EP1096028A2 - Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu - Google Patents

Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu Download PDF

Info

Publication number
EP1096028A2
EP1096028A2 EP00309071A EP00309071A EP1096028A2 EP 1096028 A2 EP1096028 A2 EP 1096028A2 EP 00309071 A EP00309071 A EP 00309071A EP 00309071 A EP00309071 A EP 00309071A EP 1096028 A2 EP1096028 A2 EP 1096028A2
Authority
EP
European Patent Office
Prior art keywords
alloy
content
aluminum alloy
cast
strength
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP00309071A
Other languages
German (de)
English (en)
Other versions
EP1096028A3 (fr
Inventor
Suzuki c/o K. K. Daiki Aluminium Kogyosho Takao
Naoto c/o K. K. Daiki Aluminium Kogyosho Oshiro
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Daiki Aluminium Industry Co Ltd
Original Assignee
Daiki Aluminium Industry Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Daiki Aluminium Industry Co Ltd filed Critical Daiki Aluminium Industry Co Ltd
Priority to EP03006408A priority Critical patent/EP1371741A2/fr
Priority to EP03006409A priority patent/EP1347066A2/fr
Publication of EP1096028A2 publication Critical patent/EP1096028A2/fr
Publication of EP1096028A3 publication Critical patent/EP1096028A3/fr
Withdrawn legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys

