FIG. 3, the cooling process is further intensified in the example according to FIG. 4, so that 20 cooling rates of between 10 K / s and 10 K / s can be achieved for the film passing into the sliding layer 13. This results in the possibility of also producing layers 20 of greater thickness, for example of 0.5 mm thickness, and so intensively quenching over their entire thickness that the amorphous state of the metallic material is frozen during the cooling process. Finally, the method of operation according to FIG. 4 also offers the possibility of producing wider strips, in particular if several crucibles 21 are arranged next to one another along the gap 30.

The strip of layer material 10 produced according to one of the working methods according to FIG. 3 or FIG. 4 is then wound up on a reel (not shown).

If a layer material 10 is to be produced with an intermediate layer 12 or 16, a metal strip 40 in the form of a laminate is supplied to the device according to FIG. 3 or 4, which is already coated on the side to be coated with the metal of the intermediate layer.

In the examples of FIGS. 5 and 6, the metal strip 40 representing the substrate to be cast is at the speed v in the direction indicated by an arrow indicated transport direction 44 continuously moved over a possibly cooled guide and transport track 45. Above the guide and transport path 45, a pouring device 46 belonging to the pouring device is attached at a distance. The mounting height of the pouring device 46 above the guiding and transport path 45 is set such that between the lower surface of the pouring device 46 lying essentially parallel to the guiding and transport path 45 and the upper surface of the on the guiding and transport path 45 lying metal strip 40 is a predetermined distance d, such that the alloy melt is held against leakage due to its surface tension in the gap thus formed, as can be seen in the left part of Figure 5. On the side on which the metal strip 40 moves out from under the casting flow device 46, a film 20 is formed due to the adhesion of the alloy melt to the surface of the metal strip 40, the thickness of which is less than the distance d from the lower surface of the casting flow Device s 46 is from the surface of the metal strip 40, but due to this distance d, the transport speed v of the metal bar 40 and due to a pressure possibly exerted on the melt and the volume flow V of the melt influenced thereby and the dimensions 1., 1_ of the casting flow -Device s 46 is reproducible and predictable.

The film which forms on the metal strip 40 when leaving the pouring-flow device 46 is produced on the one hand by the cooled metal strip 40 and on the other hand by cooling units possibly directed onto the free surface of the film 20, for example Gas jets or liquid jets cooled very quickly, for example at a cooling rate of 10 2 to 104 K / s.

As FIG. 6 shows, a casting device with a pouring-flow device 46 is particularly advantageously suitable for the multi-stage construction of the sliding layer from two or more films 20 successively cast onto the substrate. This two-stage or multi-stage construction of the sliding layer offers the advantage that the very thin alloy films 20 cooled accordingly rε.sch: can be, so that cooling speeds in the size of 10 to 10 K / s can be achieved. Between the successive pouring device and behind the last pouring device 46, cooling units, for example nozzle arrangements 27 for generating coolant jets 28, can be provided, each directed towards the free surface of the alloy film 20 that has just been formed. In the examples in FIGS. 5 and 6, the pouring device 46 extends across the guide and transport path 45, generally at right angles to the feed direction 44. However, it is also conceivable to insert the pouring device or the pouring device in FIG to arrange an angular position obliquely above the guide and "transport path 45.

In the example in FIG. 6, it is provided that the films 20 formed for coating the substrate or the metal strip 40 are made of the same alloy and in the same thickness. However, a certain structural difference in the two sub-layers of the sliding layer resulting from the films 20 can be expected, because the lower sub-layer is at least partially still when the second film is poured on - -

is warmed up once.

In general, the device in its embodiment according to FIGS. 5 and 6 offers particularly favorable control options. In this way, the defined thickness of the liquid film can be adjusted by regulating the feed rate of the solid, metallic substrate. The cooling rate of the cast layer can also be adjusted by regulating the feed rate of the solid metallic substrate. The setting of the defined thickness of the liquid film can also be carried out by changing the geometry of the outflow point of the alloy, namely by changing the distance d between the underside of the pouring device 46 and the surface of the metal strip 40 and on the other hand by changing the Dimensions of the pouring device. By setting this distance d between the underside of the pouring device 46 and the surface of the metal strip 40, the rate of cooling of the cast layer or film 20 can also be influenced and adjusted.

