JPH11209857A - Manufacture of aluminum alloy plate for valve plate - Google Patents
Manufacture of aluminum alloy plate for valve plateInfo
- Publication number
- JPH11209857A JPH11209857A JP1070898A JP1070898A JPH11209857A JP H11209857 A JPH11209857 A JP H11209857A JP 1070898 A JP1070898 A JP 1070898A JP 1070898 A JP1070898 A JP 1070898A JP H11209857 A JPH11209857 A JP H11209857A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- weight
- plate
- temperature
- valve
- 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.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 56
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 14
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 9
- 238000005098 hot rolling Methods 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 7
- 238000005097 cold rolling Methods 0.000 claims description 3
- -1 hot-rolled Substances 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 abstract description 19
- 239000010959 steel Substances 0.000 abstract description 19
- 238000010438 heat treatment Methods 0.000 abstract description 11
- 239000000203 mixture Substances 0.000 abstract description 11
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052719 titanium Inorganic materials 0.000 abstract description 2
- 229910052726 zirconium Inorganic materials 0.000 abstract description 2
- 230000008021 deposition Effects 0.000 abstract 1
- 238000002791 soaking Methods 0.000 abstract 1
- 239000000853 adhesive Substances 0.000 description 16
- 230000001070 adhesive effect Effects 0.000 description 16
- 239000000956 alloy Substances 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 229910045601 alloy Inorganic materials 0.000 description 8
- 230000035882 stress Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 230000032683 aging Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 102220253765 rs141230910 Human genes 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000003507 refrigerant Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は自動車エアコン用コ
ンプレッサのバルブプレートに使用されるバルブプレー
ト用アルミニウム合金板の製造方法に関し、更に詳述す
れば、１５０乃至１８０℃の高温雰囲気で長時間保持し
た後の高温強度（特に耐力）及び高温での耐凝着摩耗性
が優れたバルブプレート用アルミニウム合金板の製造方
法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing an aluminum alloy plate for a valve plate used for a valve plate of a compressor for an automobile air conditioner. The present invention relates to a method for producing an aluminum alloy plate for a valve plate having excellent high-temperature strength (particularly proof stress) and anti-adhesion wear at high temperatures.
【０００２】[0002]
【従来の技術】近時、環境問題及び高級化等の要請によ
り自動車の軽量化が図られており、このため、自動車用
エアコンのコンプレッサも軽量化が要望されている。2. Description of the Related Art In recent years, the weight of automobiles has been reduced due to environmental issues and demands for higher grades. For this reason, the weight of compressors of air conditioners for automobiles has also been reduced.
【０００３】従来、自動車エアコン用コンプレッサ−の
バルブプレートは、鉄板で製造されている。コンプレッ
サ運転時には冷媒のフレオンガスが高速で圧縮されるた
め、バルブプレートは１５０乃至１８０℃の高温にな
る。また、フレオンガスの吸排気を調整する鋼製弁が高
速で繰り返してバルブプレートに衝突する機構になって
いる。Conventionally, a valve plate of a compressor for an automobile air conditioner is manufactured from an iron plate. During operation of the compressor, the Freon gas of the refrigerant is compressed at a high speed, and the temperature of the valve plate becomes 150 to 180 ° C. In addition, a steel valve for adjusting the intake and exhaust of the freon gas repeatedly and collides with the valve plate at high speed.
【０００４】このような機構を有するバルブプレートに
対し、軽量化の観点からアルミニウム合金を適用しよう
とすると、そのアルミニウム合金には、第１に、高温
（１５０℃乃至１８０℃）で長期間使用に耐えることが
要求される。例えば、高温促進評価法により、１５０℃
の温度で１０００時間以上、又は１８０℃で１００時間
以上の条件で、十分な強度（主に耐力）を確保すること
が要求される。When an aluminum alloy is applied to a valve plate having such a mechanism from the viewpoint of weight reduction, first, the aluminum alloy is used for a long time at a high temperature (150 ° C. to 180 ° C.). It is required to endure. For example, 150 ° C.
It is required that sufficient strength (mainly proof stress) be ensured under the conditions of 1000 hours or more at the above temperature or 100 hours or more at 180 ° C.
【０００５】第２に、バルブプレート用アルミニウム合
金には、凝着摩耗性が優れていることが要求される。即
ち、鋼製弁がアルミニウム合金製バルブプレート（弁座
部）に高温で高速度で繰り返し衝突するとき、この衝突
により鋼製弁に弁座部のアルミニウムが付着してアルミ
ニウムの凝着が起こりやすい。そして、鋼製弁は板厚が
０．３ｍｍ程度と薄いため、鋼製弁が吐出口又は吸入口
に高速で当たったとき、弁が僅かにたわみ、繰り返し当
たると共に、微摺動を伴った動きをする。このため、鋼
製弁が当たるアルミニウム弁座部分が鋼製弁に僅かな摩
耗を伴った凝着を起こす。このため、バルブプレート用
のアルミニウム合金板としては、凝着摩耗性が優れてい
ることが要求される。Second, aluminum alloys for valve plates are required to have excellent adhesive wear resistance. That is, when a steel valve repeatedly collides with an aluminum alloy valve plate (valve seat portion) at a high temperature and at a high speed, aluminum of the valve seat portion adheres to the steel valve due to the collision, so that aluminum adhesion is likely to occur. . Since the steel valve has a small thickness of about 0.3 mm, when the steel valve hits the discharge port or the suction port at a high speed, the valve bends slightly, repeatedly hits, and moves with fine sliding. do. For this reason, the aluminum valve seat portion to which the steel valve is applied adheres to the steel valve with slight wear. For this reason, an aluminum alloy plate for a valve plate is required to have excellent adhesive wear resistance.
