Heat-resistant aluminum alloy sinter and process for production of the same

Abstract: A heat-resistant aluminium alloy sinter comprises 5 to 12% by weight of Cr, less than 10% by weight of at least one element selected from Co, Ni, Mn, Zr, V, Ce, Fe, Ti, Mo, La, Nb, Y and Hf, and the balance of Al and impurities. A silicon carbide fiber is included for reinforcing in a fiber volume franction range of 2 to 30%.

Description: The present invention relates to a heat-resistant aluminum alloy sinter having a high-temperature strength, and a process for production of the same. There are conventionally known heat-resistant aluminum alloy sinters made from Al-Fe-based alloy powders such as Al-Fe-Ce, Al-Fe-Mo, etc., by utilizing a quench solidification (see Japanese Patent Application Laid-open No. 52343/86). EP-A-105595 relates to an Al base alloy comprising 1.5-7.0% wt. Cr, 0.5-2.5% wt Zr and 4.0-0.25% wt Mn. GB-A-2179369 relates to a sintered aluminum alloy comprising 4-12% Fe, Cr or Ni together with fibrous ceramic materials as reinforceants. However, the above prior art alloys show inferior hot workability or processability in hot extrusions because of their low toughness and ductility. There is accordingly a need to improve this attribute. With the foregoing in view, it is an object of the present invention to provide a sinter of the type described above, which is made using an aluminum alloy having an excellent high-temperature strength and in which the hot processability in the process of production of members is improved. To accomplish the above object, according to the present invention, there is provided a heat-resistant aluminum alloy sinter comprising 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities. The balance may for example consist of Al containing unavoidable impurities. Further, according to the present invention, there is provided a fiber-reinforced heat-resistant aluminum alloy sinter comprising a matrix made of an aluminum alloy which comprises 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities; and a reinforcing fiber which is a short fiber with a fiber volume fraction in the range of 2 to 30%. With the above configuration, it is possible to improve the hot processability in the process of production of the sinter, and to provide the sinter with an excellent high-temperature strength. If alloy elements are added to the aluminum matrix in concentrations above the solid-solution limit and are dissolved therein, and if fine precipitates and crystallizates consisting of the alloy elements and the matrix are distributed in the matrix, it is possible to reinforce the resulting aluminum alloy. In this case, the precipitates and the like are stable at ambient temperature, but a reinforcing effect provided by the precipitates and the like is gradually lost as the temperature increases, because they are dissolved into or coalesced in the matrix. The rate of dissolving of the precipitates and the like into the matrix primarily depends upon the diffusion coefficient (cm²/sec.) of the alloy elements in the aluminum matrix and hence, in order to improve the heat resistance of the aluminum alloy sinter, it is necessary to employ alloy elements having a small diffusion coefficient. According to the present invention, Cr (having a diffusion coefficient in aluminum of 10⁻¹⁶ to 10⁻¹⁵ cm²/sec.) may be employed as an alloy element having a small diffusion coefficient and therefore, it is possible to improve the heat resistance of the resulting sinter. The alloy elements having a function similar to that of Cr include Co, Ni, Mn, Zr, V, Ce, Fe, Ti, Mo, La, Nb, Y and Hf. The use of at least one element selected from them in combination with chromium also makes it possible to improve the heat resistance of the resulting sinter. It should be noted that it is necessary to provide a sufficiently large cooling rate in the production of a powder, because the mechanical properties of the resulting sinter are damaged if the precipitates are coalesced. The cooling rate satisfying this requirement is in a range of 10² to 10⁶ °C/sec. A cooling rate in this range enables the maximum diameter of the precipitates and the like to be controlled to 10 µm or less. The function of each alloy element and the reason why the amount of each alloy element added is limited are as follows: Cr: This alloy element functions to improve the ambient-temperature strength and high-temperature strength of the resulting sinter and to improve the creep characteristic. However, if the added amount is less than 5% by weight, the ambient- and high-temperature strengths are reduced. On the other hand, if the added amount exceeds 12% by weight, the toughness and ductility are reduced, thus degrading the hot proccessibility. Co, Ni, Mn, Zr, V, Ce, Fe, Ti, Mo, La, Nb, Y, Hf : These alloy elements function to improve the ambient- and high-temperature strengths of the resulting sinter. However, if they are added in excess, the toughness and ductility are hindered, and the hot processibility is degraded. Therefore, the added amount thereof is limited to less than 10% by weight. In this case, the lower limit value of the added amount is about 1.5% by weight. In sinters with the addition of Fe and Zr selected from the above-described various alloy