Method for producing an aluminum alloy casting

Abstract

A method for manufacturing an aluminum alloy casting includes obtaining the aluminum alloy casting by casting an aluminum alloy into a mold, performing solution heat treatment, rapidly cooling the casting, performing aging treatment, and cooling the casting. The aluminum alloy includes, in terms of mass ratios, 4.0 to 7.0% of Si, 0.5 to 2.0% of Cu, 0.25 to 0.5% of Mg, no more than 0.5% of Fe, and no more than 0.5% of Mn, and at least one component selected from the group consisting of 0.002 to 0.02% of Na, 0.002 to 0.02% of Ca and 0.002 to 0.02% of Sr, a remainder being Al and inevitable impurities. An internal combustion engine cylinder head is composed of the aluminum alloy casting and manufactured by the method of the casting. The aluminum alloy casting is suitable for applications requiring superior elongation, high cycle fatigue strength and high thermal fatigue strength.

Claims

1. A method for manufacturing an aluminum alloy casting, comprising: obtaining the aluminum alloy casting by casting aluminum alloy into a metal mold with rapid cooling during solidification, the aluminum alloy comprising: in terms of mass ratios, 4.0 to 7.0% of Si, 0.5 to 2.0% of Cu, 0.25 to 0.5% of Mg, no more than 0.5% of Fe, no more than 0.07% of Mn, and 0.002 to 0.02% of Sr, a remainder being Al and inevitable impurities, wherein the Mn is present as an intentional addition, performing solution heat treatment such that the aluminum alloy casting is held at a temperature of 500 to 550 degrees Celsius for 2.0 to 8.0 hours, after performing solution heat treatment, rapidly cooling the aluminum alloy casting, performing aging treatment such that the aluminum alloy casting is held at a temperature of 190 to 250 degrees Celsius for 2.0 to 6.0 hours, and after performing aging treatment, cooling the aluminum alloy casting.

2. The method of claim 1, wherein, in terms of mass ratios, the aluminum alloy comprises 0.5 to 1.3% Cu.

3. The method of claim 1, wherein, in terms of mass ratios, the aluminum alloy comprises 0.3 to 0.4% Mg.

4. The method of claim 1, wherein a ratio of Fe:Mn is 1:1 to 2:1.

5. A method for manufacturing a cylinder head for an internal combustion engine, wherein the cylinder head comprises the aluminum alloy casting produced by the method of claim 1 and the method comprises: providing, in the cylinder head, a combustion chamber having a surface that comprises the aluminum alloy, and solidifying the cylinder head with rapid cooling during casting, wherein a spacing between dendrite arms of the aluminum alloy casting is not more than 30 μm so as to preserve a thermal fatigue strength of the cylinder head.

6. A method for manufacturing an aluminum alloy casting, comprising: obtaining the aluminum alloy casting by casting aluminum alloy into a metal mold with rapid cooling during solidification, the aluminum alloy comprising: in terms of mass ratios, 4.0 to 7.0% of Si, 0.5 to 2.0% of Cu, 0.25 to 0.5% of Mg, no more than 0.5% of Fe, no more than 0.07% of Mn, and 0.002 to 0.02% of Sr, and at least one component selected from the group consisting of 0.005 to 0.2% of Ti, 0.005 to 0.2% of B and 0.005 to 0.2% of Zr, a remainder being Al and inevitable impurities, wherein the Mn is present as an intentional addition, performing solution heat treatment such that the aluminum alloy casting is held at a temperature of 500 to 550 degrees Celsius for 2.0 to 8.0 hours, after performing solution heat treatment, rapidly cooling the aluminum alloy casting, performing aging treatment such that the aluminum alloy casting is held at a temperature of 190 to 250 degrees Celsius for 2.0 to 6.0 hours, and after performing aging treatment, cooling the aluminum alloy casting.

7. The method of claim 6, wherein, in terms of mass ratios, the aluminum alloy comprises 0.5 to 1.3% Cu.

8. The method of claim 6, wherein, in terms of mass ratios, the aluminum alloy comprises 0.3 to 0.4% Mg.

9. The method of claim 6, wherein a ratio of Fe:Mn is 1:1 to 2:1.

10. A method for manufacturing a cylinder head for an internal combustion engine, wherein the cylinder head comprises the aluminum alloy casting produced by the method of claim 6 and the method comprises: providing, in the cylinder head, a combustion chamber having a surface that comprises the aluminum alloy, and solidifying the cylinder head with rapid cooling during casting, wherein a spacing between dendrite arms of the aluminum alloy casting is not more than 30 μm so as to preserve a thermal fatigue strength of the cylinder head.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a graph showing influences of a Si content and a Cu content, which are given to a generated amount of casting defects, as results of a shrinkage test for a casting aluminum alloy.