【０００６】而して、高温強度が優れたアルミニウム合
金として、ＪＩＳ２０１４，２０２４，２２１８，２６
１８アルミニウム合金が公知である。しかしながら、こ
れらの合金はいずれもＴ６処理後の状態で使われること
が多い。特に、２２１８合金及び２６１８合金はＮｉ及
びＦｅを多量に添加したものであり、これにより、Ｔ６
処理によって高温強度を高くするこができる。As an aluminum alloy having excellent high-temperature strength, JIS2014, 2024, 2218, 26
18 aluminum alloys are known. However, all of these alloys are often used after the T6 treatment. In particular, the 2218 alloy and the 2618 alloy have a large amount of Ni and Fe added thereto.
The high temperature strength can be increased by the treatment.
【０００７】これらは、いずれも１５０乃至１８０℃の
温度範囲における初期強度、１５０℃の温度で約１００
時間程度の時効処理における高温強度、及び１８０℃の
温度で約５０時間の時効処理における高温強度が高いと
いう優れた特性を有している。[0007] Each of these has an initial strength in the temperature range of 150 to 180 ° C, and a
It has excellent characteristics such that the high-temperature strength in the aging treatment for about an hour and the high-temperature strength in the aging treatment at a temperature of 180 ° C. for about 50 hours are high.
【０００８】他にも、アルミニウム合金材中の添加成分
を選択すると共に、その組成を規定することにより、高
温強度の向上を図ったアルミニウム合金が提案されてい
る（特開昭６２−２１４１５１号公報、特開昭６２−２
３０９４９号公報）。また添加成分の組成を規定すると
共に、所定の条件で溶体化処理等を施すことにより、更
に一層高温強度の向上を図ったアルミニウム合金材の製
造方法も開示されている（特開平４−３２５６４５号公
報、特開平４−３２５６４６号公報及び特開平４−３７
１５４３号公報）。[0008] In addition, there has been proposed an aluminum alloy having improved high-temperature strength by selecting an additive component in the aluminum alloy material and defining its composition (Japanese Patent Application Laid-Open No. Sho 62-214151). JP-A-62-2
No. 30949). Also disclosed is a method for producing an aluminum alloy material in which the composition of the additional components is specified and a solution treatment or the like is performed under predetermined conditions to further improve the high-temperature strength (Japanese Patent Application Laid-Open No. 4-325645). Gazette, JP-A-4-325646 and JP-A-4-37
No. 1543).
【０００９】[0009]
【発明が解決しようとする課題】しかしながら、上述の
従来技術においては、１５０乃至１８０℃の高温下にお
いて、アルミニウム合金材を使用したときに、前述の時
効処理において１００時間又は５０時間という時効時間
を超えると、高温強度が次第に低下するという問題点が
ある。また、鋼製弁へのアルミニウムの凝着が起こり、
弁座部の凝着摩耗量が多くなり、長時間使用後には気密
性が次第に低下するという問題点もある。However, in the above-mentioned prior art, when an aluminum alloy material is used at a high temperature of 150 to 180 ° C., the aging time of 100 hours or 50 hours is required in the above-mentioned aging treatment. If it exceeds, there is a problem that the high-temperature strength gradually decreases. Also, adhesion of aluminum to the steel valve occurs,
There is also a problem that the amount of cohesive wear of the valve seat increases and the airtightness gradually decreases after long-term use.
【００１０】従って、従来のアルミニウム合金材を使用
して自動車エアコン用のバルブプレートを製造した場合
には、その剛性が低下すると共に、気密性を保持でき
ず、性能が低下し、また破損の発生原因となる。Therefore, when a valve plate for an automobile air conditioner is manufactured using a conventional aluminum alloy material, the rigidity of the valve plate is reduced, airtightness cannot be maintained, performance is reduced, and breakage occurs. Cause.
【００１１】本発明はかかる問題点に鑑みてなされたも
のであって、１５０乃至１８０℃の温度雰囲気下におい
て、約１００乃至１０００時間の長時間経過した状態に
おいても、初期と同等以上の高温強度を得ることがで
き、また鋼製弁による凝着摩耗量が少ないバルブプレー
ト用アルミニウム合金板の製造方法を提供することを目
的とする。The present invention has been made in view of the above problems, and has a high-temperature strength equal to or higher than that of the initial state even in a state where a long time of about 100 to 1000 hours has passed in a temperature atmosphere of 150 to 180 ° C. It is another object of the present invention to provide a method of manufacturing an aluminum alloy plate for a valve plate, which can obtain a low frictional adhesion by a steel valve.