elements, Fe is effective for improving the ambient-temperature strength, the high-temperature strength and the Young's modulus. However, if the amount of Fe added is less than 1% by weight, the effect of the Fe addition is smaller. On the other hand, if the amount of Fe added exceeds 5% by weight, the notch sensitivity is increased, and the elongation is also reduced. Zr functions to improve the toughness, the ductility and the creep characteristic. Zr also improves the high-temperature strength through an aging hardening mechanism. However, if the amount of Zr added is less than 0.5% by weight, the above-described effect is smaller. On the other hand, if the amount exceeds 3% by weight, the toughness and the ductility are reduced. A fiber volume fraction (Vf) of the short fiber falling in the above-described range is suitable for sufficiently exhibiting its fiber-reinforcing capacity. If the fiber volume fraction is lower than 2%, the fiber reinforcing capacity cannot be achieved. On the other hand, any fiber volume fraction exceeding 30% will cause an embrittlement, a deterioration of machinability and the like in the resulting sinter. In addition, according to the present invention, there is provided a process for producing a fiber-reinforced heat-resistant aluminum: alloy sinter consisting of an aluminum alloy matrix and whiskers of silicon carbide dispersed in the matrix, comprising the steps of mixing an aluminum alloy powder with whiskers of silicon carbide while at the same time, pulverizing them by utilizing a mechanical dispersion process, thereby preparing a composite powder consisting of the aluminum alloy and the whiskers of silicon carbide, the aluminum alloy powder comprising 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities, and then subjecting the composite powder to a sintering treatment. Here, the whisker is conveniently a thin pin-like or a stick-like single crystal. The mechanical dispersion process applied to the present invention is a method for mechanically mixing powders to be treated, while at the same time pulverizing them. By employment of this method, the aluminum alloy powder and whiskers of silicon carbide are mixed and pulverized to provide a composite powder containing whiskers of silicon carbide, which have a reduced aspect ratio (fiber length/fiber diameter), uniformly dispersed in the aluminum alloy matrix. The sintering treatment of this composite powder enables the whiskers of silicon carbide to be uniformly dispersed over the entire matrix. In addition, according to the above technique, there is no need for a disentangling operation of the silicon carbide whiskers or for a screening operation for removing coaggregates which have not been open. Hence with this method it is possible to reduce the number of steps required for producing a sinter and also to improve the yield of the whiskers of silicon carbide, thereby reducing the cost of production of the sinter. The above and other objects, features and advantages of the invention will become apparent from a reading of the following description of the preferred embodiments, taken in conjunction with the accompanying drawings. Fig.1 is a graph illustrating a relationship between the heating temperature and the hardness of a sinter; Fig.2 is a graph illustrating a relationship between the high-temperature retention time and the hardness of the sinter; Fig.3 is a perspective cutaway view of an essential portion of a vibration mill; Fig.4 is a perspective cutaway view of an essential portion of a high energy ball mill; Fig.5A is a microphotograph showing a structure of a composite powder; Fig.5B is a microphotograph showing a structure of a sinter according to the present invention; and Fig.6 is a microphotograph showing a structure of a sinter made using the prior art method. The production of a heat-resistant aluminum alloy sinter is, in principle, carried out in sequence through steps of the preparation of an alloy powder, the green compacting thereof, and the hot extrusion thereof. In this case, the sintering of the alloy powder is conducted in the hot extrusion processing. A gas atomizing process, a roll process, a centrifugal spraying process or the like may be applied for the preparation of the alloy powder. The cooling rate in this case is 10² to 10⁶ °C/sec. A vacuum pressure molding process, a CIP process (cold hydrostatically pressing process), a monoaxially pressing process or the like may be applied for the green compacting of the powder. If it is desired to provide an anti-oxidation of the green compact during heating in the hot extrusion, the heating thereof may be carried out in an inert gas atmosphere such as argon gas and/or nitrogen gas. In some cases, the green compact may be subjected to a sintering treatment prior to the hot extrusion processing. A hot pressing process, an HIP process (hot hydrostatically pressing process) or the like may be applied for this treatment. Short fibers (including whisker) as a reinforcing fiber in the resulting fiber-reinforced sinter include SiC, aluminum, Si₃N4 and carbon whiskers, as well as chopped SiC, chopped aluminum, chopped Si₃N₄ and chopped carbon fibers and the like. The mechanical dispersion process may be carried out using a vibration mill 1 shown in Fig. 3, or a