CAST ALUMINUM ALLOY FOR TRANSMISSION CLUTCH

Abstract

An aluminum alloy suitable for casting transmission clutch housings, the aluminum alloy includes about 12 to about 16 weight percent silicon; about 0.0 to about 6.0 weight percent copper; about 0.2 to about 0.5 weight percent magnesium; about 0.1 to about 0.5 weight percent chromium; about 0 to about 1.0 weight percent each of iron, manganese, and zinc; less than 0.1 weight percent each of strontium and phosphorous; and about 0.0 to about 0.25 weight percent other trace elements. Also disclosed is a high pressure die cast article, such as a transmission clutch housing.

Claims

1. An aluminum alloy suitable for casting transmission clutch housings, the aluminum alloy comprising: about 12 to about 16 weight percent silicon; about 0.0 to about 6.0 weight percent copper; about 0.2 to about 0.5 weight percent magnesium; about 0.1 to about 0.5 weight percent chromium; about 0 to about 1.0 weight percent each of iron, manganese, and zinc; less than 0.1 weight percent each of strontium and phosphorous; and about 0.0 to about 0.25 weight percent other trace elements.

2. The aluminum alloy of claim 1, further comprising about 74 to about 88 weight percent aluminum.

3. The aluminum alloy of claim 2 comprising: about 13 weight percent silicon; about 0.0 to about 6.0 weight percent copper; about 0.35 weight percent magnesium; about 0.1 to about 0.5 weight percent chromium; about 0.4 weight percent each of iron; about 0.5 weight percent each of manganese; about 0.2 weight percent of zinc; less than 0.1 weight percent each of strontium and phosphorous; and about 0.0 to about 0.25 weight percent other trace elements.

4. The aluminum alloy of claim 3, further comprising a balance of about 85 weight percent aluminum.

5. The aluminum alloy of claim 4, wherein the alloy can be used for as-cast and T5 aging conditions.

6. The aluminum alloy of claim 4, further comprising an as-cast yield strength of 185 MPa.

7. The aluminum alloy of claim 4, further comprising an as-cast ultimate tensile strength of 310 MPa.

8. The aluminum alloy of claim 4, further comprising a sludge factor is less than or equal to 1.6, up to 0.5 weight percent chromium, iron content less than or equal to 0.5 weight percent, and essentially no -Fe Phase.

9. The aluminum alloy of claim 4, further comprising a T5 yield strength of 251 MPa.

10. The aluminum alloy of claim 4, further comprising a T5 ultimate tensile strength of 340 MPa.

11. The aluminum alloy of claim 4, further comprising a T5 elongation of 1.9 percent.

12. An aluminum alloy suitable for casting transmission clutch housings, the aluminum alloy comprising: about 13.0 to about 14.0 weight percent silicon; about 0.0 to about 2.0 weight percent copper; about 0.3 to about 0.4 weight percent magnesium; about 0.2 to about 0.3 weight percent chromium; about 0.3 to about 0.5 weight percent manganese; less than 0.5 weight percent each of iron and zinc; less than 0.05 weight percent each of strontium and phosphorous; and about 0.0 to about 0.15 weight percent other trace elements.

13. The aluminum alloy of claim 12, further comprising about 83 to about 86 weight percent aluminum.

14. The aluminum alloy of claim 13, wherein the alloy can be used for as-cast and T5 aging conditions.

15. The aluminum alloy of claim 13, further comprising an as-cast yield strength of 185 MPa.

16. The aluminum alloy of claim 13, further comprising an as-cast ultimate tensile strength of 310 MPa.

17. The aluminum alloy of claim 13, further comprising a sludge factor is less than or equal to 1.6, up to 0.5 weight percent chromium, iron content less than or equal to 0.5 weight percent, and essentially no -Fe Phase.

18. The aluminum alloy of claim 13, further comprising T5 yield strength of 251 MPa.

19. The aluminum alloy according to claim 4 in the form of a HPDC transmission clutch housing.

20. The aluminum alloy according to claim 13 in the form of a HPDC transmission clutch housing.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0013] The drawings are provided for illustration purposes only and are not intended to limit this disclosure or the claims appended hereto.

[0014] FIG. 1 is a top view of a transmission clutch housing casting in accordance with aspects of an exemplary embodiment;

[0015] FIG. 2 is a bottom view of a transmission clutch housing casting in accordance with aspects of an exemplary embodiment;

[0016] FIG. 3 is a graph showing a calculated phase diagram of a HPDC aluminum alloy showing phase transformations as a function of copper (Cu) content as according to aspects of an exemplary embodiment;

[0017] FIG. 4 is a graph showing a calculated phase diagram of a HPDC aluminum alloy showing phase transformations as a function of silicon (Si) content as according to aspects of an exemplary embodiment; and

[0018] FIG. 5 is a graph showing a calculated phase diagram of a HPDC aluminum alloy showing phase transformations as a function of magnesium (Mg) content in accordance with aspects of an exemplary embodiment.

DETAILED DESCRIPTION

[0019] Cast aluminum alloys are provided having improved mechanical properties for transmission clutch housings.