【００１２】[0012]
【課題を解決するための手段】本発明に係るバルブプレ
ート用アルミニウム合金板の製造方法は、Ｃｕ：３．５
乃至４．５重量％、Ｍｎ：０．４乃至１．０重量％、Ｓ
ｉ：０．２乃至０．８重量％及びＭｇ：０．４乃至１．
０重量％を含有すると共に、Ｔｉ：０．００５乃至０．
０５重量％、Ｚｒ：０．０２乃至０．２０重量％及びＣ
ｒ０．０２乃至０．１０重量％からなる群から選択され
た少なくとも１種の元素を含有し、残部がアルミニウム
及び不可避的不純物からなる組成を有するアルミニウム
合金の鋳塊を均熱処理し、熱間圧延し、溶体化処理した
後、得られたアルミニウム合金板に１０乃至３０％の冷
間歪みを付与することを特徴とする。The method for manufacturing an aluminum alloy plate for a valve plate according to the present invention is as follows.
To 4.5% by weight, Mn: 0.4 to 1.0% by weight, S
i: 0.2 to 0.8% by weight and Mg: 0.4 to 1.
0% by weight and Ti: 0.005 to 0.5%.
05% by weight, Zr: 0.02 to 0.20% by weight and C
r Ingot heat treatment of an ingot of an aluminum alloy containing at least one element selected from the group consisting of 0.02 to 0.10% by weight and having a balance of aluminum and unavoidable impurities, Then, after the solution treatment, 10 to 30% cold strain is applied to the obtained aluminum alloy plate.
【００１３】このバルブプレート用アルミニウム合金板
の製造方法において、前記熱間圧延工程と、前記溶体化
処理工程との間に、冷間圧延工程を設けても良い。ま
た、前記冷間歪みは、１２乃至２２％であることがより
好ましい。In the method of manufacturing an aluminum alloy plate for a valve plate, a cold rolling step may be provided between the hot rolling step and the solution treatment step. Further, the cold strain is more preferably 12 to 22%.
【００１４】[0014]
【発明の実施の形態】本発明者等は、アルミニウム合金
の高温強度を向上させるべく種々実験研究した結果、成
分組成及び製造条件を適正なものとし、特に溶体化処理
後に、例えば冷間圧延率を最適化して、適正な冷間歪み
を付与することにより、１５０乃至１８０℃の高温雰囲
気で長時間保持後の高温強度が優れており、かつ高温に
おける鋼製弁との凝着摩耗性が優れたバルブプレート用
のアルミニウム合金板を得ることができることを知見
し、本発明を完成するに至ったものである。BEST MODE FOR CARRYING OUT THE INVENTION The present inventors have conducted various experiments and studies to improve the high-temperature strength of aluminum alloys. As a result, the composition of the components and the manufacturing conditions have been made appropriate. By applying a suitable cold strain by optimizing the temperature, excellent high-temperature strength after holding for a long time in a high-temperature atmosphere of 150 to 180 ° C, and excellent adhesive wear with steel valves at high temperatures It has been found that an aluminum alloy plate for a valve plate can be obtained, and the present invention has been completed.
【００１５】以下、本発明について更に詳細に説明す
る。先ず、本発明に係るアルミニウム合金板の成分添加
理由及び組成限定理由について説明する。Hereinafter, the present invention will be described in more detail. First, the reasons for adding components and the reasons for limiting the composition of the aluminum alloy sheet according to the present invention will be described.
【００１６】Ｃｕ：３．５乃至４．５重量％ Ｃｕはアルミニウム合金の強度確保のために必要不可欠
の元素であるが，その含有量が３．５重量％未満では十
分な強度が得られない。一方、Ｃｕ含有量が４．５重量
％を超えると、初期高温強度及び１５０℃の温度におけ
る約１００時間までの使用条件又は１８０℃の温度にお
ける約５０時間までの使用条件における高温強度は高く
なるが、１５０℃の温度で１０００時間以上の使用条件
又は１８０℃の温度で１００乃至３００時間の使用条件
では、過時効状態になって高温強度が低下する。また、
アルミニウム合金板の製造時に鋳造割れが起こりやすく
なったり、初期の加エ性の低下によって熱間圧延時に割
れ等が発生しやすくなる。従って、Ｃｕ量は３．５乃至
４．５重量％の範囲とする。 Cu: 3.5 to 4.5% by weight Cu is an indispensable element for securing the strength of the aluminum alloy, but if the content is less than 3.5% by weight, sufficient strength cannot be obtained. . On the other hand, when the Cu content exceeds 4.5% by weight, the initial high-temperature strength and the high-temperature strength under the operating conditions of about 100 hours at a temperature of 150 ° C. or the operating conditions of up to about 50 hours at a temperature of 180 ° C. become high. However, under a use condition of 1000 hours or more at a temperature of 150 ° C. or a use condition of 100 to 300 hours at a temperature of 180 ° C., an overaged state occurs and high-temperature strength is reduced. Also,
Casting cracks are likely to occur during the production of an aluminum alloy sheet, and cracks and the like are likely to occur during hot rolling due to a decrease in initial workability. Therefore, the Cu content is in the range of 3.5 to 4.5% by weight.