Definitions

  • the present invention relates to a high-strength aluminum alloy for casting which exhibits superior tensile strength, elongation and impact value and which will provide a good surface finish, and to a high-strength cast aluminum alloy comprising the same.
  • Aluminum alloys are widely used as materials for various components of vehicles, industrial machines, airplanes, electric appliances for domestic use and other apparatus of various types.
  • aluminum alloys there are cast aluminum alloys, a representative of which is an AC4CH alloy prescribed by JIS (equivalent to A356.0 prescribed by ASTM (U.S.), G(GK)-AlSi7Mg prescribed by DIN (Germany), or Al-Si7Mg prescribed by ISO).
  • Such cast aluminum alloys are used in important durable parts requiring higher mechanical properties such as vehicle components, metal fittings for stringing and components of hydraulic systems, and in like applications.
  • a first feature of the aluminum alloy according to the present invention resides in that the content of P is very low, specifically, not more than 0.0003 %.
  • a second feature of the aluminum alloy resides in that the alloy contains Sb or Sr and optionally Ti or a combination of Ti and B when the alloy has a typical content of P.
  • the cast aluminum alloy of the present invention satisfies higher mechanical property requirements (i.e., not less than 380 MPa in tensile strength, not less than 9 % in elongation, not less than 200 MPa in 0.2% proof strength and not less than 90 kJ/m 2 in impact value) while exhibiting satisfactory competitiveness against the conventional AC4CH alloy as to castability and cost efficiency (see sample No. 47 with a low P content in Fig. 1).
  • the content ranges of major ingredients including Cu, Si, Mg and Fe will be described by reference to experimental data of examples and comparative examples to be described later.
  • the resulting cast aluminum alloy satisfies higher mechanical property requirements (i.e., not less than 380 MPa in tensile strength, not less than 9 % in elongation, not less than 200 MPa in 0.2% proof strength and not less than 90 kJ/m 2 in impact value) while exhibiting satisfactory competitiveness against the conventional AC4CH alloy as to castability and cost efficiency.
  • the addition of 0.05 to 0.35 % of Ti and optionally not more than 0.003 % of B to the above aluminum alloys enables crystal grains to become finer thereby improving the appearance of the resulting cast product as surface-finished, though it does not contribute to an improvement in impact value.
  • the addition of Ti and B in combination can make resulting crystal grains finer than can the addition of Ti alone (see the photograph of metallic textures shown Fig. 14). It is to be noted that as crystal grains become finer, the tensile strength and 0.2% proof strength are improved.
  • any of the foregoing alloys according to the present invention is T6-treated after casting.
  • the alloys of the present invention as cast are not so different from the AC4CH alloy in tensile strength and elongation.
  • the T6 treatment allows eutectic Si grains in these alloys to become refined and granular, so that the resulting cast alloys attain the aforementioned mechanical property requirements: not less than 380 MPa in tensile strength, not less than 9 % in elongation, not less than 200 MPa in 0.2% proof strength and not less than 90 kJ/m 2 in impact value.
  • a first example of a high-strength aluminum alloy for casting (samples Nos. 47, 53, 63, 51, 54 and 55, see the microscopic photograph of sample No. 47 with a low P content in Fig. 1) according to the first example of the present invention has the following composition:
  • This example is characterized in that the content of P is lower than a typical P content (0.0004-0.0030 %), specifically not more than 0.0003 %. If the P content is higher than 0.0003 %, eutectic Si grains resulting from the T6 treatment are large and elongate. Such large and elongate grains give rise to a notching effect, which in turn causes the mechanical properties, especially the impact resistance, of the alloy to lower. However, by reducing the P content to a value not more than 0.0003 %, which was lower than the typical P content, eutectic Si grains after having undergone the T6 treatment became refined and globular, and the mechanical properties, especially impact resistance, of the alloy were improved.
  • a second example of a high-strength aluminum alloy for casting (see the microscopic photograph of sample No. 62 added with Sb in Fig. 1) according to the present invention has the following composition:
  • This example is characterized in that the alloy is added with Sb in an amount as small as 0.05 to 0.2 % though the content of P is within the range of the typical P content.
  • This alloy as T6-treated after casting had finer eutectic Si grains in the metallic texture thereof than did a corresponding alloy not added with Sb.
  • a third example of a high-strength aluminum alloy for casting (see the microscopic photograph of sample No. 60 added with Sr) according to the present invention has the following composition:
  • this example is characterized in that the alloy is added with Sr in an amount as small as 0.005 to 0.030 % though the content of P is within the typical P content range of 0.0004 to 0.0030 %.
  • This alloy as T6-treated after casting had finer eutectic Si grains in the metallic texture thereof than did a corresponding alloy not added with Sr.
  • a fourth example of a high-strength aluminum alloy for casting (sample No. 57) according to the present invention is prepared by adding 0.05 to 0.35 % of Ti to any one of the alloys of the first to third examples.
  • a fifth example of a high-strength aluminum alloy for casting (sample No. 58) according to the present invention is prepared by adding 0.05 to 0.35 % of Ti and not more than 0.003 % of B to any one of the alloys of the first to third examples.
  • the addition of a small amount of Ti or of a combination of Ti and B enables refinement of crystal grains of each alloy as T6-treated thereby contributing to improved surface finish, though it does not contribute to an improvement in the impact resistance.
  • any of the alloys according to the first and fifth examples of the present invention, as cast, is not largely different from the conventional AC4CH alloy in tensile strength and elongation.
