Heat- and abrasion-resistant aluminium alloy and retainer and valve lifter formed therefrom

Abstract: A heat- and abrasion-resistant aluminum alloy disclosed comprises; the grain size of the matrix of α-aluminum in the alloy is not more than 1,000 nm; the grain size of an intermetallic compounds contained in the alloy is not more than 500 nm; and 0.5 to 20% by volume of ceramics particle being in the range of 1.5 to 10 µm in particle size is dispersed in the alloy. By the composition, the stress concentration due to the ceramics particles is reduced. Furthermore, because powders bind well with each other, the heat resistance and abrasion resistance are compatibly improved without decreasing toughness and ductility.

Description: BACKGROUND OF THE INVENTION Field of the Invention The present invention relates to a heat- and abrasion-resistant aluminum alloy and a spring retainer and a valve lifter formed from the alloy. Description of the Related Art In recent years, various aluminum alloys with improved heat resistance and mechanical strength has been developed. A known method of producing a heat resistant aluminum alloy employs the technique of forming quenched powder followed by extrusion and so forth for the purpose of improving heat resistance. Although this kind of alloy offers high heat resistance, this does not always offer good abrasion resistance. On sliding characteristics, the level of this alloy is very similar to conventional aluminum alloys at the present stage. The plausible surface hardening methods such as plating involve complex processing, resulting in increased production costs. An aluminum alloy with relatively high abrasion resistance and mechanical strength is disclosed, for example, in JP-A-2-285043 entitled " An Al-Si alloy powder forging material with extremely low thermal expansion coefficient". The aluminum alloy contains 35 to 45% by weight of primary crystal Si with particle size of 2 to 15 µm and 5 to 20% by volume of aluminum oxide with particle size of 5 to 20 µm. However, because aluminum oxide particles are included in the texture that relatively large size, around 10 µm, of the Si crystals are included in the alloy matrix of the order of scores of µm, the alloy has the following drawbacks with the advantage of the improved abrasion resistance; the strain is easy to concentrate under the influence of the Si crystals and aluminum oxide particles; and some defects may occurs in the material due to the inhomogeneity of the powder deformation during forming and hardening process so that the toughness and the strength after fatigue decrease. EP-A 0 487 276 discloses an aluminum-based alloy strengthened with an intermetallic Al 3 X-type phase dispersoid where X may be Nb, Ti or Zr. In addition, the alloy may contain ceramics in the form of aluminum oxides and carbides as well as 1-3% Si as another strengthener. The average grain size of the intermetallic particles is stated to be 25 nm to 250 nm whereas there is no mention of the particle size of the ceramics nor is there any indication that a size restriction of those latter particles may have any advantageous effect on the properties of the alloy. SUMMARY OF THE INVENTION The inventors has investigated the study of aluminum alloys under the knowledge that the particle size and the composition of the ceramics are essential features for the improvement in the alloy. During the investigation, an aluminum alloy, which offers the compatibility between heat resistance and abrasion resistance and does not cause the decrease of toughness, was satisfactorily found by means of the optimization of the texture in the alloy matrix and the selection of an optimum particle size of the ceramics added in the matrix. An object of the present invention is to provide a heat-and abrasion-resistant aluminum alloy comprising: matrix of α-aluminum contained in the alloy and having grain size not more than 1,000 nm; intermetallic compounds contained in the alloy and having grain size not more than 500 nm; and 0.5 to 20% by volume of ceramics particles dispersed in the alloy and having particle size in the range of 1.5 to 10 µm. The alloy composition without the ceramics particles is Al bal TM a X b , wherein TM is one or two elements selected from the group of Fe and/or Ni; and X is at least one element selected from the group of Ti, Zr, Mg and rare earth elements, and a and b in atomic percentage are 4≤a≤7, and 0.5≤b≤3, respectively. A further object of the present invention is to