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WO2013114582A1 - Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité - Google Patents

Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité Download PDF

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Publication number
WO2013114582A1
WO2013114582A1 PCT/JP2012/052215 JP2012052215W WO2013114582A1 WO 2013114582 A1 WO2013114582 A1 WO 2013114582A1 JP 2012052215 W JP2012052215 W JP 2012052215W WO 2013114582 A1 WO2013114582 A1 WO 2013114582A1
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WO
WIPO (PCT)
Prior art keywords
aluminum alloy
wear resistance
forging
eutectic
extrudability
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.)
Ceased
Application number
PCT/JP2012/052215
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English (en)
Japanese (ja)
Inventor
謙介 森
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.)
Furukawa Sky Aluminum Corp
Original Assignee
Furukawa Sky Aluminum Corp
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 Furukawa Sky Aluminum Corp filed Critical Furukawa Sky Aluminum Corp
Priority to CN201280068314.4A priority Critical patent/CN104160049B/zh
Priority to PCT/JP2012/052215 priority patent/WO2013114582A1/fr
Priority to EP12867174.0A priority patent/EP2811041B1/fr
Publication of WO2013114582A1 publication Critical patent/WO2013114582A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/003—Selecting material
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent

Definitions

  • the present invention relates to an aluminum alloy having excellent wear resistance, extrudability, and forgeability that is used as a component such as a compressor in automobiles and home appliances.
  • an aluminum alloy used in a compressor is an Al—Si alloy added with 10 mass% (hereinafter “%”) or more of Si for the purpose of improving wear resistance and reducing the coefficient of thermal expansion.
  • Patent Document 1 describes a sliding aluminum alloy having excellent fatigue resistance and non-seizure properties.
  • Si is added in an amount of 1 to 15% as an essential element because it contributes to non-seizure and wear resistance.
  • the addition amount of Si exceeds 15%, the aluminum alloy becomes brittle.
  • an object of the present invention is to provide an aluminum alloy that is capable of producing a forged product that is excellent in extrudability and forgeability in an Al-Si alloy and that maintains wear resistance.
  • the present inventors have obtained knowledge that an aluminum alloy harmonized with necessary characteristics and productivity can be obtained by adjusting the addition amount of each composition and controlling the eutectic Si size. That is, it has been found that the object of the present invention can be achieved by the following means.
  • Si is 5.5 to 7.0 mass% (hereinafter referred to as%)
  • Cu is 1.0 to 2.0%
  • Mg is 0.4 to 0.8%
  • Ni is 0.05 to 0.25%
  • the balance is made of Al and unavoidable impurities
  • the eutectic Si size in the center in the cross section perpendicular to the longitudinal direction of the extruded material is Sc, when the eutectic Si size on the surface layer side is Ss, Sc—Ss ⁇ 15 ⁇ m 2 , and the number of grains having an eutectic Si size of 20 ⁇ m 2 or less is 1000 to 3000 / mm 2.
  • An aluminum alloy having excellent wear resistance, extrudability, and forgeability is provided.
  • an aluminum alloy excellent in wear resistance, extrudability, and forgeability that further contains 0.01 to 0.05% of Sr is provided.
  • an aluminum alloy material that can be provided can be provided.
  • Si contributes to wear by generating a Si compound.
  • Si is an element that forms Mg 2 Si together with Mg and contributes to strength.
  • the amount of Si added is less than 5.5%, the effects of strength and wear resistance are weak. If it exceeds 7.0%, the surface properties deteriorate and the extrudability decreases.
  • Cu contributes to strength improvement. If the added amount of Cu is less than 1.0%, the effect of improving the strength is small, and if it exceeds 2.0%, the extrusion processability and corrosion resistance deteriorate. *
  • Mg forms Mg 2 Si together with Si and contributes to strength improvement. If the added amount of Mg is less than 0.4%, the effect is small. When it exceeds 0.8%, the extrusion processability is lowered. Preferably, Mg is 0.55 to 0.65%.
  • Cr is effective for crystal grain refinement and contributes to strength improvement.
  • the amount of Cr added is less than 0.05%, the effect is small. If it exceeds 0.15%, the effect does not change greatly.
  • Cr is 0.07 to 0.10%.
