Pb-free Cu-Zn alloy

Abstract

The present invention relates to a Pb-free Cu-Zn alloy for producing alloy products to be used under lubricating conditions, the Pb-free Cu-Zn alloy having the following composition (data in wt%): Cu: 57-59%, Mn: 1.7-2.7%, Al: 1.3-2.2%, Si: 0.4-1.0%, Ni: 0.4-0.85%, Fe: 0.3-0.7%, Sn: 0.15-0.4%, the balance being Zn together with unavoidable impurities.

Description

[Technical Field]

[0001] The present invention relates to a Pb-free Cu-Zn alloy for producing alloy products, particularly for use under lubricating conditions. [Background technology]

[0002] The special brass CuZn37Mn3Al2PbSi (CW713R), listed in the German Copper Institute's material data sheet (Status 2005), has been widely used for many years and is characterized by high wear resistance and good hot workability. This material has high strength values, average machinability, and good corrosion resistance. For this reason, this alloy is used for structural components in mechanical engineering, synchronizer rings and valve guide tubes in automotive construction, as well as various plain bearing elements and hot-pressed parts. This means that alloy products made from this alloy are used under lubricated conditions. Possible applications include permanent oil immersion or lubricant supply via a system of channels and grooves designed for this purpose. Synchronizer rings are found in oil environments. This alloy can also be applied to plain bearing elements, which can only be lubricated with oil. This alloy is also used to manufacture components used in hydraulic systems, such as distributor plates. This previously known alloy has the following composition (data in % by weight): Cu: 57.0-59.0%, Mn: 1.5-3.0%, Al: 1.3-2.3%, Si: 0.3-1.3%, and the balance is zinc with unavoidable impurities. Admixtures (data in % by weight) are permitted: Ni: max. 1.0%, Fe: max. 1.0%, Sn: max. 0.4%, Pb: 0.2-0.8%.

[0003] As can be seen from the material description above, this previously known alloy contains Pb, an element responsible for machinability and which, by being incorporated into the tribological layer, influences the running-in behavior as well as friction and wear in sliding applications.

[0004] The special brass alloy CW713R is characterized by versatile application properties, such as high wear and cavitation resistance, compatibility with lubricants, and satisfactory mechanical properties, especially with regard to strength and ductility of the alloy product. These properties also include good machinability. The element Pb is introduced into the brass alloy to obtain the desired machinability.

[0005] For health and environmental reasons, recent efforts have been made to design lead-free brass alloys, where possible, without taking advantage of the properties of the Pb element.

[0006] DE 102005017574 A1 describes a wear-resistant brass alloy for synchronizer rings with any lead content: (data in % by weight) 57.5-59% copper, 2-3.5% manganese, 1-3% aluminum, 0.9-1.5% silicon, 0.15-0.4% iron, 0-1% lead, 0-1% nickel, 0-0.5% tin, and the remainder zinc.

[0007] WO 2014 / 152619 discloses a brass alloy for turbochargers having the following composition, optionally containing lead (data in % by weight): 57-60% copper, 1.5-3.0% manganese, 1.3-2.3% aluminum, 0.5-2.0% silicon, 0-1% nickel, 0-1% iron, 0-0.4% tin, 0-0.1% lead, and the balance being zinc.

[0008] For sliding applications, JP 56-127741 A discloses a brass alloy having the following composition (data in % by weight): 54-66% copper, 1.0-5.0% manganese, 1.0-5.0% aluminum, 0.2-1.5% silicon, 0.5-4.0% nickel, 0.1-2.0% iron, 0.2-2.0% tin, and the balance being zinc. Summary of the Invention

[0009] Based on the above-mentioned prior art, the present invention is based on the object of proposing a Pb-free Cu-Zn alloy that is essentially suitable for the applications or uses for which the CuZn37Mn3Al2PbSi alloy mentioned above in the prior art was also suitable. Compared to this previously known special brass alloy, it is desirable that the mechanical strength properties be further improved without adversely affecting the cold and hot workability and machinability.

