Patent Application
20230399732
The present invention relates to a method for making a braking band of a cast iron brake disc with increased resistance to wear and corrosion and a braking band thus obtained.
A brake disc of a disc brake system of a vehicle comprises an annular structure, or braking band, and a central fixing element, known as the bell, by means of which the disc is fixed to the rotating part of a vehicle suspension, e.g., a hub. The braking band is provided with opposing braking surfaces suitable to cooperate with friction elements (brake pads), housed in at least one caliper body placed straddling the braking band and integral with a non-rotating component of the vehicle suspension. The controlled interaction between the opposing brake pads and the opposite braking surfaces of the braking band determines a braking action by friction which allows the deceleration or stopping of the vehicle.
Generally, the braking band of a brake disc is made of cast iron, in particular gray cast iron, or steel. Indeed, the cast iron allows to obtain good braking performance (especially in terms of wear containment) at a relatively low cost. Braking bands made of carbon or carbon-ceramic materials offer much greater performance, but at a much higher cost.
While being harder than many metals, cast iron wears out during the operation of the brake disc, thereby reducing the thickness of the braking band and thus limiting the service life of the brake disc.
Another limitation of cast iron is related to the fact that it rapidly corrodes following exposure to water, in particular if in the presence of salts (sodium chloride, potassium chloride). This creates a layer of oxide on the surface of the braking band which can cause braking problems, in addition to being unsightly, until it is removed.
Several strategies have been implemented for treating the braking bands of cast iron brake discs to overcome these problems and are diagrammatically listed below:
Therefore, the need is strongly felt to have a method for making braking bands of cast iron brake discs which allows to form a surface layer on the surface of the braking band with characteristics of high resistance to wear and corrosion and which completely or at least partially overcomes the operational limitations of the prior art described above.
Therefore, it is an object of the present invention to eliminate, or at least reduce, the aforementioned problems related to the prior art by making available a method for making a braking band of a cast iron brake disc with increased wear and corrosion resistance which does not result in a significant increase in production costs.
It is a further purpose of the present invention to provide a method for making a braking band of a cast iron brake disc having increased wear and corrosion resistance, which does not result in a significant increase in production time.
It is a further purpose of the present invention to provide a method for making a braking band of a cast iron brake disc having increased wear and corrosion resistance, which can be performed at processing temperatures compatible with the requirement to contain distortion on the braking band.
The technical features of the invention may be clearly found in the contents of the claims presented below and the advantages thereof will become more apparent from the following detailed description, made with reference to the accompanying drawings, which show one or more embodiments thereof, merely given by way of non-limiting examples, in which:
Elements or parts in common to the embodiments described will be indicated hereafter using the same reference numerals.
The present invention relates to a method for making a braking band of a cast iron brake disc with increased resistance to wear and corrosion and braking band thus obtained.
The making method will be described first, followed by the description of the braking band obtained by such a method.
According to a general embodiment of the invention, illustrated in the chart in
The immersion in the molten aluminum is prolonged for a predetermined period of time so as to allow the diffusion of aluminum atoms in the cast iron surface microstructure with the consequent formation of intermetallic iron-aluminum compounds at a surface layer of the braking band, thereby generating in said predetermined surface region of said braking band a layer consisting of intermetallic iron-aluminum compounds.
The method comprises the following further operational steps:
It has been experimentally found that the aforesaid intermetallic iron-aluminum compound layer exposed in the surface confers a higher corrosion and wear resistance to said cast iron braking band at said predetermined surface region compared to the case in which the cast iron braking band is free from the coating and the cast iron is directly exposed in the surface.
The properties conferred by the intermetallic iron-aluminum compound layer are maintained over time by virtue of the fact that such a layer combines corrosion resistance and wear resistance. In other words, the protective layer made of intermetallic iron-aluminum compounds is less attackable not only chemically, but also mechanically, as a result of the rubbing caused by the braking action applied by the pads on the braking band. This synergistically contributes to preserving it during the operational life of the braking band.
Compared to the aforementioned traditional techniques for treating the braking bands of cast iron brake discs (application of surface coatings; reactive/diffusive processes; “in-situ” forming processes), the method according to the invention is operationally simpler to implement because it does not require the use of complex plants to build and operate.
Furthermore, the method according to the invention requires relatively short performance times, at least with regard to steps b), c), and d).