provide a heat- and abrasion-resistant aluminum alloy with improved workability by limiting the ceramics particle content to 0.5 to 8% by volume. Yet another object of the present invention is to provide an aluminum alloy as defined above but having a composition of Al bal TM a X b Si c , wherein TM is one or two elements selected from the group of Fe and/or Ni, and X is at least one element selected from the group of Ti, Zr, Mg and rare earth elements; and a, b, and c in atomic percentage are 4≤a≤7, 0.5≤b≤3 and 1≤c≤3, respectively. The ceramics particles according to the invention are preferably non-spherical with an oval like cross section. Still another object of the present invention is to provide a heat- and abrasion-resistant valve spring retainer and a valve lifter, both formed from the aluminum alloy of the invention. BRIEF DESCRIPTION OF THE DRAWINGS The details of the invention will now be described having reference to the accompanying drawings, in which: Fig. 1 is a TEM (Transmission Electron Microscope) photograph showing a texture of Example 2 in the invention; Fig. 2 is a optical microscope photograph showing a texture of Example 2 in the invention; Fig. 3 is a SEM (Scanning Electron Microscope) photograph of Al 2 O 3 particles mixed into the matrix for the preparation of the test piece in Example 25 in the invention; Fig. 4 is a SEM photograph of Al 2 O 3 particles mixed into the matrix for the preparation of the test piece in Example 26 in the invention; Fig. 5 is a SEM photograph showing the texture of the test piece in Example 25 in the invention; Fig. 6 is a SEM photograph showing the texture of the test piece in Example 26 in the invention; and Fig. 7 depicts the cross section showing an OHC (Overhead Camshaft) striking valve motion mechanism. DESCRIPTION OF THE PREFERRED EMBODIMENTS The details of the examples according to the invention will now be explained but these examples are only for illustration and should not be construed as limiting the invention. EXAMPLE 1 to 6 and COMPARATIVE EXAMPLE 1 to 5 Test pieces were prepared based on the following procedure in order to carry out various tests. Preparation of green compact The alloy having the composition of Al 91 Fe 6 Ti 1 Si 2 (where suffix means atomic percent) was air-atomized and classified to 45 µm or less. Al 2 O 3 particles having average diameter of 3.5 µm were added into the alloy in quantity of 0 to 35 volume percent and the compound was mixed thoroughly. Then, a green compact billet of 55 mm in outer diameter by 55 mm in length was prepared from the mixture by CIP (Cold Isostatic Pressing) under the pressure of 4 ton/cm 2 . Degassing of green compact The green compact prepared was placed into a muffle furnace at 530 °C and allowed to degas for 15 minutes in argon atmosphere. Extrusion The test piece was prepared based on the following indirect extrusion conditions: Inner diameter of container 56 mm Container temperature 400 °C Bore diameter of dice 15 mm Dice temperature 400 °C Extruding speed 0.5 to 1.0 m/sec Observation of texture in test piece Fig. 1 is a TEM (Transmission Electron Microscope) photograph showing the texture of the sample of Example 2 of the invention. Bright large objects mean α-aluminum matrix grains (fcc grains), and their size is measured as 500 nm on average with the scale indicated at the lower light of the photograph. Dark fields in the photograph are intermetallic compounds (IMC) having average diameter of 200 nm. No ceramics particle is found in the photograph. The average sizes of the fcc grains and the IMC grains were determined by measuring each 50 particles which were selected at random in the TEM photograph. Fig. 2 is an optical photograph at 200 magnifications, in which the scale is indicated at the lower right, showing the texture of Example 2 of the invention. Although it may be difficult to distinguish between the fcc grains and the IMC, black dots having a few µm of diameter represent ceramics particles. The grain and particle sizes in each sample of Examples and Comparative Examples were based on the above procedure. Each sample was used for the following tests. Tensile test at high temperature The test was carried out at 200 °C. Charpy impact test A smooth test piece without notch was used for Charpy impact test. Sliding abrasion test The amount of abrasion was determined by the sliding test based on the following conditions: Test piece Formed to 10 mm by 10 mm by 5 mm Rotating disc Silicon-Chromium steel 135 mm in diameter (JIS SWOSC- carburizing steel) Sliding speed 25 m/sec Sliding pressure 200 kg/cm 2 Lubricant feed speed 5 cc/sec sliding distance 18 km Amount of abrasion Reduced thickness in µm The test results are shown in Table 1 below. NO Al 2 O 3 (vol%) Tensile Strength (MPa) Elongation at break (%) Impact Strength (J/mm 2 ) Abrasion Loss (µm) Evaluation Comparative Example 1 0 400 8.0 0.18 18.4 N.G. Comparative Example 2 0.3 398 8.1 0.18 4.0 N.G. Example 1 0.5 401 8.0 0.19 0.4 Good Example 2 1 403 7.9 0.18 0.2 Good Example 3 5 400 8.0 0.17 0.1 Good Example 4 10 405 7.7 0.16 0.1 Good Example 5 15 407 7.6 0.15 0.1 Good Example 6 20 411 7.5 0.15 0.1 Good Comparative Example 3 25 415 3.0 0.06 0.1 N.G. Comparative Example 4 30 418 3.0 0.05 0.1 N.G. Comparative Example 5 35 420 2.8 0.04 0.1 N.G. Comparative Example 1 : This sample, which does not contain Al 2 O 3 in the Al 91 Fe 6 Ti 1 Si 2 matrix, exhibits poor abrasion property. Its abrasion loss is 18.0 µm. Comparative Example 2 : Although this sample had 0.3% by volume of Al 2 O 3 added into the matrix, it demonstrates improved abrasion property but the abrasion loss of 40 µm has still a poor level. Example 1 : The sample, which contains 0.5% by volume of Al 2 O 3 in the matrix, exhibits 8.0% in elongation, 0.19 J/mm 2 in impact strength, and 0.4 µm in abrasion loss which is satisfactorily improved. Example 2 to 5 : The four samples, in which 1.0, 5.0, 10, or 15% by volume of Al 2 O 3 were added, were tested. Each sample exhibits 7.9, 8.0, 7.7, or 7.6% in elongation, and 0.18, 0.17, 0.16, or 0.15 J/mm 2 in impact strength, respectively. The abrasion loss of each sample is less than 0.2 µm and reaches highly satisfactory level. Example 6 : The sample in which 20% by volume of Al 2 O 3 were added into the matrix exhibits the properties of satisfactory level: 7.5% in elongation, 0.15 J/mm 2 in impact strength, where elongation and impact strength little decrease as compared with Example 1, and 0.1 µm in abrasion loss. Comparative Example 3 : By adding 25% by volume of Al 2 O 3 into the matrix elongation and impact strength significantly decrease as compared with Example 6; i.e. 3.0% in elongation, 0.06 J/mm 2 in impact strength. The sample is not satisfactory. Comparative Example 4 and 5 : By adding 30 or 35% by volume of Al 2 O 3 into the matrix, further decrease of elongation and impact is observed in each sample. These samples are also not satisfactory. As the above results demonstrate that excessive abrasion loss is observed in the samples containing less than 0.5% by volume of Al 2 O 3 and toughness of each sample containing over 20% by volume of Al 2 O 3 drastically decreases, 0.5 to 20% by volume of Al 2 O 3 addition is selected. EXAMPLE 7 to 10 and COMPARATIVE EXAMPLE 6 and 7 The effect of size of the added ceramics particles on the properties was examined. The amount of added Al 2 O 3 was fixed at 2.5% by volume, the particle size was varied from 1.2 to 12.0 µm in diameter. Other conditions followed Example 1. NO Al 2 O 3 Average Size (µm) Tensile Strength (MPa) Elongation at break (%) Impact Strength (J/mm 2 ) Al Alloy Abrasion Loss (µm) Disk Abrasion Loss (µm) Evaluation Comparative Example 6 1.2 402 8.2 0.18 9.1 0.1 N.G. Example 7 1.5 400 8.1 0.18 0.1 0.1 Good Example 8 3.0 401 8.2 0.18 0.2 0.1 Good Example 9 8.0 399 8.0 0.18 0.2 0.1 Good Example 10 10.0 403 8.1 0.18 0.1 0.1 Good Comparative Example 7 12.0 400 7.9 0.17 0.2 4.1 N.G. Comparative Example 6 : The use of Al 2 O 3 having average particle size of 1.2 µm in diameter causes an excessive abrasion loss, i.e. 9.1 µm, of the aluminum alloy test piece. Example 7, 8, 9, and 10 : Four samples were prepared by varying the average particle size of Al 2 O 3 to 1.5, 3.0, 8.0, and 10.0 µm in diameter, respectively. The results of abrasion loss of the aluminum alloy and the disc of each example are in the range of 0.1 to 0.2 µm, and are satisfactory. Comparative Example 7 : By varying the average particle size of Al 2 O 3 to 12.0 µm in diameter, an excessive abrasion loss of the rotating disc is unsatisfactorily observed. When the average particle size of Al 2 O 3 is less than 1.5 µm in diameter, the abrasion resistance of the aluminum alloy decreases, while the aluminum alloy containing Al 2 O 3 over 10.0 µm in average particle diameter leads to the severe abrasion loss of the counterpart. Therefore, the average size of Al 2 O 3 is preferably in the range of 1.5 to 10.0 µm in diameter. EXAMPLE 11 TO 15 AND COMPARATIVE EXAMPLE 8 TO 18 The test