CA2635470A1 - Copper-zinc alloy, production method and use - Google Patents
Copper-zinc alloy, production method and use Download PDFInfo
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- CA2635470A1 CA2635470A1 CA002635470A CA2635470A CA2635470A1 CA 2635470 A1 CA2635470 A1 CA 2635470A1 CA 002635470 A CA002635470 A CA 002635470A CA 2635470 A CA2635470 A CA 2635470A CA 2635470 A1 CA2635470 A1 CA 2635470A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/04—Alloys based on copper with zinc as the next major constituent
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
- F16C33/02—Parts of sliding-contact bearings
- F16C33/04—Brasses; Bushes; Linings
- F16C33/06—Sliding surface mainly made of metal
- F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
- F16C33/121—Use of special materials
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C2204/00—Metallic materials; Alloys
- F16C2204/10—Alloys based on copper
- F16C2204/14—Alloys based on copper with zinc as the next major constituent
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Abstract
The invention relates to a copper-zinc alloy, consisting of (in wt%): from 28.0 to 36.0% Zn, from 0.5 to 2.3% Si, from 1.5 to 2.5% Mn, from 0.2 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe, optionally also up to at most 0.1% Pb, optionally also up to at most 0.2% Sn, optionally also up to at most 0.1% P, optionally also up to 0.08% S, remainder Cu and inevitable impurities, with mixed silicides of iron-nickel-manganese incorporated in the matrix.
Description
Copper-zinc alloy, production method and use Description The invention relates to a copper-zinc alloy, to methods for producing tubes or rods from the copper-zinc alloy and to its use.
Owing to the greatly increasing stress on materials for friction bearings and the rising operating pressures and temperatures in modern machines, engines and equipment, the demands on the properties of the alloys suitable for use are increasing.
For this reason there is a need to further develop the operating properties of materials for bearings. This entails on the one hand increasing the strength properties, the heat resistance of the structure and the complex wear resistance while simultaneously having sufficient ductility properties. On the other hand, the friction bearing alloy must have a sufficient performance in the event of lubrication supply failure, which avoids seizure of the bearing partners. To date, copper alloys containing lead have been used for this purpose.
Documents DE 10 2004 058 318 B4 and DE 10 2005 015 467 Al disclose the application possibilities of a copper-zinc alloy for use as a valve guide and friction bearing with high thermal and wear stability. The alloy consists of 59 - 73 wt% copper, 2.7 - 8.5 wt% manganese,
Owing to the greatly increasing stress on materials for friction bearings and the rising operating pressures and temperatures in modern machines, engines and equipment, the demands on the properties of the alloys suitable for use are increasing.
For this reason there is a need to further develop the operating properties of materials for bearings. This entails on the one hand increasing the strength properties, the heat resistance of the structure and the complex wear resistance while simultaneously having sufficient ductility properties. On the other hand, the friction bearing alloy must have a sufficient performance in the event of lubrication supply failure, which avoids seizure of the bearing partners. To date, copper alloys containing lead have been used for this purpose.
Documents DE 10 2004 058 318 B4 and DE 10 2005 015 467 Al disclose the application possibilities of a copper-zinc alloy for use as a valve guide and friction bearing with high thermal and wear stability. The alloy consists of 59 - 73 wt% copper, 2.7 - 8.5 wt% manganese,
- 2 -1. 5- 6.3 wt% aluminum, 0.2 - 4 wt% silicon, 0.2 - 3 wt%
iron, 0 - 2 wt% lead, 0 - 2 wt% nickel, 0 - 0.4 wt% tin and the remainder zinc.
Increasing the thermal and wear stability for these alloys with an extremely high alloy content of manganese and aluminum generally entails a(3-matrix, in which a-precipitates and hard phases are incorporated.
Although the wear and heat resistance of these alloys may be regarded as sufficient, this unilateral orientation of the structural adjustment detrimentally affects the ductility properties of the material.
Furthermore, DE 29 19 478 C2 discloses the use of a similar alloy for synchronous rings. In respect of this use, it is regarded as advantageous that there is an improved wear-resistance and at the same time a significantly increased coefficient of friction. The semifinished products made from the alloy furthermore have good processability; they can readily be cold-formed owing to the relatively high aluminum content, although an increase in hardness at room temperature is to be noted compared with the previously conventional special brasses.
