JPH02101125A - Manufacture of aluminum alloy excellent in tensile strength and fatigue strength - Google Patents
Manufacture of aluminum alloy excellent in tensile strength and fatigue strengthInfo
- Publication number
- JPH02101125A JPH02101125A JP25194088A JP25194088A JPH02101125A JP H02101125 A JPH02101125 A JP H02101125A JP 25194088 A JP25194088 A JP 25194088A JP 25194088 A JP25194088 A JP 25194088A JP H02101125 A JPH02101125 A JP H02101125A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- strength
- powder
- toughness
- fatigue 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.)
- Granted
Links
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 229910000838 Al alloy Inorganic materials 0.000 title abstract description 11
- 239000000956 alloy Substances 0.000 claims abstract description 24
- 238000001125 extrusion Methods 0.000 claims abstract description 19
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 18
- 239000000843 powder Substances 0.000 claims abstract description 17
- 238000007872 degassing Methods 0.000 claims abstract description 13
- 238000000034 method Methods 0.000 claims abstract description 13
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 238000002844 melting Methods 0.000 claims abstract description 4
- 230000008018 melting Effects 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 238000005242 forging Methods 0.000 claims description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- 239000000203 mixture Substances 0.000 abstract description 4
- 238000005496 tempering Methods 0.000 abstract description 4
- 229910052751 metal Inorganic materials 0.000 abstract description 3
- 239000002184 metal Substances 0.000 abstract description 3
- 238000007731 hot pressing Methods 0.000 abstract description 2
- 238000011282 treatment Methods 0.000 abstract description 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 7
- 150000001875 compounds Chemical class 0.000 description 5
- 238000010791 quenching Methods 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 238000003483 aging Methods 0.000 description 3
- 238000002485 combustion reaction Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000009661 fatigue test Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- 229910018575 Al—Ti Inorganic materials 0.000 description 1
- 230000003679 aging effect Effects 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- TZCXTZWJZNENPQ-UHFFFAOYSA-L barium sulfate Chemical compound [Ba+2].[O-]S([O-])(=O)=O TZCXTZWJZNENPQ-UHFFFAOYSA-L 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000003795 desorption Methods 0.000 description 1
- 201000010099 disease Diseases 0.000 description 1
- 208000037265 diseases, disorders, signs and symptoms Diseases 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000012856 packing Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 238000007665 sagging Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000011856 silicon-based particle Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000009849 vacuum degassing Methods 0.000 description 1
Landscapes
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、特に内燃機関のコネクティングロッド（コン
ロッド）その他バルブリフタ、バルブスプリングリテー
ナ−ロッカーアーム、ンンクロナイサリング等に適した
、引張および疲労強度にずくれたアルミニウム合金の製
造方法に関する。Detailed Description of the Invention [Industrial Field of Application] The present invention is particularly suitable for connecting rods of internal combustion engines, valve lifters, valve spring retainers, rocker arms, mechanical rings, etc. This invention relates to a method for manufacturing a sagging aluminum alloy.
［従来の技術］
自動車やオートパイなどの省エネルギ一対策としてその
軽量化の要望か高い。特に内燃機関の部品なかんづくコ
ンロッドを軽量化すれば、エンジンの性能が大幅に向上
するため、このコンロッドを中心に他の部品とともにア
ルミニウム化したいという要望が高い。[Prior Art] There is a high demand for weight reduction in automobiles, autopilots, etc. as a measure to save energy. In particular, reducing the weight of internal combustion engine parts, especially connecting rods, can greatly improve engine performance, so there is a strong desire to make these connecting rods and other parts aluminum.
ところで、コンロッドは常温から ２００℃で用いられ
る。このため、コンロッド材料には常温〜２００℃にお
ける引張強度、疲労強度が必要とされ、また縦弾性係数
が高いこと、線膨張係数が低いことも重要である。By the way, connecting rods are used at temperatures ranging from room temperature to 200°C. For this reason, connecting rod materials are required to have tensile strength and fatigue strength at room temperature to 200°C, and it is also important that they have a high modulus of longitudinal elasticity and a low coefficient of linear expansion.
従来、高温強度にすぐれたアルミニウム合金としてはＡ
２２１Ｂ、Ａ ２６１８なとか知られている。Conventionally, A is an aluminum alloy with excellent high-temperature strength.