pieces were prepared in the following procedure and served to various tests. Preparation of green compact Four alloys having different composition, Al 93 Fe 4 Y 3, Al 92 Fe 6 Zr 2, Al 92 Ni 5 Mm 3, and Al 90 Fe 6 Ti 1 Si 2 Mg 1 (where suffix means atomic percent), were classified to not more than 45 µm after air-atomization, Al 2 O 3 particles having 2.5 µm in average diameter were added in the quantity corresponding 3.0% by volume, and the compound was mixed thoroughly in a mixer. Then, a green compact billet of 55 mm in outer diameter by 55 mm in length was prepared from the mixture by CIP (Cold Isostatic Pressing) under the pressure of 4 ton/cm 2 . Where, Mm is the abbreviation of Mischmetal which is the common name of the composite materials containing La and/or Ce as major element, other rare earth elements (Lanthanoid) except for La and Ce, and unavoidable impurities such as Si, Fe, Mg, Al and so on. Degassing of green compact Each green compact prepared was degassed in argon atmosphere under the conditions of temperature and time as shown in Table 3. Extrusion The test piece was prepared based on the following indirect extrusion conditions: Inner diameter of container 56 mm Container temperature 400 °C Bore diameter of dice 15 mm Dice temperature 400 °C Extruding speed 0.5 to 1.0 m/sec Observation of texture in test piece Through TEM (Transmission Electron Microscope) observation of the texture of the test piece, the diameter of the α-aluminum matrix grains (fcc grains) and the diameter of the intermetallic compound (IMC) are obtained and shown in Table 3. These grain diameters are the averaged measurements of 50 grains randomly selected from each of the fcc and IMC grains in the TEM photograph. The following tests have then been carried out with respect to the test piece. Tensile test at hight temperature The test was carried out at 200 °C. Charpy impact test A smooth test piece without notch was used for Charpy impact test. Sliding abrasion test The amount of abrasion was determined by the sliding test based on the following conditions: Test piece Formed to 10 mm by 10 mm by 5 mm Rotating disc Silicon-Chromium steel 135 mm in diameter (JIS SWOSC - carburizing steel) Sliding speed 25 m/sec Sliding pressure 200 kg/cm 2 Lubricant feed speed 5 cc/sec sliding distance 18 km Amount of abrasion Reduced thickness in µm The results of the tests are as shown in Table 3 below. Comparative Example 8 : This sample using Al 93 Fe 4 Y 3 matrix was degassed at the condition of temperature and time shown in Table 3. Because the matrix does not contain ceramics, Al 2 O 3 , the abrasion loss is 18 µm and extremely poor level. Example 11 : This sample, Al 93 Fe 4 Y 3 matrix containing 3.0% by volume of Al 2 O 3 , offers 0.1 µm of the abrasion loss which is satisfactory level. Comparative Example 9: This sample does not contain Al 2 O 3 like Comparative Example 8. The abrasion loss is 18 µm and extremely poor level. Comparative Example 10 : This sample containing 3% by volume of Al 2 O 3 in the sample of Comparative Example 9 offers 0.1 µm of the abrasion loss which is satisfactory level. However, the fcc particle size and IMC particle size increase to 1,100 nm, and 600 nm, respectively, compared with those size of Example 11, i.e. 1,000 nm and 500 nm, due to the change of the heating temperature from 500 °C of Example 11 to 550 °C and the heating time from 1.5 hr to 2.0 hrs. As the results, the Charpy impact test value unsatisfactorily decreases. Comparative Example 11 : In this sample, Al 92 Fe 6 Zr 2 as matrix was used instead of Al 93 Fe 4 Y 3 . Because the sample also does not contain Al 2 O 3 , the abrasion loss is 17 µm and extremely poor level. Example 12 : In this sample, Al 92 Fe 6 Zr 2 containing Al 2 O 3 was degassed at 500 °C for 1.5 hr. The fcc grain size and IMC grain size are 800 nm, and 300 nm, respectively. The result of Charpy impact test is 0.18 J/mm 2 and the abrasion loss is 0.2 µm. Both properties are maintained to satisfactory level. Similarly, because the samples not containing Al 2 O 3 of Comparative Example 12, 14, 15, 17, and 18 offer excessive abrasion loss of 16 to 18 µm, these samples are not suitable for the alloy of the invention. Although the samples of Comparative Example 13 and 16 contain 3.0% by volume of Al 2 O 3 , the fcc and IMC grain sizes in each sample are too large, and the results of Charpy impact test decrease to unsatisfactory level. On the other hand, the samples containing 3.0% by volume Al 2 O 3 of the