The aluminum content lies in the range of from 4 to 6 wt%.
The further document OS 21 45 710 discloses a copper-based alloy which is wear-resistant at high temperature for a valve seat in combustion engines, which likewise has a comparatively high aluminum content of from 5 to 12 wt%. The aluminum content in the specified range improves the corrosion resistance in addition to the
iron, 0 - 2 wt% lead, 0 - 2 wt% nickel, 0 - 0.4 wt% tin and the remainder zinc.
Increasing the thermal and wear stability for these alloys with an extremely high alloy content of manganese and aluminum generally entails a(3-matrix, in which a-precipitates and hard phases are incorporated.
Although the wear and heat resistance of these alloys may be regarded as sufficient, this unilateral orientation of the structural adjustment detrimentally affects the ductility properties of the material.
Furthermore, DE 29 19 478 C2 discloses the use of a similar alloy for synchronous rings. In respect of this use, it is regarded as advantageous that there is an improved wear-resistance and at the same time a significantly increased coefficient of friction. The semifinished products made from the alloy furthermore have good processability; they can readily be cold-formed owing to the relatively high aluminum content, although an increase in hardness at room temperature is to be noted compared with the previously conventional special brasses.
The aluminum content lies in the range of from 4 to 6 wt%.
The further document OS 21 45 710 discloses a copper-based alloy which is wear-resistant at high temperature for a valve seat in combustion engines, which likewise has a comparatively high aluminum content of from 5 to 12 wt%. The aluminum content in the specified range improves the corrosion resistance in addition to the
- 3 -effect of reinforcing the matrix. A further increase in the wear resistance occurs through the formation of an intermetallic phase of manganese and silicon.
The patent application published for opposition 1 194 592 discloses a method for producing synchronous rings, which are distinguished by a high and constant coefficient of friction, a high wear resistance and good machining processability. To this end annealing treatments of the alloy, consisting substantially of R-phase at between 200 and 500 C, are proposed in order to achieve from 5 to 50% a-precipitation.
A certain lead content is usually provided in said documents for better machining processability.
It is an object of the invention to provide a copper-zinc alloy having improved cold formability, higher hardness and heat resistance.
The invention is defined in respect of the alloy by the features of Claim 1 and in respect of the method for producing tubes or rods made of the alloy by the features of Claims 8 and 9, and in respect of the use of the alloy by Claim 11. The other dependent claims define advantageous embodiments and refinements of the invention.
The invention includes the technical teaching that a copper-zinc alloy consists of (in wto):
from 28.0 to 36.0% Zn, from 0.5 to 2.3% Si, from 1.5 to 2.5% Mn, from 0.2 to 3.0% Ni,
The patent application published for opposition 1 194 592 discloses a method for producing synchronous rings, which are distinguished by a high and constant coefficient of friction, a high wear resistance and good machining processability. To this end annealing treatments of the alloy, consisting substantially of R-phase at between 200 and 500 C, are proposed in order to achieve from 5 to 50% a-precipitation.
A certain lead content is usually provided in said documents for better machining processability.
It is an object of the invention to provide a copper-zinc alloy having improved cold formability, higher hardness and heat resistance.
The invention is defined in respect of the alloy by the features of Claim 1 and in respect of the method for producing tubes or rods made of the alloy by the features of Claims 8 and 9, and in respect of the use of the alloy by Claim 11. The other dependent claims define advantageous embodiments and refinements of the invention.
The invention includes the technical teaching that a copper-zinc alloy consists of (in wto):
from 28.0 to 36.0% Zn, from 0.5 to 2.3% Si, from 1.5 to 2.5% Mn, from 0.2 to 3.0% Ni,
- 4 -from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe, optionally also up to at most 0.1% Pb, optionally also up to at most 0.2% Sn, optionally also up to at most 0.1% P, optionally also up to 0.08% S, remainder Cu and inevitable impurities, with mixed silicides of iron-nickel-manganese incorporated in the matrix.
The invention is based on the idea of providing a copper-zinc alloy which has incorporated mixed silicides of iron-nickel-manganese and can be produced with the aid of the continuous or semicontinuous extrusion casting method. Owing to the mixed silicide formation, the copper-zinc alloy has a high hard phase content which contributes to improving the material resistance against abrasive wear. Owing to their low susceptibility to seizure, the high content of silicides furthermore entails a better resistance against adhesive wear.