  • Such mechanical properties of the alloys of the present invention are modified by a subsequent heat treatment called "T6 treatment".
  • the T6 treatment is performed under the following conditions. That is, a solution treatment is performed at 500°C to 520°C for 4 to 12 hours, followed by an aging treatment at 140°C to 180°C for 2 to 7 hours.
  • the alloys of the present invention after having undergone the T6 treatment, each exhibited a tensile strength of not less than 380 MPa, elongation of not less than 9 %, 0.2% proof strength of not less than 200 MPa, and an impact value of not less than 90 kJ/m 2 .
  • the alloys of the present invention were compared with comparative examples.
  • Samples Nos. 47, 53, 63, 51, 54 and 55 according to the first example of the invention and samples Nos. 49, 46, 48, 44, 43, 50, 52 and 56 as comparative examples each had a low P content, specifically not more than 0.0003 %.
  • these samples were tested for the influence from the varying contents.
  • Sample No. 59 as a comparative example contained Cu, Si, Mg and Fe in amounts within the respective specified ranges of the present invention and had a P content of 0.0007 %, which was beyond the specified range, and was tested for the influence from the increased P content.
  • Samples Nos. 60 and 62 according to the second and third examples of the present invention had P contents of 0.0019 % and 0.0010 %, respectively, which were higher than the specified content range, and were added with Sr and Sb, respectively, to determine the respective effects of Sr and Sb.
  • Sample No. 57 according to the fourth example of the invention had necessary ingredients including P within respective specified content ranges and was added with Ti to determine the influence of Ti.
  • sample No. 58 according to the fifth example of the invention had necessary ingredients including P within respective specified content ranges and was added with Ti and B to determine the influence of the combination of Ti and B.
  • Any one of the alloys shown in Table 1 had undergone the T6 treatment under the conditions: solution treatment at 520°C for 12 hours, then aging treatment at 160°C for 5 hours after water cooling, followed by air cooling.
  • Cu causes a Cu-Al intermetallic compound such as CuAl 2 to precipitate at the aging treatment following the solution treatment thereby strengthening the ⁇ -Al phase, hence, improving the tensile strength of the resulting T6-treated cast aluminum alloy.
  • the tensile strength of the cast alloy was as low as 364 MPa.
  • the Cu content was as high as 4.51 % (sample No.
  • the elongation and impact value of the resulting cast alloy were as low as 5.2 % and 66 kJ/m 2 , respectively.
  • Sample No. 48 as a comparative example exhibited a similar tendency.
  • the resulting cast alloy exhibited a tensile strength of 395 MPa, elongation of 10.4 %, 0.2% proof strength of 229 MPa and impact value of 109 kJ/m 2 , all of which attained the respective target values.
  • a variation in each mechanical property with varying content of Cu is shown in Fig. 2. As can be seen from Fig. 2, the intended mechanical properties were attained when the Cu content was about 4 % (within the specified range of 3.5 to 4.3 %) in a Al-X%Cu-7%Si-0.2%Mg-0.1%Fe-low P alloy as T6-treated.
  • Si provides molten metal with sufficient fluidity to ensure improved castability.
  • the Si content was not less than 9 %, which was higher than the specified range, and the contents of other ingredients were within the respective specified ranges (samples Nos. 44 and 43 as comparative examples)
  • the elongation and impact value of the resulting cast alloy were as low as 3-4 % and 45-47 kJ/m 2 , respectively.
  • the fluidity of the alloy was so low that the alloy is not adaptable for casting.
  • the resulting cast alloy exhibited a tensile strength of not less than 380 MPa, elongation of 10.4 %, 0.2% proof strength of 229 MPa and impact value of 109 kJ/m 2 , all of which attained the respective target values.
  • a variation in each mechanical property with varying content of Si is shown in Fig. 3. As can be seen from Fig. 3, the intended mechanical properties were attained when the Si content was about 7 % (within the specified range of 5.0 to 7.5 %) in an Al-4%Cu-X%Si-0.2%Mg-0.1%Fe-low P alloy as T6-treated.
  • the addition of Mg causes Mg-Si intermetallic compounds such as Mg 2 Si and an Al-Cu-Mg compound to precipitate when the alloy is subjected to the solution treatment and the subsequent aging treatment thereby strengthening the ⁇ -Al phase.
  • the Mg content was as low as 0.01 % and the contents of other ingredients were within the respective specified ranges (sample No. 50 as a comparative example)
  • the tensile strength and elongation of the resulting cast alloy was lower than 380 MPa and as low as 8.9 %, respectively.
  • the Mg content was as high as 0.30 % (sample No.
  • the elongation and impact value of the resulting cast alloy were as low as 5.4 % and 75 kJ/m 2 , respectively.
  • the resulting cast alloy exhibited a tensile strength of not less than 386 MPa, elongation of not less than 10.4 %, 0.2% proof strength of not less than 219 MPa and impact value of 109 kJ/m 2 , all of which attained the respective target values.
  • a variation in each mechanical property with varying content of Mg is shown in Fig. 4. As can be seen from Fig. 4, the intended mechanical properties were attained when the Mg content was about 0.15 % (within the specified range of 0.10 to 0.25 %) in an Al-4%Cu-7%Si-X%Mg-0.1%Fe-low P alloy as T6-treated.
  • Fe is an element that causes the mechanical properties of a cast alloy to lower and, hence, the addition of a smaller amount of Fe is more preferable.
  • the Fe content was as high as 0.29 % and the contents of other ingredients were within the respective specified ranges (sample No. 56 as a comparative example)
  • the tensile strength, elongation and impact value of the resulting cast alloy was as low as 377 MPa, 8.5 % and 88 kJ/m 2 , respectively.
  • the Fe content was not more than 0.20 % (sample No.
  • the resulting cast alloy exhibited a tensile strength of not less than 383 MPa, elongation of not less than 9.9 %, 0.2% proof strength of not less than 223 MPa and impact value of 98 kJ/m 2 , all of which attained the respective target values.