high energy ball mill 2 shown in Fig. 4. The vibration mill 1 is constructed so that a stainless steel pot 4 containing a large number of stainless steel balls 3 is rotated about its axis and vibrated radially. The high energy ball mill 2 is constructed of stainless stirring impellers 5 disposed in a stainless pot 4 containing a large number of stainless steel balls 3. Example 1 Aluminum alloy powders of a particle diameter of 105 µm or less and having compositions given in Table I were produced under conditions of a cooling rate of 10² to 10³ °C/sec. by utilizing a He gas atomizing process. Then, the individual alloy powders were employed to produce a plurality of green compacts having a diameter of 50 mm and a length of 100 mm under a pressing force of 4,000 kg/cm² (3.92 x10⁶ MPa) by utilizing a CIP process. Then, each green compact was placed into a soaking furnace at 450°C in an Ar gas atmosphere and left for one hour to effect a degassing treatment, followed by a hot extrusion under conditions of heating temperature of 450°C and an extrusion ratio of 14, thus providing sinters A₁ to A₄ and a₁ to a₄. Sinter Chemical constituents (% by weight) Cr Fe Mn Zr Ti Al A₁ 11 - 1 1 0.5 Balance A₂ 11 1 - 1 - Balance A₃ 11 3 2 - - Balance A₄ 8 - 2 2 - Balance a₁ 11 5 3 2 1 Balance a₂ 5 - - - - Balance a₃ 22 2 - - 1 Balance a₄ 24 - - - - Balance a₅ 11 3 2 - - Balance In the sinters A₁ to A₄ and a₁ to a₄, the sinter A₂ corresponds to those according to the present invention, and the sinters A₁, A₃, A₄ and a₁ to a₄ correspond to those of comparative examples. The comparative example a₅ is a cast article. Test pieces were cut away from the individual sinters A₁ to A₄ and a₁ to a₄ and the cast article a₅ and subjected to a tensile test to provide results as given in Table II. "Acceptable" in the estimation column in Table II represents those having a good hot proccessibility with a tensile strength exceeding 30 kg/mm² (294 Mpa) at a temperature of 300°C and an elongation exceeding 1%, and those which do not satisfy these requirements were indicated by "failure". Sinter Tensile strength (kg/mm²)[x9.8 MPa] Elong. (%) M.D. (µm) Estimation A.T. 200°C 300°C A₁ 56 48 37 2.5 2 to 5 Acceptable A₂ 55 45 35 2.0 2 to 5 Acceptable A₃ 55 43 36 3.0 2 to 5 Acceptable A₄ 52 46 35 1.5 2 to 5 Acceptable a₁ 48 42 31 0 2 to 5 Failure a₂ 26 19 14 5.0 2 to 5 Failure a₃ 40 30 29 0 2 to 5 Failure a₄ 35 25 27 0 2 to 5 Failure a₅ 38 27 12 0 20 to 300 Failure As is apparent from comparison of the sinters A₁ to A₄ with examples a₁ to a₅, it can be seen, in the sinters A₁ to A₄, that the maximum diameter of crystallizates and precipitates is smaller, and the strengths at ambient temperature, 200°C and 300°C are sufficiently large, as compared with those of the examples a₁ to a₅. For example, the tensile strength at 300°C exceeds 35 kg/mm² (343 Mpa). The elongation also exceeds 1%, and even the hot processibility is good. As is apparent from comparison of the sinters A₁ to A₃ with the example a₁, it can be seen that if the net amount of alloy elements other than Cr are excessive, i.e., more than 10% in total, the tensile strength at ambient temperature, 200°C and 300°C is reduced, and the elongation is also lost, resulting in a significant embrittlement. As is apparent from comparison of the sinters A₁ to A₄ with a₂, it can be seen that if no alloy elements other than Cr are added, the elongation is improved, but the tensile strength at ambient temperature, 200°C and 300°C is lower and reduced as the temperature increases. Because the comparative example a₅ is the cast article, the maximum diameter of the crystallizates and precipitates is larger, and due to this, the elongation is considerably reduced, and the tensile strength is also smaller. This means that even with the alloy having a composition falling within a specified composition range, the maximum diameter of the crystallizates and precipitates should be controlled to a smaller level. It can be seen from the comparative examples a₃ and a₄ that any excessive amount of Cr added will result in an elongation loss causing a considerable embrittlement. Example 2 Aluminum alloy powders having compositions given in Table III were produced in a procedure similar to that in Example 1, and the individual alloy powders were employed to produce sinters B₁ to B₁₀ and b₁ under the same conditions as in Example 1. Sinter Chemical constituents (% by weight) Hardness (Hmv) Cr Zr Ti Mn Fe Al Before test After test B₁ 11 2 - - - Balance 157 154 B₂ 11 - 2 - - Balance 143 137 B₃ 11 - - 2 - Balance 156 147 B₄ 11 - - - 2 Balance 156 152 B₅ 11 1 1 - - Balance 148 143 B₆ 11 1 - 1 - Balance 162 153 B₇ 11 1 - - 1 Balance 159 148 B₈ 11 - 1 1 - Balance 147 144 B₉ 11 - 1 - 1 Balance 163 152 B₁₀ 11 - - 1 1 Balance 167 164 b₁ 11 - - - - Balance 125 120 In the sinters B₁ to B₁₀ and b₁, B₇ corresponds to those according to the present invention, and B₁-B₆, B₈-B₁₀ and b₁ correspond to that of comparative examples. Test pieces were cut away from the individual sinters B₁ to B₁₀ and b₁ and examined for variations in hardness due to heating to provide results given in Table III. In this case, the heating temperature is 300°C and the retention time is 100 hours. As is apparent from Table III, it can be seen that the use of Cr in combination