JPH0261038A - Production of forged product made of al alloy - Google Patents
Production of forged product made of al alloyInfo
- Publication number
- JPH0261038A JPH0261038A JP21343788A JP21343788A JPH0261038A JP H0261038 A JPH0261038 A JP H0261038A JP 21343788 A JP21343788 A JP 21343788A JP 21343788 A JP21343788 A JP 21343788A JP H0261038 A JPH0261038 A JP H0261038A
- Authority
- JP
- Japan
- Prior art keywords
- forging
- alloy
- forged
- time
- heat treatment
- 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
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 9
- 238000005242 forging Methods 0.000 claims abstract description 27
- 230000032683 aging Effects 0.000 claims abstract description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000001816 cooling Methods 0.000 claims abstract description 4
- 239000000463 material Substances 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 19
- 229910045601 alloy Inorganic materials 0.000 claims description 11
- 239000000956 alloy Substances 0.000 claims description 11
- 230000005496 eutectics Effects 0.000 abstract description 20
- 238000010438 heat treatment Methods 0.000 abstract description 16
- 150000001875 compounds Chemical class 0.000 abstract description 14
- 229910052751 metal Inorganic materials 0.000 description 17
- 239000002184 metal Substances 0.000 description 17
- 238000001000 micrograph Methods 0.000 description 5
- 238000005266 casting Methods 0.000 description 3
- 238000004904 shortening Methods 0.000 description 3
- 229910000881 Cu alloy Inorganic materials 0.000 description 2
- 238000009825 accumulation Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910018540 Si C Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000013467 fragmentation Methods 0.000 description 1
- 238000006062 fragmentation reaction Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- 210000002784 stomach Anatomy 0.000 description 1
Landscapes
- Forging (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、所定形状に鋳造されたＡｌ合金製鍛造素材を
鍛造することにより鍛造品を製造する方法の改良に関し
、特に生産効率アップ化対策に関する。Detailed Description of the Invention (Industrial Field of Application) The present invention relates to an improvement in a method for manufacturing a forged product by forging an Al alloy forged material cast into a predetermined shape, and in particular to measures for increasing production efficiency. Regarding.
（従来の技術）
一般に、ＡｆＩ−８ｔ−Ｃｕ系合金やＡｆＩ−Ｓｉ−Ｃ
ｕ −Ｍ ｇ系合金等は、鋳造性が良く、かつ熱処理を
施すことにより優れた強度および靭性等が得られること
から、自動車等車両用エンジン部品としてのロッカアー
ム等の鋳造用合金として従来より広く用いられている。(Prior art) Generally, AfI-8t-Cu alloy and AfI-Si-C
U-Mg alloys have good castability and can obtain excellent strength and toughness through heat treatment, so they have been widely used as alloys for casting rocker arms and other engine parts for automobiles and other vehicles. It is used.
しかし、エンジンの高出力化が叫ばれている今日、上記
ロッカアーム等は運転中に苛酷な条件に晒されることか
ら、上記強度および靭性等の機械的性質の向上がさらに
要求される。そこで、この要求を満たすべく、例えば特
開昭６２−１８７５３９号公報に開示されているように
、上述の如きＡｌ） −３ｉ −Ｃｕ系合金等で鍛造素
材を鋳造し、次いで、この鍛造素材を鍛造することによ
り、機械的性質の向上を図るようにする方法が知られて
いる。However, in today's world where there is a demand for higher engine output, the rocker arms and the like are exposed to severe conditions during operation, so there is a further demand for improved mechanical properties such as the strength and toughness. Therefore, in order to meet this demand, for example, as disclosed in Japanese Patent Application Laid-open No. 187539/1987, a forged material is cast from the above-mentioned Al)-3i-Cu alloy, and then this forged material is A method of improving mechanical properties by forging is known.
（発明が解決しようとする課８）
ところで、通常、Ａ９合金製鋳造品は、鋳造後に金属組
織の機械的性質を向上させるために、例えば約５００℃
の加熱条件の下で８時間保持して水冷する溶体化処理と
、その後に例えば約１７０℃の加熱条件の下で６時間保
持して空冷する時効処理とからなるいわゆるＴ６処理と
称せられる熱処理が施され、このＴ６処理により共晶Ｓ
１の針状化合物を分断して球状化することが行われる。(Issue 8 to be solved by the invention) By the way, normally, A9 alloy cast products are heated to about 500°C, for example, in order to improve the mechanical properties of the metal structure after casting.
