JP3114576B2 - Torque rod and method of manufacturing the same - Google Patents
Torque rod and method of manufacturing the sameInfo
- Publication number
- JP3114576B2 JP3114576B2 JP07184784A JP18478495A JP3114576B2 JP 3114576 B2 JP3114576 B2 JP 3114576B2 JP 07184784 A JP07184784 A JP 07184784A JP 18478495 A JP18478495 A JP 18478495A JP 3114576 B2 JP3114576 B2 JP 3114576B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- alloy
- connecting rod
- torque rod
- rod
- 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.)
- Expired - Fee Related
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60G—VEHICLE SUSPENSION ARRANGEMENTS
- B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
- B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
- B60G2206/10—Constructional features of arms
- B60G2206/11—Constructional features of arms the arm being a radius or track or torque or steering rod or stabiliser end link
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60G—VEHICLE SUSPENSION ARRANGEMENTS
- B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
- B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
- B60G2206/80—Manufacturing procedures
- B60G2206/82—Joining
- B60G2206/8201—Joining by welding
Landscapes
- Vehicle Body Suspensions (AREA)
- Forging (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、トラックのサスペンシ
ョンに装備されるトルクロッド等として使用され、両端
にリング状のエンド部材が設けられたトルクロッド及び
その製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a torque rod used as a torque rod or the like mounted on a truck suspension and provided with ring-shaped end members at both ends and a method of manufacturing the same.
【０００２】[0002]
【従来の技術】トラック等の後部サスペンションの構成
部品の一つであるトルクロッドは、棒状又はパイプ状の
両端部にリング状のエンドが設けられた構造を持ってい
る。トルクロッドとしては、鍛造によって一体に作られ
た鉄系材料が従来から使用されてきた。しかし、近年の
過積載規制の問題からトラック及びトラック部品の軽量
化が求められており、トルクロッドもその例外ではな
い。そこで、図１及び図２に示すように、トルクロッド
を二つのエンド１，２及び連結棒３に三分割した軽量化
構造が検討されている。この構造では、軽量かを図るた
めに連結棒３を鉄製の薄肉パイプで作製し、この連結棒
３にエンド１，２を溶接又は圧接している。2. Description of the Related Art A torque rod, which is one of the components of a rear suspension such as a truck, has a structure in which rod-shaped or pipe-shaped ends are provided with ring-shaped ends. As the torque rod, an iron-based material integrally formed by forging has been conventionally used. However, due to the recent problem of overloading regulations, it is required to reduce the weight of trucks and truck parts, and torque rods are no exception. Therefore, as shown in FIGS. 1 and 2, a light weight structure in which the torque rod is divided into two ends 1 and 2 and a connecting rod 3 has been studied. In this structure, the connecting rod 3 is made of an iron thin pipe in order to reduce the weight, and the ends 1 and 2 are welded or pressed to the connecting rod 3.
【０００３】[0003]
【発明が解決しようとする課題】図１，２に示したトル
クロッドは、連結棒３に薄肉の鉄製パイプを使用してい
るので、従来の鋳鍛造でできた中実のトルクロッドに比
較すると軽くなっている。しかし、素材として鉄を使用
していることから、軽量化には限界がある。更なる軽量
化を図るためには、鉄に匹敵する強度をもち、しかも鉄
よりも軽い素材を使用する必要がある。また、サスペン
ションは車体に対して車軸を保持する機能を受け持つ部
品であることから、その構成部品の一つであるトルクロ
ッドとしても、ただ単に軽い材料だけでは要求特性が満
足されない。すなわち、所定の寸法及び形状をもつ製品
として、強度，伸び，耐応力腐食割れ性等の要求特性を
満足する必要がある。具体的には、現在使用されている
鉄製トルクロッドとしては、エンド１，２の中心間距離
が５２２ｍｍのもので、３２，０００ｋｇｆ以上の引張
り強さ及び圧縮強度、±６，０００ｋｇｆの繰返し負荷
に２×１０6 回以上耐える引張り・圧縮疲労強度及び１
０％以上の伸びをもつことが要求される。本発明は、こ
のような要求特性を満足するＡｌ材料を使用してトルク
ロッドを作製することにより、トルクロッドを軽量化す
ることを目的とする。The torque rod shown in FIGS. 1 and 2 uses a thin-walled iron pipe for the connecting rod 3, so that it can be compared with a conventional solid torque rod made by casting and forging. It is getting lighter. However, since iron is used as a material, there is a limit to weight reduction. In order to achieve further weight reduction, it is necessary to use a material having strength comparable to iron and lighter than iron. In addition, since the suspension is a part having a function of holding the axle with respect to the vehicle body, the required characteristics of the torque rod, which is one of the components thereof, cannot be satisfied only with a light material. That is, it is necessary for a product having a predetermined size and shape to satisfy required characteristics such as strength, elongation, and stress corrosion cracking resistance. Specifically, the iron torque rod currently used has a center-to-center distance between the ends 1 and 2 of 522 mm, and has a tensile strength and a compressive strength of 32,000 kgf or more, and a repetitive load of ± 6,000 kgf. Tensile and compressive fatigue strength to withstand 2 × 10 6 times or more and 1
It is required to have an elongation of 0% or more. An object of the present invention is to reduce the weight of a torque rod by producing a torque rod using an Al material satisfying such required characteristics.
【０００４】[0004]
【課題を解決するための手段】本発明のトルクロッド
は、その目的を達成するため、Ａｌ合金の押出しパイプ
から作製された連結棒の両端部にＡｌ合金製のエンドが
溶接又は圧接されたトルクロッドであり、エンドがＳ
ｉ：１．０〜１．５重量％，Ｃｕ：０．４〜０．９重量
％，Ｍｎ：０．２〜０．６重量％，Ｍｇ：０．８〜１．
５重量％，Ｃｒ：０．３〜０．９重量％を含み、Ｆｅ含
有量を０．２５重量％以下に規制すると共に、Ｍｎ＋Ｃ
ｒの合計含有量が１．２重量％以下に規制された組成を
もつＡｌ合金（以下、Ａｌ−Ｍｇ−Ｓｉ系という）製
で、前記連結棒がＺｎ：４．０〜６．５重量％，Ｍｇ：
０．５〜２．０重量％，Ｃｕ：０．０１〜０．２重量
％，Ｍｎ：０．２〜０．７重量％，Ｃｒ：０．０５〜
０．３重量％，Ｚｒ：０．０５〜０．２５重量％，Ｆ
ｅ：０．０１〜０．４重量％を含むＡｌ合金（以下、Ａ
ｌ−Ｚｎ−Ｍｇ系という）製であることを特徴とする。In order to achieve the object, a torque rod according to the present invention has a connecting rod made of an extruded pipe made of an Al alloy, and a connecting rod made of an Al alloy is welded or pressed to an end made of an Al alloy at both ends. Rod and end S
i: 1.0 to 1.5% by weight, Cu: 0.4 to 0.9% by weight, Mn: 0.2 to 0.6% by weight, Mg: 0.8 to 1.
5% by weight, Cr: 0.3 to 0.9% by weight, the Fe content is restricted to 0.25% by weight or less, and Mn + C
made of an Al alloy (hereinafter, referred to as an Al-Mg-Si system) having a composition in which the total content of r is regulated to 1.2% by weight or less, wherein the connecting rod is Zn: 4.0 to 6.5% by weight. , Mg:
0.5 to 2.0% by weight, Cu: 0.01 to 0.2% by weight, Mn: 0.2 to 0.7% by weight, Cr: 0.05 to
0.3% by weight, Zr: 0.05 to 0.25% by weight, F
e: Al alloy containing 0.01 to 0.4% by weight (hereinafter referred to as A
1-Zn-Mg).
