Patent Application
20170037900
This invention relates to a sliding bearing material with a matrix material consisting of 2.1-2.6 wt. % iron, 0.05-0.2 wt. % zinc, 0.015-0.15 wt. % phosphorus, ≦0.03 wt. % lead, ≦0.2 wt. % impurities that result from the metallurgical melting process, and the rest being copper. The invention also relates to a sliding bearing composite material with a backing layer, a bearing metal layer and a sliding layer applied to said bearing metal layer, as well as a sliding element, in particular a radial sliding bearing in the form of a bushing or a bearing shell.
Lead-free materials based on copper, iron and phosphorus, hereinafter referred to as CuFe2P alloys, have been common knowledge for a long time and have also been used for a while as sliding bearing materials, particularly sliding bearing composite materials for bushings or bearing shells. The documents DE 10 2009 002 894 A1 and DE 10 2011 007 362 A1 by the applicant are referred to as examples in which the material with the aforementioned composition is described.
Copper-iron-phosphorus alloys can be processed both in casting and sintering, or applied to a carrier layer using roll bonding. They are characterised by high ductility, basic strength and basic hardness. These parameters can be adjusted to the respective requirements across a wide range using thermomechanical processing, so that the materials reach the level of hardness, strength and seizure behaviour of the lead-bronze that needs to be replaced due to insufficient environmental compatibility. In fact, the materials are considerably less machinable than these for many reasons, including their high basic strength and hardness. Poor machinability results in a shorter tool life and accordingly quick deterioration in terms of machining precision and surface quality,
The German Copper institute systematically investigates, among other things, the machinability of copper materials and publishes the results in the so-called information print-outs. Below, the 18th edition of the information print-out (i.18) from 2010 is referred to. Here, the machinability of copper materials is divided into three different major groups. Materials that are similar in terms of machinability are grouped together. Copper materials are primarily categorised based on the chip shape that is formed and the amount of wear on the tool.
Machining Group I contains copper materials with very good machinability and covers lead-copper, tellurium-copper or sulphur-copper alloys with a homogenous or heterogeneous structure. During machining, short, discontinuous chips are formed. The wear on the tool is rated as low. Machining Group II contains materials that are moderately to easily machinable. Compared with materials in Machining Group I, machining these materials results in longer chips, generally medium-length, spiral-shaped chips. The wear on the tool when machining these kinds of materials is rated as “medium”. In Machining Group III, the materials that are most difficult to machine compared to Groups I and III, are grouped together. When machining these materials, long, spiral-shaped, thread or ribbon chips are formed. The wear on the tool is high.
In order to make further differentiations regarding the machinability of the standard materials within these major groups, the data for which was obtained empirically, a machinability index is also established. For the materials in the first group, this is between 100 and 70; for those in the second group, it is between 60 and 40 and for those in the third group, it is between 30 and 20.
CuFe2P alloys are not listed in the information print-out i.18 from the German Copper institute.
The purpose of the invention is to provide a sliding bearing material which has good tribological and mechanical properties similar to those of CuFe2P alloys that are already known, but with improved machinability and, due to a longer tool life, with greater machining precision and surface quality. Another purpose of the invention is to provide a material which, in contrast to materials that are already known, is even less susceptible to seizure, particularly when there is a lack of lubrication.
The purpose is fulfilled with the sliding bearing material according to patent claim 1.
The inventive sliding bearing material features a matrix material made from 2.1-2.6 wt. % iron, 0.05-0.2 wt. % zinc, 0.015-0.15 wt. % phosphorus, ≦0.03 wt. % lead, ≦0.2 wt. % impurities that result from the metallurgical melting process, and the rest being copper, with optionally at least one hard material and optionally at least one solid lubricant, and which has at least one additive selected from a group of teliurium sulphur, chromium and zirconium.
It was ascertained that by adding tellurium, sulphur, chromium and/or zirconium as chip-breaking elements, the chip shape and therefore the machinability of these matrix alloys were also improved. The addition of Te, S, Cr and/or Zr leads to a reduction in the material's elongation at break, Whilst CuFe2P without these additions has an elongation at break of around 15%, this can be reduced to up to 2% by adding tellurium and/or sulphur. The chips therefore do not form any long ribbon or continuous chips, but rather break into fine, needle-like fragments which, in contrast to long chips, do not hinder the machining of the material. It was particularly surprising to discover that the addition of tellurium, sulphur, chromium and/or zirconium also significantly reduces the sliding bearing material's susceptibility to seizure.
According to an advantageous embodiment, the additive is fully dispersed within the matrix material with a proportion of 0.01 to 2.0 wt. % in relation to the sliding bearing material. It is preferable for the additive to be dispersed fully with a proportion of 0.05 to 1.0 wt. %, and particularly preferable fully with a proportion of 0.1 to 0.3 wt. % within the matrix material.