Thus, the method according to the invention allows to make a braking band of a cast iron brake disc with increased wear and corrosion resistance to be manufactured in a technically simple manner, without involving a significant increase in cost and production time.
More in detail, the aforesaid layer of intermetallic iron-aluminum compounds is formed at a surface layer of said cast iron braking band in contact with the molten aluminum by a diffusion process of aluminum atoms within the cast iron structure and formation of intermetallic iron-aluminum compounds.
The aforesaid intermetallic iron-aluminum compound layer may comprise a plurality of intermetallic iron and aluminum compounds, in particular Fe3Al, FeAl, FeAl2, FeAl3, Fe2Al5. The predominant intermetallic phase is FeAl3 because it is thermodynamically more stable.
Preferably, the aforesaid predetermined temperature at which the molten aluminum is maintained is not less than 680° C.
Advantageously, the aforesaid predetermined temperature at which the molten aluminum is maintained is not greater than 750° C., and is preferably comprised between 690° C. and 710° C., and even more preferably equal 5 to 700° C. Such temperature values constitute a good compromise between the need to promote the formation of intermetallic compounds and the need to preserve unaltered geometric characteristics of the braking band. Indeed, at such temperature values of molten aluminum, the chemical reaction between iron and aluminum is fast enough to allow a rapid formation of the intermetallic layer and the distortions induced on the braking band are within acceptable tolerances from an operational point of view.
Operationally, the growth thickness of the aforesaid layer of intermetallic compounds is mainly biased by the temperature of the molten aluminum and the immersion time in the molten aluminum. The temperature of the molten aluminum being equal, the thickness increases as the immersion time increases; the immersion time being the same, the thickness increases as the temperature of the molten aluminum increases.
Advantageously, as the temperature of the molten aluminum is the parameter most subject to constraints to avoid distortions on the braking band, the thickness of the layer of intermetallic compounds is controlled substantially by acting on the duration of the immersion time in the molten aluminum. The predetermined period of immersion time is then set as a function of the desired thickness of said intermetallic compound layer, taking into account the temperature of the molten aluminum.
Preferably, if the molten aluminum is maintained at a temperature of between 690° C. and 710° C., the aforementioned predetermined immersion time is comprised between 5 and 60 min, and even more preferably equal to min, to obtain a layer of intermetallic compounds comprised between 30 and 150 μm.
In accordance with a preferred embodiment of the method, illustrated in the charts of
Operationally, said step f) of decarburization is performed before said step b) of immersion and is suitable to make, at least at said predetermined surface region, a surface layer substantially free of carbon, in particular free of graphite flakes, having a thickness, which extends from the outer surface of said braking band up to the aforesaid predetermined depth.
Advantageously, the decarburized surface layer has a depth substantially either equal to or greater than the depth of the intended layer of intermetallic iron-aluminum compounds. Operationally, the decarburization is thus performed up to a depth from the outer surface of said braking band either equal to or greater than the depth of the intermetallic iron-aluminum compound layer to be obtained. Preferably, the predetermined decarburization depth is 30 μm or greater.
Advantageously, step f) of decarburization is aimed at preparing in the braking band a surface layer which facilitates the formation (by aluminization) of a more homogeneous and compact layer of intermetallic compounds.
Indeed, it has been experimentally found that, by subjecting a braking band not superficially decarburized to aluminization (immersion in molten aluminum), the intermetallic compound layer obtained is very inhomogeneous, with large detached zones and strong variability in the grown thickness. Furthermore, the growth structure appears very granular.
On the contrary, by subjecting a superficially decarburized braking band made of cast iron to aluminization (immersion in molten aluminum), the intermetallic compound layer obtained is homogeneous and substantially continuous, not interrupted by graphite flakes.
This is apparent by comparing
The different morphology of the intermetallic compound layer present on a non-decarburized braking band and on a superficially decarburized braking band is thus attributable to the presence or absence of carbon, in particular in the form of graphite flakes, in the surface layer subject to the diffusive effects of the aluminization process. In particular, it was found that the presence of graphite flakes has a strong effect of reducing the surface wettability by liquid aluminum. In addition to this, the presence of graphite flakes has the further ability to slow down the growth of the intermetallic compound layer, which in non-decarburized cast iron, indeed, appears “patchy” and still far from being a continuous rather than a compact layer.