  • Ni is effective in improving heat resistance and wear resistance, and contributes to improvement in strength. If the added amount of Ni is less than 0.05%, the effect is small. If it exceeds 0.25%, the effect does not change greatly. Moreover, extrudability is deteriorated. Preferably, Ni is 0.07 to 0.13%.
  • Sr is an element that contributes to improvement of mechanical properties when added. Sr is used for improving the crystallized Si, and when added, the crystallized Si becomes a fine form.
  • the amount of Sr added is preferably 0.01 to 0.05%. If the amount of Sr added is less than 0.01%, the effect is small. If it exceeds 0.05%, the effect does not change greatly.
  • the amount is 0.5% or less in the aluminum alloy of the present invention.
  • the aluminum alloy of the present invention comprises unavoidable impurities and Al in addition to the above elements.
  • a small amount of Ti, Zr, and Zn may be included as long as the effects of the invention are not impaired.
  • the range which is not impaired means 0.05% or less.
  • the uniformity of these properties is determined by the size and distribution of eutectic Si in the extruded and forged materials.
  • the aluminum alloy of the present invention is excellent in extrudability and forgeability by controlling the content of each composition such as Si, and further, by controlling the size and distribution of eutectic Si, the characteristics depending on the surface properties and parts. Variation of the is prevented. Therefore, it is possible to obtain an extruded material and a forged material, which have been imparted with characteristics uniformly according to the present invention, with high productivity.
  • Ss is the eutectic Si size when the central side is observed with a field of view 100 times larger than that of an optical microscope on the basis of a depth of 50 ⁇ m from the surface layer in a cross section perpendicular to the longitudinal direction of the extruded material. is there.
  • Ss is the maximum when four points are measured at intervals of a central angle of 90 degrees in the same field of view.
  • the Sc is the eutectic Si size obtained by observing the central part of the cross section of the extruded material with a field of view of 100 times the optical microscope.
  • the eutectic Si size in the present invention refers to the crystal area of eutectic Si. Furthermore, when the eutectic Si size in the extruded material is 20 ⁇ m 2 or less, the surface roughness can be suppressed.
  • the number of eutectic Si grains is 1000 to 3000 / mm 2 . When the number of grains of eutectic Si having a size of 20 ⁇ m 2 or less is less than 1000 / mm 2 , the effect of wear resistance after forging is small. When the number of eutectic Si grains exceeds 3000 / mm 2 , extrudability and forgeability are hindered.
  • the tempering of the extruded product of the present invention is preferably F, T1, or O, and more preferably tempering.
  • the tempering after forging may be selected according to the required characteristics, but is preferably T6 in the present invention.
  • the extruded material of the sample was observed at the center side in a field of view 100 times that of an optical microscope with a depth of 50 ⁇ m from the surface layer as a reference in a cross section perpendicular to the longitudinal direction.
  • four points were measured at intervals of a central angle of 90 degrees, and the maximum eutectic Si size (Ss) was measured.
  • the eutectic Si size (Sc) was observed at the center of the cross section of the extruded material with a field of view of 100 times the optical microscope.
  • the eutectic Si grain size and number were analyzed by software “image analysis software A image-kun” manufactured by Asahi Kasei Engineering Corporation.
  • the extruded round bar was annealed at 400 ° C. for 5 hours to obtain an O material. In the forging evaluation, it was confirmed that the eutectic Si size and number were within the scope of the invention.
  • the extruded round bar was cut into a length of 100 mm in the longitudinal direction, and upsetting forging with a processing rate of 80% was performed.
  • the forged product was subjected to solution treatment at 520 ° C. for 2 hours and immediately quenched with hot water at 50 ° C. Further, an artificial aging treatment was performed at 180 ° C. for 10 hours to obtain a tempering of T6.
  • the upsetting forging rate is a value calculated by (r1-r2) / r1 ⁇ 100 in FIG.
  • the test alloy forged product thus obtained was subjected to a tensile test, an appearance after upset forging, and a wear test.
  • the results are shown in Table 3.
  • (2) Tensile test Tensile test pieces were sampled so that the longitudinal direction of the extruded bar was the length direction of the test piece, and a JIS No. 4 test piece was prepared and tested. As an evaluation, a tensile strength (TS) of 300 MPa or more is regarded as acceptable, and a value less than this is regarded as unacceptable.