【０００５】エンド用Ａｌ合金としては、更にＴｉ：
０．００５〜０．０５重量％，Ｂ：０．０００１〜０．
０１重量％及びＺｒ：０．１〜０．２重量％の１種又は
２種以上を含むものが使用される。連結棒用Ａｌ合金と
しては、更にＴｉ：０．００５〜０．２重量％，Ｂ：
０．０００１〜０．０５重量％及びＶ：０．０１〜０．
１重量％の１種又は２種以上を含むものが使用される。
また、Ａｌ−Ｍｇ−Ｓｉ系のＡｌ合金をエンドに、Ａｌ
−Ｚｎ−Ｍｇ系のＡｌ合金を連結棒に使用することもで
きる。Ａｌ−Ｍｇ−Ｓｉ系のＡｌ合金では、鋳造材又は
押出し材を鍛造し、次いで５１０〜５５５℃に加熱後、
水冷して１５５〜１９０℃に５〜２０時間保持する熱処
理を施し、該熱処理後のＡｌ合金からエンド又は連結棒
が作製される。Ａｌ−Ｚｎ−Ｍｎ系では、鋳造材又は押
出し材を鍛造し、次いで４３０〜４７０℃に加熱後、空
冷又は炉冷してエンド又は連結棒が作製される。Ａｌ−
Ｚｎ−Ｍｎ系では、更に１１０〜１３０℃に２３〜２５
時間保持し、次いで１５０〜１６０℃に８〜１６時間保
持する二段時効処理を施すことにより、強度を向上させ
ることができる。As an Al alloy for end use, Ti:
0.005 to 0.05% by weight, B: 0.0001 to 0.
A material containing one or more of 01% by weight and Zr: 0.1 to 0.2% by weight is used. As the Al alloy for the connecting rod, Ti: 0.005 to 0.2% by weight, B:
0.0001-0.05% by weight and V: 0.01-0.
Those containing 1% by weight or one or more types are used.
In addition, an Al-Mg-Si-based Al alloy is
-A Zn-Mg based Al alloy may be used for the connecting rod. In an Al-Mg-Si-based Al alloy, a cast material or an extruded material is forged and then heated to 510 to 555 ° C.
Heat treatment is performed by cooling with water and maintaining the temperature at 155 to 190 ° C. for 5 to 20 hours, and an end or a connecting rod is manufactured from the heat-treated Al alloy. In the Al-Zn-Mn system, a cast material or an extruded material is forged, then heated to 430 to 470 ° C, and air-cooled or furnace-cooled to produce an end or a connecting rod. Al-
In the case of a Zn-Mn system, it is 23 to 25 at 110 to 130 ° C.
The strength can be improved by performing a two-stage aging treatment of holding for a period of time and then holding at 150 to 160 ° C. for 8 to 16 hours.
【０００６】[0006]
【作用】本発明では、Ａｌ−Ｍｇ−Ｓｉ系のＡｌ合金を
エンド又は連結棒の材料として、Ａｌ−Ｚｎ−Ｍｎ系の
Ａｌ合金を他方の連結棒又はエンドの材料として使用す
る。Ａｌ−Ｍｇ−Ｓｉ系のＡｌ合金は、微細なＭｇ2 Ｓ
ｉの析出によって必要な強度が確保される。この系統の
Ａｌ合金にＣｕ，Ｃｒ，Ｍｎ等を添加すると、マトリッ
クスの固溶，晶出及び組織制御によって強度が向上す
る。そこで、トルクロッドとしての用途に応じてより高
いＡｌ合金にするためには、先ずＳｉ及びＭｇを増量し
てＭｇ2 Ｓｉの析出量を増加させることが考えられる。
しかし、単純にＳｉ及びＭｇの含有量を増加させるだけ
では、伸び，靭性等が低下するばかりでなく、目標とす
る強度も得られない。本発明者等は、Ｍｇ2 Ｓｉ系析出
物が機械的性質に与える影響や、熱処理が鍛造材・押出
し材のマクロ組織の結晶成長に与える影響を種々の観点
から調査した。その結果、Ｍｇ2 Ｓｉ系析出物の作用を
有効に活用し、且つマクロ組織の結晶成長を抑制するた
めには、合金成分，その含有量及び熱処理条件を相互の
関連を考慮しながら定める必要があるとの結論に至っ
た。In the present invention, an Al-Mg-Si-based Al alloy is used as a material for an end or a connecting rod, and an Al-Zn-Mn-based Al alloy is used as a material for the other connecting rod or an end. Al-Mg-Si based Al alloy is fine Mg 2 S
The required strength is secured by the precipitation of i. When Cu, Cr, Mn or the like is added to the Al alloy of this system, the strength is improved by controlling the solid solution, crystallization and structure of the matrix. Therefore, in order to obtain a higher Al alloy depending on the use as a torque rod, it is conceivable to first increase the amount of Si and Mg to increase the amount of Mg 2 Si deposited.
However, simply increasing the contents of Si and Mg not only lowers elongation, toughness, etc., but also fails to achieve the desired strength. The present inventors investigated the effects of the Mg 2 Si-based precipitate on the mechanical properties and the effects of the heat treatment on the crystal growth of the macrostructure of the forged or extruded material from various viewpoints. As a result, in order to effectively utilize the action of the Mg 2 Si-based precipitates and to suppress the crystal growth of the macrostructure, it is necessary to determine the alloy components, their contents, and the heat treatment conditions in consideration of their mutual relations. I came to the conclusion.
【０００７】必要とするＭｇ2 Ｓｉ系析出物の作用及び
マクロ組織の微細化を図るためには、本発明者等の実験
から、Ｓｉ及びＭｇ含有量をそれぞれ１．０〜１．５重
量％及び０．８〜１．５重量％に規定する必要があるこ
とを見い出した。しかし、Ｓｉ及びＭｇの含有量がこの
範囲にあっても、熱間押出し後のＡｌ合金にＴ6 処理を
施したり、熱間又は冷間鍛造したＡｌ合金をＴ6 処理す
るとき、急激な結晶粒の成長によってマクロ組織が粗大
化し、強度，伸び等の機械的性質が低下する現象がみら
れる。熱処理によって加工組織の再結晶粒が粗大化する
ことは、Ｃｒ及びＭｎの複合添加と熱処理条件の適正化
によって抑制される。その結果、得られたＡｌ合金は、
微細な結晶粒をもつ組織となり、強度及び伸びが顕著に
改善される。Ｃｒ及びＭｎの複合添加による性質改善
は、熱間又は冷間での加工を行った後で溶体化処理した
際に再結晶の粗大成長を抑制する作用に起因するものと
推察される。Ｃｒ及びＭｎの複合添加に加え、更にＺｒ
を併用添加すると、伸びが一層向上すると共に結晶組織
がより微細になる。これは、Ｍｎ及びＣｒが再結晶粒の
粗大化を抑制する作用を呈するのに対し、Ｍｎ及びＣｒ
の結晶粒成長抑制効果を超えるような高加工領域におい
て再結晶する場合に、Ｚｒが再結晶粒の微細化を促進さ
せることに起因する。In order to achieve the required action of the Mg 2 Si-based precipitates and to make the macrostructure finer, experiments by the present inventors show that the contents of Si and Mg are set to 1.0 to 1.5% by weight, respectively. And 0.8 to 1.5% by weight. However, the content of Si and Mg is in the above range, or subjected to T 6 treatment Al alloy after hot extrusion, when hot or cold forged Al alloy T 6 processes, rapid crystal A phenomenon is seen in which the macrostructure is coarsened by the growth of grains, and mechanical properties such as strength and elongation are reduced. The coarsening of the recrystallized grains of the processed structure due to the heat treatment is suppressed by adding Cr and Mn in combination and optimizing the heat treatment conditions. As a result, the obtained Al alloy is
A structure having fine crystal grains is obtained, and strength and elongation are remarkably improved. The property improvement by the combined addition of Cr and Mn is presumed to be due to the action of suppressing coarse growth of recrystallization when solution treatment is performed after hot or cold working. In addition to the composite addition of Cr and Mn, Zr
When added together, elongation is further improved and the crystal structure becomes finer. This is because while Mn and Cr have the effect of suppressing the coarsening of recrystallized grains, Mn and Cr
This is because Zr promotes the refinement of recrystallized grains when recrystallizing in a highly processed region exceeding the crystal grain growth suppressing effect of the above.
【０００８】以下、本発明で使用されるＡｌ−Ｍｇ−Ｓ
ｉ系Ａｌ合金の合金成分，含有量等について説明する。
Ｓｉ：１．０〜１．５重量％ 析出効果によりＡｌ合金の強度を向上させる合金元素で
ある。本発明の合金系ではＭｇと併用添加しているの
で、Ｍｇ2 Ｓｉ系化合物が析出し、強度が向上する。こ
のようなＳｉ添加の作用は、１．０重量％以上の添加で
顕著になる。しかし、１．５重量％を超える過剰のＳｉ
添加は、Ａｌ合金の液相線温度を上昇させ、溶製や鋳造
等を困難にする。また、Ｓｉ含有量が過剰になると、押
出し性，鍛造加工性等が劣化する。 Ｃｕ：０．４〜０．９重量％ マトリックスを固溶強化し、強度向上に有効なＭｇ2 Ｓ
ｉの析出を促進させる有効な合金元素である。Ｃｕの作
用は、０．４重量％以上の添加で顕著になる。しかし、
０．９重量％を超える多量のＣｕ含有は、焼入れ感受
性，耐食性等を劣化させる。Hereinafter, the Al-Mg-S used in the present invention will be described.