with other alloy elements provides an improvement in hardness and maintains the hardness relatively high even after heating. The sinters B₁, B₈ and B₁₀ are particularly small in reduction of the hardness due to heating. Example 3 (Not forming part of the invention). Aluminum alloy powders having a particle diameter of 105 µm or less and compositions given in Table IV were produced in a manner similar to that in Example 1, and the individual alloy powders were employed to produce sinters D₁ to D₆ and d₁ to d₃ under the same conditions as in Example 1. Sinter Chemical constituents (% by weight) Cr Fe Mn Zr Ti Ni Al D₁ 11 3 - - 2 - Balance D₂ 5 - 2 2 1 - Balance D₃ 8 - 2 2 1 - Balance D₄ 11 - 1 1 0.5 - Balance D₅ 8 - 6 - 1 - Balance D₆ 8 - - 6 1 - Balance d₁ 2 - 1 1 - - Balance d₂ 8 6 2 2 2 3 Balance d₃ 8 6 - - 2 3 Balance d₄ 8 - 2 2 1 - Balance Example d₄ is a cast article. Test pieces were cut away from the individual sinters D₁ to D₆ and d₁ to d₃ and the cast article d₄ and were subjected to a tensile test to provide results given in Table V. The estimation in Table V is as defined in Example 1. Sinter Tensile strength (kg/mm²) [x9.8 MPa] Elong. (%) M.D. (µm) Estimation A.T. 200°C 300°C D₁ 45 40 30 2.5 2 to 5 Acceptable D₂ 36 30 26 9.5 2 to 5 Acceptable D₃ 52 46 35 1.5 2 to 5 Acceptable D₄ 56 48 37 2.5 2 to 5 Acceptable D₅ 48 42 30 1.2 2 to 5 Acceptable D₆ 49 40 30 5.6 2 to 5 Acceptable d₁ 21 14 10 13.0 2 to 5 Failure d₂ 51 40 33 0 2 to 5 Failure d₃ 49 36 31 0 2 to 5 Failure d₄ 38 27 12 6.0 20 to 500 Failure Example 4 Aluminum alloy powders having a diameter less than 105 µm and compositions given in Table VI were produced in a manner similar to that in Example 1, and the individual alloy powders were employed to produce sinters E₁, E₂, and e₁ to e₃ under the same conditions as in Example 1. Sinter Chemical constituents (% by weight) Tensile strength (kg/mm²) (x9.8 MPa) Elon. (%) Hot Processibility Cr Fe Zr A.T. 300°C E₁ 8 3 1 59.1 30.2 3.2 Good E₂ 8 3 2 60.3 31.5 6.3 Good e₁ 5 - - 32.5 15.0 16 Good e₂ 11 - - 42.5 18.2 10.2 Medial e₃ 15 - - 43.2 23.4 1 Bad Elon. = Elongation A.T. = Ambient temperature In the sinters E₁, E₂ and e₁ to e₃, E₁ and E₂ correspond to those according to the present invention, and e₁ to e₃ correspond to those of comparative examples. Test pieces were cut away from the individual sinters E₁, E₂, and e₁ to e₃ and subjected to a tensile test to provide results given in Table VI. The hot processibility in Table VI was decided by the presence or absence of cracks in the sinters due to the extrusion. As is apparent from Table VI, the sinters E₁ and E₂ according to the present invention and containing Cr, Fe and Zr each added in a specified amount each have a high strength at ambient and high temperatures and a moderate elongation and are good in hot processibility. As is apparent from the comparative examples e₁ to e₃, it can be seen that an increase in amount of Cr results in an improved tensile strength at ambient temperature and at 300°C, but in a reduced elongation. Particularly, with an amount of Cr of 15% by weight exceeding 12% by weight, the elongation is considerably reduced, and the hot processibility is bad. Addition of Fe is effective for improving the tensile strength at the ambient and increased temperatures, and such effect is large as compared with an effect of addition of Cr. However, if the amount of Fe added exceeds 5% by weight, the elongation is considerably reduced, and the hot processiblity is bad. The elongation characteristic and hot processibility reduced due to the addition of Fe can be compensated for by the addition of Zr. However, if the amount of Zr added exceeds 3% by weight, such compensating effect of Zr is not exhibited. The addition of Zr also improves the tensile strength at the ambient and increased temperatures. Example 5 Aluminum alloy powders having a diameter of 105 µm or less and compositions given in Table VII were produced in a manner similar to that in Example 1, and the individual alloy powders were employed to produce sinters F₁ to F₃, and f₁ to f₃ under the same conditions as in Example 1. However, in the hot extrusion, the extruding ratio was set at 12. Sinter Chemical constituents (% by weight) Cr Fe Zr Mn Ti Mo Al F₁ 8 1.5 2 - - - Balance F₂ 8 3 2 - - - Balance F₃ 11 3 2 - - - Balance f₁ 8 16 2 - - - Balance f₂ 2 3 2 - - - Balance f3 - - 2 - - 3 Balance In the sinters F₁ to F₃ and f₁ to f₃, F₁ to F₃ correspond to those according to the present invention, and the f₁ to f₃ correspond to those comparative examples. The sinter F₂ has the same composition as the sinter E₂ given in Table IV. Test pieces were cut away from the individual sinters F₁ to F₃ and f₁ to f₃ and subjected to three aging tests wherein they were maintained at heating temperatures of 300°C, 400°C and 500°C for ten hours, respectively. The individual test pieces before and after aging were subjected to a tensile test at 300°C to provide results given in Table VIII. In Table VIII, σ B corresponds to the tensile strength (kg/mm²) [x9.8 MPa] and E corresponds to the elongation (%). Sinter After aging Before aging Treating condition 300°C, 10hr. 400°C, 10hr. 550°C, 10hr. σ B ε σ B ε σ B ε σ B ε F₁ 27 2.5 32 2 23 8 27 3 F₂ 31 2 38 1.5 26 6 32 2 F₃ 34 1.5 40 1.2 29 4 34 1.5 f₁ 38 0 