Method and alloys for low pressure permanent mold without a coating

Abstract

A method and alloys for low pressure permanent mold casting without a coating are disclosed. The method includes preparing a permanent mold casting die that is devoid of die coating or lubrication along the die surface, preparing a permanent mold casting alloy, pushing the alloy into the die under low pressure, cooling the permanent mold casting, and removing the casting from the die. One alloy has 4.5-11.5% by weight silicon; 0.45% by weight maximum iron; 0.20-0.40% by weight manganese; 0.045-0.110% by weight strontium; 0.05-5.0% by weight copper; 0.01-0.70% by weight magnesium; and the balance aluminum. Another alloy has 4.2-5.0% by weight copper; 0.005-0.45% by weight iron; 0.20-0.50% by weight manganese; 0.15-0.35% by weight magnesium; 0.045-0.110% by weight strontium; 0.50% by weight maximum nickel; 0.10% by weight maximum silicon; 0.15-0.30% by weight titanium; 0.05% by weight maximum tin; 0.10% by weight maximum zinc; and the balance aluminum.

Claims

1. A method for low pressure permanent mold casting of metallic objects, the method comprising: preparing a permanent mold casting die, said die devoid of die coating or lubrication along a die casting surface; preparing a permanent mold casting alloy having 4.5-11.5% by weight silicon, 0.45% by weight maximum iron, 0.20-0.40% by weight manganese, 0.045-0.110% by weight strontium, 0.05-5% by weight copper, 0.10-0.7% by weight magnesium, and balance aluminum and wherein the alloy has a die soldering factor equivalent to or greater than 1.1, the die soldering factor defined as (10[Sr]+Mn+Fe); pushing the alloy into the permanent mold casting die under pressure of 3-15 psi to create a permanent mold casting; cooling the permanent mold casting; and removing the permanent mold casting from the die without force; wherein the permanent mold casting does not solder to the permanent mold die; and wherein the surface roughness of the casting is 500 microinches R.sub.a or less.

2. The method of claim 1, wherein the alloy includes 0.50% by weight maximum nickel.

3. The method of claim 1, wherein a step of heat treating the casting is added after the step of removing the casting from the die.

4. The method of claim 1, wherein the step of cooling the permanent mold casting further comprises solidifying the alloy without formation of primary intermetallics.

5. The method of claim 4, wherein the primary intermetallics are Al.sub.5FeSi or Al.sub.15(MnFe).sub.3Si.sub.2.

6. The method of claim 1, wherein the permanent mold casting is an L-bracket.

7. The method of claim 1, wherein the permanent mold casting is a gear case housing with an integral splash plate.

8. The method of claim 1, wherein the step of preparing a permanent mold casting die includes preparing a permanent mold casting die having at least one thin walled section.

9. The method of claim 8, wherein the step of pushing the alloy into the permanent mold casting die includes pushing the alloy into at least one thin walled section before the alloy solidifies.

10. The method of claim 1, wherein the method is fully automated.

11. A method for low pressure permanent mold casting of metallic objects, the method comprising: preparing a permanent mold casting die, said die devoid of die coating or lubrication along a die casting surface; preparing a permanent mold casting alloy having 4.2-5.0% by weight copper; 0.005-0.45% by weight iron; 0.20-0.50% by weight manganese; 0.15-0.35% by weight magnesium; 0.045-0.110% by weight strontium; 0.05% by weight maximum nickel; 0.10% by weight maximum silicon; 0.15-0.30% by weight titanium; 0.05% by weight maximum tin; 0.10% by weight maximum zinc; and balance aluminum and wherein the alloy has a die soldering factor equivalent to or greater than 1.1, the die soldering factor defined as (10[Sr]+Mn+Fe); pushing the alloy into the permanent mold casting die under pressure of 3-15 psi to create a permanent mold casting; cooling the permanent mold casting; and removing the permanent mold casting from the die without force; wherein the permanent mold casting does not solder to the permanent mold die; and wherein the surface roughness of the casting is 500 microinches or less.

12. The method of claim 11, wherein a step of heat treating the casting is added after the step of removing the casting from the die, and the steps of preparing, pushing, cooling, heat treating and removing are fully automated.

