High-Tensile Brass Alloy And High-Tensile Brass Alloy Product

Abstract

A special brass alloy containing 62.5 to 65% by weight Cu, 2.0 to 2.4% by weight Mn, 0.7 to 0.9% by weight Ni, 1.9 to 2.3% by weight Al, 0.35 to 0.65% by weight Si, 0.3 to 0.6% by weight Fe, 0.18 to 0.4% by weight Sn and Cr, either alone or in combination, ≤0.1% by weight Pb, the remainder consisting of Zn and inevitable impurities.

Claims

1. A special brass alloy with 62.5 to 65% by weight Cu, 2.0 to 2.4% by weight Mn, 0.7 to 0.9% by weight Ni, 1.9 to 2.3% by weight Al, 0.35 to 0.65% by weight Si, 0.3 to 0.6% by weight Fe, 0.18 to 0.4% by weight Sn and Cr, either alone or in combination, ≤0.1% by weight Pb, the remainder consisting of Zn and inevitable impurities.

2. The special brass alloy of claim 1, wherein the alloy contains 63 to 64% by weight Cu.

3. The special brass alloy of claim 1, wherein the alloy contains 2.1 to 2.2% by weight Mn.

4. The special brass alloy of claim 1, wherein the alloy contains 2.0 to 2.2% by weight Al.

5. The special brass alloy according to of claim 1, wherein the alloy contains 0.4 to 0.5% by weight Fe.

6. The special brass alloy according to of claim 1, wherein the alloy contains 0.2 to 0.3% by weight Sn or 0.2 to 0.27% by weight Cr.

7. A special brass alloy product with an alloy composition according to claim 1, wherein the special brass alloy product is a hot forged part and comprises an α-β mixed crystal matrix with a proportion of α-phase of 35% to 55% and with a proportion of intermetallic phases of 2% to 5%.

8. The special brass alloy product of claim 7, wherein the proportion of α-phase is lowered by annealing carried out after forging.

9. The special brass alloy product of claim 7, wherein the proportion of α-phase has been increased by annealing carried out after forging.

10. The special brass alloy product of claim 7, wherein the special brass alloy product is a product subjected to sliding.

11. The special brass alloy product of claim 10, wherein the product is a sliding shoe or a bearing bushing.

12. The special brass alloy of claim 1, wherein the alloy contains 63 to 64% by weight Cu, 2.1 to 2.2% by weight Mn, 2.0 to 2.2% by weight Al, and 0.4 to 0.5% by weight Fe.

13. The special brass alloy of claim 12, wherein the alloy contains 0.2 to 0.3% by weight Sn or 0.2 to 0.27% by weight Cr.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0034] The below descriptions are provided using embodiment examples in reference to the appended figures, wherein:

[0035] FIG. 1a to 1d shows photomicrographs of an extrusion molded sample in the pressed state made of a first special brass alloy according to the present disclosure,

[0036] FIG. 2 shows photomicrographs of the sample of the alloy of FIG. 1 in a polished longitudinal and cross section in comparison to photomicrographs of a second special brass alloy according to the present disclosure,

[0037] FIG. 3 shows detail views of the polished longitudinal section of the first special brass alloy juxtaposed with a comparison sample,

[0038] FIG. 4 shows detail views of the polished longitudinal section of the second special brass alloy juxtaposed with a comparison sample,

[0039] FIG. 5 shows a photomicrograph of a sliding shoe produced from the first special brass alloy,

[0040] FIG. 6 shows a photomicrograph of a lathed bushing produced from the first special brass alloy,

[0041] FIG. 7 shows microstructure images of a holding segment formed by forging from the first special brass alloy, after the forging,

[0042] FIG. 8 shows microstructure images of a holding segment formed by forging from the first special brass alloy, after a heat treatment (annealing) downstream of the forging,

[0043] FIG. 9 shows microstructure images of a sliding shoe formed by forging from the first special brass alloy, after the forging, and

[0044] FIG. 10 shows microstructure images of a sliding shoe formed by forging from the first special brass alloy, after a heat treatment (annealing) downstream of the forging.

DETAILED DESCRIPTION

[0045] From two special brass alloys according to the present disclosure and a comparison alloy, samples were prepared and subsequently extrusion molded at approximately 700° C. The composition of sample V of the comparison alloy and that of the two samples E1, E2 made of the special brass alloys according to the present disclosure are reproduced below (specifications in % by weight):

TABLE-US-00001 V E1 E2 Cu 61 63.5 63.7 Mn 2.3 2.2 2.0 Ni 0.4 0.73 0.73 Al 3.0 2.2 2.1 Si 0.6 0.6 0.49 Fe 0.05 0.49 0.5 Sn — 0.22 — Pb 0.05 ≤0.1 ≤0.1 Cr 0.013 — 0.21 Zn Remainder Remainder Remainder

[0046] The comparison alloy is the special brass alloy described in EP 3 269 835 B1 in the embodiment example. Sample E1 is a first special brass alloy according to the present disclosure, which represents the Sn-containing variant. FIG. 1 shows photomicrographs of this alloy in the pressed state, removed in longitudinal direction of the pressed connecting piece (FIGS. 1a and 1b) as well as in transverse direction thereto (FIGS. 1c, 1d). FIGS. 1a and 1c are removed from the core, FIGS. 1b and 1d from the radial margin zone. While samples of FIGS. 1a and 1b have been removed in longitudinal direction of the pressed connecting piece, samples of FIGS. 1c and 1d are removed in transverse direction thereto. It is noteworthy that the microstructure is homogeneous both from the core to the margin and also in longitudinal and in transverse direction. These photomicrographs moreover show the α-β structure which is typical for this alloy, in which the α-phase (light grains) interpenetrate the β grains in a lattice-like or strip-like manner.