A heat treatment called T6 treatment consists of a solution treatment in which the material is held for 8 hours under heating conditions of about 170°C and then cooled in water, followed by an aging treatment in which it is held for 6 hours and air cooled under heating conditions of about 170°C. This T6 treatment results in eutectic S
The needle-like compound of No. 1 is divided into spheres.
そして、上述の如き鋳造されたＡ９合金製鍛造素材を鍛
造する場合においても、一般には、上記従来の経験を踏
襲して鋳造品の熱処理条件と同じ条件の下で熱処理を行
うのが通例である。When forging the cast A9 alloy forged material as described above, it is generally customary to carry out the heat treatment under the same conditions as the heat treatment conditions for the cast product, following the above conventional experience. .
一方、生産の効率アップ化を達成する場合、如何にして
生産サイクルタイムを短縮するかがネックとなっており
、その達成手段として、例えば鋳造時間や鍛造時間を短
縮化することが考えられる。On the other hand, in order to improve production efficiency, the bottleneck is how to shorten production cycle time, and one possible means to achieve this is to shorten casting time or forging time, for example.
しかし、これらもさるこさながら、生産工程中に占める
時間的比率の大きい熱処理時間の短縮化を図ることがで
きれば、生産サイクルタイムを大幅に短縮し得て上記生
産の効率アップ化を達成する上において非常に好ましい
。However, if we can shorten the heat treatment time, which takes up a large proportion of the time in the production process, we can significantly shorten the production cycle time and improve the efficiency of production mentioned above. Very preferred.
本発明はかかる点に鑑みてなされたものであり、その目
的とするところは、鋳造されたＡ１合金製鍛造素材の金
属組織中に晶出している共晶Ｓｉの針状化合物が鍛造に
より分断されることに着目し、上記鍛造素材を鍛造した
後に行われる熱処理条件を種々検討した結果、従来より
踏襲されている鋳造品の熱処理条件よりも短い時間で上
記針状化合物を球状化し得ることを見い出し、これによ
り生産サイクルタイムを大幅に短縮せしめて生産の効率
アップ化を達成せんとすることにある。The present invention has been made in view of the above, and its purpose is to break up the acicular compound of eutectic Si crystallized in the metal structure of the cast A1 alloy forged material by forging. Focusing on this, we investigated various heat treatment conditions after forging the forged material, and found that the acicular compound could be spheroidized in a shorter time than the conventional heat treatment conditions for cast products. The purpose of this is to significantly shorten the production cycle time and improve production efficiency.
（課題を解決するための手段）
上記の目的を達成するため、本発明の解決手段は、所定
形状に鋳造されたＡｌ合金製鍛造素材を鍛造することに
より鍛造品を製造する方法として、まず、上記Ａｌ１合
金製鍛造素材を鍛造する。次いで、この鍛造された鍛造
品に所定温度条件の下で２〜５時間保持して水冷する溶
体化処理を施した後、時効処理を施すようにする。(Means for Solving the Problems) In order to achieve the above object, the solving means of the present invention first provides a method for manufacturing a forged product by forging an Al alloy forged material cast into a predetermined shape. The above-mentioned Al1 alloy forged material is forged. Next, the forged product is subjected to a solution treatment in which it is held under predetermined temperature conditions for 2 to 5 hours and cooled with water, and then subjected to an aging treatment.
（作用）
上記の構成により、本発明方法では、Ａｌ７合金製鍛造
素材から鍛造された鍛造品の金属組織は、鍛造前の上記
鍛造素材の金属組織中に晶出している共晶Ｓｉの針状化
合物が分断されていることから、この分断されている分
だけ上記針状化合物の球状化のための時間が短縮され、
さらには、鍛造時の塑性変形による歪エネルギの蓄積に
より上記針状化合物の球状化が促進される。よって熱処
理時間が鋳造品を熱処理する場合よりも短い時間（２〜
５時間の溶体化処理時間）でなされ、これにより生産サ
イクルタイムが大幅に短縮されて生産の効率アップ化が
達成されることとなる。(Function) With the above configuration, in the method of the present invention, the metal structure of the forged product forged from the Al7 alloy forged material is in the form of needles of eutectic Si crystallized in the metal structure of the forged material before forging. Since the compound is fragmented, the time for spheroidizing the needle-like compound is shortened by the amount of fragmentation.