36 0 27 4 39 0 f₂ 22 9 24 10 16 12 22 12 f₃ 24 2 27 1 20 5 25 2 As is apparent from comparison of the sinters F₁ and F₂ according to the present invention with the sinter f₁ of the comparative example, it can be seen that if the amount of Fe increases, the tensile strength increases whether or not the aging treatment is carried out, but the elongation is reduced. As is apparent from comparison of the sinters F₂ and F₃ according to the present invention with the sinter f₂ of the comparative example, it can be seen that if the amount of Cr increases, the tensile strength increases whether or not the aging treatment is carried out, but the elongation is reduced. In all of the Examples according to the present invention and in the comparative Examples the addition of Zr serves to increase the tensile strength of a resulting sinter whether the aging treatment is carried out or not, and particularly, those subjected to the aging treatment at 400°C are larger in strength improving effect. As is apparent from comparison of the comparative examples f₂ and f₃ with others, it can be seen that if the amount of Cr added is small, the strength improving effect provided by the aging treatment is smaller, and the reduction in tensile strength with the heating to 550°C is larger. In view of differences in tensile strength of all the sinters due to whether or not the aging treatment is carried out, it can be seen that the improvement in tensile strength cannot be expected at 300°C, and the tensile strength is reduced at an aging temperature of 550°C. The sinter according to the present invention was maintained at 25°C, 100°C, 200°C, 300°C, 400°C and 500°C for a period of up to one hour and examined for the surface hardness thereof (micro Vickers hardness Hmv; a load of 300g) after being cooled, thus providing results shown in Fig.1. Fig.1 demonstrates that the hardness increases at a heating temprature of 350°C or more and reaches the maximum level at a heating temperature of 450°C, and a sufficiently large hardness is achieved even at a heating temperature of 500°C. Further, the sinter according to the present invention was also examined for the relationship between the retention time and the surface hardness (micro Vickers hardness Hmv; a load of 300g) at heating temperatures of 400°C, 450°C and 500°C to give results shown in Fig. 2. A line X corresponds to the case at 400°C; a line Y corresponds to the case at 450°C, and a line Z corresponds to the case at 500°C. It can be seen from Fig.2 that the hardness reaches the maximum level, 217 Hmv in a retention time of 10 hours at a heating temperature of 400°C; the maximum level, 214 Hmv in a retention time of one hour at the heating temperature of 450°C; and the maximum level, 211 Hmv in a retention time of 15 minutes at the heating temperature of 500°C. It can be also seen from Figs.1 and 2 that an optimal range of temperatures for the aging treatment is of 350 to 500°C. When the heating temperature is set at a lower level rather than at a higher level, it is possible to make the maximum hardness larger, but a longer retention time is required for this purpose. Taking into consideration that a difference in maximum hardness attendant on a difference in heating temperature is small, however, it is convenient from an aspect of improvement in producitivity to increase the heating temperature and to shorten the retention time. The aging effect proceeds in the course of preheating and hot extrusion of the green compact and hence, it is unnecessary to carry out a special aging treatment depending upon the preheating temperature, processing time and processing temperature for the green compact. Example 6 Aluminum alloy powders having compositions given in Table IX were produced under a condition of a cooling rate of 10² to 10³°C/sec. by utilizing a He gas atomizing process. A solvent was mixed with a SiC whisker to effect an opening or untangling treatment. In this case, the preferred solvents are those of a kind having a low viscosity which will not react with the aforesaid alloy powders, and a lower boiling point. The solvent used here was a mixture of acetone and 13% of n-butanol. The opened or untangled SiC whisker was mixed with the individual alloy powders to provide various green compacting materials. In this case, the fiber volume fraction (Vf) of the SiC whisker was set at 20%. The above materials were employed to produce a plurality of green compacts by utilizing a vacuum pressure molding process. The molding conditions were of a pressing force of 180 kg/mm² (1764 MPa) and a pressing retention time of one minute. After molding, each green compact was subjected to a drying treatment in a vacuum at 80°C for 10 hours. Each green compact was placed into an extremely thin rubber bag and subjected to a CIP process to produce an intermediate. The producing conditions were of a pressing force of 4,000 kg/mm² (3.92x10⁴ MPa) and a pressing retention time of one minute. The intermediate was subjected to a degassing treatment at 450°C for one hour. The resulting intermediate was subjected to an HIP process to produce a sinter. The producing conditions were of a pressing force of 2,000 atmospheric pressure (2.0265x10⁸ Pa), a heating temperature of 450°C and a pressing retention time of one