The alloy component and content of the i-type Al alloy will be described.
Si: 1.0-1.5% by weight An alloy element that improves the strength of an Al alloy by a precipitation effect. In the alloy system of the present invention, since it is added in combination with Mg, the Mg 2 Si-based compound precipitates and the strength is improved. Such an effect of the addition of Si becomes remarkable when 1.0% by weight or more is added. However, excess Si over 1.5% by weight
The addition increases the liquidus temperature of the Al alloy, making it difficult to melt or cast. Further, when the Si content is excessive, the extrudability, forgeability and the like are deteriorated. Cu: 0.4 to 0.9% by weight Mg 2 S effective for strengthening the matrix by solid solution strengthening and improving the strength
It is an effective alloying element that promotes the precipitation of i. The effect of Cu becomes significant when added at 0.4% by weight or more. But,
A large amount of Cu exceeding 0.9% by weight deteriorates quenching sensitivity, corrosion resistance and the like.
【０００９】Ｍｎ：０．２〜０．６重量％ 結晶粒の成長を抑制し、熱処理後の組織を微細に維持す
る上で有効な合金元素であり、０．２重量％以上の添加
でＭｎの作用が顕著になる。しかし、０．６重量％を超
える多量のＭｎを含有させると、鍛造時の加工性が悪化
する。 Ｍｇ：０．８〜１．５重量％ Ｓｉと反応してＭｇ2 Ｓｉ系化合物となってマトリック
スに析出し、Ａｌ合金の強度を向上させる。この析出効
果を得るためには、０．８重量％以上のＭｇ含有量が必
要とされる。しかし、１．５重量％を超える多量のＭｇ
を含有させると、析出効果が飽和するばかりでなく、焼
入れ感受性が低下する。 Ｃｒ：０．３〜０．９重量％でＭｎ＋Ｃｒ≦１．２重量
％以下 Ｍｎと共同して結晶粒の粗大化を抑制する作用を呈する
合金元素である。Ｃｒの添加効果は、０．３重量％以上
の含有量で顕著になる。しかし、０．９重量％を超える
多量添加は、加工性を悪化させる。また、Ｃｒ含有量
は、Ｍｎ含有量との合計で１．２重量％以下に規制する
必要がある。Ｃｒ＋Ｍｎの合計含有量を１．２重量％に
維持しておくとき、他に悪影響を与えることなく、前述
したＣｒ及びＭｎの複合添加による効果が得られる。こ
れに対して、Ｃｒ＋Ｍｎ含有量が１．２重量％を超える
と、巨大なＡｌ−Ｍｎ−Ｃｒ系の化合物が晶出し易くな
り、Ａｌ合金の伸びが著しく低下する。Mn: 0.2-0.6% by weight Mn is an effective alloying element for suppressing the growth of crystal grains and maintaining a fine structure after heat treatment. The effect of becomes significant. However, when a large amount of Mn exceeding 0.6% by weight is contained, the workability during forging deteriorates. Mg: 0.8 to 1.5% by weight Reacts with Si to form an Mg 2 Si-based compound and precipitates on the matrix, thereby improving the strength of the Al alloy. In order to obtain this precipitation effect, a Mg content of 0.8% by weight or more is required. However, a large amount of Mg exceeding 1.5% by weight
When not only is contained, the precipitation effect is saturated, but also the quenching sensitivity is reduced. Cr: 0.3 to 0.9% by weight and Mn + Cr ≦ 1.2% by weight or less An alloy element exhibiting an effect of suppressing the coarsening of crystal grains in cooperation with Mn. The effect of adding Cr becomes remarkable at a content of 0.3% by weight or more. However, addition of a large amount exceeding 0.9% by weight deteriorates processability. Further, the Cr content needs to be regulated to 1.2% by weight or less in total with the Mn content. When the total content of Cr + Mn is maintained at 1.2% by weight, the above-described effect of the combined addition of Cr and Mn can be obtained without adversely affecting other components. On the other hand, when the content of Cr + Mn exceeds 1.2% by weight, a large Al-Mn-Cr-based compound is easily crystallized, and the elongation of the Al alloy is significantly reduced.
【００１０】Ｆｅ：０．２５重量％以下 不純物としてＡｌ合金に混入するＦｅは、伸び，耐食性
等に悪影響を及ぼすＡｌ−Ｆｅ−Ｓｉ系化合物となって
マトリックスに分散される。この点、Ｆｅ含有量は、少
なければ少ないほど好ましいが、過度にＦｅ含有量を低
減することは合金の溶製を困難にする。そこで、本発明
にあっては、Ｆｅ含有量の上限を実質的な悪影響がみら
れない０．２５重量％に設定した。 Ｔｉ：０．００５〜０．０５重量％ 必要に応じて添加される合金元素であり、組織を安定さ
せると共に、溶接部又は圧接部の機械的性質を向上させ
る作用を呈する。このような作用は、０．００５重量％
以上のＴｉ添加で顕著になる。しかし、０．０５重量％
を超える多量のＴｉを添加すると、Ａｌ合金の靭性が劣
化する。Fe: 0.25% by weight or less Fe mixed into the Al alloy as an impurity becomes an Al—Fe—Si compound which has a bad influence on elongation, corrosion resistance and the like, and is dispersed in the matrix. In this regard, the Fe content is preferably as small as possible, but excessively reducing the Fe content makes it difficult to melt the alloy. Therefore, in the present invention, the upper limit of the Fe content is set to 0.25% by weight where no substantial adverse effect is observed. Ti: 0.005 to 0.05% by weight An alloying element that is added as necessary, and has the effect of stabilizing the structure and improving the mechanical properties of the welded portion or the pressed portion. Such an effect is 0.005% by weight.
It becomes remarkable with the above Ti addition. However, 0.05% by weight
If a large amount of Ti is added, the toughness of the Al alloy deteriorates.
【００１１】Ｂ：０．０００１〜０．０１重量％ Ｔｉと同様に組織の安定化に有効な合金元素であり、
０．０００１重量％以上のＢ添加でその効果が顕著にな
る。しかし、０．０１重量％を超える多量のＢを添加す
ると、Ａｌ合金の靭性が劣化する。 Ｚｒ：０．１〜０．２重量％ 必要に応じて添加される合金元素であり、Ｍｎ及びＣｒ
と共同して結晶粒の粗大化を抑制する作用を呈する。Ｚ
ｒは、特に押出し工程を経た鍛造品に押出しによって形
成された繊維組織を残存させることにより、引っ張り強
度を向上させることにも作用する。このような添加作用
は、０．１重量％以上のＺｒ添加で顕著になる。しか
し、多量のＺｒ含有は加工性に悪影響を与えるので、Ｚ
ｒを添加する場合には０．２重量％を上限とする。B: 0.0001 to 0.01% by weight Like Ti, it is an alloy element effective for stabilizing the structure.
The effect becomes remarkable when 0.0001% by weight or more of B is added. However, when a large amount of B exceeding 0.01% by weight is added, the toughness of the Al alloy deteriorates. Zr: 0.1-0.2% by weight Alloying element added as necessary, such as Mn and Cr
In cooperation with the above, an effect of suppressing the coarsening of crystal grains is exhibited. Z
r also acts to improve the tensile strength by leaving the fiber structure formed by extrusion particularly on the forged product that has undergone the extrusion process. Such an addition effect becomes significant when Zr is added in an amount of 0.1% by weight or more. However, a large content of Zr adversely affects the processability, so that Z
When adding r, the upper limit is 0.2% by weight.