  • a variation in each mechanical property with varying content of Fe is shown in Fig. 5. As can be seen from Fig. 5, the intended mechanical properties were attained when the Fe content was not more than 0.2 % (i.e., the specified range) in an Al-4%Cu-7%Si-0.15%Mg-X%Fe-low P alloy as T6-treated.
  • Sample No. 59 was a comparative example having a higher P content and exhibited elongation and impact value as low as 7.6 % and 70 kJ/m 2 , respectively. This is because eutectic Si grew into large and elongate grains in the T6-treated cast alloy as shown in the macrophotograph of the texture of sample No. 59 in Fig. 1. By reducing the P content to the specified value or lower it is possible to make eutectic Si grains finer and granular thereby attaining the target tensile strength, 0.2% proof strength, elongation and impact value.
  • Samples Nos. 60 and 62 as examples of the invention were added with Sr and Sb, respectively, and each had a higher P content than the specified P content. Without addition of Sr or Sb, such a high P-content alloy would exhibit lower elongation and impact value. However, the addition of Sr or Sb to such an alloy causes eutectic Si grains to become refined and granular thereby making it possible to improve the elongation and impact value. In fact, sample No. 60 containing 0.0019 % of P and added with 0.0088 % of Sr attained the intended mechanical properties, and sample No. 62 containing 0.0010 % of P added with 0.158 % of Sb attained the intended mechanical properties.
  • Figs. 6 to 10 show the relationship between the mechanical properties and the modifying agents. Alloys used were T6-treated Al-4%Cu-7%Si-0.15%Mg-0.1%Fe alloys added with P in a high content (sample No. 59 as a comparative example), with P in a low content (not more than 0.0003 %), with Sb and with Sr, respectively.
  • Fig. 6 shows the relationship between the tensile strength and the modifying agents. As shown, in any one of the cases the average value exceeded the respective target value. It should be noted that the measured values of Sr-added alloys tended to be relatively widely scattered.
  • Fig. 7 shows the relationship between the 0.2% proof strength and the modifying agents. As shown, in any one of the cases the average value exceeded the respective target value. Although Sb-added alloys were found to exhibit a relatively narrow scatter of measured values, other three types of alloys were found to exhibit a relatively wide scatter of measured values.
  • Fig. 8 shows the relationship between the elongation and the modifying agents. As shown, the average value of the high P-content alloys was 7.4 %, which was significantly lower than the target value of 9 %. The respective average value of any one of other three types of alloys was 10 % or higher, which was beyond the target value.
  • Fig. 9 shows the relationship between the impact value and the modifying agents.
  • the average value of the high P-content alloys was 70 kJ/m 2 , which was significantly lower than the target value of 90 kJ/m 2 .
  • the respective average value of any one of the other three types of alloys was 100 kJ/m 2 or higher, which was beyond the target value.
  • Figs. 10 to 13 each show a variation in each mechanical property of a low P-content alloy when this alloy was added with Ti or with Ti and B.
  • An Al-4%Cu-7%Si-0.15%Mg-0.1%Fe-low P alloy was used as a reference example, and Ti or a combination of Ti and B was added to this type of alloy.
  • a macrophotograph of the texture of each alloy as T6-treated is shown in Fig. 14. As shown, the alloy added with Ti was found to have finer crystal grains than the reference example not added with Ti or with a combination of Ti and B, and the alloy added with a combination of Ti and B was found to have still finer crystal grains than the alloy added with Ti alone.
  • Fig. 10 shows a comparison between the low P-content alloy not added with Ti or with a combination of Ti and B and the low P-content alloy added with Ti or with a combination of Ti and B as to tensile strength.
  • the average values of these alloys were not so different from each other but tended to become higher as grains became finer.
  • the tensile strength of the low P-content alloy added with Ti was higher than that of the low P-content alloy not added with Ti or with a combination of Ti and B, and the tensile strength of the low P-content alloy added with a combination of Ti and B was higher than that of the low P-content alloy added with Ti alone.
  • Fig. 11 shows a comparison between the low P-content alloy not added with Ti or with a combination of Ti and B and the low P-content alloy added with Ti or with a combination of Ti and B as to 0.2% proof strength.
  • the average values of these alloys were not so different from each other, and the low P-content alloy added with a combination Ti and B exhibited the highest value, and the low P-content alloy added with Ti alone exhibited a higher value than the low P-content alloy not added with Ti or with a combination of Ti and B.
  • Fig. 12 shows a comparison between the low P-content alloy not added with Ti or with a combination of Ti and B and the low P-content alloy added with Ti or with a combination of Ti and B as to elongation.
  • the low P-content alloy added with a combination of Ti and B and the low P-content alloy without addition exhibited substantially equal values of elongation, while the low P-content alloy added with Ti alone exhibited an elongation that was lower than those of the former two alloys and slightly higher than the target value.
  • Fig. 13 shows a comparison between the low P-content alloy not added with Ti or with a combination of Ti and B and the low P-content alloy added with Ti or with a combination of Ti and B as to impact value.
  • the low P-content alloy added with a combination of Ti and B and the low P-content alloy added with Ti alone exhibited impact values that were significantly lower than that of the low P-content alloy without addition and slightly higher than the target value.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
EP00309071A 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulage sous pression et alliage d'aluminium ainsi fondu Withdrawn EP1096028A3 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP03006408A EP1371741A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu
EP03006409A EP1347066A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulage sous pression et alliage d'aluminium ainsi fondu