It has been experimentally found that the presence of carbon in the surface layer of the braking band subject to diffusion penetration of aluminum atoms (induced by aluminization) also leads to the formation of iron carbide as well as intermetallic compounds. The presence of iron carbide creates points of discontinuity in the intermetallic compound layer, which can trigger corrosive phenomena and cracking. Advantageously, the surface decarburization thus allows to avoid (or at least significantly reduce) the formation of iron carbide, leading to the formation of an intermetallic compound layer which is more resistant to corrosion and less prone to cracking.
Preferably, in said step f), the decarburization of said at least one predetermined surface region is carried out by means of an electrolytic process.
More in detail, said electrolytic process is carried out by immersing the predetermined surface region of said braking band in a molten salt bath and applying an electrical potential difference between the bath and the braking band.
In applying the electrical potential difference, the braking band is connected to a positive pole (cathode), while the aforementioned molten salt bath is connected to a negative pole (anode). Carbon, in particular in the form of graphite flakes, is oxidized to carbon dioxide by the release of electrons and atomic oxygen released at the anode. Carbon reacts primarily with oxygen and is eventually bound as carbon dioxide.
The oxidation of the surface of the braking band induced by the electrolytic process is not limited to the carbon present there, but also extends to the metal matrix of the cast iron (iron), causing the formation of a surface film of metal oxide. Reversing the polarity causes a reduction in the surface film of metal oxide, which is thus restored to its original metallic state.
Preferably, the aforementioned electrolytic process may thus provide that, after a predetermined period of time in which the surface of the braking band was connected to the cathode to oxidize the carbon, the polarity is reversed to return the metal oxide film to its original metallic state.
Advantageously, during the performance of the electrolysis process, the polarity reversal can be repeated several times in sequence.
Operationally, the decarburization depth is controlled by adjusting the duration of the electrolytic process, possibly divided into several polarity reversal cycles. By increasing the duration of the decarburization process (braking band oxidation step; cathode connection), the depth of decarburization increases, all other conditions being equal.
Decarburization can be achieved by alternative processes to the electrolytic process described above, such as by laser treatment or chemical treatment. However, the decarburization by the electrolytic process is preferred because:
In more detail, it has been observed that at the oxidized areas on the cast iron metal matrix, the wettability of the molten aluminum is greatly reduced, which negatively affects the aluminization process and the characteristics of the intermetallic compound layer. Also for this reason, the electrolytic decarburization process is preferred over the alternative processes indicated above.
As mentioned above, the growth thickness of the aforesaid intermetallic compound layer is mainly affected by the temperature of the molten aluminum and the immersion time in the molten aluminum. However, it was found that an additional factor which biases the thickness of the intermetallic compound layer is the silicon content in the molten aluminum. The higher the weight content of silicon in the molten aluminum, the thinner the intermetallic compound layer, all other conditions being equal. Preferably, the molten aluminum has a silicon content of less than 1% by weight.
Preferably, the molten aluminum has an impurity content of no more than 1% by weight. In particular, aluminum with a maximum purity of 99.7% by weight may be used, with the following impurities (% by weight): Si≤0.30%; Fe≤0.18%; Sr≤0.0010%; Na≤0.0025%; Li≤0.0005%; Ca≤0.0020%; P≤0.0020; Sn≤0.020%.
Two opposite diffusive processes occur during the aluminization process: on the one hand, the migration of iron from the cast iron metal matrix to the aluminum bath, and on the other hand, the migration of aluminum from the aluminum bath to the cast iron metal matrix. The kinetics of dissolving iron in aluminum (and the subsequent migration of iron to the aluminum bath) is extremely rapid, with an order of magnitude comparable to that of the reaction for forming intermetallic compounds and in particular FeAl3 (Fe+3Al→FeAl3). Therefore, such two processes are both very rapid and occur at the same time.
It was found in some cases that, although the braking band had been subjected to decarburization and thus the graphite flakes had been eliminated from a surface layer at which the intermetallic compound layer would have been formed, the resulting intermetallic compound layer continued to include graphite flakes, as if they had never been eliminated. Such a phenomenon can be explained by the fact that the dissolution of iron in aluminum is so rapid that the decarburized layer is rapidly consumed and consequently metal compounds are formed in the layer below the decarburized layer, i.e., where graphite flakes are present.