[0010] This objective is achieved by a Pb-free Cu-Zn alloy having the following composition (data in % by weight): Cu: 57-59%, Mn: 1.7-2.7% Al: 1.3-2.2%, Si: 0.4 to 1.0%, Ni: 0.4 to 0.85% Fe: 0.3-0.7% Sn: 0.15~0.4% The remainder is Zn along with unavoidable impurities.

[0011] Incidental impurities in the alloy are permitted at 0.05% by weight per element, with the total amount of incidental impurities not exceeding 0.15% by weight.

[0012] This alloy is characterized, inter alia, by the selection of the alloying elements Ni, Fe, and Sn, and by the content (as claimed) of these elements in the alloy composition relative to other alloying elements, particularly Mn, Al, and Si. This balanced alloy composition results in alloy products with particularly good properties in terms of cold and hot workability, machinability, strength, and wear resistance, the latter being particularly good under lubricated conditions. This result is surprising, since other special brass alloys utilize Bi instead of Pb, whereas the alloy of the present invention does not. While the previously known alloy CuZn37Mn3Al2PbSi also has good hot workability, the claimed alloy not only exhibits particularly good hot workability, but also good cold workability, the latter of which is not present in previously known alloys. Interestingly, this alloy is suitable for the production of forged products. If the forged product is then subjected to a stress-relief anneal (performed at temperatures between 300°C and 450°C), this procedure increases the embedded α-mixed crystal content to 10-15%. Annealing at temperatures in the 350-380°C range is often sufficient to achieve the desired properties. This increase in α-mixed crystal content is the reason for the improved cold formability. Without this annealing step, the alloy microstructure would have an α-mixed crystal content of less than 3-5%. Similar benefits of stress-relief annealing are seen in extruded products, where the aforementioned heat treatment can also result in a microstructure with an α-mixed crystal content of 10-15%.

[0013] The strength values ​​achievable with this alloy, and its surprisingly significantly better cavitation resistance compared to comparative alloys, were not anticipated by those involved in its development. The 0.2% yield strength of alloy products forged from the alloy of the present invention is between 330 and 350 MPa, which is significantly greater than that typically achieved by forging CuZn37Mn3Al2PbSi alloy (values ​​of 230-300 MPa). The tensile strength of alloy products forged from the alloy of the present invention is between 600 and 640 MPa. For the previously known alloy CuZn37Mn3Al2PbSi, tensile strength values ​​are typically between 590 and 670 MPa. Slightly higher tensile strength values ​​can be achieved using special processing.

[0014] Research has shown that the elements Ni, Fe and Sn not only interact with each other, but also with Mn, Al and Si, in connection with the formation of intermetallic phases, and that particularly good results are obtained when the Mn content is controlled to 1.9-2.6%, the Al content to 1.4-2.1%, the Ni content to 0.45-0.75% and the Fe content to 0.3-0.6%. It has been found that the alloy is particularly suitable for the desired purpose, possessing the special properties of good cold and hot workability, machinability, strength and wear resistance, if the alloy composition is selected as follows (data in % by weight): Cu: 57.5-58.5% Mn: 2.0-2.5% Al: 1.5-2.0%, Si: 0.50 to 0.70% Ni: 0.50~0.70% Fe: 0.5 to 0.55% Sn: 0.20~0.35%.

[0015] The special properties of alloy products manufactured from this alloy are due to the fact that the Si content is preferably equal to or greater than the Ni content. Furthermore, the Sn content of the alloy is preferably adjusted to be at most 50% of the Ni content or at most 50% of the Si content. The Ni content is preferably equal to or greater than the Si content, with a deviation of up to 0.075% allowed. The Fe content also has an effect in relation to other elements. Preferably, the Fe content is approximately 0.05% to 0.1% by weight less than the Ni content.