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP29957899 1999-10-21
JP29957899A JP2001123239A (ja) 1999-10-21 1999-10-21 高強度鋳造用アルミニウム合金及び同アルミニウム合金鋳物

Related Child Applications (2)

Application Number Title Priority Date Filing Date
EP03006409A Division EP1347066A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulage sous pression et alliage d'aluminium ainsi fondu
EP03006408A Division EP1371741A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu

Publications (2)

Publication Number Publication Date
EP1096028A2 true EP1096028A2 (fr) 2001-05-02
EP1096028A3 EP1096028A3 (fr) 2002-02-06

Family

ID=17874460

Family Applications (3)

Application Number Title Priority Date Filing Date
EP03006408A Withdrawn EP1371741A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu
EP03006409A Withdrawn EP1347066A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulage sous pression et alliage d'aluminium ainsi fondu
EP00309071A Withdrawn EP1096028A3 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulage sous pression et alliage d'aluminium ainsi fondu

Family Applications Before (2)

Application Number Title Priority Date Filing Date
EP03006408A Withdrawn EP1371741A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu
EP03006409A Withdrawn EP1347066A2 (fr) 1999-10-21 2000-10-16 Alliage d'aluminium à haute résistance mécanique pour moulage sous pression et alliage d'aluminium ainsi fondu

Country Status (2)

Country Link
EP (3) EP1371741A2 (fr)
JP (1) JP2001123239A (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103643088A (zh) * 2013-11-29 2014-03-19 哈尔滨工业大学 一种adc12铝合金的变质剂及其变质方法
CN106917014A (zh) * 2017-02-23 2017-07-04 中国第汽车股份有限公司 一种轿车铝合金转向节及其挤压铸造方法

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7390913B2 (en) 2002-12-23 2008-06-24 H. Lundbeck A/S Process for the preparation of racemic citalopram diol and/or S- or R-citalopram diols and the use of such diols for the preparation of racemic citalopram, R-citalopram and/or S-citalopram
JP4623372B2 (ja) * 2005-07-27 2011-02-02 アイシン・エィ・ダブリュ株式会社 鋳物用アルミニウム合金およびその製造方法、ならびにアルミニウム合金鋳造製品の製造方法
CN103266243A (zh) * 2013-06-06 2013-08-28 中南林业科技大学 微型车结构件低压铸造用高性能铝合金及其制备方法
GB201402323D0 (en) 2014-02-11 2014-03-26 Univ Brunel A high strength cast aluminium alloy for high pressure die casting
EP3556877B1 (fr) * 2016-12-14 2021-01-20 JFE Steel Corporation Tôle magnétique en acier à grains orientés et son procédé de fabrication
GB201713005D0 (en) 2017-08-14 2017-09-27 Univ Brunel The alloy and manufacturing method of Al-Si-Mg castings for improved mechanical performance
CN110042281B (zh) * 2019-04-23 2020-10-23 中国兵器工业第五九研究所 一种铸造铝合金及其制备方法
US20240018631A1 (en) * 2020-12-07 2024-01-18 Norsk Hydro Asa A high temperature stable alsicu alloy