In other words, the excessive solubility of iron in molten aluminum can cancel out, either in whole or in part, the beneficial effects of surface decarburization of the braking band.
Advantageously, step b) of immersion in a molten aluminum bath in which iron has been dissolved can be performed to slow down the dissolution of iron in the aluminum bath. In this manner, inhibiting the dissolution of iron in aluminum kinematically promotes the formation of FeAl3, so that intermetallic compounds can form at the decarburized layer.
Preferably, the content of iron in solution in the aluminum bath is no more than 5% by weight (solubility limit of iron in aluminum; iron-saturated aluminum) and even more preferably is comprised between 3% and 5%, and quite preferably equal to 4% by weight to ensure a significant effect of slowing down the process of dissolving iron of cast iron in aluminum.
For example, an aluminum bath with the following composition (% by weight) can be used: Al≤97%; Fe 3-5%; with the following impurities: Si≤0.30%; Fe≤0.18%; Sr≤Na 0.0025%; Li≤0.0005%; Ca≤0.0020%; P≤0.0020; Sn≤0.020%.
It has been experimentally observed that more porous intermetallic compound layers are obtained by performing the aluminization with an aluminum bath with iron in solution, especially if the iron content is close to the solubility limit. This can be explained by a higher viscosity of the molten aluminum bath containing iron and a consequent reduction in its wettability compared to cast iron.
Advantageously, as shown in the chart in
The immersion time of said braking band in said first bath is less than the immersion time of said braking band in said second bath.
Preferably, the immersion of said braking band in said first bath is prolonged a time which is for as short as possible but sufficient to obtain an initial layer consisting of iron-aluminum intermetallic compounds having a thickness not exceeding 10 μm on said predetermined surface region. In particular, the immersion time in said first bath is comprised between 3 and 5 minutes if the first bath is at a temperature of about 700° C. The immersion time must decrease as the bath temperature increases.
Operationally, it was observed that the initial intermetallic compound layer formed during the first sub-step b1) of immersion increases the wettability of the braking band by the second bath containing iron in solution. This allows to significantly reduce the porosity of the intermetallic compound layer which grows in the subsequent second sub-step b2) starting from the initial layer.
Advantageously, the immersion time of said braking band in said second bath is fixed as a function of the thickness to be obtained for said final intermetallic compound layer.
In more detail, the thickness increases as the immersion time increases, the temperature of the second bath being equal, and the thickness increases as the temperature of the second bath increases, the immersion time being equal.
Advantageously, both said first molten aluminum bath and said second bath have an impurity content of not more than 1% by weight. In particular, said two molten aluminum baths have a silicon content of less than 1% by weight.
Preferably, the content of iron in solution in the second aluminum bath is no more than 5% by weight (the solubility limit of iron in aluminum at 700° C. is equal to 4% by weight; iron-saturated aluminum) and even more preferably is comprised between 3% and 5%, and quite preferably 4% by weight. The iron content must not be less than 3% to ensure a significant effect of slowing down the process of dissolving the iron from cast iron into aluminum.
Advantageously, both said first bath and said second bath are maintained at a temperature below 680° C., preferably not more than 750° C., more preferably comprised between 690° C. and 710° C., and even more preferably 700° C.
Advantageously, the method may comprise a step of surface pre-treatment of the braking band which is carried out before said step b) of immersion at least at said predetermined surface region. Preferably said surface pretreatment step comprises lapping, degreasing, sandblasting and/or chemical removal of surface oxides.
Preferably, the method comprises a step of removing a surface layer of oxides from the molten aluminum bath before said step b) of immersion. Such a step of surface oxide removal is carried out both if the immersion is in a single bath and if immersion is in two successive steps in a first and second bath.
Advantageously, the aforesaid step (c) of extracting the braking band from the molten aluminum is carried out by controlling the extraction speed as a function of the bath viscosity, to adjust the amount of molten aluminum which remains adhered to the braking band.
If the braking band is immersed in a first bath (without iron, or present at most as an impurity) and then in a second bath with iron in solution, the extraction procedure from the first bath in solution is irrelevant because the excess aluminum will re-melt when immersed in the second bath.
According to a preferred embodiment of the invention, shown in particular in the diagram of
Preferably, the method comprises a step e) of quenching of said braking band carried out between said first sub-step d1) of removal and said second sub-step d2) of removal.