[0016] The above-mentioned special properties of alloy products made from this alloy are observed in both forged and extruded products. [Brief explanation of the drawings]

[0017] [Figure 1a] 1 is a micrograph of Sample 1 in a pressed state from the start of pressing along the pressing direction. [Figure 1b] 1 is a photomicrograph of Sample 1 in the pressed state from the start of pressing, taken across the pressing direction. [Figure 2a] 10 is the corresponding photomicrograph from the end of the press. [Figure 2b] 10 is the corresponding photomicrograph from the end of the press. [Figure 3a] 1 is a photomicrograph of Sample 2 after the stress relief annealing described above. [Figure 3b] 1 is a photomicrograph of Sample 2 after the stress relief annealing described above. [Figure 4] 1 is a micrograph of Sample CW713R in the pressed state after annealing, corresponding to the micrograph of Sample 2. [Figure 5a] The microstructure around the forged product is shown. [Figure 5b] 1 shows the core microstructure of the forged product. [Figure 6a] 1 shows the microstructure (periphery) of an annealed semi-finished product for manufacturing a fixing plate for hydraulic applications. [Figure 6b]1 shows the microstructure (core) of an annealed semi-finished product for manufacturing a fixing plate for hydraulic applications. DETAILED DESCRIPTION OF THE INVENTION [Example]

[0018] Several alloys of the present invention were cast and then extruded, and the parts were subjected to a subsequent forging process. In parallel, comparative samples made of the material CW713R were also produced. Below are examples of the alloy compositions of two samples according to the present invention (Samples 1 and 2) and the composition of the comparative sample (CW713R). TIFF0007745562000001.tif30170

[0019] After casting (continuous casting), blocks were cut and then used to press bars 50 mm in diameter and 20 m in length. The extrusion temperatures for a series of test samples were between 685°C and 710°C. The extrusion temperature for the described sample was approximately 700°C. The resulting microstructure is very homogeneous throughout the entire length of the pressed bar, both longitudinally and transversely. The only thing that can be observed is some decrease in grain size from the beginning to the end of pressing, as is typically observed in extrusion molding. The microstructure consists largely of only beta phase (mixed silicides aligned in the pressing direction) with embedded intermetallic compounds. The intermetallic compound content is approximately 3-4%.

[0020] Figures 1a and 1b show micrographs of Sample 1 in the pressed state from the beginning of pressing (Figure 1a is along the pressing direction, and Figure 1b is across the pressing direction). Figures 2a and 2b show the corresponding micrographs from the end of pressing. In the next step, samples cut from the pressed bar were thermally stress relieved, i.e., treated at 360 °C for 3 h. As a result of the stress relief annealing, an α mixed phase was formed in the microstructure, resulting in a β-mixed phase-dominated microstructure with an α mixed phase content of approximately 14%. The intermetallic phase content was approximately 3%.

[0021] 3a and 3b are photomicrographs of Sample 2 after the stress relief annealing described above.

[0022] The above microstructural parameters and strength values ​​of these samples are given in the table below. TIFF0007745562000002.tif45170

[0023] IMP indicates intermetallic phase. Hardness HBW was measured as HBW2.5 / 62.5.

[0024] The microstructure of the comparative sample CW713R in the pressed state is dominated by the β phase with an α mixed phase content of approximately 10%. The Pb content in this alloy has a grain-refining effect and acts as a chip breaker. Figure 4 shows a micrograph of the pressed sample CW713R after annealing, corresponding to the micrograph of sample 2. The α mixed phase content is approximately 40-45%.

[0025] In the next step to produce the anchor plate, a connecting piece was separated from the press bar as a pre-forged product and hot forged. The forgings of the Sample Series were forged at temperatures between 635°C and 670°C. Sample 2 and the comparative sample were forged at approximately 650°C. The microstructures of semi-finished products for forged in this way for anchor plates for hydraulic applications are shown in Figures 5a and 5b. Figure 5a shows the peripheral microstructure of the forged product, and Figure 5b shows the core microstructure of the forged product. These images show a very homogeneous microstructure across the diameter of the forged semi-finished product. The semi-finished product consisted mainly of β phase with approximately 3% embedded intermetallic phase.

[0026] In the next step, this type of sample was annealed at 360°C for 3 hours. During this annealing process, an α-phase content of approximately 12% was formed. The intermetallic phase content increased to approximately 3.7%. The microstructure of the annealed semi-finished product for manufacturing anchor plates for hydraulic applications is shown in Figures 6a and 6b (Figure 6a is the periphery, Figure 6b is the core). The α-phase content is clearly evident.