  • TS tensile strength
  • the extruded materials 1 to 10 of the present invention had good surface properties, and Comparative Examples 11 to 17 had poor surface properties.
  • Inventive Examples 1 to 10 have good surface properties because the compositions are within a preferable range. That is, since the surface was smooth, it was manufactured with good extrudability and high productivity.
  • the extruded materials of Comparative Examples 11 to 14, 16 and 17 are out of the preferred range, and thus are extruded materials having poor surface processability and poor extrusion processability.
  • the extruded material of Comparative Example 11 has a high Si content and a large Sc—Ss value. Therefore, it is an extruded material with poor surface processability and extrusion processability.
  • the extruded material of Comparative Example 12 has a low Si content and a large Sc-Ss value. Therefore, it is an extruded material with poor surface processability and extrusion processability.
  • the extruded material of Comparative Example 13 has a low content of Si and Cu. Therefore, it is an extruded material with poor surface processability and extrusion processability.
  • the extruded material of Comparative Example 14 has a high content of Si, Cu, Mg, and Cr. Therefore, it is an extruded material with poor surface processability and extrusion processability.
  • Sr is outside the preferred range, and the number of eutectic Si sizes is 20 ⁇ m 2 or less.
  • the extruded material of Comparative Example 17 has a high Si content, a low Mg content, and a high Sc—Ss value in the composition. Therefore, it is an extruded material with poor surface processability and extrusion processability.
  • the extruded material of Comparative Example 15 is an extruded material having a composition within the range, but having a high Sc—Ss value, and having poor surface processability and an extrudability.
  • the inventive examples 1 to 10 were all good in appearance after upset forging, the tensile test and the specific wear amount, and the comparative examples 11 to 17 were not good.
  • the forged materials of Invention Examples 1 to 10 have good tensile tests and specific wear. Moreover, since it is excellent in forging workability, the appearance after upsetting forging is good. Since the forged material of Comparative Example 11 has a high Si content in the composition, cracks are seen in the appearance after upsetting forging. In other words, the forging processability is poor and it is not good as a forging material.
  • the forged material of Comparative Example 12 is low in tensile strength and low in wear resistance because of its low Si content in the composition.
  • the wear resistance is inferior.
  • the forged material of Comparative Example 13 is low in the tensile strength and inferior in wear resistance because of the low content of Si and Cu in the composition. Since the forged material of Comparative Example 14 has a high content of Si, Cu, Mg, and Cr in the composition, cracks are seen in the appearance after upsetting forging. In other words, the forging processability is poor and it is not good as a forging material.
  • the forged material of Comparative Example 15 has a composition within the range, and the appearance after upset forging, the tensile test, and the specific wear amount are all good, but the extruded material of Comparative Example 15 has poor extrudability from Table 2. Productivity is not good. Therefore, in Comparative Example 15, the productivity of the forging material is poor.
  • the forged material of Comparative Example 16 has a high content of Si, Cu and Sr in the composition, and from Table 2, since the eutectic Si size of the extruded material is a large number of 20 ⁇ m 2 or less, the appearance after upsetting forging Cracks are seen. In other words, the forging processability is poor and it is not good as a forging material. Since the forged material of Comparative Example 17 has a high Si content and a low Mg content in the composition, cracks are seen in the appearance after upset forging. In other words, the forging processability is poor and it is not good as a forging material.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)
  • Extrusion Of Metal (AREA)
PCT/JP2012/052215 2012-02-01 2012-02-01 Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité Ceased WO2013114582A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201280068314.4A CN104160049B (zh) 2012-02-01 2012-02-01 耐磨损性、挤出性、锻造加工性优良的铝合金
PCT/JP2012/052215 WO2013114582A1 (fr) 2012-02-01 2012-02-01 Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité
EP12867174.0A EP2811041B1 (fr) 2012-02-01 2012-02-01 Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité

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Application Number Priority Date Filing Date Title
PCT/JP2012/052215 WO2013114582A1 (fr) 2012-02-01 2012-02-01 Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité

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EP (1) EP2811041B1 (fr)
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2020169377A (ja) * 2019-04-05 2020-10-15 昭和電工株式会社 コンプレッサー摺動部品用アルミニウム合金およびコンプレッサー摺動部品鍛造品

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018033177A1 (fr) * 2016-08-15 2018-02-22 Ksm Castings Group Gmbh Alliage de fonderie à l'aluminium
CN108193094A (zh) * 2018-01-22 2018-06-22 湖北大旗液压有限公司 用于齿轮泵浮动侧板的耐磨铝合金材料及其制备方法

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JPH01104742A (ja) * 1987-10-16 1989-04-21 Furukawa Alum Co Ltd 耐摩耗性アルミニウム合金
JPH036345A (ja) 1989-06-02 1991-01-11 Daido Metal Co Ltd 耐疲労性と非焼付性にすぐれた摺動用アルミニウム基合金
JPH05287427A (ja) * 1992-04-08 1993-11-02 Furukawa Alum Co Ltd 冷間鍛造用耐摩耗性アルミニウム合金とその製造方法
JPH07197164A (ja) * 1993-12-28 1995-08-01 Furukawa Electric Co Ltd:The 高強度高加工性アルミニウム合金とその製造方法
JPH0828493A (ja) * 1994-07-14 1996-01-30 Furukawa Electric Co Ltd:The アルミニウム合金製スクロールの製造方法
JPH10204566A (ja) * 1997-01-14 1998-08-04 Sumitomo Light Metal Ind Ltd 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

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JP4633972B2 (ja) * 2001-07-17 2011-02-16 住友電気工業株式会社 耐摩耗性アルミニウム合金長尺体およびその製造方法ならびにカーエアコンディショナ用ピストン
JP3979602B2 (ja) * 2002-02-28 2007-09-19 アイシン軽金属株式会社 かしめ性に優れた耐摩耗性アルミニウム合金及びその押出材
FR2841164B1 (fr) * 2002-06-25 2004-07-30 Pechiney Aluminium Piece moulee en alliage d'alluminium a haute resistance au fluage
EP1715084B1 (fr) * 2003-11-21 2019-01-16 Showa Denko K.K. Alliage d'aluminium anodisé et procédé de son fabrication
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JPH01104742A (ja) * 1987-10-16 1989-04-21 Furukawa Alum Co Ltd 耐摩耗性アルミニウム合金
JPH036345A (ja) 1989-06-02 1991-01-11 Daido Metal Co Ltd 耐疲労性と非焼付性にすぐれた摺動用アルミニウム基合金
JPH05287427A (ja) * 1992-04-08 1993-11-02 Furukawa Alum Co Ltd 冷間鍛造用耐摩耗性アルミニウム合金とその製造方法
JPH07197164A (ja) * 1993-12-28 1995-08-01 Furukawa Electric Co Ltd:The 高強度高加工性アルミニウム合金とその製造方法
JPH0828493A (ja) * 1994-07-14 1996-01-30 Furukawa Electric Co Ltd:The アルミニウム合金製スクロールの製造方法
JPH10204566A (ja) * 1997-01-14 1998-08-04 Sumitomo Light Metal Ind Ltd 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

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2020169377A (ja) * 2019-04-05 2020-10-15 昭和電工株式会社 コンプレッサー摺動部品用アルミニウム合金およびコンプレッサー摺動部品鍛造品
JP7318283B2 (ja) 2019-04-05 2023-08-01 株式会社レゾナック コンプレッサー摺動部品用アルミニウム合金およびコンプレッサー摺動部品鍛造品

Also Published As

Publication number Publication date
CN104160049A (zh) 2014-11-19
EP2811041A1 (fr) 2014-12-10
EP2811041B1 (fr) 2016-07-06
CN104160049B (zh) 2016-09-14
EP2811041A4 (fr) 2015-09-02

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