JPH03294036A - Manufacture of high strength magnesium alloy material - Google Patents
Manufacture of high strength magnesium alloy materialInfo
- Publication number
- JPH03294036A JPH03294036A JP2097282A JP9728290A JPH03294036A JP H03294036 A JPH03294036 A JP H03294036A JP 2097282 A JP2097282 A JP 2097282A JP 9728290 A JP9728290 A JP 9728290A JP H03294036 A JPH03294036 A JP H03294036A
- Authority
- JP
- Japan
- Prior art keywords
- forging
- temperature
- magnesium alloy
- hot
- draft
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000861 Mg alloy Inorganic materials 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 12
- 239000000956 alloy Substances 0.000 title claims description 10
- 238000005242 forging Methods 0.000 claims abstract description 106
- 238000000034 method Methods 0.000 claims abstract description 34
- 238000001125 extrusion Methods 0.000 claims abstract description 5
- 238000005266 casting Methods 0.000 claims abstract description 3
- 238000007796 conventional method Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 2
- 238000002844 melting Methods 0.000 claims description 2
- 239000000463 material Substances 0.000 description 19
- 239000000047 product Substances 0.000 description 14
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 10
- 229910052749 magnesium Inorganic materials 0.000 description 9
- 239000011777 magnesium Substances 0.000 description 9
- 229910052751 metal Inorganic materials 0.000 description 9
- 239000002184 metal Substances 0.000 description 9
- 238000012545 processing Methods 0.000 description 8
- 238000005336 cracking Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 239000013067 intermediate product Substances 0.000 description 4
- 239000011257 shell material Substances 0.000 description 4
- 239000010953 base metal Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 238000011160 research Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Forging (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、ＡＺ８０Ａマグネシウム合金素材を熱間鍛造
して得られる高強度マグネシウム合金材の製造方法に関
するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a method for manufacturing a high-strength magnesium alloy material obtained by hot forging an AZ80A magnesium alloy material.
〔従来の技術と発明が解決しようとする課題〕上記ＡＺ
８０Ａマグネシウム舎金は、航空機、コンピュータ関連
Ｉｌ器等の部品として使用されると共に、軽量化を担う
鍛造用マグネシウム合金として位置づけられているが、
実用上の諸性質は十分明確にされていない、また、製造
条件については一般的には熱間鍛造後直ちに水冷し、１
７７°Ｃ×１６時間焼戻しくＴ５処理）するとされてい
るが、安定した材譬を得るための実際的な製造条件は明
確ではない。[Problems to be solved by conventional technology and invention] Above AZ
80A magnesium alloy is used as parts for aircraft, computer-related equipment, etc., and is also positioned as a magnesium alloy for forging, which helps reduce weight.
The practical properties have not been sufficiently clarified, and the manufacturing conditions are generally water-cooled immediately after hot forging,
Although it is said that T5 treatment (tempering at 77°C for 16 hours) is carried out, the actual manufacturing conditions for obtaining a stable material are not clear.
例えば、ｒ軽金属（１９８９） νｏ１．３９． Ｎ
ｌｌ （第５２〜５７＠）」には、ＡＺ８０Ａマグネシ
ウム舎金の機械的性質に及ばず素材Ｈ歴と熱間鍛造条件
の影響について報告がなされている。これによれば機械
的性質はメタル・フローによる影響を受けるため、押出
材を素材に用いた場合、基準値（例えばＡＳＴＭ規格）
を満足させるためには、３５０℃の鍛造温度で９０％以
上の鍛造圧下率を必要とすることが指摘されている。し
かしながら、このような高い鍛造圧下率を複雑な形状を
有する鍛造品の全領域に均等に与えることは困難であり
、また鍛造割れ限界などを考慮すれば現実的な製造方法
とは言えない、また、機械的強度もより高いものが安定
して得られることが必要であり、その製造方法の開発が
望まれている。For example, r Light Metal (1989) νo1.39. N
ll (Nos. 52 to 57 @), there is a report on the influence of the material H history and hot forging conditions, which is not as good as the mechanical properties of AZ80A magnesium shell. According to this, mechanical properties are affected by metal flow, so when extruded material is used as a material, standard values (for example, ASTM standards)
It has been pointed out that in order to satisfy the requirements, a forging temperature of 350° C. and a forging reduction ratio of 90% or more are required. However, it is difficult to uniformly apply such a high forging reduction rate to the entire area of a forged product with a complex shape, and it is not a realistic manufacturing method considering the limits of forging cracking. It is necessary to stably obtain a material with higher mechanical strength, and the development of a manufacturing method is desired.