[0027] The microstructural parameters and mechanical strength values ​​of these samples are given in the table below. TIFF0007745562000003.tif43170

[0028] When the forged comparative sample (CW713R) is subjected to the annealing process described above, the α-phase content increases significantly up to about 40%.

[0029] Pipes were also produced by extrusion from Sample 2 alloy and the comparative alloy (CW713R). Sections were cut from the tubes, and then machined on a lathe to compare the machinability of the two alloys. During this lathe process, rings were produced. Interestingly, the machinability of the rings produced from Sample 2 alloy is at least as good as that of the rings produced from the comparative alloy. This is noteworthy because, in contrast to the alloy composition of the comparative sample, the inventive sample (Sample 2) does not contain Pb, i.e., the alloying element Pb in the comparative sample is responsible for the good machinability of this alloy.

[0030] The alloy products according to the invention can be directly drawn. However, it is preferable to carry out an intermediate annealing step before drawing in order to obtain an alloy product that is as stress-free as possible. Furthermore, additional investigations into different material conditions were carried out with the alloy compositions of Samples 1 and 2, and it was found that the tensile strength R of specimens drawn directly or drawn after an intermediate annealing step was significantly higher than that of semi-finished products made from the comparative alloy CW713R. m It was found that the 0.2% yield strength, elongation at break, and hardness (HB) were significantly improved. The results were similar for the material state after the final stress-relief annealing of the two samples. This was also observed in forgings made from the alloy, as well as in extrusion semi-finished products that were pressed and then drawn (stretched). In both cases, subsequent annealing can help reduce stresses in the workpiece.

[0031] Further cavitation studies were performed using the forged and annealed Sample 2. For this purpose, the surfaces of test specimens obtained from Sample 2 were first polished to a 1000-mesh grain size and then subjected to cavitation tests conducted in distilled water according to ASTM G32. It was found that the highly acclaimed cavitation resistance of the comparative alloy CW713R could be further significantly increased. This reduction in the tendency to cavitate in water indicates that alloy products made from the composition of the present invention have improved stability under high dynamic loads in lubricated environments, such as those encountered in cylinder liners of axial piston pumps. Such cylinder liners are manufactured from semi-finished products that are extruded and then cold-drawn (stretched). Therefore, cylinder liners for such applications are particularly suitable for manufacturing from the alloy of the present invention.

Claims

1. A Pb-free Cu—Zn alloy for producing alloy products to be used under lubricating conditions, comprising: Cu: 57.5 to 58.5% by weight, Mn: 2.0 to 2.5% by weight, Al: 1.5-2.0% by weight, Si: 0.50 to 0.70% by weight, Ni: 0.50 to 0.70% by weight, Fe: 0.35 to 0.55% by weight, Sn: 0.20 to 0.35 wt. %, and The balance is Zn with unavoidable impurities. It consists of The Si content is equal to or greater than the Ni content, The Sn content is at most 50% of the Ni content and at most 50% of the Si content; A Pb-free Cu-Zn alloy characterized in that the hardness of the alloy product is 160-190HBW2.5 / 62.

5.

2. The Pb-free Cu-Zn alloy according to claim 1, characterized in that the Fe content is 0.05% to 0.1% lower than the Ni content.

3. The Pb-free Cu-Zn alloy according to claim 1 or 2, characterized in that the 0.2% yield strength of the alloy product is between 300 MPa and 400 MPa and the tensile strength is 600-700 MPa.

4. The Pb-free Cu—Zn alloy according to any one of claims 1 to 3, characterized in that the elongation at break of the alloy product is between 10 and 30%.

5. The Pb-free Cu—Zn alloy according to any one of claims 1 to 3, characterized in that the elongation at break of the alloy product is 10-16%.

6. The Pb-free Cu-Zn alloy according to any one of claims 1 to 5, characterized in that the electrical conductivity of the alloy product is between 9 MS / m and 11 MS / m.

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