Example 13, 14, and 15 offer excellent abrasion loss and Charpy impact test properties because of the fine fcc and IMC grain sizes in these samples. The results shown in Table 3 demonstrate that fcc grain size should be not more than 1,000 nm and IMC grain size should be not more than 500 nm in order to obtain desirable Charpy impact test and abrasion loss properties. Then, secondary formability tests were carried out. The results will be explained referring to Table 4. The test pieces having 8 mm in outer diameter and 12 mm in length as shown in the sketch of Table 4 were prepared, and upset from the top after heating to 400 °C until a crack occurs. When the critical height at the crack occurrence is h, the upsetting ratio is expressed by the equation, (h ÷ 12) × 100 (%), where 12 means the initial height. EXAMPLE 20 TO 24 AND COMPARATIVE EXAMPLE 20 TO 22 The samples shown in Table 4 are the samples upset at high temperature the same matrix as the sample shown in Table 1, except for different Al 2 O 3 volume contents. The samples of Comparative Example 20 and Example 20 to 24 offer good formability due to high upsetting ratio of more than 55%. On the other hand, the samples of Comparative Example 21 and 22 which contain more Al 2 O 3 are brittle on the whole, so that the upsetting ratios of these samples are only 25% indicating poor formability. Accordingly, preferable secondary formability will be achieved in the range of 0.5 to 8.0% by volume of Al 2 O 3 content. EXAMPLE 25 and 26 AND COMPARATIVE EXAMPLE 23 Then, the effect of the shape of the ceramics particles added were examined. Fig. 3 is a SEM (Scanning Electron Microscope) photograph of Al 2 O 3 particles which is contained in the matrix in order to prepare the test piece of Example 25 in the invention. The sample of Example 25 is the same as that of the above-mentioned Example 3. In the photograph, the shape of the Al 2 O 3 particles is almost spherical. Fig. 4 is a SEM photograph of Al 2 O 3 particles which is contained in the matrix in order to prepare the test piece of Example 26 in the invention. In the photograph, the shape of the Al 2 O 3 particles is not spherical, but the cross section is like oval. Fig. 5 is a SEM photograph (taken as a reflected electron image) of the texture of the test piece of Example 25 in the invention. The bright fields of the photograph indicating the Al 2 O 3 particles are spherical. Fig. 6 is a SEM photograph (reflected electron image) of the texture of the test piece of Example 26 in the invention. In this sample, the bright fields of the photograph indicating the Al 2 O 3 particles are not spherical, but oval, rectangular, or like a gourd. The size of Al 2 O 3 particles were defined as follows: the particle image was put between two parallel lines and these parallel lines were rotated along the edge of the image. The width was defined as the minimum interval between the parallel lines, and the length was defined as the interval between other two parallel lines which are perpendicular to the former parallel lines at the minimum interval and circumscribed with the edge of the image, the length representing the particle size. The aspect ratio means the ratio of the length to the width. The aspect ratio was determined by measuring and averaging the size of 50 Al 2 O 3 particle images in Fig. 5 and Fig. 6. The test pieces of Examples 25 and 26 have the same composition except for the shape of the ceramics added, Al 2 O 3 particles. The Al 2 O 3 particles in the sample in Example 25 are almost spherical, 3.5 µm in the average length or diameter, and 1 in the aspect ratio, while the Al 2 O 3 particles in the sample in Example 26 are like oval, 3.5 µm in average length, and 2.0 in average aspect ratio. The test piece of the Comparative Example 23 is the aluminum alloy extender defined as JIS No.2024 alloy and has the composition by weight of 4.4% of Cu, 1.5% of Mg, 0.6% of Mn, and the balance of Al. The creep tests of these samples were carried out. The creep strength was defined as the tensile stress to make the test piece 0.1% of tensile strain after 1,000 hrs at 200 °C under the predetermined tensile stress. Table 5 shows the results of the creep test as well as other properties. The samples of Example 25 and 26 show significant improvement in the creep strength, i.e. 129 and 145 MPa, respectively. The reason will be explained as follows; since the test piece of Example 25 has fine α-aluminum matrix grains in the alloy, it is basically considered that