本発明は、上述のような事情に鑑みてなされたものであ
って、その目的は、ＡＺ８０Ａマグネシウム台金の押出
素材を元に、鍛造割れを発生させることなく且つ高い機
械的強度を有するマグネシウム台金材を安定して得られ
る、熱間鍛造による高強度マグネシウム合金材の製造方
法を従供することである。The present invention has been made in view of the above-mentioned circumstances, and its purpose is to create a magnesium base that does not cause forging cracks and has high mechanical strength based on an extruded material of AZ80A magnesium base metal. An object of the present invention is to provide a method for manufacturing a high-strength magnesium alloy material by hot forging, which can stably obtain a metal material.
上記の目的を達成するため、本発明に係わる高強度マグ
ネシウム台金材の製造方法は、常法により溶製、鋳造お
よび押出工程を経て製造されたＡＺ８０Ａマグネシウム
舎金素材合金素材造工程により鍛造するものである。In order to achieve the above object, the method for manufacturing a high-strength magnesium base metal material according to the present invention involves forging an AZ80A magnesium base metal material alloy material manufacturing process, which is manufactured through melting, casting, and extrusion processes using conventional methods. It is something.
第一へ工程：３７０℃以Ｈの鍛造温度で鍛造圧下率が７
０％以上の熱間鍛造を施す工程。First process: Forging temperature of 370℃ or higher and forging reduction rate of 7
A process that involves hot forging of 0% or more.
第二工程：ｆＪ４−工程の鍛造温度より低温域で、且つ
第三工程での鍛造圧下率が得られる範囲の鍛造圧下率で
鍛造を施す工程。Second step: a step of forging in a lower temperature range than the forging temperature in the fJ4-step and at a forging reduction rate within a range that allows the forging reduction rate in the third step to be obtained.
第三工程＝３５０℃以下の鍛造温度で鍛造圧下率が２０
％以下の熱間鍛造を施す工程。Third step = Forging temperature below 350℃ and forging reduction rate of 20
% or less hot forging process.
本発明者等が調査研究したところによれば、ＡＺ８０Ａ
マグネシウム舎金は結晶構造（六方晶構造）に起因する
異方性のために、その機械的性質は、結晶方位とその集
合としてのメタル・フローに強く依存することが判明し
た。これにより、本発明者らは、ＡＺ８０Ａマグネシウ
ム合金の鍛造品に必要な強度を持たせるためには、押出
素材のメタル・フローを変え、鍛造品のメタル・フロー
を望ましい方向に制御すること、および熱加工処理的効
果や加工硬化をもたらす微視的構造を制御することが必
要であると考えた。According to research conducted by the inventors, AZ80A
Due to the anisotropy of magnesium metal due to its crystal structure (hexagonal crystal structure), its mechanical properties were found to be strongly dependent on the crystal orientation and metal flow as a collection thereof. As a result, the present inventors found that in order to provide a forged product of AZ80A magnesium alloy with the necessary strength, it is necessary to change the metal flow of the extruded material and control the metal flow of the forged product in a desired direction, and It was considered necessary to control the microscopic structure that causes thermal processing effects and work hardening.