Advantageously, said first sub-step d1) of removal may be carried out by mechanical shaving of the still liquid aluminum.
Advantageously, said second sub-step d2) of removal can be carried out by chemical removal of solidified aluminum not mechanically removed.
Preferably, the aforesaid chemical removal is carried out by exposing the aluminum to ferric chloride for at least 4 minutes so as to cause the following reaction:
Al+FeCl3→AlCl3+Fe
The chemical removal by ferric chloride must necessarily occur after aluminum solidification. Ferric chloride boils at 315° C. and therefore cannot be brought into contact with molten aluminum. Preferably, said chemical removal is thus carried out after said step e) of quenching.
A braking band of a cast iron brake disc with increased resistance to wear and corrosion according to the invention will now be described.
In particular, such a braking band may be made according to the method of the invention, in particular as described above. Therefore, the making method will not be described again, and reference should be made to that described above for the sake of brevity.
According to a general embodiment of the invention, the disc braking band comprises a braking band body made of cast iron (gray cast iron or lamellar cast iron).
Said braking band body has at least one braking surface, comprising at at least one portion of said braking surface a protective surface layer.
According to the invention, such a protective surface layer is a surface layer comprising one or more intermetallic iron-aluminum compounds.
It has been experimentally found that the aforesaid intermetallic iron-aluminum compound layer exposed in the surface confers a higher corrosion and wear resistance to said cast iron braking band at said predetermined surface region compared to the case in which the cast iron braking band is free from the coating and the cast iron is directly exposed in the surface.
The aforesaid intermetallic iron-aluminum compound layer may comprise a plurality of intermetallic iron and aluminum compounds, in particular Fe3Al, FeAl, FeAl2, FeAl3, Fe2Al5. The predominant intermetallic phase is FeAl3 as it is thermodynamically more stable.
According to a preferred embodiment, the aforesaid protective surface layer substantially does not comprise carbon, in particular it does not comprise graphite flakes.
In particular, the aforesaid intermetallic iron-aluminum compound layer is a diffusive layer, interpenetrating with the cast iron microstructure.
As illustrated in
In
Preferably, said intermetallic iron-aluminum compound layer has an average thickness comprised between and 200 μm. The thickness is chosen as a function of the wear resistance properties that the braking band must guarantee during use.
Preferably, said braking surface has a hardness comprised between 400 and 1000HV at said layer of intermetallic iron-aluminum compounds. The hardness is variable as a function of the specific composition of the protective layer. Fe2Al5 has a hardness of 600-700 HV, while FeAl3 has a hardness of 900-1000 HV.
Some application examples of the method according to the invention carried out on samples consisting of gray cast iron discs are illustrated below. Similar results were obtained on samples of lamellar cast iron.
A gray cast iron sample, consisting of a 50 mm diameter, 6 mm thick disc, was initially subjected to an electrolytic decarburization process allowed removing the graphite flakes to a depth of at least 100 microns.
The sample was then pickled by immersing it in 37% vol hydrochloric acid for 30 seconds and then washed with demineralized water.
Immediately after pickling, the sample was immersed in succession in two different molten aluminum baths.
The first bath had the following composition: Al 99.7% by weight, containing the following impurities (% by weight): Si≤0.30%; Fe≤0.18%; Sr≤0.0010%; Na≤Li 0.0005%; Ca≤0.0020%; P≤0.0020; Sn≤0.020%.
The second bath had the same composition as the first bath with the addition of 4% by weight of 98.5% pure iron powder.
Both baths were maintained at a temperature of 700° C. The control of this temperature is ±10° C., and therefore no differences are appreciable between 690 and 710° C.
The immersion time in the first bath was 3 min, while the immersion time in the second bath was 30 min.
The extraction method from the first bath is irrelevant because even if a relatively thick layer of Al (1-2 mm) to remains adhered to the sample, it would re-melt in the second bath. In contrast, the extraction from the second bath was carried out rapidly, with times on the order of 1 second. The slower the extraction process, the greater the thickness of aluminum that remains adhered to the surface.
As soon as it was extracted from the second bath, with the aluminum still molten on the surface, the sample was shaved very quickly by passing a steel blade. The aluminum immediately solidified after just one pass of the blade. The thickness of the remaining aluminum was on the order of 0.1 to 0.3 mm.