the resistance to the creep (the creep strength) is low. However, the ceramics (Al 2 O 3 ) particles in high volume content (5% in this case) which will cause not only the abrasion resistance but also heat resistance are dispersed in the matrix, therefore this sample offers better creep strength than the aluminum extender of Comparative Example 23. More effective method for further improvement in the creep strength is the addition of a hard ceramics (Al 2 O 3 ) particles which depress the slip of the above crystal particles. On the shape of the added (Al 2 O 3 ) particles, oblong shape offers a higher creep strength than spherical shape because the crystal particles are hard to slip. In general, the addition of oblong particles causes the decrease of toughness and ductility as compared with the addition of spherical particles. However, in the sample of Example 26, such disadvantages do not appear because the stress is hard to concentrate. EXAMPLE 27 AND COMPARATIVE EXAMPLE 24 An example, in which a aluminum alloy in the invention was applied to a valve spring retainer and valve lifter, especially, a valve spring retainer and valve lifter attached to the suction and exhaust valve of an engine will be explained with Table 6. Fig. 7 is the cross section showing an OHC (Overhead Camshaft) striking valve motion mechanism. The valve motion mechanism has a valve spring retainer and valve lifter which are formed from the aluminum alloy of the invention, wherein cylinder head is assigned as 1, cam to open and shut the suction and exhaust valve as 2, camshaft as 3, guide hole bored as 4 in the cylinder head 1, and striking valve lifter as 5 inserted to slide in the guide hole 4, respectively. The valve lifter 5 is made of the aluminum alloy. Furthermore, valve stem is assigned as 11, cock as 12, valve spring retainer as 13 made of the aluminum alloy, respectively. Then, the action of the valve motion mechanism will be described. In the valve motion mechanism, the camshaft 3 controls gas exchange by directly driving the suction valve 10; when the camshaft 3 rotates along the axis perpendicular to the figure, cam 2 strikes against the upper surface of the upper wall 7 of the inverted bottom cylindrical valve lifter 5, the lower surface of the upper wall 7 strikes against the top of the valve stem 11, the outer surface of the side wall 6 slides on the guide hole 4 in the cylinder head 1, and the displacement of the cam 2 transmitted to the suction valve 10 through the valve lifter 5. Consequently, the outer surface and the cam-striking surface of the valve lifter 5 require excellent abrasion resistance. Similarly, the flange part of the valve spring retainer 13 also requires excellent abrasion resistance because the valve spring 15 strikes against the flange part of the valve spring retainer 13 by the expansion and contraction of the valve spring 15 with displacement of the suction valve 10. The durability tests of the above retainer and lifter applied the above aluminum alloy were carried out. The results are shown in Table 6. Example 27 : The material containing 3.0% by volume of Al 2 O 3 in the Al 91 Fe 6 Ti 1 Si 2 matrix was prepared so that the fcc grain size is 500 nm and the IMC grain size is 200 nm. Preparation of green compact The alloy having the composition of Al 91 Fe 6 Ti 1 Si 2 (where suffix means atomic percent) was air-atomized and classified to 45 µm or less. 3.0% by volume of Al 2 O 3 particles having average diameter of 3.5 µm were added into the alloy and the compound was mixed thoroughly. Then, a green compact billet of 78 mm in outer diameter by 50 mm in length was prepared from the mixture by CIP (Cold Isostatic Pressing) under the pressure of 4 ton/cm 2 . Degassing of green compact The green compact prepared was placed into a muffle furnace at 530 °C and allowed to degas for 25 minutes in argon atmosphere. Extrusion The test piece was prepared based on the following indirect extrusion conditions: Inner diameter of container 80 mm Container temperature 400 °C Bore diameter of dice 25 mm Dice temperature 400 °C Extruding speed 0.5 to 1.0 m/sec The retainer and lifter were formed from the material by cutting with machine work, and subjected to durability test in the actual valve for 100 hours. The abrasion loss of the spring striking surface and the cam striking surface of the lifter are 11 µm and 15 µm, respectively. Comparative Example 24 : A similar test was carried out for the sample and procedure described in Example 27 except