The alloy thus has high hardness and strength values but a requisite degree of ductility is nevertheless ensured, as expressed by an elongation at break value in a tensile test. With this combination of properties, the subject of the invention is particularly suitable for Pb-free friction bearing elements in engines, for example piston bore liners, and in transmissions.
When casting the alloy, early precipitation of iron- and nickel-rich mixed silicides initially takes
The invention is based on the idea of providing a copper-zinc alloy which has incorporated mixed silicides of iron-nickel-manganese and can be produced with the aid of the continuous or semicontinuous extrusion casting method. Owing to the mixed silicide formation, the copper-zinc alloy has a high hard phase content which contributes to improving the material resistance against abrasive wear. Owing to their low susceptibility to seizure, the high content of silicides furthermore entails a better resistance against adhesive wear.
The alloy thus has high hardness and strength values but a requisite degree of ductility is nevertheless ensured, as expressed by an elongation at break value in a tensile test. With this combination of properties, the subject of the invention is particularly suitable for Pb-free friction bearing elements in engines, for example piston bore liners, and in transmissions.
When casting the alloy, early precipitation of iron- and nickel-rich mixed silicides initially takes
- 5 -place. During further growth, these precipitates can develop to form mixed silicides of iron-nickel-manganese with a considerable size, often with a columnar shape.
Furthermore, a considerable proportion also remains rather small with a globular configuration, which is finely distributed in the matrix. In particular, the finely distributed silicides are regarded as the reason why stabilization of the R-phase takes place. This makes an important contribution to increasing the heat resistance and complex wear resistance.
The particular advantage of the alloy according to the invention is due to a combination of properties, optimized for an application purpose, in the form of increasing the strength, the heat resistance of the structure and the complex wear resistance while simultaneously having sufficient ductility properties.
Furthermore, the alloy has good performance in the event of lubrication supply failure for friction bearing applications, which avoids seizure of the bearing partners. Owing to the substituted lead content compared with conventional alloys, the claimed material solution also accommodates the need for an environmentally friendly lead-free alloy alternative.
This material is furthermore intended for particular applications in which a requisite degree of plasticizability is important, despite stringent requirements for the hardness and strength. This is the case for example in the field of hydraulic equipment, the
Furthermore, a considerable proportion also remains rather small with a globular configuration, which is finely distributed in the matrix. In particular, the finely distributed silicides are regarded as the reason why stabilization of the R-phase takes place. This makes an important contribution to increasing the heat resistance and complex wear resistance.
The particular advantage of the alloy according to the invention is due to a combination of properties, optimized for an application purpose, in the form of increasing the strength, the heat resistance of the structure and the complex wear resistance while simultaneously having sufficient ductility properties.
Furthermore, the alloy has good performance in the event of lubrication supply failure for friction bearing applications, which avoids seizure of the bearing partners. Owing to the substituted lead content compared with conventional alloys, the claimed material solution also accommodates the need for an environmentally friendly lead-free alloy alternative.
This material is furthermore intended for particular applications in which a requisite degree of plasticizability is important, despite stringent requirements for the hardness and strength. This is the case for example in the field of hydraulic equipment, the
- 6 -sliding pad of which is partly produced by pressing together the respective connection partners. Particularly in this field of hydraulic mechanical engineering, for example for axial piston machines, future developments are likely to entail increasing operating pressures which place greater demands on the strength properties of the materials being used.
In a preferred configuration, the alloy according to the invention may contain from 28.0 to 36.0% Zn, from 0.5 to 1.5% Si, from 1.5 to 2.5% Mn, from 0.2 to 1.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
Owing to the somewhat reduced elementary contents of silicon and nickel, the iron-nickel-manganese mixed silicide formation can be specially oriented toward an optimized combination of properties, particularly in relation to the requisite degree of ductility.