Furthermore, the accumulation of strain energy due to plastic deformation during forging promotes spheroidization of the acicular compound. Therefore, the heat treatment time is shorter (2 to 2
5 hours of solution treatment time), thereby significantly shortening the production cycle time and achieving increased production efficiency.
（実施例）
以下、本発明の実施例に係るＡΩ合金製鍛造品製造方法
を図面に基づいて説明する。(Example) Hereinafter, a method for manufacturing an AΩ alloy forged product according to an example of the present invention will be described based on the drawings.
まず、Ｃｕ：２，５ｗｔ％、Ｓｉ：１０．０ｗｔ％、Ｍ
ｇ：０．７ｗｔ％、Ｆｅ：０．３ｗｔ％、Ｍｎ ： ０
． ３ｗ ｔ％、残部がＡｆｆおよび上記各元素以外の
不可避的不純物からなるＡ１合金の地金を用意する。次
いで、この地金を溶解した後、脱環や脱ガス等を目的と
した溶湯処理を行う。その後、例えば７１０℃に設定さ
れた溶湯を鋳型に注入してブランク材としてのＡ４７合
金製鍛造素材を所定形状に鋳造する。First, Cu: 2.5 wt%, Si: 10.0 wt%, M
g: 0.7wt%, Fe: 0.3wt%, Mn: 0
．． An A1 alloy base metal consisting of 3wt% and the balance being Aff and inevitable impurities other than the above-mentioned elements is prepared. Next, after melting this metal, molten metal treatment is performed for the purpose of deringing, degassing, etc. Thereafter, a molten metal set at, for example, 710° C. is poured into a mold to cast an A47 alloy forged material as a blank into a predetermined shape.
その後、この鋳造された鍛造素材を鋳型内に溶湯を注入
する堰と切断分離し、例えば４５０℃に加熱された鍛造
素材を型ａ１５０℃に設定された鍛造装置のグイとパン
チとで１５分に亘って圧縮して塑性変形させることによ
り、鍛造品を得る。After that, this cast forged material is cut and separated from the weir for injecting the molten metal into the mold, and the forged material heated to, for example, 450°C is heated to 450°C for 15 minutes using a goo and a punch in a forging device set at 150°C. By compressing and plastically deforming the material, a forged product is obtained.
しかる後、この得られた鍛造品を熱処理炉に搬入し、Ｔ
６処理を施す。つまり、約５００℃の加熱雰囲気中で２
〜５時間保持したのち水冷する溶体化処理を施した後、
約１７０℃の加熱雰囲気中で６時間保持したのち空冷す
る時効処理を施す。After that, the obtained forged product is carried into a heat treatment furnace and T
6. Perform treatment. In other words, 2
After solution treatment by holding for ~5 hours and cooling with water,
Aging treatment is carried out by holding in a heated atmosphere at about 170° C. for 6 hours and then cooling in air.
上記Ｔ６処理中、溶体化処理の保持時間つまり溶体化時
間を２〜５時間に設定したのは、Ｔ６処理後の鍛造品の
機械的性質を調べた結果に基づく。During the T6 treatment, the holding time of the solution treatment, that is, the solution treatment time, was set to 2 to 5 hours based on the results of examining the mechanical properties of the forged product after the T6 treatment.