FIG. 7 shows an embodiment of the device in which a film 47 forming the sliding layer is first produced independently of the substrate or metal strip 40 and, after it has cooled and solidified, is combined with the metal strip 40 by joining with the aid of a laser beam. In this device, the alloy or dispersion alloy is introduced in the molten state into a crucible 21 which has an outlet 22 for a melt jet at its lower end. This melt jet hits the surface of a directly strongly force-cooled cylinder 26 and there forms a film 47, which is cooled very quickly by the cylinder 26 and is passed under a nozzle arrangement 27, from which rays 28 of cold gas or cold liquid are directed onto the free surface of the film 47. The thickness of the film 47 can be determined by the rotational speed of the cylinder 26 and by the extrusion pressure built up in the interior of the crucible 21 by means of inert gas, as indicated by the arrow 24. The dispersion alloy or alloy is poured onto the surface of the cylinder 26 at an angle / r which is set up in such a way that no parts of the alloy spray off when it hits the surface of the cylinder 26. The surface of the cylinder 26 is designed such that there is no bond between the cast alloy and the cylinder surface, but only an intense heat transfer.

The cooling rate of the film 47 on the force-cooled cylinder 26 and the counteraction of the g

Cooling jets 28 are between about 10 K / s and about

8 9

10 K / s up to about 10 K / s. Accordingly, a real alloy that forms foil 47 is kept substantially in an amorphous state. Will one

Dispersion alloy with a miscibility gap

Ingredients in the manner specified to a film

47 processed, this results in 47 in this film

Matrix in an essentially amorphous state, while the constituent dispersed in this matrix is globular, extraordinarily, finely distributed. The so educated

Foil 47 is transferred to a strongly forced-cooled roller 32. This roller 32 is opposed to a roller 31, which is also strongly cooled, so that a

Gap 30 is formed, in which the film 47 and a __

band-shaped substrate, for example a metal band 40, can be fed around the roller 31. A laser beam 48 with an angle OC is directed into this feed gap in such a way that a slight warm-up occurs on the converging surfaces of the foil 47 and the metal strip 40. The film 47 and the metal strip 40 are soldered to one another on the heated surfaces by lightly compressing them without any appreciable reduction in thickness. The belts thus combined are further cooled between the roller 31 and another cooling roller opposite it and transferred to a fourth cooling roller 36. This further cooling roller 36 is juxtaposed with a likewise cooled deflection roller 38. The strip of layer material 10 is then removed from the fourth cooling roller 36 by means of a strip remover 39. Compared to the mode of operation according to FIGS. 3 and 4 and the mode of operation according to FIGS. 5 and 6, it is necessary to carry out a certain warm-up of the surfaces to be soldered to one another. This results in certain structural changes to the soldered surface areas, as shown in FIG. 8. FIG. 8 shows a structure of the layer material 10, which essentially corresponds to that according to FIG. 1, that is to say a layer material with carrier material 11 made of steel, intermediate layer 12 made of AlZn5SiCuPbMg and sliding layer 13 made of AlPb8Si4SnCu dispersion alloy. In contrast to the layer material according to FIG. 1, in the layer material according to FIG. 8 a certain coarsening of structure has occurred in the intermediate layer 12 at the connection surface 49 to the sliding layer 13. In the sliding layer 13 are in the area of the soldered connection surface 49 to the intermediate layer - __:H-

12 out due to the warm-up required for soldering somewhat larger lead particles 14. This coarsening of the structure and the formation of somewhat larger lead particles 14 can, however, be readily accepted in view of the fact that the production of the sliding layer 12 as a film enables a much faster cooling of the film forming the sliding layer 13, so that in the sliding layer 12 itself the aluminum matrix is very much stronger. ^has cer amorphous properties as in the example in FIG. 1, a difference which, however, is not visible in the magnification selected in FIG.