【００１２】溶体化処理及び焼入れの条件：前述した組
成をもつＡｌ合金の強度を向上させるためには、先ず強
度改善元素を完全に固溶させる必要がある。そのために
は、少なくとも５１０℃以上の温度にＡｌ合金を加熱す
ることが必要となる。しかし、５５５℃を超える温度で
は、部分的な溶解が生じ、欠陥が発生する。溶体化処理
後のＡｌ合金は、粗大なＭｇＳｉ系析出物が生じないよ
うに水焼入れすることが要求される。仮に溶体化後のＡ
ｌ合金を徐冷すると、析出したＭｇ2 Ｓｉ系析出物が粗
大に成長し、目標とする強度が得られない。 時効処理条件：水焼入れされたＡｌ合金は、合金元素が
過飽和で固溶した状態にある。このＡｌ合金を１５５〜
１９０℃に５〜２０時間保持すると、組織全体に微細な
Ｍｇ2 Ｓｉ系化合物が析出し、目標とする強度が得られ
る。しかし、温度条件又は保持時間が１５５〜１９０℃
又は５〜２０時間から外れると、析出したＭｇ2 Ｓｉが
大きく成長し、或いは十分なＭｇ2 Ｓｉが析出せず、目
標とする強度が得られない。このようにして成分・組成
が調整され、熱処理されたＡｌ合金は、３８ｋｇｆ／ｃ
ｍ2 以上の引張り強さ及び１３％以上の伸びを示し、ト
ルクロッドの連結棒やエンドとしての要求特性を十分に
満足する。Solution treatment and quenching conditions: In order to improve the strength of an Al alloy having the above-described composition, it is necessary to completely dissolve the strength improving element first. For that purpose, it is necessary to heat the Al alloy to at least a temperature of 510 ° C. or higher. However, at temperatures above 555 ° C., partial melting occurs and defects occur. The Al alloy after the solution treatment is required to be water-quenched so as not to generate coarse MgSi-based precipitates. Assuming that A after solution
When the 1 alloy is gradually cooled, the precipitated Mg 2 Si-based precipitate grows coarsely, and the desired strength cannot be obtained. Aging treatment conditions: The water-quenched Al alloy is in a state in which the alloy elements are supersaturated and dissolved. 155-
When the temperature is maintained at 190 ° C. for 5 to 20 hours, a fine Mg 2 Si-based compound is precipitated over the entire structure, and a target strength can be obtained. However, the temperature condition or the holding time is 155 to 190 ° C.
Otherwise, if it is out of the range of 5 to 20 hours, the deposited Mg 2 Si grows large, or sufficient Mg 2 Si does not precipitate, and the target strength cannot be obtained. The component and composition adjusted in this way and the heat-treated Al alloy is 38 kgf / c
It exhibits a tensile strength of not less than m 2 and an elongation of not less than 13%, and sufficiently satisfies the required characteristics as a connecting rod or end of a torque rod.
【００１３】他方、Ａｌ−Ｚｎ−Ｍｎ系のＡｌ合金に含
まれる合金成分等の作用・効果は、次の通りである。 Ｚｎ：４．０〜６．５重量％ Ｍｇと共にＺｎ−Ｍｇ系の微細な析出物を形成し、Ａｌ
合金の強度を向上させる合金元素である。このような強
度向上の効果は、Ｚｎ含有量４．０重量％以上で顕著に
なる。しかし、６．５重量％を超える多量のＺｎが含ま
れると、耐応力腐食割れ性や加工性が劣化する。 Ｍｇ：０．５〜２．０重量％ Ｚｎと同様に強度向上に不可欠の合金元素であり、０．
５重量％以上の含有量で十分な強度が得られる。しか
し、２．０重量％を超える多量のＭｇが含まれると、耐
応力腐食割れ性や加工性が劣化する。 Ｃｕ：０．０１〜０．２重量％ 耐応力腐食割れ性を改善する合金元素であり、０．０１
重量％以上でＣｕの添加効果が顕著になる。しかし、Ｃ
ｕ含有量が０．２重量％を超えると、却って耐応力腐食
割れ性が劣化し、また溶接性も劣化する。On the other hand, the functions and effects of the alloy components contained in the Al-Zn-Mn Al alloy are as follows. Zn: 4.0-6.5% by weight A Zn-Mg-based fine precipitate is formed together with Mg,
An alloy element that improves the strength of the alloy. Such an effect of improving the strength becomes remarkable when the Zn content is 4.0% by weight or more. However, when a large amount of Zn exceeding 6.5% by weight is contained, the stress corrosion cracking resistance and the workability deteriorate. Mg: 0.5 to 2.0% by weight Like Zn, it is an alloy element indispensable for improving the strength.
Sufficient strength can be obtained with a content of 5% by weight or more. However, when a large amount of Mg exceeding 2.0% by weight is contained, stress corrosion cracking resistance and workability deteriorate. Cu: 0.01 to 0.2% by weight An alloying element for improving the stress corrosion cracking resistance.
The effect of adding Cu becomes remarkable when the content is not less than% by weight. But C
If the u content exceeds 0.2% by weight, the stress corrosion cracking resistance deteriorates and the weldability also deteriorates.
【００１４】Ｍｎ：０．２〜０．７重量％ 組織の安定化を図り、強度を向上させる作用を呈する。
Ｍｎの添加効果は、０．２重量％以上の含有量で顕著に
なる。しかし、０．７重量％を超える多量のＭｎが含ま
れると、巨大化合物が生成し、靭性や加工性を劣化させ
る虞れがある。 Ｃｒ：０．０５〜０．３重量％ Ｍｎと同様に組織安定化のために有効な合金元素であ
り、０．０５重量％以上の含有量でＣｕの添加効果が顕
著になる。しかし、０．３重量％を超える多量のＣｒ含
有は、組織安定化効果が飽和するばかりでなく、靭性や
加工性に有害な巨大化合物を生成させる原因となる。 Ｚｒ：０．０５〜０．２５重量％ Ｍｎと同様に組織の安定化に有効な合金元素であり、
０．０５重量％以上の含有量でＺｒの添加効果が顕著に
なる。しかし、０．２５重量％をこえる多量のＺｒを含
有させると、組織安定化効果が飽和するばかりでなく、
靭性や加工性に有害な巨大化合物を生成させる原因とな
る。Mn: 0.2 to 0.7% by weight The effect of stabilizing the structure and improving the strength is exhibited.
The effect of adding Mn becomes remarkable at a content of 0.2% by weight or more. However, when a large amount of Mn exceeding 0.7% by weight is contained, a giant compound may be generated, and toughness and workability may be deteriorated. Cr: 0.05 to 0.3% by weight Similar to Mn, Cr is an effective alloying element for stabilizing the structure. At a content of 0.05% by weight or more, the effect of adding Cu becomes remarkable. However, the presence of a large amount of Cr exceeding 0.3% by weight not only saturates the structure stabilizing effect but also causes the formation of a giant compound harmful to toughness and workability. Zr: 0.05-0.25% by weight Like Mn, it is an alloy element effective for stabilizing the structure.
When the content is 0.05% by weight or more, the effect of adding Zr becomes remarkable. However, when a large amount of Zr exceeds 0.25% by weight, not only the tissue stabilizing effect is saturated, but also
It can cause the formation of giant compounds harmful to toughness and workability.
【００１５】Ｆｅ：０．０１〜０．４重量％ 組織を安定化させ、耐応力腐食割れ性を改善する合金元
素である。このような効果は、０．０１重量％以上の含
有量で顕著になる。しかし、０．４重量％を超える多量
のＦｅ含有量は、却って靭性や加工性を劣化させる。 Ｔｉ：０．００５〜０．２重量％ 必要に応じて添加される合金元素であり、組織の安定化
を図り、溶接部又は圧接部の機械的性質を向上させる作
用を呈する。このような効果は、０．００５重量％以上
の含有量で顕著になる。しかし、０．２重量％を超える
多量のＴｉ含有量は、靭性や加工性に有害な巨大化合物
を生成させる原因となる。 Ｂ：０．０００１〜０．０５重量％ 必要に応じて添加される合金元素であり、０．０００１
重量％以上のＢ添加で組織安定化の効果が顕著になる。
しかし、０．０５重量％を超えて過剰に添加しても、Ｂ
の添加効果が飽和するばかりでなく、靭性や加工性に有
害な巨大化合物を生成させる原因となる。 Ｖ：０．０１〜０．１重量％ 必要に応じて添加される合金元素であり、耐応力腐食割
れ性を改善する作用を呈する。このような添加効果は、
０．０１重量％以上で顕著になる。しかし、０．１重量
％を超える過剰添加は、却って加工性及び靭性を劣化さ
せる。Fe: 0.01 to 0.4% by weight An alloy element that stabilizes the structure and improves the resistance to stress corrosion cracking. Such effects become remarkable at a content of 0.01% by weight or more. However, a large content of Fe exceeding 0.4% by weight deteriorates toughness and workability. Ti: 0.005 to 0.2% by weight An alloy element added as necessary, and has a function of stabilizing the structure and improving the mechanical properties of the welded portion or the press-welded portion. Such effects become remarkable at a content of 0.005% by weight or more. However, a large Ti content exceeding 0.2% by weight causes formation of a giant compound harmful to toughness and workability. B: 0.0001 to 0.05% by weight An alloy element added as necessary,
The effect of stabilizing the structure becomes remarkable when B is added in an amount of not less than% by weight.