13. The method of claim 11, wherein the step of preparing a permanent mold casting die includes preparing a permanent mold casting die having at least one thin walled section, and wherein the step of pushing the alloy into the permanent mold casting die includes pushing the alloy into at least one thin walled section before the alloy solidifies.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) The patent or application file contains at least one drawing executed in color. Copies of this patent or patent application publication with color drawing(s) will be provided by the Office upon request and payment of the necessary fee. The present disclosure is described with reference to the following Figures. The same numbers are used throughout the Figures to reference like features and like components.

(2) FIG. 1 is a photograph of an L-Bracket made with a traditional low pressure permanent mold casting process where a coating or lubrication is used to coat the die cavity.

(3) FIG. 2 is a photograph of an L-Bracket made with the new low pressure permanent mold casting process of the present application.

(4) FIG. 3 is a photograph comparing the L-Brackets of FIGS. 1 and 2 in a side by side comparison.

(5) FIG. 4 is a close-up photograph of FIG. 3.

(6) FIG. 5 is a surface roughness measurement of an L-Bracket manufactured in accordance with the present application.

(7) FIG. 6 is a surface roughness measurement of an L-Bracket manufactured in accordance with the present application.

(8) FIG. 7 is a surface roughness measurement of an L-Bracket made in accordance with the present application.

(9) FIG. 8 is a surface roughness measurement of an L-Bracket made with a traditional low pressure permanent mold casting having a coating or lubricant in the die cavity.

(10) FIG. 9 is a surface roughness measurement of an L-Bracket made with a traditional low pressure permanent mold casting having a coating or lubricant in the die cavity.

(11) FIG. 10 is a side view of a gear case housing with having a thin integral splash plate made in accordance with the method of the present application.

(12) FIG. 11 is a bottom view photograph of the gear case housing of FIG. 10.

(13) FIG. 12 is a photographic side view of a gear case housing with a thin integral splash plate made with a traditional permanent mold casting process using a die coating or lubricant.

(14) FIG. 13 is a bottom view of the gear case housing of FIG. 12.

(15) FIGS. 14A-14E are a series of phase diagrams for the aluminum-manganese-iron-silicon quaternary system.

DETAILED DESCRIPTION

(16) The present inventors have discovered the formula to determine when permanent mold die soldering does or does not occur. That formula is:
(10[Sr]+Mn+Fe)>1.1
The result of the formula is herein referred to as the die soldering factor. If the die soldering factor is less than 1.1, die soldering is expected to occur; conversely if the die soldering factor is greater than 1.1, then die soldering is not expected to occur.

(17) In application, alloys 367 and 368 have a strontium (Sr) range of 0.05% to 0.08% with a midpoint of 0.065%; a manganese (Mn) range of 0.25% to 0.35% with a midpoint of 0.30%; and an iron (Fe) range of 0% to 0.25% with a midpoint of 0.125%. Applying the formula yields ([10]0.065+0.30+0.125)=1.075. The 1.075 number is rounded up to 1.1, indicting no die soldering.

(18) The present inventors have found that the die soldering factor may be used in converting permanent mold alloys to strontium-containing permanent mold alloys with die soldering resistance that do not precipitate primary intermetallics on solidification. Unexpectedly, such alloys may be cast in the low pressure permanent mold casting process without a coating on the dies. Absence of the coating permits a faster cooling rate, which increases the mechanical properties; promotes a shorter cycle time, which lowers the manufacturing cost; and provides a much smoother surface finish which replicates the uncoated die surface topography and not the very rough surface topography of the coating.

(19) When die soldering resistance is provided by low levels of strontium in the range of 0.045-0.110, the total bulk concentration level of iron and manganese, the two elements that traditionally provide die soldering resistance, can be lowered ultimately benefiting the mechanical properties of the alloy. Manganese is a key element in the inventive unexpected discoveries because manganese determines the specific iron concentration below which primary Mn/Fe-intermetallics will not form. Above this concentration, intermetallics precipitate and mechanical properties decrease, particularly the ductility.