このことを、機械的性質の代表としてブリネル硬さを例
に挙げて説明すると、第１図実線にて示すように、溶体
化時間が約１．５時間未満になるとブリネル硬さが１０
０未満となって十分な硬さを得ることができなくなる一
方、５時間を越えるとブリネル硬さが横這い状態となっ
て溶体化時間に比例した硬さの向上効果が得られなくな
るからである。なお、この鍛造品の金属組成とほぼ同一
の金属組成からなるＪＩＳ ＡＣ８Ｃでは、ＪＩＳ規
格によればＴ６処理後のブリネル硬さは１１０以上と規
定されていることから、溶体化時間を４時間以上に設定
することが好ましい。また、この鍛造品と同一金属組織
からなる鋳造品の場合では、第１図破線にて示すように
、ブリネル硬さが１００になるまでに約５．５時間の溶
体化時間を要し、かつ溶体化時間が８時間を越えて初め
てブリネル硬さが１１０に達することから考えて、本発
明方法により得られた鍛造品の方が鋳造品よりも短時間
にＴ６処理を行うことができる。このように、本発明方
法により得られた鍛造品の方が鋳造品の場合よりもＴ６
処理を短時間に行い得るのは、鍛造素材の金属組織中に
晶出している共晶Ｓｔの針状化合物が鍛造によって分断
され、かつ鍛造時の塑性変形による歪エネルギが蓄積さ
れており、このため、上記共晶ＳｉＯ針状化合物の球状
化が促進されることによるものであると推量される。To explain this using Brinell hardness as a representative example of mechanical properties, as shown by the solid line in Figure 1, when the solution time is less than about 1.5 hours, Brinell hardness increases by 10.
If it is less than 0, sufficient hardness cannot be obtained, while if it exceeds 5 hours, Brinell hardness levels off and the hardness improvement effect proportional to the solution time cannot be obtained. In addition, JIS AC8C, which has a metal composition that is almost the same as the metal composition of this forged product, has a Brinell hardness of 110 or more after T6 treatment according to the JIS standard, so the solution treatment time is 4 hours or more. It is preferable to set it to . In addition, in the case of a cast product having the same metal structure as this forged product, as shown by the broken line in Figure 1, it takes about 5.5 hours of solution time to reach a Brinell hardness of 100, and Considering that the Brinell hardness does not reach 110 until the solution treatment time exceeds 8 hours, forged products obtained by the method of the present invention can be subjected to T6 treatment in a shorter time than cast products. In this way, the forged product obtained by the method of the present invention has a higher T6 value than the cast product.
The reason why the process can be carried out in a short time is that the needle-like compound of eutectic St crystallized in the metal structure of the forged material is divided by forging, and the strain energy due to plastic deformation during forging is accumulated. Therefore, it is presumed that this is due to the promotion of spheroidization of the eutectic SiO needle compound.
このことを実証するために、溶体化時間を変えた場合に
おける本発明方法により得られた鍛造品の金属組織を３
４０倍に拡大した顕微鏡写真を第２図（ａ）〜（ｄ）に
、上記鍛造品と同一金属組織からなる鋳造品の同様な顕
微鏡写真を第３図（ａ）〜（ｄ）にそれぞれ示す。なお
、各顕微鏡写真中、黒く表われているのは共晶Ｓｉの針
状化合物であることを、白く表われているのはＡＮのマ
トリックス（６品）であることをそれぞれ示す。In order to demonstrate this, the metallographic structures of forged products obtained by the method of the present invention when the solution treatment time was varied were investigated.
Micrographs magnified 40 times are shown in Figures 2 (a) to (d), and similar micrographs of a cast product having the same metal structure as the forged product are shown in Figures 3 (a) to (d), respectively. . In each micrograph, what appears in black indicates the needle-like compound of eutectic Si, and what appears in white indicates the matrix of AN (6 items).