However, even if it is added in excess of 0.05% by weight, B
Not only saturates the effect of addition, but also causes the formation of giant compounds harmful to toughness and workability. V: 0.01 to 0.1% by weight An alloy element added as needed, and has an effect of improving stress corrosion cracking resistance. Such an addition effect
It becomes remarkable at 0.01% by weight or more. However, excessive addition exceeding 0.1% by weight rather deteriorates workability and toughness.
【００１６】Ａｌ−Ｚｎ−Ｍｎ系のＡｌ合金は、以上の
合金元素の他に、不純物として０．３重量％未満のＳ
ｉ、単独で０．０５重量％未満の他の元素を含むことが
許容される。これら不純物元素を許容範囲に規制してお
くとき、トルクロッドとしての要求特性が満足される。 溶体化処理及び焼入れの条件：前述した組成をもつＡｌ
合金の強度を向上させるためには、先ず強度改善元素を
完全に固溶させる必要がある。そのためには、少なくと
も４３０℃以上の温度にＡｌ合金を加熱することが必要
となる。しかし、４７０℃を超える温度では、部分的な
溶解が生じ、欠陥が発生する。溶体化処理後のＡｌ合金
は、水冷のような急冷を施すと、内部歪みが大きくなり
すぎて応力腐食割れの原因となることから、空冷又は炉
冷により冷却される。ただし、押出し材では、押出し工
程中に各合金元素が固溶されることから、溶体化処理工
程を省略することができる。The Al—Zn—Mn Al alloy contains less than 0.3% by weight of S as impurities in addition to the above alloy elements.
i. It is permissible to contain less than 0.05% by weight of other elements alone. When these impurity elements are restricted to an allowable range, required characteristics as a torque rod are satisfied. Solution treatment and quenching conditions: Al with the above composition
In order to improve the strength of the alloy, it is first necessary to completely dissolve the strength improving element in solid solution. For that purpose, it is necessary to heat the Al alloy to at least 430 ° C. or higher. However, at temperatures above 470 ° C., partial melting occurs and defects occur. If the Al alloy after the solution treatment is subjected to rapid cooling such as water cooling, the internal strain becomes too large and causes stress corrosion cracking. Therefore, the Al alloy is cooled by air cooling or furnace cooling. However, in the case of an extruded material, the solution treatment step can be omitted since each alloy element is dissolved in the extrusion step.
【００１７】時効処理条件：冷却されたＡｌ合金は、合
金元素が過飽和で固溶した状態にある。このＡｌ合金
は、室温に保持しておくとＺｎ−Ｍｇ系の微細な析出物
が形成され、品質が安定して目標とする強度が得られ
る。しかし、このような自然時効は１か月以上の長期間
が必要とされる。そこで、Ｚｎ−Ｍｇ系微細析出物の生
成を促進させるため、１１０〜１３０℃に２３〜２５時
間保持した後、１５０〜１６０℃に８〜１６時間保持す
る人工時効によって、早期に品質を安定化させることが
好ましい。また、押出し材のように溶体化処理を省略し
た材料では、Ｚｎ−Ｍｇ系の微細化合物を均一に析出さ
せると共に、応力腐食割れの原因になることもある押出
し加工時の内部歪みを除去する上でも時効処理が有効で
ある。時効温度及び保持時間が前述した範囲を外れる
と、時効効果が十分でなく、或いは過時効による問題が
発生する。このようにして成分・組成が調整され、熱処
理されたＡｌ合金は、３２ｋｇｆ／ｃｍ2 以上の引張り
強さ及び１１％以上の伸びを示し、トルクロッドの連結
棒やエンドとしての要求特性を十分に満足する。Aging treatment condition: The cooled Al alloy is in a state where the alloy elements are supersaturated and dissolved. When this Al alloy is kept at room temperature, Zn-Mg based fine precipitates are formed, and the quality is stabilized and the target strength is obtained. However, such natural aging requires a long period of one month or more. Therefore, in order to promote the formation of Zn-Mg based fine precipitates, after maintaining at 110 to 130 ° C for 23 to 25 hours, the quality is stabilized early by artificial aging at 150 to 160 ° C for 8 to 16 hours. Preferably. In the case of a material such as an extruded material which is not subjected to a solution treatment, a Zn-Mg based fine compound is uniformly precipitated, and internal strain during extrusion which may cause stress corrosion cracking is removed. But aging is effective. If the aging temperature and the holding time are out of the ranges described above, the aging effect is not sufficient, or a problem due to overaging occurs. The Al alloy heat-treated with its components and compositions adjusted in this manner exhibits a tensile strength of 32 kgf / cm 2 or more and an elongation of 11% or more, and sufficiently satisfies the required characteristics as a connecting rod or end of a torque rod. To be satisfied.
【００１８】[0018]
【実施例】表１に示した組成をもつＡｌ−Ｍｇ−Ｓｉ系
の各種Ａｌ合金及び表２に示した組成をもつＡｌ−Ｚｎ
−Ｍｎ系の各種Ａｌ合金を熱処理し、図３（ａ）及び
（ｂ）に示すように外径φ1 ＝１３０ｍｍ，内径φ2 ＝
１０５ｍｍ及び幅Ｗ＝５１ｍｍのエンド１，２を作製し
た。エンド１，２の環状部４の一側に、曲率半径５０ｍ
ｍで立ち上がった先端径６０ｍｍの接合用突出部５を形
成した。他方、連結棒３としては、熱処理した同様なＡ
ｌ合金押出し材から作製された外径６０ｍｍのパイプを
使用した。接合用突出部５の端面に連結棒３を押し当
て、ＭＩＧ溶接又は摩擦圧接によって接合部６を形成
し、エンド１，２を連結棒３に一体化した。なお、連結
棒３としては、ＭＩＧ溶接による場合は内径３５ｍｍ、
摩擦圧接による場合は内径４０ｍｍのパイプを使用し
た。ＭＩＧ溶接条件は、溶接棒Ａ５３５６を使用し、電
圧２８Ｖ，電流２８０Ａ，溶接速度１ｍ／分に設定し
た。摩擦圧接には、加熱圧力５００ｋｇｆ／ｃｍ2 ，加
熱時間５秒，アプセット圧力１０００ｋｇｆ／ｃｍ2及
びアプセット量１０ｍｍを採用した。DESCRIPTION OF THE PREFERRED EMBODIMENTS Various Al-Mg-Si Al alloys having the compositions shown in Table 1 and Al-Zn having the compositions shown in Table 2
-Heat treatment of various Mn-based Al alloys, as shown in FIGS. 3A and 3B, outer diameter φ 1 = 130 mm, inner diameter φ 2 =
Ends 1 and 2 having 105 mm and a width W = 51 mm were produced. A radius of curvature of 50 m is provided on one side of the annular portion 4 of the ends 1 and 2.
Thus, a joining protruding portion 5 having a tip diameter of 60 mm and rising at m was formed. On the other hand, as the connecting rod 3, a similar heat-treated A
A pipe having an outer diameter of 60 mm made from an extruded alloy was used. The connecting rod 3 was pressed against the end face of the joining protrusion 5 to form a joint 6 by MIG welding or friction welding, and the ends 1 and 2 were integrated with the connecting rod 3. The connecting rod 3 has an inner diameter of 35 mm in the case of MIG welding,
In the case of friction welding, a pipe having an inner diameter of 40 mm was used. The MIG welding conditions were set to a voltage of 28 V, a current of 280 A, and a welding speed of 1 m / min using a welding rod A5356. For the friction welding, a heating pressure of 500 kgf / cm 2 , a heating time of 5 seconds, an upset pressure of 1000 kgf / cm 2 and an upset amount of 10 mm were employed.