【００１７】Ｍｎ：０．４乃至１．０重量％ Ｍｎは高温強度の向上のために有効な元素である。アル
ミニウム合金中のＭｎ含有量が０．４重量％未満である
と、例えば１５０℃の温度で１０００時間という長時間
が経過した後に十分な強度を得ることができなくなる。
一方、Ｍｎ含有量が１．０重量％を超えると、その効果
が飽和すると共に、粗大な化合物が増加して強度（靭
性）が低下する。また、Ｍｎ含有量が１．０重量％を超
えると、初期の高温強度及び長時間経過後の高温強度が
低下する。従って、Ｍｎ量は０．４乃至１．０重量％の
範囲とする。 Mn: 0.4 to 1.0% by weight Mn is an element effective for improving high-temperature strength. If the Mn content in the aluminum alloy is less than 0.4% by weight, sufficient strength cannot be obtained after a long time of, for example, 1000 hours at a temperature of 150 ° C.
On the other hand, when the Mn content exceeds 1.0% by weight, the effect is saturated, and at the same time, coarse compounds increase and strength (toughness) decreases. On the other hand, when the Mn content exceeds 1.0% by weight, the initial high-temperature strength and the high-temperature strength after a long period of time decrease. Therefore, the Mn content is in the range of 0.4 to 1.0% by weight.
【００１８】Ｓｉ：０．２乃至０．８重量％ Ｓｉはアルミニウム合金板の高温強度を向上させるため
に必要な元素である。アルミニウム合金中のＳｉ含有量
が０．２重量％未満では十分な高温強度が得られない。
一方、Ｓｉ含有量が０．８重量％を超えると、初期の高
温強度は得られるものの、１５０℃温度で１０００時間
の使用環境又は１８０℃温度で１００乃至３００時間の
使用環境では、所定の強度が得られない。従って、Ｓｉ
量は０．２乃至０．８重量％の範囲とする。 Si: 0.2 to 0.8% by weight Si is an element necessary for improving the high-temperature strength of the aluminum alloy plate. If the Si content in the aluminum alloy is less than 0.2% by weight, sufficient high-temperature strength cannot be obtained.
On the other hand, when the Si content exceeds 0.8% by weight, the initial high-temperature strength can be obtained, but in a use environment at 150 ° C. for 1000 hours or a use environment at 180 ° C. for 100 to 300 hours, the predetermined strength is obtained. Can not be obtained. Therefore, Si
The amount ranges from 0.2 to 0.8% by weight.
【００１９】Ｍｇ：０．４乃至１．０重量％ Ｍｇはアルミニウム合金の高温強度確保のために必要不
可欠な元素である。しかし、Ｍｇを添加すると、高温で
の凝着摩耗性が劣化するという難点がある。合金中のＭ
ｇ含有量が、０．４重量％未満では凝着摩耗性は向上す
るが、バルブプレートに要求される十分な強度が得られ
ない。一方、Ｍｇ含有量が１．０重量％を超えると、初
期強度は高くなるが、高温雰囲気下において長時間経過
後の強度低下が大きくなる。更に、高速で繰り返し動い
ている弁との接触部において、弁座の凝着摩耗量が多く
なり、所定の圧力が得られなくなり、コンプレッサとし
ての機能を果さなくなる可能性がある。また、初期の加
工性が悪くなり、熱間圧延時に割れ等が発生しやすくな
る。従って、Ｍｇ量は０．４乃至１．０重量％の範囲と
する。 Mg: 0.4 to 1.0% by weight Mg is an indispensable element for ensuring high-temperature strength of an aluminum alloy. However, when Mg is added, there is a disadvantage that the adhesive wear at high temperatures is deteriorated. M in alloy
When the g content is less than 0.4% by weight, the adhesive wear resistance is improved, but sufficient strength required for the valve plate cannot be obtained. On the other hand, when the Mg content exceeds 1.0% by weight, the initial strength increases, but the strength decreases after a long time in a high-temperature atmosphere. Further, at a contact portion with a valve that is repeatedly moving at a high speed, the amount of cohesive wear of the valve seat increases, a predetermined pressure cannot be obtained, and the function as a compressor may not be achieved. In addition, the initial workability is deteriorated, and cracks and the like are likely to occur during hot rolling. Therefore, the Mg content is set in the range of 0.4 to 1.0% by weight.