[0047] This special microstructure of the pressed connecting piece also becomes clear from the photomicrographs of FIG. 2, which are shown with slight magnification. In this figure, sample E1 is shown on the left and sample E2 is shown on the right with its structure. Sample E2 is a second special brass alloy according to the present disclosure, which represents the Cr-containing variant. The upper image pair in each case shows the structure in longitudinal extension of the pressed connecting piece (of the preform). The lower image pair of FIG. 2 shows the structure in transverse direction. From these photomicrographs as well, the interestingly highly homogeneous structural formation in longitudinal and in transverse direction of samples E1, E2 can be seen. In these photomicrographs also, the α-phase is the lighter component.

[0048] FIGS. 3 and 4 show in each case juxtaposed photomicrographs of sample E1 juxtaposed with a photomicrograph of sample V (FIG. 3) and the second sample E2 juxtaposed with a photomicrograph of the sample of comparison alloy V (FIG. 4). These juxtapositions clarify the structural formation of the special brass alloy according to the present disclosure which is significantly different in comparison to the comparison alloy. While the comparison alloy of the “pressed connecting piece” in the processing state exclusively exhibits β-phase, in the alloys according to the present disclosure the β-phase interpenetrated by the α-phase can be seen, wherein the grains of the α-phase extend beyond the grain boundaries of adjoining β-phase grains.

[0049] The semi-finished products initially formed from the special brass alloy according to the present disclosure, for example, in the form of extrusion molded connecting pieces, have a proportion of α-phase of approximately 35 to 55%, in particular between approximately 40% and approximately 50%. The α-phase proportion in samples E1 and E2 in each case is approximately 45%. The β-phase forms the remainder. The proportion of intermetallic phases is approximately 3%.

[0050] In the special brass alloys according to the present disclosure, the above-described alloy-dependent structural formation is used not only for the discussed thermal and mechanical purposes. Instead, this structural formation with the homogeneous distribution of the α-phase and of the (3-phase is suitable for enabling the adjustment of the proportion of the α-phase as a function of the requirements placed on the finished product. This can be carried out by a heat treatment (annealing). If the semi-finished product is subjected to annealing at lower temperature but for a longer treatment duration, the proportion of α-phase is reduced. In order to achieve this, the semi-finished product is treated at temperatures between 260° C. and 300° C. for 4 h to 6 h, in particular at approximately 280° C. for 5 h. By performing the heat treatment with these parameters, the proportion of the α-phase can be reduced to 30% and less.

[0051] However, if the heat treatment is carried out at higher temperature for a shorter time, the proportion of the α-phase with respect to the proportion in the pressed connecting piece is increased. This heat treatment is carried out at temperatures between 430° C. and 470° C. for 2.5 h to 4 h, in particular at a temperature of approximately 450° C. for 3 h. The proportion of α-phase can then be increased to 65% and more.

[0052] A lowering of the proportion of α-phase leads to a certain increase of the proportion of intermetallic phases, which can then proportionally comprise in such annealed products a proportion of 4.5% to 5.5%.

[0053] The special brass alloy according to the present disclosure is particularly suitable, and the homogeneous extrusion molding structure also contributes to this, for forming pressed connecting piece segments by forging. FIG. 7 shows a forged holding segment from sample E1. The forging is carried out at 700° C. Even after the forging, as can be seen in the microstructure images of FIG. 7, the original structural formation can in principle still be seen and thus has remained preserved.

[0054] FIG. 8 shows the holding segment after a heat treatment has been carried out at 280° C. for 5 h. The heat treatment has contributed to a further homogenization of the structure. In this heat treatment, the proportion of α-phase of approximately 40% after the forging was reduced by the heat treatment to approximately 29%. In addition, the hardness was increased from approximately 140 HB [HBW 2.5/62.5] to approximately 148 HB.

[0055] From sample E1, by forging, a sliding shoe was also produced. FIG. 9 shows the structure after the forging step which was carried out at 710° C. The microstructure set in the pressed connecting piece also remains preserved in principle in this sample in spite of the forging. The forged sliding shoe was subsequently heat treated at 450° C. for 3 h. FIG. 10 shows that the proportion of α-phase has been increased by the annealing step and namely from approximately 50% after the forging, which corresponds to the α-phase proportion in the pressed connecting piece, to approximately 68%. The hardness HB was only slightly raised by the annealing in comparison to the hardness after the forging, and namely from 155 HB [HBW 2.5/62.5] to 159 HB.

[0056] In sample V of the comparison alloy, the matrix of the pressed connecting piece contained a proportion of α-phase of <1%.

[0057] In the special brass alloy according to the present disclosure, it is interesting that, in comparison to sample V of the comparison alloy, it has an electrical conductivity lower by slightly more than 10%. While the electrical conductivity is 10.4 to 10.7 MS/m in the comparison alloy, it is only 8.8 MS/m in alloy E1. This improves the corrosion resistance of this special brass alloy.

[0058] The mechanical characteristics of samples E1 and E2 can be obtained from the following table:

TABLE-US-00002 Tensile strength Elongation at break 0.2% elasticity limit Rm [N/mm.sup.2] A.sub.5 [%] R.sub.p0.2 [N/mm.sup.2] E1 550 18 250 E2 545 21 243