hour. The sinter was employed to produce a bar-like aluminum alloy sinter reinforced with the SiC whisker by utilizing a hot extrusion process. The extruding conditions were of a heating temperature of 450 to 490°C and an extrusion ratio of 10 or more. The compositions and physical properties of the sinters G₁ to G₆ of the present invention produced by the above procedure are given in Table IX. As is apparent from Table IX, the sinters G₁ to G₆ of the present invention each have an excellent tensile strength and elongation at ambient temperature and an increased temperature (300°C). In this case, it is desired that the maximum diameter of precipitates and crystallizates is 10 µm or less. Table X shows physical properties of the aluminum alloys used as a matrix, i.e., the sinters E₁, E₂ and e₁ to e₃ given in the above Table VI. The tensile test was carried out at ambient temperature. Alloy (Sinter) Tensile strength after aging (kg/mm²), at ambient temperature [x9.8 MPa] Hardness (Hmv) Treating condition T.U.T. T.T. 300°C, 10hr 400°C, 10hr 550°C, 10 hr E₁ 58 65 59 180 200 E₂ 60 69 61 183 217 e₁ 28 20 12 62 56 e₂ 38 25 15 111 85 e₃ 40 28 25 172 120 T.U.T. = Thermally untreated T.T. = Thermally treated As is apparent from Table VI and X, the aluminum alloys E₁ and E₂ used in the present invention each have an excellent tensile strength at ambient temperature and increased temperatures and are relatively large in elongation and further are good in hot processibility., Moreover, the tensile strength at ambient temperature can be substantially improved, particularly by setting the aging conditions at 400°C and 10 hours, and the hardness resulting from the thermal treatment also can be increased. The alloy E₂ has properties shown in Figs.1 and 2 and hence, in producing the fiber-reinforced sinter G₂, it is recommended that the operation of a degassing treatment, an HIP treatement, a hot extrusion or the like is carried out at a temperature of 300 to 500°C, preferably 400 to 500°C. It is also possible to perform a thermal treatment at a temperature in the above range. Table XI shows a relationship between the maximum diameter of the alloy in a powder form and the physical properties of the sinter G₂ formed of the alloy E₂ and the SiC whisker having a fiber volume fraction (Vf) of 20%. The sinter G₂ is produced by the above-described procedure. In this case, the extruding conditions are of a heating temperature of 450°C and an extruding ratio of 20. Maximum diameter (µm) Relative density (%) Tensile strength (kg/mm²)[x9.8 MPa], at ambient temperature Elongation (%) Estimation 20 99 91 2.1 Good 40 99 90 2.0 Good 105 97 85 ≦ 1 Acceptable >105 89 51 ≦ 1 Failure 105 99 68 4.2 - As apparent from Table XI, if the maximum diameter of the alloy E₂ is 105 µm or less, preferably 40 µm or less, it is possible to produce a sinter G₂ having excellent properties. Table XII shows a relationship between the extrusion ratio and properties in producing a sinter using a powder of the alloy E₂ having an average diameter of 20 µm. E.R. P.T. (°C) R.D. (%) T.S. (kg/mm2) Elo. (%) T.P. Estimation 4 450 92 - - Bad Failure 6 450 98 65 ≦1 Medial Failure 10 450 99 89 2.0 Good Good 10 700 99 50 3.5 Good Failure 14 450 99 89 2.0 Good Good ≧20 450 99 91 2.1 Good Good As apparent from Table XII, it is desirable that the extrusion ratio is 10 or more, and the processing temperature is on the order of 450°C. Example 7 (Not forming part of the invention.) Aluminum alloy powders having a diameter of 105 µm or less and compositions given in Table XIII were produced under conditions of a cooling rate of 10² to 10⁶ °C/sec. by utilizing a He gas atomizing process. Then, the individual alloy powders were each mixed with SiC whisker having a fiber volume fraction given in Table XIII to provide various green compacting materials. The individual compacting materials were employed to produce a plurality of green compacts under a pressing force of 4,000 kg/cm² (3.92x10⁶ MPa) by utilizing a CIP process. Then, the green compacts were placed into a soaking furnace at 450°C and maintained for one hour to effect a degassing treatment, followed by a hot extrusion under conditions of a heating temperature of 450°C and an extrusion ratio of 14, thus providing sinters H₁ to H₃, h₁ and h₂. Sinter Chemical constituents (% by weight) SiC W. Vf (%) Cr Mn Zr Fe Cu Mg Al H₁ 8 2 2 - - - Balance 15 H₂ 8 2 - 3 - - Balance 20 H₃ 8 2 - 6 - - Balance 20 h₁ 0.04 0.15 - - 0.4 10 Balance 15 h₂ 0.04 0.15 0.7 - - Balance 20 Test pieces were cut away from the individual sinters H₁ to H₃, h₁ and h₂, and subjected to a tensile test to provide results given in Table XIV. Sinter Tensile strength (kg/mm²) [x9.8 MPa] Elongation (%) A.T. 200°C 300°C A.T. 200°C 300°C H₁ 68 43 32 1.5 1.2 1.9 H₂ 70 50 38 1.0 1.5 2.0 H₃ 72 51 40 0.5 0.7 0.9 h₁ 70 38 18 2 1.5 0.8 h₂ 57 35 15 3 2.5 2.7 As is apparent from comparison of the sinters H₁ to H₃ with those h₁ and h₂, it can be seen that there is not a large difference in tensile strength at ambient temperature between the sinters reinforced with the SiC whisker, even if the compositions of the matrices thereof are different. At an increased temperature of 300°C, however, the strength of the sinters h₁ and h₂ is reduced considerably, whereas the sinters H₁ to H₃ are less