In another preferred configuration, the alloy according to the invention may contain from 28.0 to 36.0% Zn, from 1.0 to 2.3% Si, from 1.5 to 2.5% Mn, from 1.5 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
In a preferred configuration, the alloy according to the invention may contain from 28.0 to 36.0% Zn, from 0.5 to 1.5% Si, from 1.5 to 2.5% Mn, from 0.2 to 1.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
Owing to the somewhat reduced elementary contents of silicon and nickel, the iron-nickel-manganese mixed silicide formation can be specially oriented toward an optimized combination of properties, particularly in relation to the requisite degree of ductility.
In another preferred configuration, the alloy according to the invention may contain from 28.0 to 36.0% Zn, from 1.0 to 2.3% Si, from 1.5 to 2.5% Mn, from 1.5 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
- 7 -The ratio Mn/Ni of the elementary contents of the elements manganese and nickel may preferably lie between 0.7 and 1.3. With a higher silicon content, particularly in conjunction with the preferred Mn/Ni ratio, this material has good plasticizability. This is important particularly for friction bearing elements which need to receive their bearing partners by producing a press-fit connection just before operation.
Advantageously, the structure comprises a R-phase content of up to 50 vol.% in the cast state. This is regarded as a necessary prerequisite for sufficiently good hot formability of the copper alloy by extrusion.
In a preferred configuration of the invention, after post-processing which involves at least hot forming or cold forming and further annealing steps, the structure comprises a R-phase content of up to 45 vol.%, the mixed silicides of Fe-Ni-Mn up to 20 vol.% and a remainder of a-phase.
With these R-inclusions and hard phases of different size distribution in an a-matrix, this alloy ensures advantageous heat resistance of the structure with sufficient ductility properties as well as a suitable complex wear resistance of the components. In particular, owing to the low cold seizure susceptibility of silicides, the high silicide content contributes to improving the frictional and lubricant-failure properties in bearing elements, so that the omission of the Pb content can be compensated for. The demand for improved environmental
Advantageously, the structure comprises a R-phase content of up to 50 vol.% in the cast state. This is regarded as a necessary prerequisite for sufficiently good hot formability of the copper alloy by extrusion.
In a preferred configuration of the invention, after post-processing which involves at least hot forming or cold forming and further annealing steps, the structure comprises a R-phase content of up to 45 vol.%, the mixed silicides of Fe-Ni-Mn up to 20 vol.% and a remainder of a-phase.
With these R-inclusions and hard phases of different size distribution in an a-matrix, this alloy ensures advantageous heat resistance of the structure with sufficient ductility properties as well as a suitable complex wear resistance of the components. In particular, owing to the low cold seizure susceptibility of silicides, the high silicide content contributes to improving the frictional and lubricant-failure properties in bearing elements, so that the omission of the Pb content can be compensated for. The demand for improved environmental
- 8 -compatibility of these machine and system components has therefore likewise been accommodated.
The ratio Rpp,z/Rm of the values for the yield point and tensile strength of the alloy may advantageously lie between 0.5 and 0.95.
In the field of another application, i.e.
hydraulic machine and system technology, future developments are likely to entail increasing stress on the friction bearings due to increasing operating pressures.
Besides a strength increase, this configuration ensures the required ratio Rpp,z/Rm in the range of between 0.5 and 0.95. This is an important prerequisite for the production of a bearing seat by press-fit connection of the friction bearing partners.
Another aspect of the invention relates to a method for producing tubes or rods made of the copper-zinc alloy according the invention, wherein a post-processing of the alloy comprises the following steps:
- extrusion in a temperature range of from 600 to 800 C, - at least one cold forming.
These tubes and rods may be used as starting material for the machining manufacture of friction bearing elements.
Another alternative aspect of the invention relates to a method for producing tubes or rods made of the copper-zinc alloy according the invention, wherein a
The ratio Rpp,z/Rm of the values for the yield point and tensile strength of the alloy may advantageously lie between 0.5 and 0.95.
In the field of another application, i.e.
hydraulic machine and system technology, future developments are likely to entail increasing stress on the friction bearings due to increasing operating pressures.
Besides a strength increase, this configuration ensures the required ratio Rpp,z/Rm in the range of between 0.5 and 0.95. This is an important prerequisite for the production of a bearing seat by press-fit connection of the friction bearing partners.
Another aspect of the invention relates to a method for producing tubes or rods made of the copper-zinc alloy according the invention, wherein a post-processing of the alloy comprises the following steps:
- extrusion in a temperature range of from 600 to 800 C, - at least one cold forming.