Reference list

- Folie - Laserstrahl-Bündel - Verbindungsfläche

- foil - laser beam bundle - connecting surface

Claims

Patent claims 1.) Method for producing a Layer material for sliding elements with a sliding layer applied to a carrier layer made of at least one alloy in the form of a metallurgical two- or multi-component system with a mixing gap (monotectic), characterized in that the sliding layer is continuously cast from the alloy and immediately following the casting in a continuous cycle of cooling with for the prevention of particle growth of the immiscible metallurgical components over particle dimensions of 0.01 to 1µm, preferably t. 1 μm, is subjected to a sufficiently high solidification rate. 2.) Method according to claim 1, characterized in that the alloy or alloys are produced by melt metallurgy and are kept at a temperature above the segregation temperature corresponding to the system and the composition as well as when they are kept ready for casting. . ) Method according to claim 1 or 2, characterized in that the alloy or alloys to be cast contain nucleating agents adapted to the respective alloy type, P, B, Ti, Si, borides, nitrides and oxides, in a proportion by weight between 0.1 and 3.5% are added. - __ö - 4.) Method according to one of claims 1 to 3, characterized in that the setting of the defined thickness of the liquid film is carried out by metering the molten alloy stream from the crucible. 5.) Method according to one of claims 1 to 4, characterized in that the cooling rate of the cast alloy layer is adjusted by metering the molten alloy stream from the crucible. 6.) Method according to one of claims 1 to 5, characterized in that the setting of the defined thickness is carried out by regulating the withdrawal speed of the cast layer from the casting point. 7.) Method according to one of claims 1 to ^" 6, characterized in that the following alloys with a mixture gap are cast: AlPb, FePb, CuPb, MnPb and NiPb, the lead content being greater than the system-related eutectic composition and up to 40 parts by mass in percent. 8.) Method according to one of claims 1 to 7, characterized in that the sliding layer is cast in the form of a strip free of the carrier layer and, after cooling, is continuously applied to the carrier layer by means of a joining process, for example by means of a laser beam. 9.) Method according to one of claims 1 to 7, characterized in that the alloy or alloys in the form of a metallurgical two- or multi-component system are applied continuously as a liquid film with a defined layer thickness in one or more to a solid, preferably band-shaped, metallic substrate forming the carrier layer poured in several successive stages and then immediately cooled together with the substrate in connection with the substrate at a high solidification rate. 10.) Method according to claim 9, characterized in that the defined thickness of the liquid film is adjusted by regulating the feed speed of the solid, metallic substrate. 11.) Method according to claim 10, characterized in that the cooling rate of the cast layer is adjusted by regulating the feed rate of the solid metallic substrate. 12.) Method according to claim 10, characterized in that the setting of the defined thickness of the liquid film is carried out by changing the geometry of the outflow point of the alloy. 13.) Method according to claim 10, characterized in that the adjustment of the defined thickness of the liquid film by adjusting the distance between the outflow point the alloy and surface of the solid metallic substrate is made. 1 . ) Method according to claim 10, characterized in that the cooling rate of the cast layer is carried out by adjusting the distance between the outflow point of the alloy and the surface of the substrate. 15.) Method according to one of claims 10 to 14, characterized in that an overall layer made up of several individual layers is built up by multiple, successive watering and interim cooling of the substrate strip. 16.) Method according to claim 15, characterized in that the overall layer is made from individual layers of different thicknesses. 17.) Method according to one of claims 15 and 16, characterized in that the individual layers are cast from alloys with modified compositions. 18.) Method according to one of claims 15 to 17, characterized in that the individual layers are produced with different structures by changing the composition of the alloy and / or by changing the cooling conditions. 19.) Method according to one of claims 10 to 18, characterized in that the substrate is placed on a corresponding surface before watering Cooling parameters and a temperature designed according to the adhesion formation is brought. 20.) Method according to one of claims 10 to 19, characterized in that a tape is used for the substrate tape to be cast, onto which an intermediate layer with good sliding properties is applied before the sliding layer is poured on. 21.) Method according to claim 20, characterized in that the intermediate layer consists of the following alloys: Copper-lead alloys, for example Pb 9 to 25%, Sn 1 to 11%, Fe, Ni, Mn less than or equal to 0.7%, Cu balance; Copper-aluminum alloys, for example Al 5 to 8%, Cu balance, aluminum-tin alloys, for example Cu 0.5 to 1.5%, Sn 5 to 23%, Ni 0.5 to 1.5%, Al Rest; Aluminum-Niσkel alloys, for example Ni 1 to 5%, Mn 0.5 to 2%, Cu less than or equal to 1%, Al remainder; - Aluminum-zinc alloys, for example Zn 4 to 6%, Si 0.5 to 3%, Cu to 2%, Mg to 1%, Al remainder. 