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4786340A (en) * 1985-09-27 1988-11-22 Ube Industries, Ltd. Solution heat-treated high strength aluminum alloy
JPH059637A (ja) * 1991-07-03 1993-01-19 Nippon Light Metal Co Ltd 鍛造用アルミニウム合金
JPH06145866A (ja) * 1992-11-13 1994-05-27 Ube Ind Ltd 鋳造性に優れた高圧鋳造用アルミニウム合金
EP0618303A1 (fr) * 1993-03-26 1994-10-05 Hitachi Metals, Ltd. Pièce étanche à l'air en alliage d'aliminium coulé et procédé de fabrication
JPH07242975A (ja) * 1994-03-03 1995-09-19 Hitachi Metals Ltd 気密性に優れたアルミニウム合金鋳物
JPH08199275A (ja) * 1995-01-20 1996-08-06 Daiki Alum Kogyosho:Kk Ａｌ−Ｓｉ系合金
JPH09263867A (ja) * 1996-01-24 1997-10-07 Mitsubishi Chem Corp 鋳物用アルミニウム合金
JPH10158772A (ja) * 1996-11-29 1998-06-16 Hitachi Metals Ltd ロッカーアームおよびその製造方法
JPH10251790A (ja) * 1997-03-13 1998-09-22 Hitachi Metals Ltd 熱疲労強度に優れるアルミニウム合金鋳物
JPH10317085A (ja) * 1997-05-21 1998-12-02 Toyota Motor Corp 高耐熱アルミニウム合金鋳物

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4786340A (en) * 1985-09-27 1988-11-22 Ube Industries, Ltd. Solution heat-treated high strength aluminum alloy
JPH059637A (ja) * 1991-07-03 1993-01-19 Nippon Light Metal Co Ltd 鍛造用アルミニウム合金
JPH06145866A (ja) * 1992-11-13 1994-05-27 Ube Ind Ltd 鋳造性に優れた高圧鋳造用アルミニウム合金
EP0618303A1 (fr) * 1993-03-26 1994-10-05 Hitachi Metals, Ltd. Pièce étanche à l'air en alliage d'aliminium coulé et procédé de fabrication
JPH07242975A (ja) * 1994-03-03 1995-09-19 Hitachi Metals Ltd 気密性に優れたアルミニウム合金鋳物
JPH08199275A (ja) * 1995-01-20 1996-08-06 Daiki Alum Kogyosho:Kk Ａｌ−Ｓｉ系合金
JPH09263867A (ja) * 1996-01-24 1997-10-07 Mitsubishi Chem Corp 鋳物用アルミニウム合金
JPH10158772A (ja) * 1996-11-29 1998-06-16 Hitachi Metals Ltd ロッカーアームおよびその製造方法
JPH10251790A (ja) * 1997-03-13 1998-09-22 Hitachi Metals Ltd 熱疲労強度に優れるアルミニウム合金鋳物
JPH10317085A (ja) * 1997-05-21 1998-12-02 Toyota Motor Corp 高耐熱アルミニウム合金鋳物