(20) In applications where the alloy is made from A356 with iron at 0.2% and manganese at the maximum of 0.1%, die soldering will occur unless the strontium is at its upper limit of 0.08%. For alloy 362 with an iron specification max of 0.4%, under the same conditions, die soldering will occur when the strontium is below its midrange value. However, when the iron content is at 0.2%, for either alloys 367 or 368, and the manganese at its midrange, die soldering will not occur when the strontium is at or above its lower spec limit of 0.05%. When the Silafont-36 alloy is at the specified upper limit for manganese at 0.80% and upper limit for iron at 0.12%, and if the eutectic silicon is not modified with strontium, the value of the equation yields a die soldering factor of 0.92, and die soldering is expected. Further, the Aural-2 alloy and Aural-3 alloy at their manganese limit of 0.6% with an iron limit of 0.25% have a die soldering factor of 0.85. Thus, die soldering is expected if the eutectic silicon is not modified. To modify the eutectic silicon, 0.03% strontium could be added to the Silafont-36 alloy Aural-2 alloy and Aural-3 alloy, adding 0.3 to the die soldering factors of the three alloys and bringing the Silafont-36 alloy to 1.22 and the Aural-2 alloy and Aural-3 alloy to 1.15 to avoid die soldering in permanent mold castings.

(21) Now referring to Table 1, therein is tabulated the entire Aluminum Association permanent mold alloys listed in the February 2008 pink sheets entitled Designations and Chemical Composition Limits for Aluminum Alloys in the Form of Castings and Ingots. The listed manganese concentration specifies the iron level below which primary intermetallics do not form, and impacts the alloy's ductility. The value of the die soldering factor is provided and as previously noted, a value equal to or greater than 1.1 indicates the absence of die soldering. While high iron levels (i.e. 0.6% by weight or greater, and preferably 0.45% by weight or greater) result in no die soldering, the high iron creates poor ductility, and is not the optimal solution.

(22) TABLE-US-00001 TABLE 1 PERMANENT MOLD CANDIDATE ALLOYS AND THEIR DIE SOLDERING FACTOR VALUES alloy process Si Fe Cu Mn Mg Die Soldering Factor Primary Precipitation of Intermetallics 308 PM 5.0-6.0 1.0 4.0-5.0 0.50 0.10 1.5 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 318 PM 5.5-6.5 1.0 3.0-4.0 0.50 0.10-0.6 1.5 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 319 PM 5.5-6.5 1.0 3.0-4.0 0.50 0.10 1.5 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 320 PM 5.0-8.0 1.2 2.0-4.0 0.8 0.05-0.6 2.0 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 332 PM 8.5-10.5 1.2 2.0-4.0 0.5 0.50-1.5 1.7 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 333 PM 8.0-10.0 1.0 3.0-4.0 0.50 0.05-0.50 1.5 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 336 PM 11.0-13.0 1.2 0.50-1.5 0.35 0.7-1.3 1.55 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 339 PM 11.0-13.0 1.2 1.5-3.0 0.50 0.50-1.5 1.7 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 354 PM 8.6-9.4 0.20 1.6-2.0 0.10 0.40-0.6 0.3 .fwdarw. die soldering no precipitation of intermetallics 355 PM 4.5-5.5 0.6 1.0-1.5 0.50 0.40-0.6 1.1 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC A356 PM 6.5-7.5 0.20 0.20 0.10 0.25-0.45 0.3 .fwdarw. die soldering; no precipitation of intermetallics 357 PM 6.5-7.5 0.15 0.05 0.03 0.45-0.6 0.18 .fwdarw. soldering; no precipitation of primary intermetallics 358 PM7. 7.6-8.6 0.30 0.20 0.20 0.40-0.6 0.5 .fwdarw. soldering; no precipitation of primary intermetallics 359 PM 8.5-9.5 0.20 0.20 0.10 0.50-0.7 0.3 .fwdarw. soldering; no precipitation of primary intermetallics 362 Stru 10.5-11.5 0.20 0.15 0.25-0.35 0.55-0.7 1.3, with 0.06 Sr, no soldering & no primary intermetallics 363 PM 4.5-6.0 1.1 2.5-3.5 0.15-0.40 1.1 .fwdarw. no soldering yes .fwdarw. poor ductility, like HPDC 365 Stru 9.5-11.5 0.15 0.03 0.50-0.8 0.10-0.50 1.1, with 0.015 Sr .fwdarw. no soldering & good ductility A365 Stru 9.5-11.5 0.25 0.15 0.40-0.6 0.10-0.50 1.0, with 0.015 Sr .fwdarw. almost no soldering & good ductility 366 PM 6.5-7.5 0.15 0.05 0.03 0.5-1.2 0.18 .fwdarw. soldering but no intermetallics & good ductility 367 Stru 8.5-9.5 0.25 0.25 0.25-0.35 0.30-0.50 1.15, with 0.06 Sr .fwdarw. no soldering & very good ductility 368 Stru 8.5-9.5 0.25 0.25 0.25-0.35 0.10-0.30 1.15, with 0.06 Sr .fwdarw. no soldering & very good ductility