(2) FIG. 2 shows high cycle fatigue strength, fracture elongation and hardness Rockwell B-scale (HRB) of test pieces.

(3) FIG. 3 shows high cycle fatigue strength, fracture elongation, and hardness Rockwell B-scale (HRB) of test pieces.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

(4) A description will be made below in detail of a casting aluminum alloy of the present invention and an aluminum alloy casting made of the alloy together with limitation reasons such as alloy components and heat treatment conditions, functions thereof, and the like. Note that, in this specification, “%” represents a mass percent unless otherwise specified.

(5) (1) Si Content: 4.0 to 7.0%

(6) Si (silicon) has a function to enhance castability. Accordingly, in the case of casting an article, such as a cylinder head, having a complicated shape and a thin-walled portion, it is necessary to add some amount of Si to the article from a viewpoint of fluidity of molten metal (molten aluminum alloy), that is, moldability of a casting. Specifically, if a Si content is less than 4.0%, then the fluidity of the molten aluminum alloy becomes insufficient. Moreover, a semisolid region is spread, shrinkage cavities are dispersed to cause porosities, and a shrink breakage becomes prone to occur. Moreover, Si has a function to enhance a mechanical strength, abrasion resistance and vibration resistance of a casting material.

(7) However, as the Si content is increased, thermal conductivity and ductility of the alloy are decreased, leading to a deterioration of thermal fatigue properties. If the Si content exceeds 7.0%, then elongation of the alloy is decreased significantly, and moreover, the alloy begins to exhibit a tendency to concentrate the shrinkage cavities. Accordingly, an occurrence of porous cavities is sometimes seen.

(8) FIG. 1 is a graph showing results of a shrinkage test. Specifically, FIG. 1 shows results, each of which is of measuring a casting defect rate from a difference between a standard specific gravity of the alloy and a specific gravity of a bottom center of a test piece, which was measured by the Archimedean method when the test piece was cast into a conical shape. From this graph, it is understood that casting defects (sum of the porosities and the porous cavities) become the minimum when the Si content is 4.0 to 7.0%, and in addition, an amount of the casting defects is reduced as a Cu content becomes smaller.

(9) Note that it is more preferable that the Si content be within a range of 5.0 to 7.0%.

(10) (2) Cu Content: 0.5 to 2.5%

(11) Cu (copper) has an effect to enhance the mechanical strength of the aluminum alloy. This effect becomes significant when a Cu content becomes 0.5% or more. However, as the Cu content is increased, the thermal conductivity and ductility of the alloy are decreased, leading to the deterioration of the thermal fatigue properties. Moreover, as the Cu content is increased, a coagulation form of the alloy becomes like mush, and the shrinkage cavities are dispersed to cause the porosities.

(12) As apparent from FIG. 1, if the Si content is unchanged, then the amount of casting defects is increased as the Cu content is increased, and adverse effects from such an increase of the Cu content become significant by the fact that the Cu content exceeds 2.5%. Accordingly, the Cu content is set within a range of 0.5 to 2.5%, more preferably within a range of 0.8 to 1.3%.

(13) (3) Mg: 0.25 to 0.5%

(14) If Mg (magnesium) is added to the alloy, then the alloy exhibits a tendency to increase a tensile strength and hardness by being subjected to heat treatment, and to decrease a thermal fatigue strength and elongation thereby. If Mg is added excessively, then Mg is precipitated as Mg.sub.2Si to decrease the thermal fatigue strength and the elongation. Accordingly, an added amount of Mg is set within a range of 0.25 to 0.5%, more preferably within a range of 0.3 to 0.4%.

(15) By setting the added amount of Mg within the above-described range, a matrix of the alloy is strengthened by aging precipitation of an inter mediate phase of Mg.sub.2Si. Meanwhile, if the Mg content exceeds 0.5%, then a surface oxidation amount of the molten aluminum alloy is significantly increased to cause a malfunction that inclusion defects are increased.