These tubes and rods may be used as starting material for the machining manufacture of friction bearing elements.
Another alternative aspect of the invention relates to a method for producing tubes or rods made of the copper-zinc alloy according the invention, wherein a
- 9 -post-processing of the alloy comprises the following steps:
- extrusion in a temperature range of from 600 to 800 C, - a combination of at least one cold forming with at least one anneal in a temperature range of from 250 to 700 C.
By means of a combination of cold forming by drawing and one or more intermediate anneals of the rods and tubes in the temperature range of from 250 to 700 C, it is possible to set up a fine distribution of the heterogeneous structure.
The demand for improving the complex operating properties of the bearing materials will thereby have been satisfied, since modern machines, engines, transmissions and equipment entail greatly increasing stress on the friction bearing elements. A significant increase in the tensile strength Rm, yield point Rpo.2 and hardness of the material are achieved with this particular configuration of the copper-zinc alloy. The elongation at break of the alloy likewise moves to a sufficiently high level, so that the required ductility properties are achieved. The extraordinarily high content of hard phases, in particular the mixed silicides of iron-nickel-manganese and the heterogeneous matrix structure of a- and R-phases, ensures a suitable complex wear resistance of the components made of this material.
- extrusion in a temperature range of from 600 to 800 C, - a combination of at least one cold forming with at least one anneal in a temperature range of from 250 to 700 C.
By means of a combination of cold forming by drawing and one or more intermediate anneals of the rods and tubes in the temperature range of from 250 to 700 C, it is possible to set up a fine distribution of the heterogeneous structure.
The demand for improving the complex operating properties of the bearing materials will thereby have been satisfied, since modern machines, engines, transmissions and equipment entail greatly increasing stress on the friction bearing elements. A significant increase in the tensile strength Rm, yield point Rpo.2 and hardness of the material are achieved with this particular configuration of the copper-zinc alloy. The elongation at break of the alloy likewise moves to a sufficiently high level, so that the required ductility properties are achieved. The extraordinarily high content of hard phases, in particular the mixed silicides of iron-nickel-manganese and the heterogeneous matrix structure of a- and R-phases, ensures a suitable complex wear resistance of the components made of this material.
- 10 -The relationship between the level and distribution of the (3-phase content and the heat resistance of the structure is already known. Yet since this body-centered cubic crystal type fulfills an indispensable strength-increasing function in the copper-zinc alloys, minimizing the P-content should not exclusively be paramount. By means of the manufacturing sequence of extrusion/drawings/intermediate anneals, the structure of the copper-zinc alloy can be modified in its phase distribution so that it also has a sufficient heat resistance besides a high strength.
In a preferred configuration, the forming may be followed by a stress-relieving anneal in a temperature range of from 250 to 450 C.
In the manufacturing procedure, it is necessary to reduce the level of residual stresses with the aid of one or more stress-relieving anneals. Reducing the residual stresses is also important for guaranteeing a sufficient heat resistance of the structure, and for ensuring sufficient straightness of the rods and tubes.
Furthermore, as already mentioned above, the copper-zinc alloy according to the invention may be used for friction bearing elements in combustion engines, transmissions or hydraulic equipment.
Further exemplary embodiments of the invention will be explained in more detail with the aid of the table. Cast bolts made of the copper-zinc alloy according
In a preferred configuration, the forming may be followed by a stress-relieving anneal in a temperature range of from 250 to 450 C.
In the manufacturing procedure, it is necessary to reduce the level of residual stresses with the aid of one or more stress-relieving anneals. Reducing the residual stresses is also important for guaranteeing a sufficient heat resistance of the structure, and for ensuring sufficient straightness of the rods and tubes.
Furthermore, as already mentioned above, the copper-zinc alloy according to the invention may be used for friction bearing elements in combustion engines, transmissions or hydraulic equipment.
Further exemplary embodiments of the invention will be explained in more detail with the aid of the table. Cast bolts made of the copper-zinc alloy according
- 11 -to the invention were produced by ingot casting. The chemical composition of the castings is shown in Tab. 1.