221B and A 2618 are known.
又、急冷凝固粉末を成形したアルミニウム合金材が提案
されており、本出願人もさきに特願昭６２−２８３６５
７号、特願昭６２−２１＋３［ｉ５ｇ号を提案した。In addition, an aluminum alloy material formed from rapidly solidified powder has been proposed, and the present applicant also previously filed Japanese Patent Application No. 62-28365.
No. 7, proposed patent application No. 1982-21+3 [i5g.
［発明が解決しようとする課題］
上記従来の高温強度にすぐれたアルミニウム合金とされ
ている合金であっても、その引張強度、疲労強度、切欠
疲労強度は１５０℃以上においては未だ十分ではない。[Problems to be Solved by the Invention] Even with the above-mentioned conventional aluminum alloys that are considered to have excellent high-temperature strength, their tensile strength, fatigue strength, and notch fatigue strength are still insufficient at temperatures of 150° C. or higher.
そこで本出願人は上記の発明をさきに出願したが引張お
よび疲労強度を重視すると靭性が劣り、靭性を重視する
と強度が十分でないなど、未だ改良の余地がある。Therefore, the present applicant filed the above-mentioned invention earlier, but there is still room for improvement, such as when emphasis is placed on tensile and fatigue strength, the toughness is inferior, and when emphasis is placed on toughness, the strength is insufficient.
本発明は、高強度（例えば５４ｋｇｒ／ｌｌ１ｍ’ 以
上）を維持したままその靭性をも改良した合金を提供せ
んとするものである。The present invention aims to provide an alloy with improved toughness while maintaining high strength (for example, 54 kgr/11 m' or more).
［課題を解決するための手段］
本発明は、重量％で、Ｓ ｉ ： １５．５〜１８．５
％、Ｆｅ：４〜７％、Ｃｕ：Ｉ 〜Ｂ９６、ＭｇＯ，３
〜３％、Ｔｉ：０．旧〜２％あるいはさらにＭｎ：０．
３〜３％［ただしＦｅ＋Ｍｎ≦ ８％］を含み、残り不
可避不純物とＡＩとからなる合金材料を、溶解後、平均
冷却速度１０３℃／ｓｅｃ以上で冷却する粉末製造工程
、４００〜５２０℃における脱ガス工程、３００〜５０
０℃において押出比４以上に押出す押出工程、４００〜
５００℃における熱間鍛造工程および熱処理工程に付す
ることを特徴とする引張および疲労強度にすぐれたアル
ミニウム合金の製造方法である。[Means for Solving the Problems] The present invention provides Si: 15.5 to 18.5 in weight%.
%, Fe: 4-7%, Cu:I-B96, MgO, 3
~3%, Ti:0. Old ~2% or even Mn:0.
A powder manufacturing process in which an alloy material containing 3% to 3% [however, Fe+Mn≦8%] and remaining unavoidable impurities and AI is cooled at an average cooling rate of 103°C/sec or more after melting, and desorption at 400 to 520°C. Gas process, 300-50
Extrusion step of extruding at an extrusion ratio of 4 or more at 0°C, 400 ~
This is a method for producing an aluminum alloy with excellent tensile and fatigue strength, which is characterized by subjecting the aluminum alloy to a hot forging process and a heat treatment process at 500°C.
本発明における合金材料の組成の限定理由は下記のとお
りである。The reasons for limiting the composition of the alloy material in the present invention are as follows.
Ｓｉ：Ｆｅと共存してＡｌ−５ｔ−Ｆｅ系化合物として
分散し、疲労強度、切欠疲労強度を高める。また、弾性
係数を高め、線膨脹係数をドげる。その量が１５．５％
未満では疲労強度、切欠疲労強度が低くなり、線膨脹係
数が大きくなる。１８．５％を越えると靭性が劣ってく
る。Si: Coexists with Fe and disperses as an Al-5t-Fe based compound, increasing fatigue strength and notch fatigue strength. It also increases the elastic modulus and lowers the linear expansion coefficient. The amount is 15.5%
If it is less than that, the fatigue strength and notch fatigue strength will be low and the linear expansion coefficient will be large. If it exceeds 18.5%, the toughness will deteriorate.