Afterward, the sample was immersed in 40% wt. ferric chloride aqueous solution for 40 min. It was then washed with demineralized water. In this manner, the aluminum was removed almost completely from the surface.
At the end of the process described above, the sample had a layer of iron-aluminum intermetallic compounds having an average thickness of about 100 microns, with variation ±30 microns.
Under the electron microscope, the intermetallic compound layer appeared very compact and homogeneous.
The intermetallic layer had an average hardness value of not less than 400 HV.
The sample was tested in a climatic cell according to UNI EN ISO 6270-2 CH (condensation water).
The entire duration of the test was 120 h. The surface sample was corrosion-free for approximately 75% of the surface area. The sample had pronounced corrosion only in a central sector triggered after 1 hour. The scanning electron microscopic analysis showed that there were no signs of condensation water penetration down to the cast iron. Therefore, it can be concluded that the intermetallic compound layer preserved the iron in the cast iron from oxidation.
A gray cast iron sample, consisting of a 50 mm diameter, 6 mm thick disc, was subjected to the same process as described in example 1, except for the initial decarburization process, which was not carried out.
At the end of the process described above, the sample had a layer of iron-aluminum intermetallic compounds having an average thickness of about 100 microns, with variation ±30 microns.
Under the scanning electron microscope, the intermetallic compound layer appeared inhomogeneous as the one obtained in the sample of example 1. Indeed, the intermetallic layer alternated large, very homogeneous, and compact zones with some (less extensive) fractured and defective (porous) zones. It was hypothesized that probably, as the coating grew on undecarburized cast iron, the first aluminum bath would leave some graphite flakes exposed on the surface. The zones of the sample which have graphite flakes fail to be well wetted by the second bath and give rise to porosity in the coating.
The intermetallic layer had an average hardness value of not less than 400 HV.
This sample was also tested in a climatic cell according to UNI EN ISO 6270-2 CH (condensation water). The entire duration of the test was 120 h. After testing, the above porous zones were found to be subject to earlier corrosion than the rest of the layer. With the exception of these zones, the coating appeared well homogeneous and compact.
Despite the presence of zones subject to early corrosion on the coating, the scanning electron microscopic analysis showed that there were no signs of condensation water penetration down to the cast iron. Therefore, it can be concluded that despite the earlier localized corrosion phenomena in the porous zones, the intermetallic compound layer preserved the iron in the cast iron from oxidation.
A gray cast iron sample, consisting of a 50 mm diameter, 6 mm thick disc, was subjected to the same process as described in example 2. The only difference is the immersion time in the first bath: 30 seconds instead of 3 minutes. At the end of the process, the sample was subjected to the same tests as the samples in the previous examples.
Also in this case, the sample had an intermetallic iron-aluminum compound layer having an average thickness of about 100 microns, with variation ±30 microns.
Unlike the previous examples, the intermetallic compound layer appeared to have a two-layer structure under the scanning electron microscope. A first (innermost) layer had a lot of porosity and defects and a patchy conformation. Above this first layer was a second, more homogeneous, and compact layer, which, however, maintained a high degree of defects within it, induced by the structure of the first intermetallic layer. It has been hypothesized that this phenomenon, in addition to being related to the presence of graphite flakes on the surface (absence of surface decarburization), is due to the significantly shorter duration of immersion in the first bath.
The intermetallic layer had an average hardness value of not less than 400 HV.
Also this sample was tested in a climatic cell according to UNI EN ISO 6270-2 CH (condensation water). The entire duration of the test was 120 h. After testing, the porous zones were found to be subject to earlier corrosion than the rest of the layer.
Despite the presence of zones subject to early corrosion on the coating, the scanning electron microscopic analysis showed that there were no signs of condensation water penetration down to the cast iron. Therefore, it can be concluded that despite the earlier localized corrosion phenomena in the porous zones, the intermetallic compound layer preserved the iron in the cast iron from oxidation.
A gray cast iron sample, consisting of a 50 mm diameter, 6 mm thick disc, was subjected to the same process as described in example 1, with the following differences:
At the end of the process, the sample was subjected to the same tests as the samples in the previous examples.
Also in this case, at the end of the process described above, the sample had a layer of iron-aluminum intermetallic compounds having an average thickness of about 100 microns, with variation ±30 microns.