【００１９】[0019]
【表１】 [Table 1]
【００２０】[0020]
【表２】 [Table 2]
【００２１】実施例１：合金番号１の鋳造棒を熱間鍛造
してエンドを作製した後、５３０℃に加熱し、水冷し、
１８０℃に８時間保持する熱処理を施した。連結棒は、
合金番号６の鋳造棒を押出し加工した後、冷却し、１２
０℃に２４時間保持する時効処理によって製造した。こ
れらエンド及び連結棒をＭＩＧ溶接して得られたトルク
ロッドは、引張り強さ４１，０００ｋｇｆ，圧縮強度３
５，５００ｋｇｆ，エンド部の伸び１５．０％，連結棒
部の伸び１４．１％，接合部の伸び１３．１％で、±
６，０００ｋｇｆの繰返し負荷を２×０6 回与えた後で
も疲労により破損することがなかった。また、接合され
たトルクロッドから試験片を切り出し、ＪＩＳ Ｈ８７
１１に準拠した応力腐食割れ試験に供した。すなわち、
耐力の７５％を加えた状態で３．５％ＮａＣｌ溶液に浸
漬し、１０分浸漬→５０分乾燥の繰返しを３０日間継続
させた。そして、試験後のトルクロッドを観察したとこ
ろ、エンド部，連結棒部，接合部共に応力腐食割れが検
出されなかった。他方、摩擦圧接によって連結棒にエン
ドを接合したトルクロッドは、引張り強さ４１，０００
ｋｇｆ，圧縮強度３４，５００ｋｇｆ，エンド部の伸び
１５．１％，連結棒部の伸び１４．０％，接合部の伸び
１１．０％で、±６，０００ｋｇｆの繰返し負荷を２×
０6 回与えた後でも疲労により破損することがなかっ
た。また、同様な応力腐食割れ試験の結果では、エンド
部，連結棒部，接合部共に応力腐食割れが検出されなか
った。Example 1 A cast bar of alloy No. 1 was hot forged to produce an end, and then heated to 530 ° C. and cooled with water.
Heat treatment was performed at 180 ° C. for 8 hours. The connecting rod is
After extruding a casting rod of alloy number 6, the rod was cooled,
Manufactured by aging kept at 0 ° C. for 24 hours. The torque rod obtained by MIG welding the end and the connecting rod has a tensile strength of 41,000 kgf and a compressive strength of 3
5,500 kgf, end portion elongation 15.0%, connecting rod elongation 14.1%, joint elongation 13.1%, ±
The repeated load of 6,000kgf even after giving 2 × 0 6 times had never damaged by fatigue. In addition, a test piece was cut out from the joined torque rod, and JIS H87
It was subjected to a stress corrosion cracking test according to No. 11. That is,
With 75% of the proof stress added, it was immersed in a 3.5% NaCl solution, and repeated immersion for 10 minutes → drying for 50 minutes was continued for 30 days. When the torque rod after the test was observed, no stress corrosion cracking was detected in any of the end, the connecting rod, and the joint. On the other hand, the torque rod whose end is joined to the connecting rod by friction welding has a tensile strength of 41,000.
kgf, compressive strength 34,500 kgf, end part elongation 15.1%, connecting rod part elongation 14.0%, joint part elongation 11.0%, and a repetitive load of ± 6,000 kgf is 2 ×
Even after giving 0 6 times had never damaged by fatigue. Further, in the results of the similar stress corrosion cracking test, no stress corrosion cracking was detected in any of the end portion, the connecting rod portion, and the joint portion.
【００２２】実施例２：合金番号２の押出し棒を冷間鍛
造してエンドを作製した後、５５５℃に加熱し、水冷
し、１９０℃に８時間保持する熱処理を施した。連結棒
は、実施例１と同様な工程によって製造した。これらエ
ンド及び連結棒をＭＩＧ溶接して得られたトルクロッド
は、引張り強さ３９，０００ｋｇｆ，圧縮強度３５，０
００ｋｇｆ，エンド部の伸び１６．５％，連結棒部の伸
び１４．０％，接合部の伸び１３．６％で、±６，００
０ｋｇｆの繰返し負荷を２×０6 回与えた後でも疲労に
より破損することがなかった。また、実施例１と同じ応
力腐食割れ試験に供したところ、エンド部，連結棒部，
接合部共に応力腐食割れが検出されなかった。他方、摩
擦圧接によって連結棒にエンドを接合したトルクロッド
は、引張り強さ４１，０００ｋｇｆ，圧縮強度３４，０
００ｋｇｆ，エンド部の伸び１６．３％，連結棒部の伸
び１３．９％，接合部の伸び１１．１％で、±６，００
０ｋｇｆの繰返し負荷を２×０6 回与えた後でも疲労に
より破損することがなかった。また、同様な応力腐食割
れ試験の結果では、エンド部，連結棒部，接合部共に応
力腐食割れが検出されなかった。Example 2 An extruded rod of alloy No. 2 was cold forged to form an end, and then heated to 555 ° C., water-cooled, and heat-treated at 190 ° C. for 8 hours. The connecting rod was manufactured by the same process as in Example 1. A torque rod obtained by MIG welding these ends and the connecting rod has a tensile strength of 39,000 kgf and a compressive strength of 35.0 kg.
00kgf, end portion elongation 16.5%, connecting rod portion elongation 14.0%, joint portion elongation 13.6%, ± 6,00
The repeated load of 0kgf even after giving 2 × 0 6 times had never damaged by fatigue. When subjected to the same stress corrosion cracking test as in Example 1, the end portion, the connecting rod portion,
No stress corrosion cracking was detected in any of the joints. On the other hand, the torque rod whose end is joined to the connecting rod by friction welding has a tensile strength of 41,000 kgf and a compressive strength of 34,0.
± 6,00 kgf, elongation at the end 16.3%, elongation at the connecting rod 13.9%, and elongation at the joint 11.1%.
The repeated load of 0kgf even after giving 2 × 0 6 times had never damaged by fatigue. Further, in the results of the similar stress corrosion cracking test, no stress corrosion cracking was detected in any of the end portion, the connecting rod portion, and the joint portion.
【００２３】実施例３：合金番号６の押出し棒を熱間鍛
造してエンドを作製した後、４５０℃に加熱し、空冷し
た。連結棒は、合金番号２の押出しパイプを５４０℃に
加熱し、水冷した後、１８５℃で７時間保持する時効処
理によって製造した。これらエンド及び連結棒をＭＩＧ
溶接して得られたトルクロッドは、引張り強さ３７，０
００ｋｇｆ，圧縮強度３６，０００ｋｇｆ，エンド部の
伸び１３．２％，連結棒部の伸び１７．０％，接合部の
伸び１２．５％で、±６，０００ｋｇｆの繰返し負荷を
２×０6 回与えた後でも疲労により破損することがなか
った。また、実施例１と同じ応力腐食割れ試験に供した
ところ、エンド部，連結棒部，接合部共に応力腐食割れ
が検出されなかった。他方、摩擦圧接によって連結棒に
エンドを接合したトルクロッドは、引張り強さ３７，０
００ｋｇｆ，圧縮強度３５，０００ｋｇｆ，エンド部の
伸び１３．５％，連結棒部の伸び１６．８％，接合部の
伸び１１．４％で、±６，０００ｋｇｆの繰返し負荷を
２×０6 回与えた後でも疲労により破損することがなか
った。また、同様な応力腐食割れ試験の結果では、エン
ド部，連結棒部，接合部共に応力腐食割れが検出されな
かった。Example 3 An extruded rod of alloy No. 6 was hot forged to form an end, and then heated to 450 ° C. and air-cooled. The connecting rod was manufactured by heating the extruded pipe of alloy No. 2 to 540 ° C., cooling with water, and then keeping the pipe at 185 ° C. for 7 hours. MIG these end and connecting rod
The torque rod obtained by welding has a tensile strength of 37,0.
00Kgf, compressive strength 36,000Kgf, elongation 13.2% of the end portion, elongation 17.0 percent of the connecting rod portions, elongation 12.5% of the joint, 2 × 0 6 times repeated load ± 6,000Kgf Even after being given, there was no breakage due to fatigue. When subjected to the same stress corrosion cracking test as in Example 1, no stress corrosion cracking was detected in any of the end portion, the connecting rod portion, and the joint portion. On the other hand, the torque rod whose end is joined to the connecting rod by friction welding has a tensile strength of 37,0.
00Kgf, compressive strength 35,000Kgf, elongation 13.5% of the end portion, elongation 16.8% of the connecting rod portions, elongation 11.4% of the joint, 2 × 0 6 times repeated load ± 6,000Kgf Even after being given, there was no breakage due to fatigue. Further, in the results of the similar stress corrosion cracking test, no stress corrosion cracking was detected in any of the end portion, the connecting rod portion, and the joint portion.