(23) In Table 2 below, the manganese levels of the same alloys in Table 1 have been modified to a range 0.25-0.35%, in turn modifying the iron value to 0.45% max. Thus, with the strontium added at its midrange value of 0.065 for a preferable range of 0.05-0.08, the manganese at its midrange value of 0.30 for a range of 0.25-0.35, and the iron at a conservative limit of 0.40 for better ductility, the value of the die soldering factor is (10[0.065]+0.30+0.40)=1.35. Note that the preferable range of strontium is 0.05 to 0.08% by weight, but that the compatible Sr range is 0.045 to 0.110% by weight strontium. The alloys in Table 2 are the alloys uniquely identified for low pressure permanent mold casting without a coating, by adding 0.045 to 0.11% by weight strontium.

(24) TABLE-US-00002 TABLE 2 NEW PERMANENT MOLD ALLOYS WITH DIE SOLDERING RESISTANCE THAT DO NOT PRECIPITATE PRIMARY INTERMETALLICS ON SOLIDIFICATION Die Soldering Primary Alloy Process Si Fe Sr Cu Mn Mg Factor Intermetallics Dies A308 PM 5.0- 0.45 0.065 4.0- 0.25- 0.10 1.35 .fwdarw. no no .fwdarw. high Uncoated 6.0 5.0 0.35 soldering ductility A318 PM 5.5- 0.45 0.065 3.0- 0.25- 0.10- 1.35 .fwdarw. no no .fwdarw. high Uncoated 6.5 4.0 0.35 0.6 soldering ductility C319 PM 5.5- 0.45 0.065 3.0- 0.25- 0.10 1.35 .fwdarw. no no .fwdarw. high Uncoated 6.5 4.0 0.35 soldering ductility A320 PM 5.0- 0.45 0.065 2.0- 0.25- 0.05- 1.35 .fwdarw. no no .fwdarw. high Uncoated 8.0 4.0 0.35 0.6 soldering ductility A332 PM 8.5- 0.45 0.065 2.0- 0.25- 0.50- 1.35 .fwdarw. no no .fwdarw. high Uncoated 10.5 4.0 0.35 1.5 soldering ductility B333 PM 8.0- 0.45 0.065 3.0- 0.25- 0.05- 1.35 .fwdarw. no no .fwdarw. high Uncoated 10.0 4.0 0.35 0.50 soldering ductility A336 PM 11.0- 0.45 0.065 0.50- 0.25- 0.7- 1.35 .fwdarw. no no .fwdarw. high Uncoated 13.0 1.5 0.35 1.3 soldering ductility A339 PM 11.0- 0.45 0.065 1.5- 0.25- 0.50- 1.35 .fwdarw. no no .fwdarw. high Uncoated 13.0 3.0 0.35 1.5 soldering ductility A354 PM 8.6- 0.45 0.065 1.6- 0.25- 0.40- 1.35 .fwdarw. no no .fwdarw. high Uncoated 9.4 2.0 0.35 0.6 soldering ductility D355 PM 4.5- 0.45 0.065 1.0- 0.25- 0.40- 1.35 .fwdarw. no no .fwdarw. high Uncoated 5.5 1.5 0.35 0.6 soldering ductility G356 PM 6.5- 0.45 0.065 0.20 0.25- 0.25- 1.35 .fwdarw. no no .fwdarw. high Uncoated 7.5 0.35 0.45 soldering ductility G357 PM 6.5- 0.45 0.065 0.05 0.25- 0.45- 1.35 .fwdarw. no no .fwdarw. high Uncoated 7.5 0.35 0.6 soldering ductility A358 PM 7.6- 0.45 0.065 0.20 0.25- 0.40- 1.35 .fwdarw. no no .fwdarw. high Uncoated 8.6 0.35 0.6 soldering ductility B359 PM 8.5- 0.45 0.065 0.20 0.25- 0.50- 1.35 .fwdarw. no no .fwdarw. high Uncoated 9.5 0.35 0.7 soldering ductility A362 Stru 10.5- 0.45 0.065 0.15 0.25- 0.55- 1.35 .fwdarw. no no .fwdarw. high Uncoated 11.5 0.35 0.7 soldering ductility A363 PM 4.5- 0.45 0.065 2.5- 0.25- 0.15- 1.35 .fwdarw. no no .fwdarw. high Uncoated 6.0 3.5 0.35 0.40 soldering ductility B365 Stru 9.5- 0.45 0.065 0.03 0.25- 0.10- 1.35 .fwdarw. no no .fwdarw. high Uncoated 11.5 0.35 0.50 soldering ductility C365 Stru 9.5- 0.45 0.065 0.15 0.25- 0.10- 1.35 .fwdarw. no no .fwdarw. high Uncoated 11.5 0.35 0.50 soldering ductility A366 PM 6.5- 0.45 0.065 0.05 0.25- 0.5- 1.35 .fwdarw. no no .fwdarw. high Uncoated 7.5 0.35 1.2 soldering ductility A367 Stru 8.5- 0.45 0.065 0.25 0.25- 0.30- 1.35 .fwdarw. no no .fwdarw. high Uncoated 9.5 0.35 0.50 soldering ductility A368 Stru 8.5- 0.45 0.065 0.25 0.25- 0.10- 1.35 .fwdarw. no no .fwdarw. high Uncoated 9.5 0.35 0.30 soldering ductility