for not containing Al 2 O 3 . The abrasion loss of the retainer and the lifter drastically increase to 580 µm and 620 µm, respectively, these are quite unsatisfactory results. A forging retainer was made instead of the cutting retainer in Example 27, and tested. The satisfactory results are obtained. These results demonstrate that the aluminum alloy of the invention is preferably used for the valve retainer and valve lifter. On the action of the invention, controlling the fcc grain size of the matrix of α-aluminum and the grain size of the intermetallic compound to not more than 1 µm, in other words in the nanometer order, the stress concentration due to the intermetallic compound is reduced, and the stress concentration due to the ceramics particles is also reduced because the ceramics particles are dispersed so as to be surrounded with plural fine particles. Furthermore, on the powder molding and solidification process, grain boundary sliding among the plastic deformations of individual powder predominates due to the nanometer order texture, the inhomogeneity of the individual powder is prevented effectively, and powders well bind each other. As the results, the decreasing toughness and ductility are satisfactorily depressed. Furthermore, controlling the ceramics particle content to the low level will cause the improvement in workability. The TM (Fe or Ni) included in the aluminum alloy leads to the improvement of heat resistance. The TM content less than 4.0 atomic percent causes low strength at a high temperature, while the content more than 7.0 atomic percent offers poor toughness due to increasing intermetallic compound. X (Ti, Zr, Mg, or a rare earth element) promotes the thinning of the intermetallic compounds in the texture. The thinning can not be achieved the X content less than 0.5 atomic percent, while the content over 3.0 atomic percent causes decreasing toughness due to the formation of Al-X intermetallic compound. The addition of Si to the aluminum alloy will lead to further thinning of the texture. The Si content over 3.0 atomic percent causes decreasing toughness due to the precipitation of the primary Si crystals. In the invention, when the shape of the ceramics particle is non spherical having oval like cross section, the creep strength of the aluminum alloy will increase. Because aluminum alloy based on the invention offers excellent workability, strength at a high temperature, and abrasion resistance, the alloy is most preferably used for a valve spring retainer and valve lifter of engine. The following advantages will be provided by the above Examples in the invention; In the heat resistant and abrasion resistant aluminum alloy of the present invention, because the grain size of the matrix of α-aluminum in the alloy is not more than 1,000 nm, the grain size of intermetallic compound contained in the alloy is not more than 500 nm, and 0.5 to 20% by volume of ceramics particles being in the range of 1.5 to 10 µm in diameter are dispersed in the alloy, the stress concentration due to the added ceramics particles can be reduced. Furthermore, as the powders well bind each other on the powder molding and solidification process, heat resistance and abrasion resistance can compatibly improve without the decreasing toughness and ductility. In another Example of the present invention, the most suitable secondary workability can be achieved by limiting the ceramics particle content in the heat resistant and abrasion resistant aluminum alloy to 0.5 to 8% by volume. In yet another Example of the present invention, the heat resistant and abrasion resistant aluminum alloy containing TM (Fe and/or Ni) offer improved heat resistance, and the alloy containing X (Ti, Zr, Mg, and rare earth elements) can promotes thinning of intermetallic compound in the texture. In still another Example of the present invention, the heat resistant and abrasion resistant aluminum alloy additionally containing Si will promotes further thinning of intermetallic compound in the texture. In another Example of the invention, non-spherical ceramics particles having oval like cross section, which are added into the heat resistant and abrasion resistant aluminum alloy, cause further improvement in creep strength. Furthermore, a valve spring retainer and valve lifter based on another concept of the invention formed from the heat resistant and abrasion resistant aluminum alloy has excellent durabilities for the use at a high temperature and for the repeated load.