reduced in strength. This is due to the difference in strength of the matrices at the increased temperature. It can be also seen that in the sinters H₁ to H₃, the elongation increases as the temperature increases, the characteristic of elongation at the increased temperature depends upon the matrix, and that the hot processibility of the matrix is good. In contrast, in the sinters h₁ and h₂, the elongation decreases as the temperature increases, and the matrix tends to be embrittled due to the heating. Example 8 Used as aluminum alloy powder is a quenched and solidified powder of a diameter of 25 µm or less produced by a He gas atomizing process and having a composition of 8% by weight of Cr, 2% by weight of Zr, 3% by weight of Fe and the balance of Al. For the aluminum alloy powder, it is desirable that the maximum diameter of precipitates and crystallizates in the powder is 10 µm or less in order to provide a good tensile strength and elongation. Placed into a pot 4 of the vibration mill 1 shown in Fig. 3 were the above aluminum alloy powder and a whisker of silicon carbide having a fiber volume fraction (Vf) of 20% and not subjected to opening or untangling treatment and screening treatment, and they were subjected to a mechanical dispersion process to provide a composite powder. The operating conditions are of 4.0 kg steel balls, a 2.6 liter solvent (hexane), a rate of rotation of 49 rpm, a frequency of 1,200/min., and an operation time of 100 hours. Fig.5A is a microphotograph (400 times) showing a structure of the composite powder. In the composite powder, it can be seen that the black spots-like whisker of silicon carbide having a reduced aspect ratio is dispersed in the white aluminum alloy matrix. The composite powder was subjected to a dry green compacting to provide a green compact having a diameter of 80 mm and a length of 70 mm. The molding conditions were of a primary molding pressure of 200 kg/cm² and a secondary molding pressure of 9.3 t/cm² (9.114 MPa). The green compact was heated to 500°C and then placed into a container of an extruder where it was subjected to an extrusion with an extrusion ratio of 13.2, while at the same time, being subjected to a sintering, thus providing a bar-like sinter having a diameter of 22 mm and a length of 900 mm. Fig.5B is a microphotograph (400 times magnification) showing a structure of the sinter. It can be seen from Fig.5B that a variety of large and small black spots-like whisker of silicon carbide is uniformly dispersed in the gray aluminum alloy matrix, and no aggregate of whisker of silicon carbide is present therein. For comparison, observations were made by a microscope, of a mixed powder resulting from mixing of an aluminum alloy powder having the same composition as that described above with a whisker of silicon carbide subjected to opening or untangling treatment and screening treatment and having a fiber volume fraction of 20% in a mixer and as a result, it was found that the gray aluminum alloy powder and the black whisker of silicon carbide were not dispersed uniformly. Aggregations of the whisker of silicon carbide were produced. Fig.6 is a microphotograph (400 times) showing a structure of the bar-like sinter produced via a green compacting and extrusion under the same conditions as in the above-described example of production according to the present invention by use of the above mixed powder, wherein the gray portion corresponds to the aluminum alloy matrix, and the smaller black spot portion corresponds to the whisker of silicon carbide. It can be seen from Fig.6 that an aggregation of whisker of silicon carbide is produced in the form of a layer. The larger black spots are voids. Test pieces were cut away from each of a sinter J produced according to the present invention and a sinter K produced in the prior art method and were tested for tensile strength (σ B ) and elongation (ε) at ambient temperature and 300°C to provide results given in Table XV. In Table XV, a sinter L corresponds to one produced by use of particles of silicon carbide, wherein the composition of the aluminum alloy matrix and the conditions of a green compacting and extrusion are identical with those in the present invention. It was confirmed that an aggregation of silicon carbide particles was produced even in this sinter L. Sinter Ambient temperature 300°C Tensile strength (kg/mm²) Elongation (%) Tensile strength (kg/mm²) [x9.8 MPa] Elongation (%) J 85 1.0 41 1.5 K 67 0 32 0 L 69 0.5 32 1.0 As is apparent from the above Table XV, the sinter J produced according to the present invention is high in tensile strength and elongation at ambient temperature and 300°C as compared with those of the other sinters K and L and hence, has a high strength. This is attributable to the uniform dispersion of the silicon carbide whisker relative to the aliuminum alloy matrix. It should be noted that the above-described green compacting step can be omitted when a sinter is produced by application of a powder direct forging or powder direct extrusion process. The sinters in the above-described various examples are applicable to various structural members and particularly, most suitable for structural members for internal combustion engines, e.g., connecting rods, valves, piston pins, etc.