Non-Patent Citations (8)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 017, no. 274 (C-1064), 27 May 1993 (1993-05-27) & JP 05 009637 A (NIPPON LIGHT METAL CO LTD;OTHERS: 02), 19 January 1993 (1993-01-19) *
PATENT ABSTRACTS OF JAPAN vol. 018, no. 468 (C-1244), 31 August 1994 (1994-08-31) & JP 06 145866 A (UBE IND LTD), 27 May 1994 (1994-05-27) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 01, 31 January 1996 (1996-01-31) -& JP 07 242975 A (HITACHI METALS LTD), 19 September 1995 (1995-09-19) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 12, 26 December 1996 (1996-12-26) -& JP 08 199275 A (DAIKI ALUM KOGYOSHO:KK), 6 August 1996 (1996-08-06) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 02, 30 January 1998 (1998-01-30) & JP 09 263867 A (MITSUBISHI CHEM CORP;MITSUBISHI MOTORS CORP), 7 October 1997 (1997-10-07) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 11, 30 September 1998 (1998-09-30) -& JP 10 158772 A (HITACHI METALS LTD), 16 June 1998 (1998-06-16) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 14, 31 December 1998 (1998-12-31) & JP 10 251790 A (HITACHI METALS LTD), 22 September 1998 (1998-09-22) *
PATENT ABSTRACTS OF JAPAN vol. 1999, no. 03, 31 March 1999 (1999-03-31) -& JP 10 317085 A (TOYOTA MOTOR CORP), 2 December 1998 (1998-12-02) *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103643088A (zh) * 2013-11-29 2014-03-19 哈尔滨工业大学 一种adc12铝合金的变质剂及其变质方法
CN106917014A (zh) * 2017-02-23 2017-07-04 中国第汽车股份有限公司 一种轿车铝合金转向节及其挤压铸造方法
CN106917014B (zh) * 2017-02-23 2019-03-01 中国第一汽车股份有限公司 一种轿车铝合金转向节及其挤压铸造方法

Also Published As

Publication number Publication date
EP1371741A2 (fr) 2003-12-17
EP1096028A3 (fr) 2002-02-06
EP1347066A2 (fr) 2003-09-24
JP2001123239A (ja) 2001-05-08

Similar Documents

Publication Publication Date Title
JP3255560B2 (ja) ダイカスト合金およびダイカスト品
JPH10204566A (ja) 陽極酸化処理性に優れた高強度耐摩耗アルミニウム合金材およびその製造方法
CN108779522B (zh) 基于Al-Mg-Si的能时效硬化的铝合金
EP1096028A2 (fr) Alliage d'aluminium à haute résistance mécanique pour moulages sous pression et alliage d'aluminium ainsi fondu
JP3332885B2 (ja) セミソリッド加工用アルミニウム基合金及びその加工部材の製造方法
JP2009506215A (ja) アルミニウム鋳造合金
JPS62158851A (ja) リチウム含有アルミニウム基合金
JP4328927B2 (ja) 電気伝導性および熱伝導性に優れたアルミニウム合金材
JPH0469218B2 (fr)
US6416710B1 (en) High-strength aluminum alloy for pressure casting and cast aluminum alloy comprising the same
EP1802782A1 (fr) Plaque de moulage d'aluminium de haute durete et procede de production de la plaque
EP0196369A1 (fr) Alliage d'aluminium
WO2005106057A2 (fr) Alliage al-zn-mg apte au traitement thermique pour pieces coulees automobiles et aerospatiaux
JPS6151017B2 (fr)
CN118339319A (zh) 压铸铝合金
KR100909699B1 (ko) 충격에너지가 향상된 알루미늄 합금 및 이로부터 제조된압출재
JPS6154853B2 (fr)
JPH04173935A (ja) 耐摩耗性アルミニウム合金
KR20220141725A (ko) 알루미늄 합금
JPH07216487A (ja) 耐摩耗性、耐熱性に優れたアルミニウム合金およびその製造方法
JP2002348626A (ja) ダイカスト用アルミニウム合金材
KR20220141485A (ko) 알루미늄 합금
JPH0649572A (ja) ダイカスト用高強度亜鉛合金及び亜鉛合金ダイカスト部品
US2290026A (en) Aluminum alloy
JP3684245B2 (ja) 冷間鍛造用アルミニウム合金

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A2

Designated state(s): CH DE ES FR GB IT LI

Kind code of ref document: A2

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT SE

AX Request for extension of the european patent

Free format text: AL;LT;LV;MK;RO;SI

17P Request for examination filed

Effective date: 20010710

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A3

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT SE

AX Request for extension of the european patent

Free format text: AL;LT;LV;MK;RO;SI

AKX Designation fees paid

Free format text: CH DE ES FR GB IT LI

17Q First examination report despatched

Effective date: 20021125

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20040129