而して、本発明においては、鍛造の初期工程（第一工程
）では、大変形を与えて押出素材の持つ強いメタル・フ
ローを破壊すると共に、続く型鍛造工程（第二工程）の
ために、鍛造品のメタル・フローを考慮した中間形状を
準備する鍛造を施し、第二工程では、最終仕上げ鍛造（
第二工程）の前段階として最終に近い形状を与え、製品
形状を整える鍛造を施し、そして第三工程では、最終仕
上げ鍛造として最終形状と必要材質を与える程度の比較
的低温域で且つ軽圧下率の＠造を施すこととしたもので
ある。Therefore, in the present invention, in the initial forging process (first process), large deformation is applied to destroy the strong metal flow of the extruded material, and at the same time, for the subsequent die forging process (second process), , forging is performed to prepare an intermediate shape that takes into consideration the metal flow of the forged product, and in the second process, final forging (
As a pre-step to the second step, forging is performed to give a shape close to the final shape and adjust the product shape, and in the third step, final forging is performed at a relatively low temperature and under light reduction to give the final shape and required material. It was decided to use the @ symbol for the rate.
一方、本発明者等は、本発明の研究の過程で、ＡＺ８０
Ａマグネシウム舎金の熱間鍛造性を把握するために、鍛
造割れに及ぼす鍛造温度と鍛造圧下率との関係を調査し
た。この調査結果を第４図に示す、この図では、横軸に
鍛造温度を、縦軸に鍛造圧下率を示し、実線Ａは鍛造割
れを起こす限界線を示す、この調査結果によれば、鍛造
割れを起こす鍛造圧下率は、鍛造温度が３８０〜４００
℃で約ＢＯ％、鍛造温度が３００℃で約５０％まで低下
するように温度依存性のあることが判明した。On the other hand, in the course of research on the present invention, the present inventors
In order to understand the hot forgeability of A magnesium shell metal, the relationship between forging temperature and forging reduction rate on forging cracking was investigated. The results of this investigation are shown in Figure 4. In this figure, the horizontal axis shows the forging temperature, the vertical axis shows the forging reduction rate, and the solid line A indicates the limit line at which forging cracks occur. The forging reduction rate that causes cracks is when the forging temperature is 380 to 400.
It was found that there is a temperature dependence such that the BO% decreases at a temperature of 300°C and decreases to approximately 50% at a forging temperature of 300°C.
このようなことから、上記の考え方に基づく本発明に係
わる鍛造工程において、第一工程では、押出素材の持つ
強いメタル・フローを破壊し材質を改善するため、鍛造
圧下率７０％以トの大きな加工量を加えることが必要で
あり、このため、鍛造割れが生じない高鍛造性の条件下
で鍛造を施さなければならない、すなわち、鍛造温度と
しては、３７０°Ｃ以上、好ましくは３８０°Ｃ以上が
よい、またそのト限は、ＡＺ８０Ａマグネシウム合金の
共晶温度が約４３７°Ｃにあること、および加工発熱を
考慮すれば４００℃以下とすることが望ましい。For this reason, in the forging process according to the present invention based on the above-mentioned concept, in the first process, a large forging reduction rate of 70% or more is used in order to destroy the strong metal flow of the extruded material and improve the material quality. It is necessary to increase the amount of processing, and for this reason, forging must be performed under conditions of high forgeability without forging cracks, that is, the forging temperature is 370°C or higher, preferably 380°C or higher. It is desirable that the temperature limit is 400°C or less, considering that the eutectic temperature of the AZ80A magnesium alloy is about 437°C and the heat generated during processing.
第二工程では、最終仕上げ鍛造（第二工程）の前段階と
して製品形状のほとんどを成形し、最終仕上げ鍛造の準
備をすることから、鍛造品内部の加工量は各部分で不均
一・となり局部的に高い変形部分も生じる。このため、
ある程度以上の鍛造性を有する条件下で鍛造する必要が
ある。同時に熱加工処理的な材質調整を行うため、第一
・工程よりやや低温域で鍛造する必要がある。これらの
条件を満たす鍛造温度としては３５０〜３７０°Ｃとす
ることが望ましい、また加えるべき加工量は、最終仕上
げ鍛造の材質調整に必要な加工量（２０％以下）を残し
て決定する。In the second process, as a step before the final finish forging (second process), most of the product shape is formed and prepared for the final finish forging, so the amount of processing inside the forged product is uneven in each part, resulting in localized areas. Some parts are highly deformed. For this reason,
It is necessary to forge under conditions that have a certain level of forgeability. At the same time, in order to adjust the material through heat processing, it is necessary to forge at a slightly lower temperature than the first step. The forging temperature that satisfies these conditions is preferably 350 to 370°C, and the amount of processing to be added is determined by leaving the amount of processing (20% or less) required for material adjustment in final finish forging.