Claims: A heat-resistant aluminum alloy sinter comprising 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities. A heat-resistant aluminum alloy sinter as claimed in claim 1 wherein the maximum diameter of precipitates and crystallizates is 10 µm or less. A heat-resistant aluminum alloy sinter as claimed in claim 1 or claim 2, wherein said sinter is produced through an aging treatment at a temperature of 350 to 500°C. A heat-resistant aluminum alloy sinter as claimed in claim 1, comprising: a matrix made of an aluminum alloy which comprises 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities, and a reinforcing fiber which is a short fiber with a fiber volume fraction in the range of 2 to 30%. A heat-resistant aluminum alloy sinter as claimed in claim 4, wherein the maximum diameter of precipitates and crystallizates in said matrix is 10 µm or less. A heat-resistant aluminum alloy sinter as claimed in claim 4 or claim 5, wherein said sinter is produced through an aging treatment at a temperature of 350 to 500°C. A heat-resistant aluminum alloy sinter as claimed in any one of claims 4 to 6, wherein the aluminum alloy matrix is a powder having a maximum particle diameter of 105 µm or less. A heat-resistant aluminum alloy sinter as claimed in any one of claims 4 to 7, wherein the aluminum alloy matrix is a powder having a particle maximum diameter of 40 µm or less. A process for producing a fiber-reinforced heat-resistant aluminum alloy sinter comprising an aluminium alloy matrix and whiskers of silicon carbide dispersed in the matrix, comprising the steps of: mixing an aluminum alloy powder with whiskers of silicon carbide and at the same time pulverizing them by utilizing a mechanical dispersion process, thereby preparing a composite powder consisting of the aluminum alloy and the whiskers of silicon carbide, said aluminum alloy powder comprising 5 to 12% by weight or Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities, and then subjecting said composite powder to a sintering treatment. A process for producing a fiber-reinforced heat-resistant aluminium alloy sinter as claimed in claim 4, said process comprising mixing an aluminium alloy powder, comprising 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities, with reinforcing fibers which are short fibers with a fiber volume fraction in the range of 2 to 30%; pulverizing the resulting mixture by a mechanical dispersion process, thereby forming a composite powder; and subjecting the composite powder to sintering. A process for producing a heat-resistant aluminium alloy sinter as claimed in claim 1, said process comprising subjecting an aluminium alloy powder, comprising 5 to 12% by weight of Cr, 1.5 to 10% by weight of Fe, Zr and optionally at least one element selected from Co, Ni, Mn, V, Ce, Ti, Mo, La, Nb, Y and Hf, wherein the Fe content is in a range of 1 to 5% by weight and the Zr content is in a range of 0.5 to 3% by weight, and the balance of Al and impurities, to sintering.

Inventors: HORIMURA HIROYUKI C O KABUSHIK, ICHIKAWA MASAO C O KABUSHIKI K, KOIKE SEIICHI C O KABUSHIKI KA, MATSUMOTO NORIAKI C O KABUSHIK, HORIMURA, HIROYUKI, ICHIKAWA, MASAO, KOIKE, SEIICHI, MATSUMOTO, NORIAKI, HORIMURA, HIROYUKI, C/O KABUSHIKI KAISHA HONDA, Ichikawa, Masao, c/o Kabushiki Kaisha Honda, Koike, Seiichi, c/o Kabushiki Kaisha Honda, Matsumoto, Noriaki, c/o Kabushiki Kaisha Honda
Applicants: HONDA MOTOR CO LTD, HONDA GIKEN KOGYO KABUSHIKI KAISHA
Application year: 1988
Main classification: C22C1
IPC codes: C22C49, C22C1