The effect of the reduced elongation at break is only desirable up to a certain point, because if the elongation at break is too low, then it only allows for a limited amount of deformation of the CuFe2P material after casting, and this deformation ability is essential when manufacturing a bearing. Therefore, the elongation at break must never be below 1%. If the amount is above 2 wt. %, then this is no longer guaranteed and essential properties of the matrix material, such as strength, deformation ability etc., could be affected. If the amounts are too low, i.e. below 0.01 wt. %, the chip-breaking effect does not manifest itself sufficiently. The chip-breaking effect is already very well pronounced with additive quantities of 0.1 to 0.3 wt. %, without the matrix material's properties being significantly worsened. This quantity range therefore appears to be a very good compromise.
The added tellurium, sulphur, chromium and/or zirconium are undissolved within the CuFe2P matrix and are therefore in a separate phase. This phase is predominantly found at the grain boundaries of the matrix material, where they cause cracks to be diverted in the matrix structure under heavy, localised, mechanical loads such as during machining, and therefore ultimately encourage the chip to break off under a continuous load. Preferably, 90% of the measurable particles in the matrix material have a maximum dimension of 30 μm, and even more preferable 15 μm. “Measurable” refers to all particles that have a minimum size of 500 nm. This minimum size only serves as an explicit “cut-off” point for detection and therefore for the purposes of unambiguity in the parameters.
If the additives form particles of this size, then the additive is dispersed in the CuFe2P matrix in such a way that it significantly increases the machinability of the sliding bearing material, whilst the other mechanical and tribological properties of the matrix materials are either influenced in a very small amount or not at all, or even, in the case of susceptibility to seizure, surprisingly positively influenced. This is due to the fact that a finer distribution of particles causes widespread disruption in the grain boundaries of the matrix structure, and therefore the chips break more easily. To prevent this leading to a significant loss in strength, the contents of the chip-breaking additive within the boundaries outlined above must be retained. However, if the particles are larger than 15 μm and can therefore only be found sporadically and locally throughout the structure with a proportion of 2 wt. % or less, there will be no sufficient chip-breaking effect in the whole material.
Following the dispersion of at least one additive within the matrix, the sliding bearing material has an advantageous machinability index of 100-70. With a machinability index of 100 to 70, the sliding bearing material is categorised into Machining Group I. It forms discontinuous chips during machining, which do not affect the machining of the material because they can be effectively removed from the machining area. This increases the surface quality, machining precision and reduces wear on the tool.
In another advantageous embodiment, on a sliding bearing material below the limit of a load and sliding speed of 720 MPa m/s, preferably below 800 MPa m/s, no adhesive wear occurs.
The maximum load and sliding speed measurement is recorded in a seizure test as described below in
The sliding bearing material should also preferably include at least one hard material selected from a group consisting of silicides, oxides, carbides and nitrides, in particular AlN, Al2O3, SO2, TiO2, ZrO2, Mo2C, MoSi2, SiC, B4C, Si3N4 and c-BN.
It is also advantageous if the sliding bearing material includes at least one solid lubricant selected from a group consisting of h-BN and graphite.
The sliding bearing material described above can be used as a solid material in a sliding bearing element, such as a bushing or a bearing shell. A solid material means that the material has a sufficient level of strength and therefore supports itself. At the same time, the material takes on the role of a bearing metal.
The invention also includes a sliding bearing composite material with a backing layer, a bearing metal layer and a sliding layer applied to said bearing metal layer. The bearing metal layer consists of a sliding bearing material of the type described above.
Sliding bearing composite materials, particularly in the form of sliding bearing elements converted into bearing shells, are calibrated to their final dimension in the final working stage by drilling. As bearing shells must fundamentally be mass-produced, there is currently a need for optimising this stage of machining. For example, several of the same bearing shells can be placed in a row and drilled in one working step. Further, a high cutting and feed speed is demanded. The tool life must be high so that as little time as possible is lost in changing the tool and the following setup procedure. Last but not least, wet machining must be ruled out because residue from coolants and lubricants would have to be laboriously removed from the bearing she surface. Machinability is therefore currently the most important factor in this application.
The backing layer in the sliding bearing composite material should preferably be a steel layer.
The so-called steel backing ensures the required press fit due to its stiffness, so the composition of the bearing material's structure can be adjusted regardless of strength requirements. The microstructure of the claimed copper alloys can therefore be designed in such a way that their strength and hardness, as well as theft tribological properties such as seizure behaviour, are similar to those of traditional lead-bronze materials. Overall, the scope of application for the sliding bearing composite material is significantly expanded. With steel backings, the composite materials also offer advantages due to their thermal expansion coefficient in situations where steel casing is used.
The aim of the manufacturing process described below, using the tellurium phase as an example, is for the phase of the additive to be present in the end product in a defined size which has proven to be beneficial in terms of seizure behaviour. There is also no need for a finishing ageing heat treatment, which is not used when—as in this case—the main focus is optimising the sliding properties, but rather for improving strength or electrical conductivity.