Claims: A heat- and abrasion-resistant aluminum alloy comprising: matrix of α-aluminum contained in the alloy and having an average grain size not larger than 1,000 nm; intermetallic compounds contained in the alloy and having an average grain size not larger than 500 nm; and 0.5 to 20% by volume of ceramics particles dispersed in the alloy and having an average particle size in the range of 1.5 to 10 µm, wherein the composition of the aluminum alloy without the ceramics particles is either Al bal TM a X b or Al bal TM a X b Si c , where TM is one or two element selected from the group consisting of Fe and/or Ni; X is at least one element selected from the group consisting of Ti, Zr, Mg and rare earth elements; suffixes a, b and c in atomic percentage are 4≤a≤7, 0.5 ≤ b ≤ 3 and 1 ≤c≤3, respectively; and Al bal means balance aluminum and unavoidable impurities. A heat- and abrasion-resistant aluminum alloy according to claim 1, wherein the ceramics particle content is limited to the range of 0.5 to 8% by volume. A heat- and abrasion-resistant aluminum alloy according to claim 1 or 2, wherein the shape of the ceramics particle is non-spherical having a substantially oval cross section. A valve spring retainer of an engine, formed from a heat- and abrasion-resistant aluminum alloy, comprising: matrix of α-aluminum contained in the alloy and having an average grain size not larger than 1 ,000 nm; intermetallic compounds contained in the alloy and having an average grain size not larger than 500 nm; and 0.5 to 20% by volume of ceramics particles dispersed in the alloy and having an average particle size in the range of 1.5 to 10µm, wherein the composition of the aluminum alloy without the ceramics particles is either Al bal TM a X b or Al bal TM a X b Si c , where TM is one or two element selected from the group consisting of Fe and/or Ni; X is at least one element selected from the group consisting of Ti, Zr, Mg and rare earth elements; suffixes a, b and c in atomic percentage are 4≤a≤7, 0.5≤b≤3 and 1≤c≤3, respectively; and Al bal means balance aluminum and unavoidable impurities. A valve lifter, mounted between a valve and a camshaft of an engine, formed from a heat- and abrasion-resistant aluminum alloy, comprising: matrix of α-aluminum contained in the alloy and having an average grain size not larger than 1,000 nm; intermetallic compounds contained in the alloy and having an average grain size not larger than 500 nm; and 0.5 to 20% by volume of ceramics particles dispersed in the alloy and having an average particle size in the range of 1.5 to 10 µm, wherein the composition of the aluminum alloy without the ceramics particles is either Al bal TM a X b or Al bal TM a X b Si c where TM is one or two element selected from the group consisting of Fe and/or Ni; X is at least one element selected from the group consisting of Ti, Zr, Mg and rare earth elements; suffixes a, b and c in atomic percentage are 4≤a≤7, 0.5 ≤b≤3 and 1 ≤c≤3, respectively; and Al bal means balance aluminum and unavoidable impurites.

Inventors: HONMA KENSUKE, HORIMURA HIROYUKI, MINEMI MASAHIKO, OKAMOTO KENJI, HONMA, KENSUKE, HORIMURA, HIROYUKI, MINEMI, MASAHIKO, OKAMOTO, KENJI, Honma, Kensuke, c/o Honda R &amp; D Co., Ltd., Horimura, Hiroyuki, c/o Honda R &amp; D Co., Ltd., Minemi, Masahiko, c/o Honda R &amp; D Co., Ltd., Okamoto, Kenji, c/o Honda R &amp; D Co., Ltd.
Applicants: HONDA MOTOR CO LTD, HONDA GIKEN KOGYO KABUSHIKI KAISHA
Application year: 1995
Main classification: C22C21
IPC codes: C22C32, F01L1, C22C21, F01L3, C22C1