(25) As noted, manganese is an important element in any alloy that uses uncoated metal molds because the manganese specifies the iron level below which detrimental primary intermetallics of Al.sub.5FeSi and AL.sub.15(MnFe).sub.3Si.sub.2 cannot form, according to the AlSiMnFe phase diagrams of FIGS. 14A-14E.

(26) The best heat treatment condition (i.e., as cast, T5, T6 or T7) and the best mechanical properties (i.e., ultimate strength, yield strength, or elongation) were determined to then assess the difference between low pressure permanent mold casting process, with and without a coating. A review of the mechanical properties in ASM Specialty Handbook Aluminum and Aluminum Alloys First printing: December 1993, Table 14, pages 113 and 114, suggest the as cast elongation is an acceptable measure. From Table 14 of that reference, the following Table 3 was tabulated.

(27) TABLE-US-00003 TABLE 3 As Cast PM Alloy Elongation T5 Elongation T6 Elongation T7 Elongation 308 2.0% 319 2.0% 2.0% 2.0% 324 4.0% 3.0% 3.0% 332 1.0% 333 2.0% 1.0% 1.5% 2.0% 336 0.5% 0.5% 354 6.0% 355 4.0% 356 5.0% 2.0% 5.0% 6.0% A356 10.0% 357 6.0% 4.0% 5.0% A357 5.0% 358 6.0% 359 7.0%
The as cast condition was selected because it was nearly (but not always) the highest elongation value, with the other temper conditions generally having a lower elongation.

(28) Referring to FIGS. 1 and 2, an L-bracket with a solid back and two bars for a seat as demonstrated. FIG. 1 was made in low pressure permanent mold casting with the normal coating and FIG. 2 was made in low pressure permanent mold casting without a coating. The superior aesthetics of FIG. 2 is apparent. FIGS. 3 and 4 show the L-bracket of FIGS. 1 and 2 at higher magnification, where both L-brackets are side by side. The L-bracket made without a coating is on the left, and it is apparent that the L-bracket made without a coating exhibits superior aesthetics.

(29) The smoothness of the respective finishes was quantified with surface roughness, of FIGS. 5-9. FIGS. 5-7 measured the surface roughness of uncoated L-bracket dies at 500 microinches or less, while coated dies exhibited a surface roughness at 2200 microinches R.sub.a, as demonstrated by FIGS. 8-9. This means that uncoated dies result in a surface finish that is almost five times better, as the surface scans of FIGS. 5-9 indicate. More specifically, for uncoated L-bracket dies, FIG. 5 and FIG. 6 had ranges between +300 microinches R.sub.a and 300 microinches R.sub.a, while FIG. 7 had a range between +250 microinches R.sub.a and 250 microinches R.sub.a. For coated L-bracket dies, FIG. 8 had a range between +1,000 microinches R.sub.a and 1,200 microinches R.sub.a and FIG. 9 had a range between +1,200 microinches R.sub.a and 1,300 microinches R.sub.a, demonstrating a significantly rougher finish than the uncoated die results. Accordingly, the surface roughness of castings obtained by the method and alloys of the present application is 500 microinches R.sub.a or better.