この各顕微鏡写真から明らかなように、溶体化時間が零
の場合は、鍛造品および鋳造品の金属組織は共に、第２
図（ａ）および第３図（ａ）に示すように、共晶Ｓｉが
針状に晶出しているが、鋳造品の共晶Ｓｉが長いのに対
し、鍛造品の共晶Ｓｉは短くなっていることが判る。こ
のように鍛造品の共晶Ｓｉが短くなっているのは、鍛造
時に共晶Ｓｉが分断されることによるものである。そし
て、鍛造品の方は溶体化時間が３時間になると、第２図
（ｂ）に示すように、上記分断された共晶Ｓｉが球状化
している。このように共晶Ｓｔが短時間に球状化するの
は、鍛造時に、上述の如く共晶Ｓｉが分断されているこ
とと、塑性変形による歪エネルギが蓄積されることとに
より、共晶Ｓｔの球状化か促進されることによるもので
ある。そして、溶体化時間がさらに経過して５時間およ
び８時間と経過する従って、第２図（ｃ）および（ｄ）
に示すように、共晶Ｓｉの球状化が一層促進されている
ことが判る。しかし、鋳造品の方は溶体化時間が３時間
になっても、第３図（ｂ）に示すように、共晶Ｓｉの分
断化は進むものの未だ球状化されるに至らず、第３図（
ｃ）に示すように、溶体化時間が５時間になった時点で
やつと第２図（ａ）とほぼ同様の状態となることが判る
。そして、第３図（ｄ）に示すように、溶体化時間が８
時間になっても、第２図（ｂ）のように速やかには球状
化されず、その球状化に時間がかかることが判る。As is clear from these micrographs, when the solution time is zero, the metal structure of both the forged product and the cast product is
As shown in Figures (a) and 3(a), eutectic Si crystallizes in a needle shape, but while the eutectic Si in the cast product is long, the eutectic Si in the forged product is short. It can be seen that The reason why the eutectic Si of the forged product is short in this way is that the eutectic Si is divided during forging. In the case of the forged product, when the solution treatment time reached 3 hours, the divided eutectic Si became spheroidal, as shown in FIG. 2(b). The reason why the eutectic St becomes spheroidized in a short time is because the eutectic Si is divided as mentioned above and the strain energy due to plastic deformation is accumulated during forging. This is due to the promotion of spheroidization. Then, the solution time further elapses to 5 hours and 8 hours. Therefore, FIGS. 2(c) and (d)
As shown in the figure, it can be seen that the spheroidization of the eutectic Si is further promoted. However, in the case of the cast product, even after 3 hours of solution time, the eutectic Si fragmented as shown in Figure 3(b), but it still did not become spheroidized. (
As shown in c), it can be seen that when the solution time reaches 5 hours, the state becomes almost the same as that shown in FIG. 2(a). As shown in Figure 3(d), the solution time was 8.
It can be seen that even after the time has elapsed, the particles are not spheroidized quickly as shown in FIG. 2(b), and it takes time for the spheroidization to take place.
このように、本発明方法により得られた鍛造品では、金
属組織中の共晶Ｓｉが鍛造時に分断され、かつ塑性変形
による歪エネルギが蓄積されていることから、この共晶
Ｓｉの球状化を鋳造品の場合に比べて短時間に行い得、
これによりＴ６６処理間を大幅に短縮することができる
ので、生産サイクルタイムを大幅に短縮して生産の効率
アップ化を達成することができる。As described above, in the forged product obtained by the method of the present invention, the eutectic Si in the metal structure is fragmented during forging, and the strain energy due to plastic deformation is accumulated, so that the spheroidization of the eutectic Si is prevented. It can be done in a shorter time than in the case of cast products,
As a result, the time between T66 processes can be significantly shortened, thereby significantly shortening the production cycle time and increasing production efficiency.
その後、上記鍛造品に形成されているフラッシュ（パリ
）をトリム型で除去した後、このフラッシュを除去した
鍛造品をショットビーニング工程で表面の研掃を行い、
鍛造作業を終了する。After that, the flash formed on the forged product is removed using a trim die, and the surface of the forged product from which the flash has been removed is polished in a shot beaning process.
Finish the forging work.
（発明の効果）
以上説明したように、本発明方法によれば、所定形状に
鋳造されたＡＮ合金製鍛造素材を鍛造することにより、
その金属組織中に晶出している共晶Ｓｔの針状化合物を
鍛造時に分断するので、この分断している分だけ針状化
合物の球状化のための時間を短縮し得、さらには、鍛造
時の塑性変形による歪エネルギの蓄積により上記針状化
合物の球状化を促進し得る。よって熱処理時間を鋳造品
を熱処理する場合よりも短い時間（２〜５時間の溶体化
処理時間）でなし得、これにより生産サイクルタイムを
大幅に短縮して生産の効率アップ化を達成することがで
きる。(Effects of the Invention) As explained above, according to the method of the present invention, by forging an AN alloy forged material cast into a predetermined shape,
Since the acicular compound of eutectic St crystallized in the metal structure is divided during forging, the time for spheroidizing the acicular compound can be shortened by the amount of division, and furthermore, during forging. Accumulation of strain energy due to plastic deformation can promote spheroidization of the acicular compound. Therefore, the heat treatment time can be completed in a shorter time (2 to 5 hours of solution treatment time) than when heat treating a cast product, thereby significantly shortening the production cycle time and increasing production efficiency. can.