【００２０】Ｔｉ：０．００５乃至０．０５重量％、Ｚ
ｒ：０．０２乃至０．２０重量％及びＣｒ０．０２乃至
０．１０重量％ Ｔｉ、Ｚｒ及びＣｒは、結晶粒を微細化すると共に、高
温強度を向上させる効果を有する元素である。Ｔｉ含有
量が０．００５重量％未満、Ｚｒ含有量が０．０２重量
％未満、Ｃｒ含有量が０．０２重量％未満であるとその
効果を十分に得ることができない。一方、アルミニウム
合金中にＴｉを含有させる場合はＴｉ含有量が０．０５
重量％を超えた場合、Ｚｒを含有させる場合はＺｒ含有
量が０．２０重量％を超えた場合及びＣｒを含有させる
場合はＣｒ含有量が０．１０重量％を超えた場合は、そ
の効果が飽和し、且つ粗大な化合物が多くなり、強度
（靱性）が低下するようになる。従って、Ｔｉ含有量量
は０．００５乃至０．０５重量％、Ｚｒ含有量は０．０
２乃至０．２０重量％、Ｃｒ含有量は０．０２乃至０．
１０重量％の範囲とする。 Ti: 0.005 to 0.05% by weight, Z
r: 0.02 to 0.20% by weight and Cr 0.02 to
0.10% by weight Ti, Zr and Cr are elements that have the effect of refining crystal grains and improving high-temperature strength. If the Ti content is less than 0.005% by weight, the Zr content is less than 0.02% by weight, and the Cr content is less than 0.02% by weight, the effect cannot be sufficiently obtained. On the other hand, when Ti is contained in the aluminum alloy, the Ti content is 0.05%.
If the content exceeds 0.2% by weight, the content of Zr exceeds 0.20% by weight, and if the content of Cr exceeds 0.10% by weight, the effect is obtained. Saturates and the amount of coarse compounds increases, and the strength (toughness) decreases. Therefore, the Ti content is 0.005 to 0.05% by weight, and the Zr content is 0.0
2 to 0.20% by weight, and the Cr content is 0.02 to 0.1%.
The range is 10% by weight.
【００２１】不可避的不純物 アルミニウム合金中には、上記元素の他に不可避的不純
物として、Ｆｅ，Ｚｎ，Ｎｉ及びＶ等が含有されるが、
これらの不可避的不純物は夫々Ｆｅ：０．７重量％以
下、Ｚｎ；０．２５重量％以下、Ｎｉ；０．１重量％以
下、Ｖ：０．１重量％以下であると、アルミニウム合金
板の性能に影響を与えることはない。しかし、不純物は
可及的に少ないことが望ましい。 Inevitable impurities The aluminum alloy contains Fe, Zn, Ni and V as inevitable impurities in addition to the above elements.
If these unavoidable impurities are Fe: 0.7% by weight or less, Zn: 0.25% by weight or less, Ni: 0.1% by weight or less, and V: 0.1% by weight or less, It does not affect performance. However, it is desirable that impurities be as small as possible.
【００２２】次に、製造条件についての限定理由を述べ
る。Next, the reasons for limiting the manufacturing conditions will be described.
【００２３】冷間歪み：１０乃至３０％ 本発明においては、溶体化処理後の素材に所定の歪み量
で冷間加工を施すことが高温強度を高めるために重要で
ある。この冷間加工の歪み量が１０％未満であると、そ
の後の加熱時の析出が不十分で初期強度が低下すると共
に、１５０℃の温度で１０００時間又は１８０℃の温度
で１００時間経過後において、所定の高温強度が得られ
ない。 Cold strain: 10 to 30% In the present invention, it is important to subject the material after solution treatment to cold working with a predetermined strain to increase the high-temperature strength. When the strain amount of the cold working is less than 10%, the precipitation at the time of subsequent heating is insufficient and the initial strength is reduced, and after a lapse of 1000 hours at a temperature of 150 ° C. or 100 hours at a temperature of 180 ° C. In addition, a predetermined high-temperature strength cannot be obtained.
【００２４】一方、冷間歪みを付与するための加工にお
いて、歪み量が３０％を超えると、初期の高温強度は高
くなるものの、１５０乃至１８０℃での長時間加熱後に
おいて、強度が著しく低下する。従って、本発明におい
ては、溶体化処理後の素材に１０乃至３０％量で冷間歪
みを付与する。この歪み量は、好ましくは１５乃至２５
％である。なお、本発明において、溶体化処理後の素材
に冷間歪みを与える方法としては、冷間圧延に限定され
ず、例えば、レベラー、ストレッチ等により冷間歪みを
付与しても良い。On the other hand, in the process for imparting cold strain, if the amount of strain exceeds 30%, the initial high-temperature strength is increased, but the strength is significantly reduced after prolonged heating at 150 to 180 ° C. I do. Therefore, in the present invention, the material after the solution treatment is subjected to cold strain in an amount of 10 to 30%. This distortion amount is preferably 15 to 25.
%. In the present invention, the method for imparting cold strain to the material after the solution treatment is not limited to cold rolling, and cold strain may be imparted by, for example, a leveler, stretch, or the like.
【００２５】なお、工業的に実施されている焼き入れ後
の歪み付与は、通常、１乃至５％程度である。The distortion applied after quenching, which is industrially practiced, is usually about 1 to 5%.