Table 1.: Chemical composition of the cast bolts (embodiment A) No. Cu Zn Si Mn Ni Sn Al Fe 1-0-1 L%] L%] L%] L%] L%] L0-61 L%]
Alloy type 64.1 31.2 1.20 1.76 0.40 <0.01 0.92 0.30 Alloy type 63.6 31.7 1.17 1.75 0.55 <0.01 0.87 0.33 Alloy type 59.3 33.4 1.7 2.0 2.3 <0.01 0.9 0.5 Manufacturing sequence for alloy types 1 and 2:
= extrusion to form tubes at a temperature of = combination of cold forming/intermediate anneals (650 C/50-60 min)/rectifying/stress-relieving anneals (300-350 C/3 h) At the end of manufacturing, the mechanical properties of the tubes are at the level which is represented as numerical values in Tab. 2.
Table 2: Mechanical properties of the tubes (alloy type 1 and alloy type 2) No. (3-content Grain R. RPO.Z RPO.z/ A5 HB
[o] size [MPa] [MPa] Rm [$]
[um]
Alloy 5 5-10 715 656 0.92 12.0 222 type
Table 1.: Chemical composition of the cast bolts (embodiment A) No. Cu Zn Si Mn Ni Sn Al Fe 1-0-1 L%] L%] L%] L%] L%] L0-61 L%]
Alloy type 64.1 31.2 1.20 1.76 0.40 <0.01 0.92 0.30 Alloy type 63.6 31.7 1.17 1.75 0.55 <0.01 0.87 0.33 Alloy type 59.3 33.4 1.7 2.0 2.3 <0.01 0.9 0.5 Manufacturing sequence for alloy types 1 and 2:
= extrusion to form tubes at a temperature of = combination of cold forming/intermediate anneals (650 C/50-60 min)/rectifying/stress-relieving anneals (300-350 C/3 h) At the end of manufacturing, the mechanical properties of the tubes are at the level which is represented as numerical values in Tab. 2.
Table 2: Mechanical properties of the tubes (alloy type 1 and alloy type 2) No. (3-content Grain R. RPO.Z RPO.z/ A5 HB
[o] size [MPa] [MPa] Rm [$]
[um]
Alloy 5 5-10 715 656 0.92 12.0 222 type
- 12 -Alloy 5-10 10-15 660 577 0.87 13.2 207 type Manufacturing sequence:
= Hot rolling at a temperature of 750 C on the laboratory scale = Combination of cold forming/intermediate anneals (300-400 C/2-3 h) At the end of manufacturing, the mechanical properties of the tubes are at the level which is represented as numerical values in Tab. 3.
Table 3: Mechanical properties (alloy type 3) No. (3- Grain Rm Rpo.2 Rp0,2/ A5 HB
Alloy type content size [MPa [MPa Rm [o]
3 [%] [um] ] ]
Treatment 1 30-40 10 674 399 0.59 7.3 222 (300 C/2 h) Treatment 2 30-40 10 621 424 0.68 13.1 206 (400 C/2 h)
= Hot rolling at a temperature of 750 C on the laboratory scale = Combination of cold forming/intermediate anneals (300-400 C/2-3 h) At the end of manufacturing, the mechanical properties of the tubes are at the level which is represented as numerical values in Tab. 3.
Table 3: Mechanical properties (alloy type 3) No. (3- Grain Rm Rpo.2 Rp0,2/ A5 HB
Alloy type content size [MPa [MPa Rm [o]
3 [%] [um] ] ]
Treatment 1 30-40 10 674 399 0.59 7.3 222 (300 C/2 h) Treatment 2 30-40 10 621 424 0.68 13.1 206 (400 C/2 h)
Claims (11)
1. Copper-zinc alloy, consisting of (in wt%):
from 28.0 to 36.0% Zn, from 0.5 to 2.3% Si, from 1.5 to 2.5% Mn, from 0.2 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe, optionally also up to at most 0.1% Pb, optionally also up to at most 0.2% Sn, optionally also up to at most 0.1% P, optionally also up to 0.08% S, remainder Cu and inevitable impurities, with mixed silicides of iron-nickel-manganese incorporated in the matrix.
from 28.0 to 36.0% Zn, from 0.5 to 2.3% Si, from 1.5 to 2.5% Mn, from 0.2 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe, optionally also up to at most 0.1% Pb, optionally also up to at most 0.2% Sn, optionally also up to at most 0.1% P, optionally also up to 0.08% S, remainder Cu and inevitable impurities, with mixed silicides of iron-nickel-manganese incorporated in the matrix.