図面は本発明の実施例を示し、第１図は本発明方法によ
り得られた鍛造品および鋳造品の溶体化時間とブリネル
硬さとの関係を示すデータ図、第２図（ａ）〜（ｄ）は
溶体化時間を変えた場合における本発明方法により得ら
れた鍛造品の金属組織をそれぞれ３４０倍に拡大して示
す顕微鏡写真である。第３図（ａ）〜（ｄ）は溶体化時
間を変えた場合における鋳造品の金属組織をそれぞれ３
４０倍に拡大して示す顕微鏡写真である。
特 許 出 願 人 広島アルミニウム工業い、＝フ
ー＋＋モ≧胃へ′ノ
図面の浄書で内容シ、二変更なし）
図面の浄書（内容に変更な１．）
手
続
補
正
書（方式）
事件の表示
昭和６３年
特
許
願
第２１３４３７号
２゜
発明の名称
Ａｐ合金製鍛造品の製造方法
３゜
補正をする者
事件との関係The drawings show examples of the present invention, FIG. 1 is a data diagram showing the relationship between solution time and Brinell hardness of forged products and cast products obtained by the method of the present invention, and FIGS. 2(a) to (d) ) are micrographs showing the metal structures of forged products obtained by the method of the present invention when the solution treatment time was varied, each magnified 340 times. Figures 3(a) to 3(d) show the metallographic structure of the cast product when the solution treatment time was changed.
This is a photomicrograph magnified 40 times. Patent Applicant: Hiroshima Aluminum Industry Co., Ltd. = Fu + + Mo ≧ Stomach - Engraving of the drawings (Contents C, 2 No changes) Engraving of the drawings (No changes to the contents 1.) Procedural amendment (formality) Indication of the case Patent Application No. 213437 of 1988 2゜Name of the Invention Method for Manufacturing Ap Alloy Forgings 3゜Relationship with the Amendment Case
Claims (1)
することにより鍛造品を製造する方法であって、上記Ａ
ｌ合金製鍛造素材を鍛造し、次いで、この鍛造された鍛
造品に所定温度条件の下で２〜５時間保持して水冷する
溶体化処理を施した後、時効処理を施すことを特徴とす
るＡｌ合金製鍛造品の製造方法。(1) A method for manufacturing a forged product by forging an Al alloy forged material cast into a predetermined shape, the method comprising:
It is characterized by forging a forged material made of l-alloy, and then subjecting this forged product to a solution treatment of holding it under predetermined temperature conditions for 2 to 5 hours and cooling it with water, and then subjecting it to an aging treatment. A method for manufacturing an Al alloy forged product.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21343788A JPH0261038A (en) | 1988-08-26 | 1988-08-26 | Production of forged product made of al alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21343788A JPH0261038A (en) | 1988-08-26 | 1988-08-26 | Production of forged product made of al alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0261038A true JPH0261038A (en) | 1990-03-01 |
Family
ID=16639216
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21343788A Pending JPH0261038A (en) | 1988-08-26 | 1988-08-26 | Production of forged product made of al alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0261038A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105689613A (en) * | 2016-03-25 | 2016-06-22 | 大冶特殊钢股份有限公司 | Special forging method suitable for super duplex stainless steel bars |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62192567A (en) * | 1986-02-17 | 1987-08-24 | Kobe Steel Ltd | Heat treatment for al alloy |
-
1988
- 1988-08-26 JP JP21343788A patent/JPH0261038A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62192567A (en) * | 1986-02-17 | 1987-08-24 | Kobe Steel Ltd | Heat treatment for al alloy |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105689613A (en) * | 2016-03-25 | 2016-06-22 | 大冶特殊钢股份有限公司 | Special forging method suitable for super duplex stainless steel bars |
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