Ｆｅ：Ｓｉと共存してＡｌ−８ｉ−Ｆｅ系化合物として
分散し、またＳｉ粒子を微細にする。これらにより引張
強度、疲労強度、切欠疲労強度を高める。また、弾性係
数を高め、線膨脹係数を下げる。その量が４％未満では
引張強度、疲労強度、切欠疲労強度が不足する。７％を
越えると靭性が著しく低下する。また、鍛造性も劣って
くる。Fe: Coexists with Si and is dispersed as an Al-8i-Fe-based compound, and also makes Si particles fine. These increase tensile strength, fatigue strength, and notch fatigue strength. It also increases the elastic modulus and lowers the linear expansion coefficient. If the amount is less than 4%, tensile strength, fatigue strength, and notch fatigue strength will be insufficient. If it exceeds 7%, the toughness will decrease significantly. Furthermore, forgeability is also deteriorated.
Ｃｕ：Ｍｇと共存し、時効硬化性を付与する。Cu: Coexists with Mg and imparts age hardening properties.
時効硬化により引張強度、疲労強度、切欠疲労強度が向
上する。その量が１２６未満ては効果か十分でなく、６
％を越えると靭性が劣る。Age hardening improves tensile strength, fatigue strength, and notch fatigue strength. If the amount is less than 126, the effect is not sufficient, and 6
If it exceeds %, the toughness will be poor.
Ｍ ｇ ： Ｃｕと共存し、時効効果を生じ、引張強度
、疲労強度、切欠疲労強度が向上する。Mg: Coexists with Cu, produces an aging effect, and improves tensile strength, fatigue strength, and notch fatigue strength.
その量が０．３％未満では効果が十分でなく、３％を越
えると効果が飽和するばかりでなく、靭性も低下する。If the amount is less than 0.3%, the effect will not be sufficient, and if it exceeds 3%, the effect will not only be saturated, but also the toughness will decrease.
Ｔｉ ：Ａｌ−Ｔｉ、Ａｌ−５ｉ−Ｔｉ系化合物として
分散し、靭性の向上に寄与する。その量が０．０１％未
満では効果が十分でなく、２％を越えると逆に靭性が低
下する。Ti: Dispersed as an Al-Ti, Al-5i-Ti based compound and contributes to improving toughness. If the amount is less than 0.01%, the effect will not be sufficient, and if it exceeds 2%, the toughness will decrease.
Ｍｎ ： Ａ ｌ−３ｉ−Ｍｎ系化合物として分散し、
靭性をほとんど低下させることなく、引張強度、疲労強
度、切欠疲労強度を向上させる。その量が０．３％未満
では効果が十分でなく、３％を越えると靭性が低下する
。また、Ｆｅ＋ＭｎＱが８％を越えるとやはり靭性が低
下し、鍛造性も劣ってくる。Mn: Dispersed as an Al-3i-Mn-based compound,
Improves tensile strength, fatigue strength, and notch fatigue strength with almost no reduction in toughness. If the amount is less than 0.3%, the effect will not be sufficient, and if it exceeds 3%, the toughness will decrease. Moreover, if Fe+MnQ exceeds 8%, the toughness will decrease and the forgeability will also deteriorate.
次に製造工程の限定理由について説明する。Next, the reasons for limiting the manufacturing process will be explained.
粉末製造工程：ガスアトマイズ、単ロール法、双ロール
法、噴霧ロール法などの急冷凝固法をもいる。平均冷却
速度は１０３℃／ｓｅｃ以上とすることが、強度および
靭性向上のために必要である。Powder manufacturing process: There are also rapid solidification methods such as gas atomization, single roll method, twin roll method, and spray roll method. It is necessary to set the average cooling rate to 103° C./sec or more in order to improve strength and toughness.
脱ガス工程：靭性の向上のために脱ガスは重要である。Degassing process: Degassing is important for improving toughness.
脱ガス温度が４００℃未満では脱ガス効果が不十分とな
って靭性か低くなり、５２０℃を越えると化合物粒子の
成長が生じて強度が低ドする。脱ガスは粉末を缶に詰め
で行ったり、真空炉中で行ったりする。If the degassing temperature is less than 400°C, the degassing effect will be insufficient and the toughness will be reduced, and if it exceeds 520°C, compound particles will grow and the strength will be reduced. Degassing can be done by packing the powder into cans or in a vacuum furnace.