Under the electron microscope, the layer of intermetallic compounds appeared inhomogeneous. Indeed, the intermetallic layer alternated very homogeneous and compact zones with fractured zones with defects (pinholes). Also in this case, it was hypothesized that the surface porosity, in addition to being related to the presence of graphite flakes on the surface (absence of surface decarburization), is due to the lack of immersion in the second saturated iron bath.
The intermetallic layer had an average hardness value of not less than 400 HV.
Also this sample was tested in a climatic cell according to UNI EN ISO 6270-2 CH (condensation water). The entire duration of the test was 120 h. After testing, the porous zones were found to be subject to earlier corrosion than the rest of the layer. With the exception of these zones, the coating appeared well homogeneous and compact.
Despite the presence of zones subject to early corrosion on the coating, the scanning electron microscopic analysis showed that there were no signs of condensation water penetration down to the cast iron. Therefore, it can be concluded that despite the earlier localized corrosion phenomena in the porous zones, the intermetallic compound layer preserved the iron in the cast iron from oxidation.
A gray cast iron sample, consisting of a 50 mm diameter, 6 mm thick disc, was subjected to the same process as described in example 1, except that the superficially decarburized sample was immersed only in the first (substantially iron-free) bath for 30 minutes.
At the end of the process described above, the sample had a layer of iron-aluminum intermetallic compounds having an average thickness of about 100 microns, with variation ±30 microns.
Under the scanning electron microscope, the intermetallic compound layer appeared inhomogeneous as the one obtained in the sample of example 1. Indeed, the intermetallic layer alternated large, very homogeneous, and compact zones with some (less extensive) fractured and defective (porous) zones. It was hypothesized that probably, although the coating grew on decarburized cast iron, the aluminum bath (not being saturated with iron) dissolved iron from the decarburized surface causing the underlying graphite flakes to emerge and thus canceling out the effect of the decarburization. The zones of the sample which have the graphite flakes that emerged after decarburization, fail to be well wetted by the second bath and give rise to porosity in the coating.
The intermetallic layer had an average hardness value of not less than 400 HV.
Also this sample was tested in a climatic cell according to UNI EN ISO 6270-2 CH (condensation water). The entire duration of the test was 120 h. After testing, the above porous zones were found to be subject to earlier corrosion than the rest of the layer. With the exception of these zones, the coating appeared well homogeneous and compact.
Despite the presence of zones subject to early corrosion on the coating, the scanning electron microscopic analysis showed that there were no signs of condensation water penetration down to the cast iron. Therefore, it can be concluded that despite the earlier localized corrosion phenomena in the porous zones, the intermetallic compound layer preserved the iron in the cast iron from oxidation.
The invention allows obtaining several advantages which have been explained throughout the description.
In particular, the application examples illustrated above highlight how the method according to the invention allows making a braking band of a cast iron brake disc which is provided with a coating which imparts a higher resistance to wear and corrosion to the braking band.
Indeed, in all examples, the coating obtained, consisting of a layer of intermetallic iron/aluminum compounds, displays hardness values higher than bare cast iron, not less than 400 HV.
The coating obtained, although it has different homogeneity and porosity characteristics from example to example, was always able to protect the underlying cast iron from corrosion. This attests to the ability of the coating obtained by the method according to the invention to increase the corrosion resistance of the braking band of a brake disc.
The examples shown above highlight how the embodiments of the method according to the invention, which guarantee the best effects in terms of corrosion resistance, comprise decarburization of the surface to be coated and immersion in two different aluminum baths, the first of which is substantially free of iron or having iron in an amount classifiable as an impurity.
The method for making a braking band according to the invention can be carried out without requiring complex plants and with very little lead time. All of this results in a very limited increase in the cost and production time of a cast iron braking band.
Finally, the method according to the invention is feasible at processing temperatures compatible with the need to contain distortion on the braking band.
Therefore, the invention thus devised achieves the set objects.
Obviously, in the practice, it may also take shapes and configurations different from the one disclosed above, without for this reason departing from the present scope of protection.
Furthermore, all details may be replaced by technically equivalent elements, and any size, shape, and material may be used according to the needs.
| Number | Date | Country | Kind |
|---|---|---|---|
| 102020000025549 | Oct 2020 | IT | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/IB2021/059925 | 10/27/2021 | WO |