(30) Accordingly, by removing the coating from the dies in permanent mold casting while improving mechanical properties, the present application improves the surface aesthetics of permanent mold casting and also the ability of the casting to be extracted from the mold with low forces. The later characteristic allows the low pressure permanent casting process in accordance with the present application to be fully automated as a lower cost casting process, which is not possible with a coating because of the non-chemical sticking issue. This is all possible because a permanent mold casting alloy with die soldering resistance provided by low levels strontium, instead of high levels of iron and manganese, is utilized. When iron and manganese are used for die soldering resistance at bulk levels of 0.6% and 0.8% in structural aluminum die casting, and at 1.0% or more in conventional high pressure die casting, compounds containing these elements that decrease ductility and impact properties are visible in the microstructure. At the slower cooling rates of permanent mold casting, the iron and manganese compounds grow larger than in die casting and are more damaging to mechanical properties. By contrast, adding strontium at 0.05% to 0.08% does not result in visible compounds containing strontium in the microstructure, and so is the ideal element to provide die soldering resistance in low pressure permanent mold casting without a coating on the dies. Moreover, by removing the coating from the permanent mold dies, the casting cools faster, increasing the high mechanical properties of permanent mold castings to an even higher degree and the cycle time, which thereby reduces the manufacturing cost of permanent mold casting.

(31) Eight inch long by inch width, flat full thickness bars ( inch thickness), and half thickness bars ( inch thickness), with one-side [i.e., the 8 by inch side] containing the as cast surface, were cut out of the L-brackets exhibited in FIGS. 1 and 2 for testing as cast mechanical properties. The as cast mechanical properties of these two types of tensile specimens with a 2 gauge length in alloy 367 are listed in Table 4, below.

(32) TABLE-US-00004 TABLE 4 0.2% Yield UTS UTS Offset Strength Elongation Quality Sample [ksi] [MPa] ksi MPa [%] Index Full Flat 29.6 204 14.84 102 6.03 321 MPa Uncoated Dies Full Flat 22.7 157 14.77 102 2.10 205 MPa Coated Dies One sided- 27.8 192 14.90 103 4.47 289 MPa Skin Flat Uncoated Dies One sided- 27.1 187 15.20 105 4.40 283 MPa Skin Flat Coated Dies Averaging 28.7 198 14.87 103 5.25 306 MPa all Uncoated Dies Averaging 24.9 172 14.99 103 3.35 250 MPa all Coated Dies

(33) Both the Full Flat samples and One-side Skin Flat samples had higher UTS, elongation and quality index values for Uncoated Dies than for Coated Dies. The average of the averages indicates that uncoated dies produce a 15% higher UTS, equal yield strength, 57% higher elongation and 22% higher quality index [where the quality index =UTS [in MPa]+150 log(elongation)] than coated dies.

(34) In addition to the above, six round tensile bars (0.5 in diameter and 2 gauge length) each were cut out of the as cast 1 inch thick set sections of FIGS. 1 and 2. The mechanical properties are listed in Table 5.

(35) TABLE-US-00005 TABLE 5 TENSILE PROPERTIES OF ROUND SAMPLE Ultimate Tensile 0.2% Offset Yield Elongation Sample Stress (km) Strength (ksi) (%) Coated Mold 1 23.25 13.92 2.59 Coated Mold 2 23.6 14.229 2.6 Coated Mold 3 23.16 14.236 2.54 Coated Mold 4 23.54 14.199 2.6 Coated Mold 5 22.68 13.832 2.26 Coated Mold 6 24.18 14.657 2.47 Polished Mold 1 23.37 14.085 2.28 Polished Mold 2 23.93 14.163 2.49 Polished Mold 3 24.32 14.271 2.58 Polished Mold 4 24.63 14.395 2.98 Polished Mold 5 24.56 14.24 2.92 Polished Mold 6 23.77 14.344 2.37 Average Coated 23.40 14.18 2.51 Average Polished 24.10 14.25 2.60

(36) Using the Student's t-analysis, it was determined that the calculated t-value for the ultimate tensile stress was 2.418. The table t-value for the data in Table 5 for the degrees of freedom=6+62=10 is 2.228. Thus, since the calculated t value of 2.418 is greater than the table value of 2.228 for 10 degrees of freedom, we conclude that the probability of selecting from two populations with identical means and identical standard deviations is considerably less than 5%, indicating that this result is statistically significant. Accordingly, the difference between use of uncoated dies versus coated dies is sufficient to warrant the conclusion that the uncoated dies provide better mechanical properties.