脱ガス時の雰囲気は、真空、Ｎ２ガス、不活性ガスなど
としたり、場合によっては空気中加熱後短時間真空引き
をしたりする。The atmosphere during degassing may be vacuum, N2 gas, inert gas, or the like, or, depending on the case, may be evacuated for a short time after heating in air.
押出工程；押出によりメタルフローを与えることは靭性
の向上に重要である。押出比４未満ては粉末同士の結合
が不十分てあり、靭性が不足する。押出温度が３００℃
末病では変形抵抗が大きく押出が困難となり、又押出温
度か５００℃を越えると、押出割れが生じる。Extrusion process: Providing metal flow through extrusion is important for improving toughness. If the extrusion ratio is less than 4, the bonding between the powders is insufficient and the toughness is insufficient. Extrusion temperature is 300℃
In terminal diseases, the deformation resistance is large, making extrusion difficult, and if the extrusion temperature exceeds 500°C, extrusion cracks occur.
熱間鍛造：熱間鍛造によって所望形状とする。Hot forging: A desired shape is obtained by hot forging.
鍛造温度が４００℃未１ｘ−では変形能か十分てなく割
れを生じる。また、５００°Ｃを越えても鍛造割れを生
じる。If the forging temperature is less than 400°C, the deformability will not be sufficient and cracks will occur. Furthermore, forging cracks occur even when the temperature exceeds 500°C.
熱処理工程・溶体化処理、焼入れ、焼戻しにより時効硬
化を生じさせ、強度を向上させる。The heat treatment process, solution treatment, quenching, and tempering causes age hardening and improves strength.
通當焼入れは水冷によって行い、焼戻しは最高強度が得
られる条件で行う。たたし、焼入れ歪みや残留応力を緩
和するために温水焼入れや比較的高温での過時効焼戻し
も行われる。Through-quenching is performed by water cooling, and tempering is performed under conditions that provide maximum strength. However, hot water quenching and over-aging tempering at relatively high temperatures are also performed to alleviate quenching distortion and residual stress.
本発明は上記各り程を必須の要件とするが、必要に応じ
て工程を付加することができる。例えば、脱ガス工程の
前に粉末をｒ備圧縮しておいたり、脱ガス後真空を保持
したままホットプレスによって緻密化し、それから押出
を行うなとの工程を採用することかできる。さらには、
粉末やフレーク、リボンの粉砕、分級なども適宜実施す
る。The present invention requires each of the above steps as essential requirements, but steps can be added as necessary. For example, the powder may be compressed before the degassing step, or the powder may be densified by hot pressing while maintaining a vacuum after degassing, and then extrusion may be performed. Furthermore,
Grinding and classification of powder, flakes, and ribbons are also carried out as appropriate.
［実施例コ
実施例１
第１表に示す組成の各種合金を溶解後、エアアトマイズ
により粉末を製造した。そして１４９μｍ以下に分級し
た。こうして得た粉末の平均粒径は６０μｍであり、・
１′均冷却速度はＢＸＩ（］３℃／ｓｅｃであった。[Example 1] After melting various alloys having the compositions shown in Table 1, powders were produced by air atomization. Then, it was classified to 149 μm or less. The average particle size of the powder thus obtained was 60 μm,
The 1' uniform cooling rate was BXI (]3°C/sec.
この粉末をＣＩ Ｐ （Ｃｏｌｄ ｌ５ｏｓｔａＬｉｃ
Ｐｒｅｓｓｉｎｇ）により］’ ６ｉｉｉ圧縮し、ア
ルミニウム）ＩＩの中に装入して真空脱ガスを行った。This powder was mixed with CI P (Cold l5ostaLic).
Pressing)]' 6iii was compressed and placed in aluminum) II for vacuum degassing.
脱ガス温度は４９０°Ｃとした。その後、アルミニウム
缶を密封し、押出用ビレットとじた。この後、４００℃
において押出を行い、断面形状３０Ｘ １１０ ｍｍの
角棒を得た。The degassing temperature was 490°C. Thereafter, the aluminum can was sealed and formed into a billet for extrusion. After this, 400℃
Extrusion was performed to obtain a square bar with a cross-sectional shape of 30 x 110 mm.