2. Copper-zinc alloy according to Claim 1, characterized by:
from 28.0 to 36.0% Zn, from 0.5 to 1.5% Si, from 1.5 to 2.5% Mn, from 0.2 to 1.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
from 28.0 to 36.0% Zn, from 0.5 to 1.5% Si, from 1.5 to 2.5% Mn, from 0.2 to 1.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
3. Copper-zinc alloy according to Claim 1, characterized by:
from 28.0 to 36.0% Zn, from 1.0 to 2.3% Si, from 1.5 to 2.5% Mn, from 1.5 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
from 28.0 to 36.0% Zn, from 1.0 to 2.3% Si, from 1.5 to 2.5% Mn, from 1.5 to 3.0% Ni, from 0.5 to 1.5% Al, from 0.1 to 1.0% Fe.
4. Copper-zinc alloy according to Claim 3, characterized in that the ratio Mn/Ni of the elementary contents of the elements manganese and nickel lies between 0.7 and 1.3.
5. Copper-zinc alloy according to one of Claims 1 to 4, characterized in that in the cast state, the structure comprises a .beta.-phase content of up to 50 vol.%.
6. Copper-zinc alloy according to one of Claims 1 to 4, characterized in that after post-processing which involves at least hot forming or cold forming and further annealing steps, the structure comprises a .beta.-phase content of up to 45 vol.%, the mixed silicides of Fe-Ni-Mn up to 20 vol.% and a remainder of .alpha.-phase.
7. Copper-zinc alloy according to Claim 6, characterized in that the ratio R p0.2/R m of the values for the yield point and tensile strength of the alloy lies between 0.5 and 0.95.
8. Method for producing tubes or rods made of a copper-zinc alloy according to one of Claims 1 to 7, characterized in that a post-processing of the alloy comprises the following steps:
- extrusion in a temperature range of from 600 to 800°C, - at least one cold forming.
- extrusion in a temperature range of from 600 to 800°C, - at least one cold forming.
9. Method for producing tubes or rods made of a copper-zinc alloy according to one of Claims 1 to 7, characterized in that a post-processing of the alloy comprises the following steps:
- extrusion in a temperature range of from 600 to 800°C, - a combination of at least one cold forming with at least one anneal in a temperature range of from 250 to 700°C.
- extrusion in a temperature range of from 600 to 800°C, - a combination of at least one cold forming with at least one anneal in a temperature range of from 250 to 700°C.
10. Method for producing tubes or rods made of a copper-zinc alloy according to Claim 8 or 9, characterized in that the forming is followed by a stress-relieving anneal in a temperature range of from 250 to 450°C.
11. Use of a copper-zinc alloy according to one of Claims 1 to 7 for friction bearing elements in combustion engines, transmissions or hydraulic equipment.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102007029991A DE102007029991B4 (en) | 2007-06-28 | 2007-06-28 | Copper-zinc alloy, method of manufacture and use |
| DE102007029991.7-24 | 2007-06-28 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2635470A1 true CA2635470A1 (en) | 2008-12-28 |
| CA2635470C CA2635470C (en) | 2017-03-28 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2635470A Active CA2635470C (en) | 2007-06-28 | 2008-06-20 | Copper-zinc alloy, production method and use |
Country Status (5)
| Country | Link |
|---|---|
| EP (2) | EP2806044B1 (en) |
| JP (1) | JP5684448B2 (en) |
| CA (1) | CA2635470C (en) |
| ES (2) | ES2527296T3 (en) |
| PL (2) | PL2806044T3 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2017156721A1 (en) * | 2016-03-16 | 2017-09-21 | 湖南特力新材料有限公司 | Ultra-high strength and self-lubricating copper alloy and preparation method therefor |