(37) The average mechanical properties of the tensile specimens having a 0.5 diameter and 2 gage length obtained from the L-brackets with and without a coating on the dies are listed in Table 6 for alloy 367 (9.1% by weight Si, 0.06% by weight Sr, 0.20% by weight Fe, 0.13% by weight Cu, 0.31% by weight Mn, 0.49% by weight Mg). The Student-t test indicates the relative ultimate tensile strengths with and without a coating are significant at the 5% level of significance for both the T61 and T62 heat treatments. Conversely, only the relative yield strength with and without a coating for the T62 heat treatment is significant at the 5% level of significance. Thus, strength properties appear to be higher when the coating is removed.

(38) TABLE-US-00006 TABLE 6 MECHANICAL PROPERTIES OF ALLOY 367 MADE WITH AND WITHOUT A COATING Alloy and heat treatment UTS Yield Strength Elongation Quality Index 367-T61 with a 330 MPa (47.9 ksi) 255 MPa (37.0 ksi) 7.0% 457 MPa coating 367-T61 without 340 MPa (49.3 ksi) 260 MPa (37.7 ksi) 7.3% 469 MPa a coating 367-T62 with a 345 MPa (50.0 ksi) 290 MPa (42.1 ksi) 5.1% 451 MPa coating 367-T62 without 355 MPa (51.5 ksi) 300 MPa (43.5 ksi) 5.3% 463 MPa a coating

(39) These same mechanical properties were measured for alloy 362 (11.5% by weight Si, 0.07% by weight Sr, 0.41% by weight Fe, 0.10% by weight Cu, 0.69% by weight Mg) and an off spec 319 alloy (4.5% by weight Si, 0.05% by weight Sr, 0.45% by weight Fe, 3.9% by weight Cu, 0.40% by weight Mn, 0.14% by weight Mg) with similar results in Table 7, but the five specimen averages were from extracted bars from five separate L-bracket seats each, where the surfaces of the bars had the as cast surface of the L-bracket. Both the faster cooling rate and the smoother surface finish contributed to the higher mechanical properties for samples when the coating was removed.

(40) TABLE-US-00007 TABLE 7 MECHANICAL PROPERTIES OF ALLOYS 362 & 319 MADE WITH & WITHOUT A COATING Alloy and heat treatment YTS Yield Strength Elongation Quality Index 362-T6 with a 310 MPa (45.0 ksi) 240 MPa (34.8 ksi) 6.0% 427 MPa coating 362-T6 without a 320 MPa (46.4 ksi) 250 MPa (36.3 ksi) 6.4% 441 MPa coating 319-T6 with a 260 MPa (37.7 ksi) 180 MPa (26.1 ksi) 3.0% 300 MPa coating 319-T6 without a 270 MPa (39.2 ksi) 190 MPa (27.6 ksi) 3.5% 322 MPa coating

(41) Referring now to FIGS. 10 and 11, low pressure permanent mold castings were made without a coating on the dies for a gear case housing with an integral splash plate. Both of these parts have a thin walled section perpendicular to a thick walled section, and demonstrate that a complex part configuration may be made in low pressure permanent mold without a coating on the dies. FIGS. 10 and 11 are a 35 lb. gear case housings with a thin integral splash plate made in low pressure permanent mold casting process without a coating on the dies. FIGS. 12 and 13 are similar gear cast housings with a thin integral splash plate made in low pressure permanent mold with a conventional coating on the dies and it is evident the casting surface finish is rougher and duller in color, when compared to the gearcase housings in FIGS. 10 and 11 made without a coating. Taking the coating off the dies, which was conventionally expected to extract massive amounts of heat from the molten metal during the quiescent slow filling of the low pressure permanent mold casting process, unexpectedly did not hinder filling of the dies, even the thin narrow sections perpendicular to thicker sections, before solidification starts. Conventionally the industry was discouraged even from trying to remove the die coating because die soldering was expected. Indeed, this is an issue with the current permanent mold casting process, where segments of the coating that spall off dies have to be recoated to avoid expected die soldering. Because of this expected die soldering problem when coating segments spall off the dies, one of ordinary skill in the art would not purposely remove all of the coating.