このとき押出比は１５であった。この押出棒を鍛造素材
として、第１図に示すようなコンロッド形状に鍛造した
。鍛造温度は４５０℃であった。At this time, the extrusion ratio was 15. This extruded rod was used as a forging material and was forged into a connecting rod shape as shown in FIG. The forging temperature was 450°C.
この後、４９０℃×１ｈｒ→水冷−１７５℃Ｘ（ｉｔ＋
ｒの熱処理を行った。After this, 490℃ x 1hr → water cooling -175℃X (it+
A heat treatment of r was performed.
第１図中の中央部（棹部）Ｊより丸棒試験片を切り出し
、各種試験を行った。すなわち、常温および１５０℃に
おける引張試験（１５０℃の場合はＩ ００ ｈ ｒ保
持後）、常温における切欠引張試験（切欠の形状係数２
．４）を行い、又、常温において形状係数３．１の切欠
を持つ試験片を用いて応力振幅１１ｋｇｆ／ｎ＋ｍ２に
よる疲労試験（小野式回転曲げ試験）を行い、破断まで
の繰返し数（寿命）を測定した。靭性は切欠耐力比（切
欠引張強さ／平滑試験での耐力）の大きさにより評価し
た。A round bar test piece was cut out from the center part (shape part) J in FIG. 1, and various tests were conducted. That is, tensile tests at room temperature and 150°C (after holding I 00 hr at 150°C), notch tensile tests at room temperature (notch shape factor 2),
．． 4), and also conducted a fatigue test (Ono type rotating bending test) using a test piece with a notch with a shape factor of 3.1 at room temperature using a stress amplitude of 11 kgf/n+m2 to determine the number of repetitions until rupture (life). It was measured. Toughness was evaluated based on the notch yield strength ratio (notch tensile strength/proof stress in smoothness test).
結宋は第２表に示す通りであった。本発明により得られ
た合金Ｎｏ、１〜８の場合、常温および１５０℃におけ
る強度が高く、切欠耐力比も０．９１以上とかなり大き
く、靭性がかなり高いとみなされる。また、疲労試験に
おける寿命も長い。比較例合金Ｎｏ、９はＳｉｎが少な
いため強度か低い。Ｎｏ、１０合金はＳｉ瓜が多いため
切欠耐力比（靭性）か低い。Ｎｏ、１１合金はＦｅｎが
少ないため強度が低い。Ｎｏ、１２合金はＦｅ１ｉが多
いため切欠耐力比（靭性）か小さい。Ｎｏ、１３合金は
Ｃｕが少ないため強度、寿命が小さい。The ending of the Sung Dynasty was as shown in Table 2. In the case of alloy Nos. 1 to 8 obtained according to the present invention, the strength at room temperature and 150° C. is high, the notch yield strength ratio is also quite large at 0.91 or more, and the toughness is considered to be quite high. It also has a long life in fatigue tests. Comparative example alloy No. 9 has low strength because it has a small amount of Sin. No. 10 alloy has a low notch yield strength ratio (toughness) because it has a large amount of Si. Alloy No. 11 has low strength because it contains less Fen. Since the No. 12 alloy has a large amount of Fe1i, the notch yield strength ratio (toughness) is small. Alloy No. 13 has a small amount of Cu, so its strength and life are short.
ＮＯ，１４合金はＣｕが多いため切欠耐力比（靭性）が
小さい。Ｎｏ、１５合金はＭｇが少ないため強度か低い
。Ｎｏ、Ｉ［ｉ合金はＭｇが多いため強度向上効果かみ
られないばかりか、切欠耐力比（靭性）もやや低い。Ｎ
ｏ、１７ａ金はＴｉを含まないため靭性かやや低い。Ｎ
ｏ、１．８合金はＴｉｆｆ１が多いため靭性が低い。Ｎ
ｏ、１９合金はＭｎが多く、また、Ｎ ｏ、２０合金は
Ｆ ｅ ＋ Ｍ ｎか多いため、靭性が低い。Since the NO,14 alloy contains a lot of Cu, the notch yield strength ratio (toughness) is low. Alloy No. 15 has low strength due to low Mg content. Since the No. I [i alloy contains a large amount of Mg, not only is it not effective in improving strength, but also the notch yield strength ratio (toughness) is somewhat low. N
o, 17a Since gold does not contain Ti, its toughness is somewhat low. N
o, 1.8 alloy has a large amount of Tiff1 and therefore has low toughness. N
The o,19 alloy has a large amount of Mn, and the no,20 alloy has a large amount of Fe + Mn, so its toughness is low.