| CN115927888A (en) * | 2022-10-14 | 2023-04-07 | 安阳工学院 | Method for improving silicon brass hardness through electric pulse treatment |
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| JP5253440B2 (en) * | 2010-03-01 | 2013-07-31 | 大同メタル工業株式会社 | Sliding bearings for turbochargers for internal combustion engines |
| JP5312510B2 (en) | 2011-03-31 | 2013-10-09 | 大同メタル工業株式会社 | Thrust bearings for turbochargers for internal combustion engines |
| KR101485746B1 (en) | 2011-11-04 | 2015-01-22 | 미쓰비시 신도 가부시키가이샤 | Hot-forged copper alloy article |
| JP6023557B2 (en) * | 2012-11-09 | 2016-11-09 | 大豊工業株式会社 | Copper alloy |
| DE102013008822A1 (en) * | 2013-05-24 | 2014-11-27 | Wieland-Werke Ag | Mine for pens and use |
| KR101820036B1 (en) | 2014-02-04 | 2018-01-18 | 오토 푹스 카게 | Lubricant-compatible copper alloy |
| DE102014106933A1 (en) | 2014-05-16 | 2015-11-19 | Otto Fuchs Kg | Special brass alloy and alloy product |
| DE102014014239B4 (en) * | 2014-09-25 | 2024-04-11 | Wieland-Werke Ag | Electrical connecting element |
| DE102015003687A1 (en) * | 2015-03-24 | 2016-09-29 | Diehl Metall Stiftung & Co. Kg | Copper-zinc alloy and its use |
| DE202016102696U1 (en) | 2016-05-20 | 2017-08-29 | Otto Fuchs - Kommanditgesellschaft - | Special brass alloy as well as special brass alloy product |
| DE202016102693U1 (en) | 2016-05-20 | 2017-08-29 | Otto Fuchs - Kommanditgesellschaft - | Special brass alloy as well as special brass alloy product |
| DE202020101700U1 (en) * | 2020-03-30 | 2021-07-01 | Otto Fuchs - Kommanditgesellschaft - | Pb-free Cu-Zn alloy |
| KR102666985B1 (en) * | 2020-12-29 | 2024-05-21 | 주식회사 대창 | Low silicon copper alloy with improved machinability |
| CN113755715A (en) * | 2021-09-07 | 2021-12-07 | 大连理工大学 | High-performance copper alloy and preparation method thereof |
| DE102022122831A1 (en) | 2022-09-08 | 2024-03-14 | Diehl Brass Solutions Stiftung & Co. Kg | Lead-free brass alloy and machine element made therefrom |
| DE102022122830A1 (en) | 2022-09-08 | 2024-03-14 | Diehl Brass Solutions Stiftung & Co. Kg | Lead-free brass alloy and bearing component made therefrom |
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-
2008
- 2008-06-14 PL PL14002857T patent/PL2806044T3/en unknown
- 2008-06-14 ES ES08010860.8T patent/ES2527296T3/en active Active
- 2008-06-14 PL PL08010860T patent/PL2009122T3/en unknown
- 2008-06-14 EP EP14002857.2A patent/EP2806044B1/en active Active
- 2008-06-14 EP EP08010860.8A patent/EP2009122B1/en active Active
- 2008-06-14 ES ES14002857.2T patent/ES2645466T3/en active Active
- 2008-06-20 CA CA2635470A patent/CA2635470C/en active Active
- 2008-06-24 JP JP2008164098A patent/JP5684448B2/en active Active
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2017156721A1 (en) * | 2016-03-16 | 2017-09-21 | 湖南特力新材料有限公司 | Ultra-high strength and self-lubricating copper alloy and preparation method therefor |
| CN115927888A (en) * | 2022-10-14 | 2023-04-07 | 安阳工学院 | Method for improving silicon brass hardness through electric pulse treatment |
Also Published As
| Publication number | Publication date |
|---|---|
| ES2645466T3 (en) | 2017-12-05 |
| CA2635470C (en) | 2017-03-28 |
| EP2009122A1 (en) | 2008-12-31 |
| PL2806044T3 (en) | 2018-03-30 |
| JP2009007673A (en) | 2009-01-15 |
| EP2009122B1 (en) | 2014-10-08 |
| JP5684448B2 (en) | 2015-03-11 |
| EP2806044A3 (en) | 2015-02-18 |
| EP2806044B1 (en) | 2017-09-13 |
| ES2527296T3 (en) | 2015-01-22 |
| EP2806044A2 (en) | 2014-11-26 |
| PL2009122T3 (en) | 2015-03-31 |
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