According to an advantageous embodiment, the bearing metal layer is a sinter layer.
The sinter layer is applied to the steel backing in powder form. The additive or additives can already be contained in the pre-alloyed matrix material and pulverised together with this, or can be added as a separate powder to the sinter powder of the matrix material. If the CuFe2P matrix and the additives are in separate powder forms, these powders can be mixed with the appropriate weight distribution and then sintered on the backing layer. The sinter powder that is applied to the steel backing is heated in an inert atmosphere to a sinter temperature of between 800° C. and 1000° C. over a period of 10-30 minutes, rolled, then sintered again at the same temperature and for a similar period of time, and then, depending on the hardness requirements, put through another rolling procedure. The aim in particular is to achieve the lowest possible or no residual porosity. Further procedures are not necessary. In particular, annealing can be omitted, as annealing is essentially integrated in the sinter process. The details of the sinter process are as follows: The sinter powder is applied to the steel backing in a defined thickness; then, the first sinter process takes place at a temperature of between 800° C. and 1000° C. Before the second sinter process is carried out at a similar temperature, the sinter layer is compacted using a rolling process during deformation of between 10-30%, and therefore condensed. One final round of roiling completes the process, which adjusts the bimetallic strip to the desired strength and thickness tolerance, in both sinter processes, the cooling conditions are controlled in such a way that the separate tellurium particles do not exceed maximum dimension of 30 μm, preferably of 15 μm.
According to an alternative embodiment, there is a roll cladding connection between the bearing metal layer and the backing layer, if necessary via an intermediate layer.
First, the bearing metal is manufactured in the form of strip material, the intermediate layer is optionally pre-cladded and then the bearing metal is rolled out onto the backing layer (with or without the intermediate layer). Thereby, the bearing metal undergoes a deformation of 35-70%, which makes it necessary to then carry out subsequent thermomechanical treatment in order to adjust the mechanical properties of the bearing metal to the desired level. This includes an initial annealing of the composite at 550° C. to 700° C. for 2 to 5 hours, at least one initial roiling of the composite, whereby a deformation degree of 20 to 30% is achieved, at least one second annealing process at 500° C.-600° C. for more than 1 hour, if necessary a second rolling of the composite, whereby a deformation degree of max. 30% is achieved, with a subsequent third round of annealing at a temperature of >500° C. for at least 1 hour. The annealing temperature and the time for which it is kept at this temperature are selected in such a way that the tellurium phase forms within the aforementioned size range here as well. There is no ageing heat treatment, which is usually used to increase strength and electrical conductivity. As the third round of annealing described above is preceded by odd rolling, this annealing process causes the size of the tellurium phase to be adjusted, as well as causing a recrystallization of the matrix material.
For the intermediate layer, either copper or a copper alloy can be used, for example a copper-zinc alloy or a copper-tin alloy.
In another alternative embodiment, the bearing metal layer is a cast layer. The casting on the backing layer typically takes place at a temperature of 1000° C. to 1250° C. Here too, it is followed by thermomechanical treatment using rolling and annealing to achieve the desired material properties, in particular, for example, the tellurium size distribution and therefore an improved resistance to seizure. After casting on a steel strip, the composite material undergoes a homogenisation procedure at a temperature of more than 650° C. for several hours (>4 h), There is a subsequent deformation of the composite of between 35 and 70% in several rolling passes, followed by another final annealing process which adjusts the size of the tellurium phase, as well as causing the matrix material to recrystallize. Here too, temperatures of above 500° C. are used for a period of more than 1 hour.
Along with the sliding bearing material and the sliding bearing composite material, the invention also includes a sliding element, in particular a sliding bearing which consists of a sliding bearing material of the type described above.
To manufacture the sliding bearing element, boards are slit and then separated from the solid or sliding bearing composite material, manufactured as described above, and the boards are transformed into sliding bearing elements (e.g. bearing shells or bushings) using known deformation processes. This is followed by a machining process to create the dimensional accuracy of the bearing bore and, if necessary, applying a sliding layer.
Other properties and features of the invented sliding bearing material are explained in the following drawings. These are:
The inventive material and a comparative material underwent a wear test according to the diagram shown in
In
In the pure matrix material (10), an average load limit of 723 MPa m/s was measured.
The inventive material with tellurium had a significantly higher average load limit of 800 MPa m/s without seizure.
The inventive sliding bearing materials therefore have an improved level of machinability compared to known sliding bearing materials without additives, as well as a surprisingly significantly reduced susceptibly to seizure. They are therefore especially suitable for use in the event of insufficient lubrication, even without solid lubricants.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10 2014 207 332.4 | Apr 2014 | DE | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2015/058235 | 4/16/2015 | WO | 00 |