【００２４】実施例４：合金番号７の押出し棒を熱間鍛
造してエンドを作製した後、冷却し、次いで９０℃×８
時間→１６０℃×８時間の時効処理を施した。連結棒
は、実施例３と同様に製造した。これらエンド及び連結
棒をＭＩＧ溶接して得られたトルクロッドは、引張り強
さ３３，０００ｋｇｆ，圧縮強度３６，０００ｋｇｆ，
エンド部の伸び１２．１％，連結棒部の伸び１６．８
％，接合部の伸び１１．５％で、±６，０００ｋｇｆの
繰返し負荷を２×０6 回与えた後でも疲労により破損す
ることがなかった。また、実施例１と同じ応力腐食割れ
試験に供したところ、エンド部，連結棒部，接合部共に
応力腐食割れが検出されなかった。他方、摩擦圧接によ
って連結棒にエンドを接合したトルクロッドは、引張り
強さ３３，５００ｋｇｆ，圧縮強度３５，０００ｋｇ
ｆ，エンド部の伸び１２．０％，連結棒部の伸び１６．
８％，接合部の伸び１１．２％で、±６，０００ｋｇｆ
の繰返し負荷を２×０6 回与えた後でも疲労により破損
することがなかった。また、同様な応力腐食割れ試験の
結果では、エンド部，連結棒部，接合部共に応力腐食割
れが検出されなかった。Example 4: An extruded rod of alloy No. 7 was hot forged to form an end, cooled, and then cooled to 90 ° C. × 8
Time → aged at 160 ° C. × 8 hours. The connecting rod was manufactured in the same manner as in Example 3. The torque rod obtained by MIG welding the end and the connecting rod has a tensile strength of 33,000 kgf, a compressive strength of 36,000 kgf,
12.1% elongation at end, 16.8 at connecting rod
%, Elongation 11.5% of the joint, never be broken due to fatigue even after giving 2 × 0 6 times repeated load of ± 6,000kgf. When subjected to the same stress corrosion cracking test as in Example 1, no stress corrosion cracking was detected in any of the end portion, the connecting rod portion, and the joint portion. On the other hand, the torque rod whose end is joined to the connecting rod by friction welding has a tensile strength of 33,500 kgf and a compressive strength of 35,000 kg.
f, elongation of end part 12.0%, elongation of connecting rod part
± 6,000kgf at 8%, elongation of joint 11.2%
It had never be damaged by the fatigue of repeated load, even after giving 2 × 0 6 times. Further, in the results of the similar stress corrosion cracking test, no stress corrosion cracking was detected in any of the end portion, the connecting rod portion, and the joint portion.
【００２５】[0025]
【発明の効果】以上に説明したように、本発明において
は、成分が規制され、特定条件下で熱処理が施されたＡ
ｌ−Ｍｇ−Ｓｉ系及びＡｌ−Ｚｎ−Ｍｎ系のＡｌ合金を
組み合わせてエンド部材及び連結棒部材を作製し、これ
らエンド部材及び連結棒部材を溶接又は圧接することに
より、従来から使用されている鉄製のトルクロッドとほ
ぼ同じ寸法・形状で鉄製に匹敵する特性をもつアルミ合
金製のトルクロッドを得ている。このアルミ合金製トル
クロッドは、鉄製に比較して５５〜６０％程度に軽量化
されており、しかもエンド部に圧入するブッシュやトル
クロッドを固定する部品に対する設計変更の必要性がな
く、従来の鉄製トルクロッドと同様に使用され、トラッ
クの軽量化に寄与する。As described above, according to the present invention, the components of which are regulated and heat-treated under specific conditions
An end member and a connecting rod member are manufactured by combining an l-Mg-Si-based and an Al-Zn-Mn-based Al alloy, and the end member and the connecting rod member are conventionally used by welding or pressing. An aluminum alloy torque rod with almost the same dimensions and shape as an iron torque rod and characteristics comparable to iron is obtained. The aluminum alloy torque rod is reduced in weight by about 55 to 60% as compared with the iron alloy torque rod. Further, there is no need to change the design of the bush or the part for fixing the torque rod into the end portion, and the conventional torque rod is made. Used in the same way as iron torque rods, it contributes to the weight reduction of trucks.
【図１】 エンド及び連結棒に三分割した従来の鉄製ト
ルクロッドの側面図FIG. 1 is a side view of a conventional iron torque rod divided into three parts, an end and a connecting rod.
【図２】 同鉄製トルクロッドの平面図FIG. 2 is a plan view of the iron torque rod.
【図３】 本発明実施例でアルミ製エンド（ａ）をアル
ミ製連結棒に溶接又は圧接したトルクロッドの一部
（ｂ）FIG. 3 shows a part (b) of a torque rod obtained by welding or pressing an aluminum end (a) to an aluminum connecting rod in the embodiment of the present invention.
１，２：エンド ３：連結棒 ４：環状部
５：接続用突出部 ６：ＭＩＧ溶接又は摩擦圧接した接合部1,2: end 3: connecting rod 4: annular part
5: Connection protrusion 6: MIG welded or friction welded joint
───────────────────────────────────────────────────── フロントページの続き (72)発明者 山田 達 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社 グループ技術セ ンター内 (72)発明者 土屋 健二 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社 グループ技術セ ンター内 (72)発明者 樋野 治道 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社 グループ技術セ ンター内 (72)発明者 堀田 元司 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社 グループ技術セ ンター内 (56)参考文献 特開 平５−270225（ＪＰ，Ａ) 特開 平７−69021（ＪＰ，Ａ) 実開 平４−109608（ＪＰ，Ｕ) (58)調査した分野(Int.Cl.7，ＤＢ名) B60G 7/00 B21K 1/06 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Tatsu Yamada 1-34-1 Kambara, Kambara-cho, Abara-gun, Shizuoka Prefecture Nippon Light Metal Co., Ltd. Group Technology Center (72) Inventor Kenji Tsuchiya Kambara-cho, Abara-gun, Shizuoka 1-34-1, Nippon Light Metal Co., Ltd., in the Group Technology Center (72) Inventor Harumichi Hino 1-34-1, Kambara, Kambara-cho, Anbara-gun, Shizuoka Prefecture Nippon Light Metal Co., Ltd., in the Group Technology Center (72) Inventor Hotta Motoshi 1-34-1 Kambara, Kambara-cho, Anbara-gun, Shizuoka Prefecture Nippon Light Metal Co., Ltd. Group Technology Center (56) References JP-A-5-270225 (JP, A) JP-A-7-69021 (JP, A) Hira 4-109608 (JP, U) (58) Fields investigated (Int. Cl. 7 , DB name) B60G 7/00 B21K 1/06
Claims (10)
連結棒の両端部にＡｌ合金製のエンドが溶接又は圧接さ
れたトルクロッドであり、エンドがＳｉ：１．０〜１．
５重量％，Ｃｕ：０．４〜０．９重量％，Ｍｎ：０．２
〜０．６重量％，Ｍｇ：０．８〜１．５重量％，Ｃｒ：
０．３〜０．９重量％を含み、Ｆｅ含有量を０．２５重
量％以下に規制すると共に、Ｍｎ＋Ｃｒの合計含有量が
１．２重量％以下に規制された組成をもつＡｌ合金製
で、前記連結棒がＺｎ：４．０〜６．５重量％，Ｍｇ：
０．５〜２．０重量％，Ｃｕ：０．０１〜０．２重量
％，Ｍｎ：０．２〜０．７重量％，Ｃｒ：０．０５〜
０．３重量％，Ｚｒ：０．０５〜０．２５重量％，Ｆ
ｅ：０．０１〜０．４重量％を含むＡｌ合金製であるト
ルクロッド。1. A torque rod in which ends of an Al alloy are welded or pressed to both ends of a connecting rod made of an extruded pipe of an Al alloy.
5% by weight, Cu: 0.4 to 0.9% by weight, Mn: 0.2
-0.6% by weight, Mg: 0.8-1.5% by weight, Cr:
It is made of an Al alloy having a composition containing 0.3 to 0.9% by weight and controlling the Fe content to 0.25% by weight or less and the total content of Mn + Cr to 1.2% by weight or less. The connecting rod is Zn: 4.0-6.5% by weight, Mg:
0.5 to 2.0% by weight, Cu: 0.01 to 0.2% by weight, Mn: 0.2 to 0.7% by weight, Cr: 0.05 to
0.3% by weight, Zr: 0.05 to 0.25% by weight, F
e: Torque rod made of Al alloy containing 0.01 to 0.4% by weight.