22.) Device for carrying out the method according to claim 1 with a crucible for melting and / or keeping ready for casting an alloy in the form of a metallurgical two-or alloy with a mixing gap Multi-component system, with a pouring device connected to the crucible for pouring a strip made of the alloy, further with devices for catching the cast strip and for removing it from the casting point, as well as with cooling devices for the cast alloy strip leaving the casting point, characterized in that the casting devices (outlet 22, casting flow device 46) for Formation of a film or foil-shaped thin strip (20, 47) is formed freely or as a support on a substrate (metal strip 40) and the cooling device has a forced-cooled collecting surface (cylinder 26) for the film (47) to be cast or a forced-cooled abutment surface (cylinder 26, roller 31, guide and transport track (45)) for the substrate to be cast (metal strip 40) and highly effective cooling units (nozzle arrangement 27) cooling rollers directed onto the free surface of the cast foil (47) or the cast film (20). 32, 35, 36). 23.) Device according to claim 22, characterized in that a cooled roller (26, 31) is arranged under the casting device as a catcher for the cast film (47) or carrier for the substrate to be cast (metal strip 40) and becomes one of the desired The removal speed of the film (47) or the film (20) from the casting point is driven at a corresponding, preferably controllable, rotational speed. 24.) Device according to claim 22 or 23, characterized in that a nozzle arrangement (27) for coolant in the area of the collecting surface for the film (47) or the abutment surface for the Substrate (metal strip 40) is provided behind the casting point in the transport direction (44). 25.) Device according to one of claims 22 to 24, characterized in that in the transport direction (44) behind the casting point there is a cooling roller (32) which grips the free surface of the foil (47) or the film (20) opposite the collecting surface ( Cylinder 26) or abutment surface (cylinder 26, roller 31, guide and transport track 45) is arranged. 26.) Device according to claim 24 or 25, characterized in that an arrangement of several force-cooled cooling rollers (31, 32, 35, 36) for Hi carrying out the film (47) or the cast substrate (metal strip 40) is provided behind the casting point is, wherein between cooling rollers (32, 35, 36) arranged one behind the other in the transport direction (44), cooling nozzles (34, 34*) directed onto the film 47 or onto the coated substrate can be arranged. 27.) Device according to claim 22, characterized in that a strongly forced-cooled guide or transport track (45) is arranged under the casting device as a catcher for the cast film (47) or carrier for the substrate to be cast (metal strip 40) and becomes one of the desired The removal speed (v) of the film (47) or the film (20) from the casting point is driven at a corresponding, preferably controllable running speed, while the casting device moves transversely over the guide or transport path (45) extending casting flow device (46), under which the guide or transport path (45) or the substrate placed on it (metal strip 40) is in a fixed, preferably adjustable. Distance (at) moves through at a fixed, preferably adjustable, speed (v). 28.) Device according to claim 27, characterized in that two or more pouring flow devices (46) are arranged one behind the other at a fixed mutual distance in the transport direction (44) of the guide or transport track (45). 29.) Device according to claim 28, characterized in that between successive casting flow devices (46) and in the transport direction behind the last casting flow device (46) on the free surface of the cast foil (47) or the cast film (20) acting cooling units, for example coolant nozzles (27), are arranged. 30.) Device according to claim 22, characterized in that the casting device is designed to form a thin film (47) from the alloy and in the transport direction of the film (47) behind the casting point and a first cooling device (nozzle arrangement 27) a joining device, in particular laser beam joining device (laser beam bundle 48), for continuously firmly connecting the cast first-cooled alloy foil (47) via a first forced-cooled roller (32) and and the substrate strip is brought together via a second forced-cooled roller (31) and a laser beam bundle (48) is directed into the joining gap (30) of these two rollers (31, 32). 31.) Device according to one of claims 22 to 30, characterized in that the loading of the casting point with the molten alloy and its quantitative dosage via an adjustable pressure (arrow 24) acting on the surface of the alloy melt located in the crucible (21). Protective gas is carried out. 32.) Device according to one of claims 22 to 31, characterized in that the casting point is provided with a device which supplies protective gas and holds it above the casting point (protective gas hood 42). 33.) Device according to one of claims 22 to 31, characterized in that those device areas in which the casting and cooling of the alloy foil (47) or the alloy film (20) take place with devices that supply protective gas and hold it in these device areas (protective gas hood 42) are provided.