【００２６】[0026]
【実施例】以下、本発明の実施例についてその比較例と
比較して説明する。第１実施例 下記表１に示す組成のアルミニウム合金のうち、供試材
Ｎｏ１のアルミニウム合金の鋳塊（厚さ５０ｍｍ）を使
用し、４８０℃に８時間加熱して均質化処理した後、更
に４３０℃に２時間加熱した後、熱間圧延を行い、厚さ
が２．５ｍｍの板を製作した。次いで、４９０℃に３０
分間加熱して溶体化処理した後、水冷して焼き入れ処理
し、その後、アルミニウム合金板に０乃至３５％の冷間
歪み量で冷間歪みを付与し、バルブプレート用アルミニ
ウム合金板を得た。なお、表１中、本発明の組成範囲を
最上段に付し、比較例の各供試材において成分組成が本
発明の範囲から外れるものについて、下線を付した。ま
た、比較例のうち、供試材４乃至７は、現在工業的に量
産されている市販材であり、供試材４はＪＩＳ２０１４
合金、供試材５は２０２４合金、供試材６は２６１８合
金、供試材７は２２１８合金である。また、供試材８乃
至１０は組成範囲が本発明の範囲を外れたものである。EXAMPLES Examples of the present invention will be described below in comparison with comparative examples. First Example Of the aluminum alloys having the compositions shown in Table 1 below, an ingot (thickness: 50 mm) of the aluminum alloy of the test material No. 1 was used, and after being heated to 480 ° C. for 8 hours and homogenized, furthermore, After heating at 430 ° C. for 2 hours, hot rolling was performed to produce a 2.5 mm thick plate. Then at 490 ° C for 30
After heat treatment for 5 minutes, a solution treatment is performed, followed by quenching by water cooling, and thereafter, a cold strain is applied to the aluminum alloy plate at a cold strain amount of 0 to 35% to obtain an aluminum alloy plate for a valve plate. . In addition, in Table 1, the composition range of the present invention is shown at the top, and those of the test materials of the comparative examples which are out of the range of the present invention are underlined. Further, among the comparative examples, the test materials 4 to 7 are commercially available materials that are currently mass-produced industrially, and the test material 4 is JIS2014
The alloy and the test material 5 were a 2024 alloy, the test material 6 was a 2618 alloy, and the test material 7 was a 2218 alloy. Further, the test materials 8 to 10 have composition ranges outside the scope of the present invention.
【００２７】その後、得られたアルミニウム合金板を１
５０℃の温度で０．５時間加熱した後の引張強さ及び耐
力を測定すると共に、１０００時間連続加熱した後の引
張強さ及び耐力を測定することにより、アルミニウム合
金板の高温特性を評価した。また、同じ板から高温での
凝着摩耗試験用試験片を切り出し、実機の鋼製弁に相当
する鋼板をこのアルミニウム合金板に高速で繰り返し衝
突させ、アルミニウムの凝着摩耗量を測定した。Thereafter, the obtained aluminum alloy plate was
The high temperature properties of the aluminum alloy plate were evaluated by measuring the tensile strength and proof stress after heating at a temperature of 50 ° C. for 0.5 hour and measuring the tensile strength and proof stress after continuous heating for 1000 hours. . Further, a test piece for an adhesive wear test at a high temperature was cut out from the same plate, and a steel plate corresponding to a steel valve of an actual machine was repeatedly hit against this aluminum alloy plate at a high speed to measure the amount of adhesive wear of aluminum.
【００２８】図１は凝着摩耗量を測定する試験方法を示
す図であり、この図１に示すように、突起を有するアル
ミニウム合金板からなる試験片１に対し、鋼板２を繰り
返し衝突させ、弁座相当のアルミニウム試験片１の滅失
量（高さ減少量）ｍｍを測定した。但し、試験温度は１
８０℃、面圧は１５ｋｇ／ｍｍ2、繰り返し衝突のサイ
クルは２４００ｒｐｍ、試験時間は１８８時間、繰り返
し衝突回数は２．７×１０7回である。その結果を下記
表２に示す。但し、高温特性欄の引張強さ及び耐力の単
位はN/mm2である。FIG. 1 is a view showing a test method for measuring the amount of adhesive wear. As shown in FIG. 1, a steel plate 2 is repeatedly hit against a test piece 1 made of an aluminum alloy plate having projections. The loss amount (height reduction amount) mm of the aluminum test piece 1 corresponding to the valve seat was measured. However, the test temperature is 1
At 80 ° C., the surface pressure is 15 kg / mm 2 , the cycle of repeated collision is 2400 rpm, the test time is 188 hours, and the number of repeated collisions is 2.7 × 10 7 times. The results are shown in Table 2 below. However, the unit of tensile strength and proof stress in the column of high temperature properties is N / mm 2 .