第１表
第２表
注・σｌＩ：引張強さ、σ。、：耐力、δ 伸びσ７．
切欠引張強さ（切欠の形状係数２．４）実施例２
Ａ Ｉ −１７，０ｓ ｉ −５，５Ｆ ｅ −４，５
Ｃｕ −０，８Ｍ ｇ −０，２０Ｔ ｉ −０，５Ｍ
ｎ合金を用いて製造条件の影響について検討した。す
なわち、第３表に示す条件でコンロッドを製造した。こ
の後４９０℃Ｘ１ｈｒ−ｅ水冷→１７５℃Ｘ６１＋ｒの
熱処理を行った。Ｎ ｏ、２Ｌ’ Ｎ ｏ、２２は本発
明による方法であり、Ｎｏ、２３〜２８は製造条件のい
ずれかが本発明方法と異なる比較例である。なお熱処理
条件はいずれも同・−とした。Table 1 Table 2 Note: σlI: Tensile strength, σ. , : proof stress, δ elongation σ7.
Notch tensile strength (notch shape factor 2.4) Example 2 A I -17,0s i -5,5F e -4,5
Cu -0,8M g -0,20T i -0,5M
The influence of manufacturing conditions was investigated using n-alloy. That is, connecting rods were manufactured under the conditions shown in Table 3. Thereafter, heat treatment was performed at 490°C x 1hr water cooling → 175°C x 61+r. No. 2L' No. 22 is the method according to the present invention, and No. 23 to 28 are comparative examples in which any of the manufacturing conditions are different from the method of the present invention. Note that the heat treatment conditions were the same in both cases.
試験結果は第４表に示す通りである。Ｎｏ、２１．２２
は強度゛および疲労寿命ともにすぐれ、靭性もかなり高
い。Ｎｏ、２３は冷却速度が小さいために、強度、靭性
が低い。’Ｎｏ、２４は脱ガス温度が低いために靭性が
低い。Ｎｏ、２５は脱ガス温度が高いために強度が低い
。Ｎｏ、２６は押出温度が高いために押出割れを生じた
ものである。Ｎｏ、２７は押出比が低いために靭性が低
い。Ｎ ｏ、２８は鍛造温度が高いために鍛造割れが生
じたものである。The test results are shown in Table 4. No, 21.22
It has excellent strength and fatigue life, and has considerably high toughness. No. 23 has low strength and toughness because the cooling rate is low. 'No. 24 has low toughness due to low degassing temperature. No. 25 has low strength due to high degassing temperature. In No. 26, extrusion cracking occurred due to the high extrusion temperature. No. 27 had low toughness due to the low extrusion ratio. In No. 28, forging cracks occurred due to the high forging temperature.
σＮ：切欠引張強さ（切欠の形状係数２．４）［発明の
効果］
本発明によれば、引張および疲労強度にすぐれ、靭性も
かなり高いアルミニウム合金か得られる。このものは、
特に内燃機関のコンロッドに適用して、その軽量化とエ
ンジンの出力増加、旨効率化、騒音減少を可能にする。σN: Notch tensile strength (notch shape factor 2.4) [Effects of the invention] According to the present invention, an aluminum alloy with excellent tensile and fatigue strength and considerably high toughness can be obtained. This thing is
It is especially applied to internal combustion engine connecting rods, making it possible to reduce their weight, increase engine output, improve efficiency, and reduce noise.
その他、ロッカーアーム、バルブリフタ、バルブスプリ
ングリテーナ−シンクロナイザ−リング等にも適用して
、それらの軽量化をｒ＋工能にする。In addition, it can also be applied to rocker arms, valve lifters, valve spring retainers, synchronizer rings, etc., making their weight reduction an R+ technology.