Ｔｉ：０．００５〜０．０５重量％，Ｂ：０．０００１
〜０．０１重量％及びＺｒ：０．１〜０．２重量％の１
種又は２種以上を含むトルクロッド。2. The aluminum alloy for an end according to claim 1, further comprising: 0.005 to 0.05% by weight of Ti, B: 0.0001.
To 0.01% by weight and Zr: 0.1 to 0.2% by weight
A torque rod containing one or more species.
Ｔｉ：０．００５〜０．２重量％，Ｂ：０．０００１〜
０．０５重量％及びＶ：０．０１〜０．１重量％の１種
又は２種以上を含むトルクロッド。3. The Al alloy for a connecting rod according to claim 1, further comprising: 0.005 to 0.2% by weight of Ti, and 0.0001 to 0.2% by weight of B.
A torque rod containing 0.05% by weight and one or more of V: 0.01 to 0.1% by weight.
連結棒の両端部にＡｌ合金製のエンドが溶接又は圧接さ
れたトルクロッドであり、前記連結棒がＳｉ：１．０〜
１．５重量％，Ｃｕ：０．４〜０．９重量％，Ｍｎ：
０．２〜０．６重量％，Ｍｇ：０．８〜１．５重量％，
Ｃｒ：０．３〜０．９重量％を含み、Ｆｅ含有量を０．
２５重量％以下に規制すると共に、Ｍｎ＋Ｃｒの合計含
有量が１．２重量％以下に規制された組成をもつＡｌ合
金製で、前記エンドがＺｎ：４．０〜６．５重量％，Ｍ
ｇ：０．５〜２．０重量％，Ｃｕ：０．０１〜０．２重
量％，Ｍｎ：０．２〜０．７重量％，Ｃｒ：０．０５〜
０．３重量％，Ｚｒ：０．０５〜０．２５重量％，Ｆ
ｅ：０．０１〜０．４重量％を含むＡｌ合金製であるト
ルクロッド。4. A torque rod in which ends of an Al alloy are welded or pressed to both ends of a connecting rod made of an extruded pipe of an Al alloy, wherein the connecting rod is made of Si: 1.0 to 1.0.
1.5% by weight, Cu: 0.4 to 0.9% by weight, Mn:
0.2 to 0.6% by weight, Mg: 0.8 to 1.5% by weight,
Cr: contains 0.3 to 0.9% by weight and has an Fe content of 0.1%.
It is made of an Al alloy having a composition in which the content of Mn + Cr is controlled to be not more than 1.2% by weight while the content is limited to 25% by weight or less, and the above-mentioned ends are 4.0 to 6.5% by weight of Zn, M
g: 0.5 to 2.0% by weight, Cu: 0.01 to 0.2% by weight, Mn: 0.2 to 0.7% by weight, Cr: 0.05 to
0.3% by weight, Zr: 0.05 to 0.25% by weight, F
e: Torque rod made of Al alloy containing 0.01 to 0.4% by weight.
Ｔｉ：０．００５〜０．０５重量％，Ｂ：０．０００１
〜０．０１重量％及びＺｒ：０．１〜０．２重量％の１
種又は２種以上を含むトルクロッド。5. The connecting rod Al alloy according to claim 4, further comprising: Ti: 0.005 to 0.05% by weight, B: 0.0001.
To 0.01% by weight and Zr: 0.1 to 0.2% by weight
A torque rod containing one or more species.
Ｔｉ：０．００５〜０．２重量％，Ｂ：０．０００１〜
０．０５重量％及びＶ：０．０１〜０．１重量％の１種
又は２種以上を含むトルクロッド。6. The aluminum alloy for an end according to claim 4, further comprising 0.005 to 0.2% by weight of Ti and 0.0001 to 0.2% by weight of B.
A torque rod containing 0.05% by weight and one or more of V: 0.01 to 0.1% by weight.
の鋳造材又は押出し材を鍛造し、次いで５１０〜５５５
℃に加熱後、水冷して１５５〜１９０℃に５〜２０時間
保持する熱処理を施し、該熱処理後のＡｌ合金から作製
したエンドに、請求項１又は３記載の組成をもつ連結棒
用Ａｌ合金の鋳造材又は押出し材を鍛造し、次いで４３
０〜４７０℃に加熱後、空冷又は炉冷して作製した連結
棒を溶接又は圧接することを特徴とするトルクロッドの
製造方法。7. A cast or extruded material of the aluminum alloy for an end according to claim 1 or 2, forged, and then 510 to 555.
5 ° C., water-cooled, heat-treated at 155 to 190 ° C. for 5 to 20 hours, and an aluminum alloy for a connecting rod having a composition according to claim 1 or 3 on an end produced from the heat-treated Al alloy. Of the cast or extruded material of
A method for manufacturing a torque rod, comprising heating or press-welding a connecting rod produced by air-cooling or furnace-cooling after heating to 0 to 470 ° C.
０〜１３０℃に２３〜２５時間保持し、次いで１５０〜
１６０℃に８〜１６時間保持する二段時効処理を施した
ものを使用するトルクロッドの製造方法。8. The connecting rod according to claim 7, further comprising:
Hold at 0-130 ° C for 23-25 hours, then 150-
A method for producing a torque rod using a two-stage aging treatment at 160 ° C. for 8 to 16 hours.
の鋳造材又は押出し材を鍛造し、次いで５１０〜５５５
℃に加熱後、水冷して１５５〜１９０℃に５〜２０時間
保持する熱処理を施し、該熱処理後のＡｌ合金から作製
した連結棒に、請求項４又は６記載の組成をもつエンド
用Ａｌ合金の鋳造材又は押出し材を鍛造し、次いで４３
０〜４７０℃に加熱後、空冷又は炉冷して作製したエン
ドを溶接又は圧接することを特徴とするトルクロッドの
製造方法。9. A cast or extruded material of the Al alloy for a connecting rod according to claim 4 or 5, forged, and then 510 to 555.
7. An aluminum alloy for end use having a composition according to claim 4 or 6, which is subjected to a heat treatment of cooling to a temperature of 155 ° C. and then maintaining the temperature at 155 to 190 ° C. for 5 to 20 hours. Of the cast or extruded material of
A method for producing a torque rod, comprising heating to 0 to 470 ° C., and then welding or pressing an end produced by air or furnace cooling.
１０〜１３０℃に２３〜２５時間保持し、次いで１５０
〜１６０℃に８〜１６時間保持する二段時効処理を施し
たものを使用するトルクロッドの製造方法。10. The end according to claim 9, further comprising:
Hold at 10-130 ° C for 23-25 hours, then 150
A method for producing a torque rod using a two-stage aging treatment at 8 to 16 hours at 160 ° C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP07184784A JP3114576B2 (en) | 1995-06-28 | 1995-06-28 | Torque rod and method of manufacturing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP07184784A JP3114576B2 (en) | 1995-06-28 | 1995-06-28 | Torque rod and method of manufacturing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0911721A JPH0911721A (en) | 1997-01-14 |
| JP3114576B2 true JP3114576B2 (en) | 2000-12-04 |
Family
ID=16159236
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP07184784A Expired - Fee Related JP3114576B2 (en) | 1995-06-28 | 1995-06-28 | Torque rod and method of manufacturing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3114576B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1318035B1 (en) * | 2001-12-05 | 2008-06-18 | Benteler Automobiltechnik GmbH | Arm and method of manufacturing an arm |
| DE20120098U1 (en) * | 2001-12-10 | 2002-03-14 | Sachsenring Fahrzeugtechnik Gm | Component connection for chassis components |
| KR20060108179A (en) * | 2005-04-12 | 2006-10-17 | 현대자동차주식회사 | Radius rod structure |
| JP5098968B2 (en) * | 2008-11-21 | 2012-12-12 | 日本軽金属株式会社 | Suspension component shaped material and method of manufacturing suspension component shaped material |
| AU2014262128A1 (en) * | 2013-05-01 | 2015-10-29 | Bradken Resources Pty Limited | Drawbar for rail wagons |
| CN114454678B (en) * | 2022-01-24 | 2023-12-29 | 天润工业技术股份有限公司 | Cast thrust rod for automobile |
-
1995
- 1995-06-28 JP JP07184784A patent/JP3114576B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0911721A (en) | 1997-01-14 |
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