[0020] In FIG. 1, the clutch housing 10 has a generally cup-shaped open bowl configuration with an end wall (also called piston stop face) 12, an inner axial hub 14 and an outer wall 16. The outer wall 16 includes an interior surface 18 defining an inner diameter and an exterior surface 20 defining an outer diameter. In accordance with the operating characteristics of the clutch housing 10, a series of longitudinal splines 22 are formed in the interior surface 18 of the outer wall 16. The splines 22 may be formed at varying intervals, lengths and depths for operation in a predetermined manner. In FIG. 2, a series of shallow metal saver pockets 30 are formed in the outer back surface 32 of the end wall 12. The splines 22 and metal saver pockets 30 may be formed at varying intervals, lengths and depths for operation in a predetermined manner. The splines 22 receive impact and torsional loading and require high strength and wear resistance especially at very high speeds (>12000 rpm). In comparison to other aluminum alloys, these new alloys exhibit a lower tendency for porosity, better castability, and higher mechanical properties (see Table 1). These alloys may also exhibit improved ductility and high fracture toughness, as well as high strength and wear resistance. As a result, the scrap rate for aluminum casting and the manufacturing cost can be reduced. And warranty cost can be reduced due to crack elimination and no need for crack detection in the manufacturing process.

The new alloys can be applied to both permanent mold and HPDC processes.

TABLE-US-00001 TABLE 1 Mechanical Properties of New Alloy and 380/390 As-Cast T5 UTS UTS El ALLOY YS (MPa) (MPa) El (%) YS (MPa) (MPa) (%) New Alloy 185 310 2.8 251 340 1.9 A380 145 240 2.2 146 270 1.6 A380_mod 156 301 3.3 218 330 2 B390 177 212 0.2 194 194 0.18 The new alloy: Al13% Si0.35% Mg0.4% Fe0.5% Mn0.2% Zn

[0021] The alloy may contain at least one of the castability and strength enhancement elements such as silicon, copper, magnesium, manganese, iron, zinc, and nickel. The microstructure of the alloy contains one or more insoluble solidified and/or precipitated particles with at least one alloying element.

[0022] Two examples of composition ranges of the new alloy (called Version 1 and Version 2 in these examples) are listed in Table 2, compared with the other commercially available alloys for transmission clutch housings or other articles.

TABLE-US-00002 TABLE 2 Chemical compositions of two versions of the new alloy and commercial alloys A380, 390, A390, and B390 Alloy Si Cu Mg Fe Mn Zn Cr P Sr A380 7.5-9.5 3.0-4.0 <0.1 0.7-1.5 <0.5 1.5-3.0 390.0 16.0-18.0 4.0-5.0 0.45-0.65 <1.3 <0.1 <0.1 A390.0 16.0-18.0 4.0-5.0 0.45-0.65 <0.5 <0.1 <0.1 B390.0 16.0-18.0 4.0-5.0 0.45-0.65 <1.3 >0.5 <1.5 V1 12.0-16.0 0.0-6.0 0.2-0.5 0.0-1.0 0.0-1.0 0.0-1.0 0.1-0.5 <0.1 <0.1 (wt %) V2 13.0-14.0 0.0-2.0 0.3-0.4 <0.5 0.3-0.5 <0.5 0.2-0.3 <0.05 <0.05 (wt %)

[0023] Though copper is generally known to increase strength and hardness in aluminum alloys, on the downside, copper generally reduces the corrosion resistance of aluminum; and, in certain alloys and tempers, copper increases stress corrosion susceptibility. Copper also increases the alloy freezing range and decreases feeding capability, leading to a high potential for shrinkage porosity. Furthermore, copper is expensive and heavy.

[0024] Aluminum alloy castings known to the HPDC parts have generally been limited to temper T5 treatment aging (natural or artificial). Aging strengthens castings by facilitating the precipitation of the hardening solutes of the aluminum alloy composition. Artificial aging is to heat castings to an intermediate temperature (e.g., 160-240 degrees C.), and then holding the castings for a period of time to achieve hardening or strengthening through precipitation. Considering that precipitation hardening is a kinetic process, the contents (supersaturation) of the retained solute elements in the casting play an important role in the aging responses of the castings. Therefore, the availability and actual amount of hardening solutes in the aluminum soft matrix solution after HPDC process has an effect on subsequent aging, which depends on the alloy composition, such as Cu and Mg content, and quenching temperature after casting is extracted from the die.

[0025] In AlSiMgCu based HPDC cast aluminum alloy, like A380 alloy, the strengthening precipitates include Mg2Si, Al2Cu, and Q phase (AlCuMgSi) after the casting is subject to a solution treatment at high temperature such as 490 C. However, HPDC components are not usually subject to solution treatment, the hardening efficacy and contribution of Cu may be surprisingly limited. Although typical HPDC aluminum alloys, such as A380, 380 or 383, contain 34% Cu in nominal composition, the actual Cu solute remaining in as-cast aluminum matrix for the subsequent aging is actually much reduced. Excess Cu in the alloy however will form other low melting phases. The Cu-containing low-melting phases can significantly affect alloy castability and increase porosity in the castings. One of the measures for castability of an alloy is freezing range between liquidus and solidus. The larger the freezing range, the higher the shrinkage porosity and lower castability.