第三工程の最終仕上げ鍛造では、製品の寸法形状を最終
的に与えると共に、強度向上を目指した材質調整を行う
ため、ある程度の鍛造性を有し、加工硬化を残すことの
できる条件下で鍛造する必要がある。これらの条件を満
たず鍛造温度としては３００〜３５０℃とすることが望
ましい、また加えるべき加工量は、加工硬化を有効に与
え、製品の延性の極端な低下が生じない量として３〜２
０％がよく、より好ましくは５〜１５％がよい。In the third process, final forging, the final dimensions and shape of the product are given, and the material is adjusted to improve strength. Forging is performed under conditions that allow forgeability to a certain extent and allow work hardening to remain. There is a need to. It is desirable to set the forging temperature to 300 to 350℃ without satisfying these conditions, and the amount of processing to be applied is 3 to 2, which is an amount that effectively imparts work hardening and does not cause an extreme decrease in the ductility of the product.
It is preferably 0%, more preferably 5 to 15%.
と述の如き鍛造工程でＡＺ８０Ａマグネシウム合金の押
出素材を熱間鍛造することにより、鍛造割れを発生させ
ることな（且つ高い機械的強度を有するマグネシウム舎
金材が安定して得られる。By hot forging an extruded AZ80A magnesium alloy material in the forging process as described above, a magnesium shell material that does not cause forging cracks (and has high mechanical strength) can be stably obtained.
次に、本発明の効果を実施例によってさらに具体的に説
明する。Next, the effects of the present invention will be explained in more detail with reference to Examples.
先ず、常法により溶製、鋳造したＡＺ８０Ａマグネシウ
ム舎金からなる鋳塊を押出比６で押出して直径１２０ｍ
＋＊の押出素材を得た６次いで、この押出素材を高さ２
１０ｍ−に切断し、これを出発素材として下表に示す鍛
造条件で据え込み鍛造を行った後、熱間鍛造後直ちに水
冷し、１７７℃×１６時間の焼戻し処理（Ｔ５処理）を
施した。これにより得られた製品の円周方向および半径
方向の機械的性質を調査した。その調査結果を下表に併
せて示す。First, an ingot made of AZ80A magnesium shell, melted and cast using a conventional method, was extruded at an extrusion ratio of 6 to a diameter of 120 m.
+* extruded material was obtained 6 Next, this extruded material was made to a height of 2
It was cut into 10 m-pieces and was used as a starting material for upsetting forging under the forging conditions shown in the table below. Immediately after hot forging, it was water-cooled and tempered at 177° C. for 16 hours (T5 treatment). The circumferential and radial mechanical properties of the resulting product were investigated. The survey results are also shown in the table below.
（以 下 余 白）
上表に示すように、阻１〜４は本発明例であって、第一
工程、第二工程は同一の鍛造条件下で熱間鍛造を行った
。すなわち、第一工程では、鍛造温度３８０℃で鍛造圧
下率７５％を、第二工程では、鍛造温度３５０℃″′ｃ
＠造圧下率３５％を与えた。各工程後鍛造中間品は水冷
されたが鍛造割れも無く良好な外観を示していた。そし
てさらに第二工程では、磁１〜３の鍛造中間品に対して
は鍛造圧下率を同一の１５％で鍛造温度をそれぞれ３０
０℃、３２０℃、３５０℃に変えた鍛造条件下で、また
胤４の鍛造中間品に対しては鍛造圧下率６％、鍛造温度
３２０℃の鍛造条件下で、熱間鍛造を行った。得られた
最終鍛造品も鍛造中間品と同様にｔＢ遣割れも無く良好
な外観を示していた。(Left below) As shown in the table above, Samples 1 to 4 are examples of the present invention, and the first and second steps were hot forged under the same forging conditions. That is, in the first step, the forging temperature was 380°C and the forging reduction rate was 75%, and in the second process, the forging temperature was 350°C'''c.