第１図は本発明によって得られるコンロッドの正面図で
ある。
１・・・中央部（棟部）
第
図
特許出願人 住友軽金属工業株式会社
代理人 弁理士 小 松 秀 岳
代理人 弁理士 旭 宏FIG. 1 is a front view of a connecting rod obtained by the present invention. 1...Central part (ridge part) Figure Patent applicant Sumitomo Light Metal Industries Co., Ltd. Agent Patent attorney Hide Komatsu Agent Patent attorney Hiroshi Asahi
Claims (1)
４〜７％、Ｃｕ：１〜６％、Ｍｇ０．３〜３％、Ｔｉ：
０．０１〜２％あるいはさらにＭｎ：０．３〜３％［た
だしＦｅ＋Ｍｎ≦８％］を含み、残り不可避不純物とＡ
ｌとからなる合金材料を、溶解後、平均冷却速度１０＾
３℃／ｓｅｃ以上で冷却する粉末製造工程、４００〜５
２０℃における脱ガス工程、３００〜５００℃において
押出比４以上に押出す押出工程、４００〜５００℃にお
ける熱間鍛造工程および熱処理工程に付することを特徴
とする引張および疲労強度にすぐれたアルミニウム合金
の製造方法。(1) In weight%, Si: 15.5-18.5%, Fe:
4-7%, Cu: 1-6%, Mg0.3-3%, Ti:
Contains 0.01-2% or further Mn: 0.3-3% [however, Fe+Mn≦8%], and the remaining unavoidable impurities and A
After melting an alloy material consisting of l, the average cooling rate is 10^
Powder manufacturing process cooling at 3°C/sec or more, 400-5
Aluminum with excellent tensile and fatigue strength characterized by being subjected to a degassing process at 20°C, an extrusion process at 300 to 500°C to an extrusion ratio of 4 or more, a hot forging process and a heat treatment process at 400 to 500°C. Alloy manufacturing method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63251940A JP2746390B2 (en) | 1988-10-07 | 1988-10-07 | Manufacturing method of aluminum alloy with excellent tensile and fatigue strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63251940A JP2746390B2 (en) | 1988-10-07 | 1988-10-07 | Manufacturing method of aluminum alloy with excellent tensile and fatigue strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02101125A true JPH02101125A (en) | 1990-04-12 |
| JP2746390B2 JP2746390B2 (en) | 1998-05-06 |
Family
ID=17230240
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63251940A Expired - Lifetime JP2746390B2 (en) | 1988-10-07 | 1988-10-07 | Manufacturing method of aluminum alloy with excellent tensile and fatigue strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2746390B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0250902A (en) * | 1988-05-12 | 1990-02-20 | Sumitomo Electric Ind Ltd | Method for forming aluminum alloy for product having large diameter |
| JPH02277731A (en) * | 1989-04-20 | 1990-11-14 | Honda Motor Co Ltd | Production of product by using rapidly solidified powder of aluminum |
| JPH05305380A (en) * | 1992-04-28 | 1993-11-19 | Mazda Motor Corp | Manufacture of magnesium alloy member |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62188739A (en) * | 1986-02-14 | 1987-08-18 | Honda Motor Co Ltd | Al alloy stock |
| JPS62188738A (en) * | 1986-02-15 | 1987-08-18 | Honda Motor Co Ltd | Structural member made of sintered al or al alloy and its production |
| JPS6342344A (en) * | 1986-08-06 | 1988-02-23 | Honda Motor Co Ltd | Al alloy for powder metallurgy excellent in high temperature strength characteristic |
-
1988
- 1988-10-07 JP JP63251940A patent/JP2746390B2/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62188739A (en) * | 1986-02-14 | 1987-08-18 | Honda Motor Co Ltd | Al alloy stock |
| JPS62188738A (en) * | 1986-02-15 | 1987-08-18 | Honda Motor Co Ltd | Structural member made of sintered al or al alloy and its production |
| JPS6342344A (en) * | 1986-08-06 | 1988-02-23 | Honda Motor Co Ltd | Al alloy for powder metallurgy excellent in high temperature strength characteristic |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0250902A (en) * | 1988-05-12 | 1990-02-20 | Sumitomo Electric Ind Ltd | Method for forming aluminum alloy for product having large diameter |
| JPH02277731A (en) * | 1989-04-20 | 1990-11-14 | Honda Motor Co Ltd | Production of product by using rapidly solidified powder of aluminum |
| JPH05305380A (en) * | 1992-04-28 | 1993-11-19 | Mazda Motor Corp | Manufacture of magnesium alloy member |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2746390B2 (en) | 1998-05-06 |
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