(16) (4) Fe: 0.5% or Less

(17) Fe (iron) is precipitated as a needle-like iron compound, and in general, adversely affects the tensile strength, the fatigue strength, the they dial fatigue strength, the elongation, and the like. Accordingly, an upper limit value of a Fe content is set at 0.5%.

(18) Note that, since Fe is a harmful component as described above, a smaller content thereof is desirable. It is preferable that the Fe content be set at 0.2% or less. Moreover, it is ideal Fe content be substantially 0%.

(19) (5) Mn: 0.5% or Less

(20) By adding Mn (manganese) to the alloy, a shape of such a crystallized object containing Fe can be changed from the needle shape that is prone to bring up the decrease of the strength to a massive shape that is less likely to cause a stress concentration.

(21) If a Mn content is larger than necessary, then an amount of the iron compound (Al—Fe, Mn—Si) is increased. Accordingly, the Mn content is set at 0.5% or less, desirably 0.2% or less. Note that a ratio of Fe:Mn becomes preferably 1:1 to 2:1.

(22) (6) One or More of Na, Ca and Sr: 0.002 to 0.02% Per Each

(23) In particular, with regard to a material of the cylinder head, in order to enhance thermal fatigue resistance thereof, it is desirable that one or more of these components (Na, Ca and Sr) be added to the alloy, thereby microfabricating Si particles in a cast texture.

(24) By the improvement treatment for the Si particles, mechanical properties of the alloy, such as the tensile strength and the elongation, are enhanced, and the thermal fatigue strength is also enhanced. However, if the above-described components are added in large amounts, then a region occurs, where a band-like coarse Si phase is crystallized. Such an occurrence of the coarse Si phase is called overmodification, and sometimes results in the decrease of the strength. Accordingly, in the case where these components described above are added to the alloy, a content of each thereof is set within a range of 0.002 to 0.02%. Note that, for a surface of a combustion chamber, where the thermal fatigue strength is an important subject, it is desirable that the alloy be rapidly cooled and coagulated, thereby reducing dendrite arm spacing to 30 μm or less.

(25) (7) One or More of Ti, B and Zr: 0.005 to 0.2% Per Each

(26) Each of these components (Ti, B and Zr) is an effective component for microfabrication of crystal particles of the cast texture, and accordingly, is added to the alloy according to needs within a range of 0.005 to 0.2%. Moreover, these components are added in a component range where the amount of the casting defects is large, whereby the porous cavities are dispersed, and the shrinkage cavities are removed.

(27) In the case where the added amount of each of these components is less than 0.005%, no effect is brought up. In the case where the added amount exceeds 0.2%, Al—Fe, Al—B, Al—Zr, TiB, ZrB and the like, which become cores of the crystal particles, are coagulated, whereby a risk of causing the defects is increased.

(28) (8) T7 Treatment (Solution Heat Treatment, and then Stabilization Treatment)

(29) Solution heat treatment: rapid cooling after holding at 500 to 550° C. for 2.0 to 8.0 hours

(30) Aging treatment: air cooling after holding at 190 to 250° C. for 2.0 to 6.0 hours

(31) Usually, in order to enhance the strength, the cylinder head is subjected to T6 treatment (solution heat treatment, and then artificial aging treatment) or T7 treatment. In the present invention, though being slightly inferior in strength to the T6 treatment, the T7 treatment (solution heat treatment, and then stabilization treatment) is performed since the enhancement of the thermal fatigue strength, the reduction of the residual stress, and the dimensional stability, which are necessary for the cylinder head, are obtained.

(32) Specifically, the casting aluminum alloy of the present invention, which has the above-described component composition, is subjected to the solution heat treatment under conditions where the temperature is 500 to 550° C. and the treatment time is 2.0 to 8.0 hours, and to the aging treatment under conditions where the temperature is 190 to 250° C. and the treatment time is 2.0 to 6.0 hours.

(33) By the T7 treatment as described above, there can be obtained 50 HRB as hardness necessary from a viewpoint of preventing permanent set in fatigue of a seating surface of a head bolt and a gasket seal surface and ensuring abrasion resistance on a fastening surface of the cylinder head with a cylinder block, a sliding portion of a camshaft, and the like.

(34) When the time of the solution heat treatment is ensured sufficiently, eutectic Si comes to have a roundish shape by diffusion, whereby the stress concentration is relieved, and the mechanical properties such as the ductility will be improved.

Examples

(35) The present invention will be described below more in detail based on examples; however, the present invention is not limited to these examples.