@ A rolling reduction rate of 35% was given. After each process, the forged intermediate product was water-cooled, but it had no forging cracks and had a good appearance. Furthermore, in the second process, for the forged intermediate products of Magnesium 1 to 3, the forging reduction rate is the same 15% and the forging temperature is 30%.
Hot forging was performed under forging conditions of 0° C., 320° C., and 350° C., and for the forging intermediate product of Seed 4, under forging conditions with a forging reduction rate of 6% and a forging temperature of 320° C. The obtained final forged product had no tB cracking and had a good appearance, similar to the forged intermediate product.
隘５〜７は比較例であって、鍛造温度を同一の３８０℃
で鍛造圧下率をそれぞれ７０％、７５％、８０％に変え
た鍛造条件下で熱間鍛造を行った。得られた鍛造品の外
観を調査した結果、阻５とＮｌ１６には割れが認められ
なかったが、鍛造圧下率が高かった随７には外周表面部
に小さな鍛造割れが認められた。Nos. 5 to 7 are comparative examples, and the forging temperature was the same at 380°C.
Hot forging was carried out under forging conditions in which the forging reduction ratio was changed to 70%, 75%, and 80%, respectively. As a result of examining the appearance of the obtained forged products, no cracks were found in No. 5 and No. 16, but small forging cracks were found on the outer peripheral surface of No. 7, which had a high forging reduction ratio.
また、上表の機械的性質の結果から明らかなように、本
発明例では、円周方向、半径方向の耐力、引張強さがそ
れぞれ２１．７〜２４．６ｋｇ／ｓ＋■” 、３１．７
〜３３．２ｋｇ／ｍｓ”の範囲にあるのに対して、比較
例のそれらは１８．７〜２１．８ｋｇ／ｍ−’ 、２６
．２〜３１．０ｋｇ／ｍｍ”の範囲であり、明らかに本
発明例の方が強度が向上している。また伸びについては
、本発明例、比較例共に得られた値のバラツキが大きく
比較することは離しいが、本発明例の伸び（延性）が比
較例のそれより劣化する傾向にあるとは認められない。Furthermore, as is clear from the results of the mechanical properties in the table above, in the example of the present invention, the yield strength and tensile strength in the circumferential direction and radial direction are 21.7 to 24.6 kg/s+■'' and 31.7, respectively.
~33.2 kg/ms'', whereas those of the comparative example ranged from 18.7 to 21.8 kg/m-', 26
．． 2 to 31.0 kg/mm'', and the strength of the inventive example is clearly improved.Also, regarding elongation, the variation in the values obtained for both the inventive example and the comparative example is large. Although this is a far cry, it is not recognized that the elongation (ductility) of the inventive examples tends to be worse than that of the comparative examples.
以上詳細に説明したように、本発明に係わる高強度マグ
ネシウム合金材の製造方法によれば、鍛造割れの無い且
つ高い機械的強度を有するＡＺ８０Ａマグネシウム合金
の鍛造品が得られると共に、Ａ７：８０Ａマグネシウム
合金の押出素材を元に、鍛造割れを発生させることな（
且つ高い機械的強度を有するように安定して熱間鍛造す
ることができAs explained in detail above, according to the method for manufacturing a high-strength magnesium alloy material according to the present invention, a forged product of AZ80A magnesium alloy having no forging cracks and high mechanical strength can be obtained, and a forged product of A7:80A magnesium alloy can be obtained. Based on alloy extrusion material, forging cracks will not occur (
It also has high mechanical strength and can be stably hot forged.