【００２９】表２に示すように、本発明の実施例におい
ては、溶体化処理後、冷間加工率１２乃至２２％の冷間
ひずみを与えて製造したアルミニウム合金板であるの
で、高温での初期強度及び長時間経過後の高温強度差が
少なく、かつ高温での凝着摩耗性が優れている。これに
対し、比較例の場合は、高温特性が悪く、また、凝着摩
耗量も多いものであった。As shown in Table 2, in the embodiment of the present invention, since the aluminum alloy plate is manufactured by applying a cold working rate of 12 to 22% after the solution treatment, a cold working rate is high. The difference between the initial strength and the high-temperature strength after a long time has passed is small, and the adhesive wear at high temperatures is excellent. On the other hand, in the case of the comparative example, the high-temperature characteristics were poor and the amount of adhesive wear was large.
【００３０】[0030]
【表１】 [Table 1]
【００３１】[0031]
【表２】 [Table 2]
【００３２】第２実施例 前記表１に示す各組成のアルミニウム合金鋳塊（厚さ５
０ｍｍ）を夫々使用し、４８０℃に８時間加熱して均質
化処理した後、更に４３０℃に２時間加熱し、その後、
熱間圧延し、厚さが２．５ｍｍのアルミニウム合金板を
製作した。次いで、４９０℃に３０分間加熱して溶体化
処理した後、水冷により焼き入れ処理し、その後１８％
の冷間歪み量を付与して所定の板を製造した。 Second Embodiment An aluminum alloy ingot (having a thickness of 5
0 mm), respectively, and heated to 480 ° C. for 8 hours to homogenize, and further heated to 430 ° C. for 2 hours,
Hot rolling was performed to produce an aluminum alloy plate having a thickness of 2.5 mm. Next, after heating to 490 ° C. for 30 minutes to perform a solution treatment, a quenching treatment is performed by water cooling, and then 18%
A predetermined plate was manufactured by imparting the amount of cold strain.
【００３３】その後、得られたアルミニウム合金板を１
５０℃の温度で０．５時間加熱後の引張強さ及び耐力を
測定すると共に、１０００時間連続加熱した後の引張強
さ及び耐力を測定することにより、アルミニウム合金板
の高温特性を評価した。また、同じ板から高温での凝着
摩耗試験片を製作し、実機の鋼製弁に相当する鋼板を使
用し、高速で繰り返し衝突させアルミニウムの凝着摩耗
量を測定した。凝着摩耗量は、前述のとおり、図１に示
す試験方法により、弁座相当の鋼板の減失量（高さ減少
量）ｍｍを測定して評価した。その結果を下記表３に示
す。但し、高温特性欄の引張強さ及び耐力の単位はN/mm
2である。Thereafter, the obtained aluminum alloy plate was
The high-temperature properties of the aluminum alloy sheet were evaluated by measuring the tensile strength and proof stress after heating at a temperature of 50 ° C. for 0.5 hour and measuring the tensile strength and proof stress after continuous heating for 1000 hours. Further, an adhesive wear test specimen at a high temperature was manufactured from the same plate, and a steel plate corresponding to a steel valve of an actual machine was used. As described above, the amount of adhesive wear was evaluated by measuring the loss (height reduction) mm of the steel sheet corresponding to the valve seat by the test method shown in FIG. The results are shown in Table 3 below. However, the unit of tensile strength and proof stress in the high temperature property column is N / mm
2
【００３４】本発明の組成範囲に入る各実施例のアルミ
ニウム合金板であって、本発明の範囲に入る冷間歪みを
付与したものは、高温での初期強度及び長時間経過後の
高温強度差が少なく、かつ高温での凝着摩耗性が優れて
いる。これに対し、比較例のアルミニウム合金板は本発
明の範囲の冷間歪みを付与しても、高温特性及び凝着摩
耗量が悪いものであった。The aluminum alloy sheets of the respective examples which fall within the composition range of the present invention and which have been subjected to cold strain falling within the range of the present invention are those having a difference in the initial strength at a high temperature and the high temperature strength after a long time. And excellent adhesive wear at high temperatures. On the other hand, the aluminum alloy plate of the comparative example was poor in high-temperature characteristics and adhesive wear even when cold strain was applied within the range of the present invention.
【００３５】[0035]
【表３】 [Table 3]
【００３６】[0036]
【発明の効果】以上説明したように、本発明によれば、
アルミニウム合金板の成分組成を適切なものにし、その
製造条件を適正化し、特に溶体化処理後に適正な冷間歪
みを付与するので、１５０乃至１８０℃の高温雰囲気で
長時間保持後の高温強度が優れていると共に、高温にお
ける鋼製弁との凝着摩耗性が優れたバルブプレート用の
アルミニウム合金板を得ることができる。As described above, according to the present invention,
Since the component composition of the aluminum alloy plate is made appropriate and its production conditions are optimized, and particularly, appropriate cold strain is given after the solution treatment, the high-temperature strength after long-term holding in a high-temperature atmosphere of 150 to 180 ° C. It is possible to obtain an aluminum alloy plate for a valve plate which is excellent and has excellent adhesive wear resistance to a steel valve at a high temperature.
【図１】凝着摩耗性を評価する方法を示す図である。FIG. 1 is a diagram showing a method for evaluating adhesive wear properties.