(36) (1) Boat-Like Sample Casting Test

(37) Aluminum alloys with compositions shown in FIG. 2 were molten by an electric furnace, and were subjected to the microfabrication treatment and the Si improvement treatment, and thereafter, boat-like samples with dimensions of 190×40×25 mm were cast. Then, the boat-like samples were subjected to the T7 treatment (solution heat treatment at 530° C. for 5 hours, and then aging treatment at predetermined temperature between 180 to 260° C. for 4 hours). Thereafter, fatigue test pieces and tensile test pieces were cut out of the treated boat-like samples. For each of the test pieces, the high cycle fatigue strength and the fracture elongation were measured, and the hardness Rockwell B-scale (HRB) was measured.

(38) Results of these are shown in FIG. 2 in combination. With regard to target values of these, a target value of the high cycle fatigue strength is set at 100 MPa or more, a target value of the elongation as the alternative properties of the thermal fatigue strength is set at 10.0% or more, and a target value of the hardness is set at 50 HRB or more.

(39) Note that, in the high cycle fatigue test, an Ono-type rotating bending fatigue test machine was used, and the number of revolutions thereof was set at 3600 rpm. Then, the fatigue strength of each test piece was evaluated based on a stress amplitude value when the number of repeated bending cycles up to the fracture was 10.sup.7 times.

(40) As apparent from FIG. 2, in Examples 1 to 9 where the test pieces contained the alloy components with mass percents of the predetermined ranges and were subjected to the T7 treatment at the aging temperatures of 200 to 240° C., it was confirmed that the test pieces exhibited good performance in all of the high cycle fatigue strength, the fracture elongation and the hardness.

(41) As opposed to this, in Comparative examples 1 to 10 where the alloy components and the aging temperatures went out of the ranges defined by the present invention, and in Conventional materials 1 and 2 using the AC4CH alloy and the AC2A alloy, which have been used as the conventional cylinder head material, it was found out that at least one of the properties, that is, the fatigue strength, the fracture elongation and the hardness, was low in each test piece thereof, whereby it was impossible to obtain such strength as meeting requirements for a cylinder head material of a high-performance engine.

(42) (2) Cylinder Head Casting Test

(43) The alloys showing relatively good performance in the boat-like sample casting test were chosen from the above described Examples and Comparable Examples. Then, actual bodies of the cylinder heads of the alloys chosen were cast in a metal die, and were subject to the T7 treatment corresponding to that in the boat-like sample casting test. Thereafter, fatigue test pieces and tensile test pieces were cut out of positions of the cylinder heads cast and treated, which were in the vicinities of the surfaces of the combustion chambers, and were subjected to measurements of the high cycle fatigue strength and the fracture elongation in a similar way to the above, and in addition, were subjected to measurements of the hardness Rockwell B-scale (HRB).

(44) Results of these are shown in FIG. 3. With regard to target values in this case, a target value of the high cycle fatigue strength is set at 85 MPa or more, and a target value of the hardness is set at 50 HRB or more.

(45) Moreover, with regard to the thermal fatigue strength, a simple thermal fatigue test in which a temperature cycle was set as 40° C.-270° C.-40° C. was carried out under completely restrained conditions by using flat test pieces added with V notches, and a target value of results of the simple thermal fatigue strength was set at no less than 100 that is a thermal fatigue lifetime of a TIG-remolten article from the conventional AC2A alloy.

(46) As apparent from the results shown in FIG. 3, also in the castings of the actual bodies of the cylinder heads, it was confirmed that the test pieces in Examples 2-2 and 6-2 corresponding to Examples 2 and 6 of the boat-like sample casting test exhibited good performance in the high cycle fatigue strength, the thermal fatigue lifetime and the hardness, and met, at a high level, the properties required for the cylinder head.

(47) As opposed to this, though relatively good evaluation results were obtained by the boat-like samples in Comparative examples 4-2 and 8-2 corresponding to Comparative examples 4 and 8 of the boat-like sample casting test, the fatigue strength and the thermal fatigue lifetime were decreased in Comparative example 4-2 owing to an influence of the casting defects, which did not appear in the boat-like samples, since the actual body of the cylinder head was thick-walled.

(48) Meanwhile, with regard to Comparative example 8-2 where the target value was almost achieved in the boat-like sample casting test, the strength thereof was also low in the actual body test. This is considered to be because Si was not improved by Sr.