(42) Again, it is the strontium that functions at ten times lower concentrations than either iron or manganese and provides die soldering resistance equivalent or better than iron or manganese, permitting a manganese range of 0.25-0.35% by weight and requiring an iron content below 0.45% to avoid the precipitation of primary intermetallics that makes this new innovative uncoated permanent mold die process workable.

(43) Accordingly, a method for low pressure permanent mold casting of metallic objects is disclosed. The method contemplates preparing a permanent mold casting die that is devoid of die coating or lubrication along the die casting surface. The need for a mechanically bonded barrier coating on the steel permanent mold die for protection from die soldering by the molten alloy is simply not needed with the present application. Further, the absence of such mechanically bonded barrier coatings also cause the absence of thermal insulation, reducing the cycle time of the solidification process. The method next contemplates preparing a permanent mold casting alloy. Permanent mold casting alloy, in one embodiment, consists essentially of 4.5-11.5% by weight silicon; 0.005-0.45% by weight iron; 0.20-0.40% by weight manganese; 0.045-0.110% by weight strontium; and the balance aluminum. In another embodiment, the alloy further consists of 0.05-5% by weight copper. In yet another embodiment, the alloy further consists of 0.10-0.70% by weight magnesium. In yet another embodiment, the alloy further consists of 0.50% by weight maximum nickel, in still another embodiment the alloy further consists of 4.5% by weight maximum zinc. In yet another embodiment, the alloy may be an aluminum permanent mold casting alloy consisting essentially of 4.2-5% by weight copper; 0.005-0.15% by weight iron; 0.20-0.50% by weight manganese; 0.15-0.35% by weight magnesium; 0.045-0.110% by weight strontium; 0.05% by weight maximum nickel; 0.10% by weight maximum silicon; 0.15-0.30% by weight titanium; 0.05% by weight maximum tin; 0.10% by weight maximum zinc; and the balance aluminum.

(44) The method of the present application contemplates pushing the prepared alloy into the permanent mold casting die under low pressure to create a permanent mold casting. The pressure may be in the range of 3-15 psi. Next, the method contemplates cooling the permanent mold casting, and removing the permanent mold casting from the die. In certain embodiments, a step of heat treating the casting is added after the step of removing the casting from the die. The method of the present invention contemplates a low pressure permanent mold casting process without coating or lubrication on the die. Since the coating of lubrication is not present, the cast product does not adhere or stick to the die it may be removed with low force. This permits the method of the present application to be fully automated, because human intervention is not needed to add the coating or to remove the casting from the die. Accordingly, one or more of the steps of preparing a permanent mold casting die, preparing an alloy, pushing the alloy into the permanent mold die, cooling the permanent mold casting, heat treating the casting, or removing the casting from the permanent mold die may be fully automated. In certain embodiments, the entire method is fully automated, while in other embodiments selected steps are automated.

(45) When the method of the present application is utilized, the permanent mold casting does not solder to the permanent mold die. Moreover, the surface roughness of the casting is 500 microinches R.sub.a or less. Further, the step of cooling the permanent mold casting contemplates solidifying the alloy without the formation of primarily intermetallics such as Al.sub.5FeSi or AL.sub.15(MnFe).sub.3Si.sub.2. The method may be used to create simple or complex permanent mold castings. As previously noted, the method may be used to create L brackets or gear case housings with integral splash plates.

(46) In the instance where the present method is used to create complex castings, such as castings having at least one thin walled section, the step of pushing the alloy into the permanent mold casting die includes pushing the alloy into the thin walled sections before the alloy solidifies.

(47) In the present disclosure, certain terms have been used for brevity, clearness and understanding. No unnecessary limitations are to be inferred therefrom beyond the requirement of the prior art because such terms are used for descriptive purposes only and are intended to be broadly construed. The different apparatuses described herein may be used alone or in combination with other apparatuses. Various equivalents, alternatives and modifications are possible within the scope of the appended claims. Each limitation in the appended claims is intended to invoke interpretation under 35 U.S.C. 112, sixth paragraph only if the terms means for or step for are explicitly recited in the respective limitation.