１：試験片 ２：鋼板 1: Test piece 2: Steel plate
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｃ２２Ｆ 1/00 ６５１ Ｃ２２Ｆ 1/00 ６５１Ａ ６８５ ６８５Ｚ ６９４ ６９４Ａ ──────────────────────────────────────────────────の Continuation of front page (51) Int.Cl. 6 Identification code FI C22F 1/00 651 C22F 1/00 651A 685 685Z 694 694A
Claims (3)
０．４乃至１．０重量％、Ｓｉ：０．２乃至０．８重量
％及びＭｇ：０．４乃至１．０重量％を含有すると共
に、Ｔｉ：０．００５乃至０．０５重量％、Ｚｒ：０．
０２乃至０．２０重量％及びＣｒ０．０２乃至０．１０
重量％からなる群から選択された少なくとも１種の元素
を含有し、残部がアルミニウム及び不可避的不純物から
なる組成を有するアルミニウム合金の鋳塊を均熱処理
し、熱間圧延し、溶体化処理した後、得られたアルミニ
ウム合金板に１０乃至３０％の冷間歪みを付与すること
を特徴とするバルブプレート用アルミニウム合金板の製
造方法。1. Cu: 3.5 to 4.5% by weight, Mn:
0.4 to 1.0% by weight, 0.2 to 0.8% by weight of Si and 0.4 to 1.0% by weight of Mg, and 0.005 to 0.05% by weight of Ti; Zr: 0.
02 to 0.20% by weight and Cr 0.02 to 0.10
Weight percent of an ingot of an aluminum alloy containing at least one element selected from the group consisting of aluminum and inevitable impurities, hot-rolled, and solution-treated. A method for producing an aluminum alloy plate for a valve plate, wherein 10 to 30% cold strain is imparted to the obtained aluminum alloy plate.
程との間に、冷間圧延工程を有することを特徴とする請
求項１に記載のバルブプレート用アルミニウム合金板の
製造方法。2. The method for producing an aluminum alloy plate for a valve plate according to claim 1, further comprising a cold rolling step between the hot rolling step and the solution treatment step.
ことを特徴とする請求項２に記載のバルブプレート用ア
ルミニウム合金板の製造方法。3. The method according to claim 2, wherein the cold distortion is 12% to 22%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1070898A JPH11209857A (en) | 1998-01-22 | 1998-01-22 | Manufacture of aluminum alloy plate for valve plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1070898A JPH11209857A (en) | 1998-01-22 | 1998-01-22 | Manufacture of aluminum alloy plate for valve plate |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH11209857A true JPH11209857A (en) | 1999-08-03 |
Family
ID=11757815
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1070898A Pending JPH11209857A (en) | 1998-01-22 | 1998-01-22 | Manufacture of aluminum alloy plate for valve plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH11209857A (en) |
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| ITMI20102307A1 (en) * | 2010-12-16 | 2012-06-17 | Omb Saleri S P A | VALVE PERFECTED FOR CYLINDERS CNG |
| WO2012044450A3 (en) * | 2010-09-08 | 2012-07-05 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
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| KR20220131403A (en) * | 2021-03-18 | 2022-09-28 | (주) 동양에이.케이코리아 | Manufacturing method of high-strength aluminum alloy rolled sheet and high-strength aluminum alloy rolled sheet using same |
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1998
- 1998-01-22 JP JP1070898A patent/JPH11209857A/en active Pending
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|---|---|---|---|---|
| WO2012044450A3 (en) * | 2010-09-08 | 2012-07-05 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
| US8999079B2 (en) | 2010-09-08 | 2015-04-07 | Alcoa, Inc. | 6xxx aluminum alloys, and methods for producing the same |
| US9194028B2 (en) | 2010-09-08 | 2015-11-24 | Alcoa Inc. | 2xxx aluminum alloys, and methods for producing the same |
| US9249484B2 (en) | 2010-09-08 | 2016-02-02 | Alcoa Inc. | 7XXX aluminum alloys, and methods for producing the same |
| US9359660B2 (en) | 2010-09-08 | 2016-06-07 | Alcoa Inc. | 6XXX aluminum alloys, and methods for producing the same |
| CN103168111A (en) * | 2010-10-08 | 2013-06-19 | 美铝公司 | Improved 2XXX aluminum alloy and production method thereof |
| CN103168111B (en) * | 2010-10-08 | 2015-07-29 | 美铝公司 | Improved 2XXX aluminum alloys, and methods for producing the same |
| ITMI20102307A1 (en) * | 2010-12-16 | 2012-06-17 | Omb Saleri S P A | VALVE PERFECTED FOR CYLINDERS CNG |
| US9926620B2 (en) | 2012-03-07 | 2018-03-27 | Arconic Inc. | 2xxx aluminum alloys, and methods for producing the same |
| US9587298B2 (en) | 2013-02-19 | 2017-03-07 | Arconic Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
| KR20220131403A (en) * | 2021-03-18 | 2022-09-28 | (주) 동양에이.케이코리아 | Manufacturing method of high-strength aluminum alloy rolled sheet and high-strength aluminum alloy rolled sheet using same |
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