[0026] Referring to FIG. 3 which illustrates a calculated phase diagram 50 of AlCu-14 wt % Si0.35 wt % Mg-0.4 wt % Fe-0.5 wt % Mn-0.25 wt % Cr-0.25 wt % Zn based alloy with preferred alloys having a Cu content that varies from 0 to 2 weight percent. The diagram 50 includes a liquidus boundary line 55 above which alloy material remains liquid and a solidus boundary line 60 below which alloy material becomes solid. The temperature range between the liquidus 55 and solidus 60 boundary lines is the alloy freezing range 65. The freezing range 65 is maximized and is almost kept constant when the Cu content is between 4.0 and 6.0 weight percent. When Cu content is less than 2%, the freezing range is significantly reduced. The phase diagram 50 also indicates that with the alloy composition range particularly for the Fe and Mn content proposed no beta-Fe phase (AlFeSi) formed in the casting. Beta-Fe phase (AlFeSi) looks like needle in 2D and plate in 3D, which is brittle and significantly reduces the material ductility by initiating cracks in the material.

[0027] Si is an important element for cast aluminum alloy. Si increases alloy castability by increasing fluidity and releasing high latent heat during solidification to reduce shrinkage and improve feeding. High Si content also reduces alloy freezing range. For example, referring to FIG. 4, a calculated phase diagram 70 of AlSi-1.5 wt % Cu-0.35 wt % Mg-0.4 wt % Fe-0.5 wt % Mn-0.25 wt % Cr-0.25 wt % Zn based alloy with new alloys having a Si content that varies from 12 to 16 weight percent is provided. The diagram 50 includes a liquidus boundary line 75 above which alloy material remains liquid and a solidus boundary line 80 below which alloy material becomes solid. The temperature range between the liquidus 75 and solidus 80 boundary lines is the alloy freezing range 85. The freezing range 85 is small and is almost kept constant when the Si content is between 12 and 16.0 weight percent. This improves alloy castability. With the preferred alloy composition, there is no brittle beta-Fe phase forming in the material which shall help improve the mechanical properties particularly ductility

[0028] To further improve the aging response of cast aluminum alloy, magnesium content in the new alloy for transmission clutch components should be kept no less than 0.2 wt %, and the preferred level is above 0.3 wt %. The maximum Mg content should be kept below 0.6 wt %, with a preferable level of 0.35 wt %, so that a majority of the Mg addition will stay in Al solid solution after HPDC to mainly form only Q-phase (AlCuMgSi) precipitates. FIG. 5 illustrates a calculated phase diagram 100 of AlMg-14 wt % Si-15 wt % Cu-0.4 wt % Fe-0.5 wt % Mn-0.25 wt % Cr-0.2 wt % Zn based alloy with new alloys having a Mg content that varies from 0.2 to about 0.45 weight percent. The diagram 100 includes a liquidus boundary line 105 above which alloy material remains liquid and a solidus boundary line 110 below which alloy material becomes solid. The temperature range between the liquidus 105 and solidus 110 boundary lines is the alloy freezing range 115. The freezing range 115 is small and almost kept constant when the Mg content is between 0.2 and 0.4 weight percent. The small freezing range leads to a good castability. With the preferred alloy composition, there is no brittle beta-Fe phase forming in the material which shall help improve the mechanical properties particularly ductility.

[0029] Phosphorous is added to refine the primary Si particle sizes and also make the primary Si particles distributed more uniformly. Strontium is added to modified and refine the eutectic Si particles and convert the eutectic Si particles from flakes to fibers so that the ductility of the material is significantly. The aluminum alloy includes less than 0.1 weight percent each of strontium and phosphorous.

[0030] Further additional features may be provided, such as: the iron, manganese and chromium content being provided each in an amount so that a sludge factor is less than or equal to 1.6, wherein the sludge factor is calculated by the following equation: Sludge factor=(1wt % iron)+(2wt % manganese)+(3wt % chromium), and wherein the aluminum alloy may contain up to 0.5% chromium; the aluminum alloy containing iron content less than or equal to manganese content and essentially no Beta Iron Phase (-Fe Phase).

[0031] The alloys described herein may be used to manufacture a permanent mold or high pressure die cast article, such as transmission clutch housings. Therefore, it is within the contemplation of the inventors herein that the disclosure extend to cast articles, including transmission clutch housings, containing the improved alloy (including examples, versions, and variations thereof).

[0032] Furthermore, while the above examples are described individually, it will be understood by one of skill in the art having the benefit of this disclosure that amounts of elements described herein may be mixed and matched from the various examples within the scope of the appended claims.

[0033] It is further understood that any of the above described concepts can be used alone or in combination with any or all of the other above described concepts. Although an embodiment of this invention has been disclosed, a worker of ordinary skill in this art would recognize that certain modifications would come within the scope of this invention. For that reason, the following claims should be studied to determine the true scope and content of this invention.