第１図は、ＡＺ８０Ａマグネシウム合金の鍛造割れに及
ぼす鍛造温度と鍛造圧下率との関係を示す図である。
Ａ：鍛造割れを起こす限界線
第１図FIG. 1 is a diagram showing the relationship between forging temperature and forging reduction rate on forging cracking of AZ80A magnesium alloy. A: Limit line that causes forging cracking (Fig. 1)
Claims (1)
ＡＺ８０Ａマグネシウム合金素材を下記鍛造工程により
鍛造することを特徴とする高強度マグネシウム合金材の
製造方法。 第一工程：３７０℃以上の鍛造温度で鍛造圧下率が７０
％以上の熱間鍛造を施す工程。 第二工程：第一工程の鍛造温度より低温域で、且つ第三
工程での鍛造圧下率が得られる範囲の鍛造圧下率で鍛造
を施す工程。 第三工程：３５０℃以下の鍛造温度で鍛造圧下率が２０
％以下の熱間鍛造を施す工程。[Scope of Claims] A method for producing a high-strength magnesium alloy material, which comprises forging an AZ80A magnesium alloy material produced through melting, casting, and extrusion processes using conventional methods through the following forging process. First step: Forging temperature of 370℃ or higher and forging reduction rate of 70
% or more hot forging process. Second step: A step of forging in a lower temperature range than the forging temperature of the first step and at a forging reduction rate within a range that allows the forging reduction rate in the third step to be obtained. Third process: Forging temperature below 350℃ and forging reduction rate of 20
% or less hot forging process.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2097282A JP2763175B2 (en) | 1990-04-11 | 1990-04-11 | Manufacturing method of high strength magnesium alloy material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2097282A JP2763175B2 (en) | 1990-04-11 | 1990-04-11 | Manufacturing method of high strength magnesium alloy material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03294036A true JPH03294036A (en) | 1991-12-25 |
| JP2763175B2 JP2763175B2 (en) | 1998-06-11 |
Family
ID=14188160
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2097282A Expired - Lifetime JP2763175B2 (en) | 1990-04-11 | 1990-04-11 | Manufacturing method of high strength magnesium alloy material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2763175B2 (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05305380A (en) * | 1992-04-28 | 1993-11-19 | Mazda Motor Corp | Manufacture of magnesium alloy member |
| EP1044742A2 (en) * | 1999-03-29 | 2000-10-18 | Kurimoto Limited | Threaded fastener and a method of making the same |
| EP0945199A3 (en) * | 1998-03-26 | 2001-04-25 | Tokyo Seitan Inc. | Thin, forged magnesium alloy casing and method for producing the same |
| JP2008195984A (en) * | 2007-02-09 | 2008-08-28 | Japan Steel Works Ltd:The | Method for producing high strength metallic material |
| US20110188967A1 (en) * | 2010-02-03 | 2011-08-04 | Kuo-Chen Hung | Magnesium Nut Manufacturing Method and Magnesium Nut Member Produced Thereby |
| CN103706740A (en) * | 2013-12-06 | 2014-04-09 | 陕西宏远航空锻造有限责任公司 | Forging method of circular GH105 high-temperature alloy forging |
| CN104438996A (en) * | 2014-09-28 | 2015-03-25 | 洛阳镁鑫合金制品有限公司 | ZK61M magnesium alloy slab ingot forging and rolling process |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60221142A (en) * | 1984-04-05 | 1985-11-05 | Kobe Steel Ltd | Forging of mg-zn-zr alloy |
-
1990
- 1990-04-11 JP JP2097282A patent/JP2763175B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60221142A (en) * | 1984-04-05 | 1985-11-05 | Kobe Steel Ltd | Forging of mg-zn-zr alloy |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05305380A (en) * | 1992-04-28 | 1993-11-19 | Mazda Motor Corp | Manufacture of magnesium alloy member |
| EP0945199A3 (en) * | 1998-03-26 | 2001-04-25 | Tokyo Seitan Inc. | Thin, forged magnesium alloy casing and method for producing the same |
| US6316129B1 (en) | 1998-03-26 | 2001-11-13 | Tokyo Seitan Inc. | Thin, forged magnesium alloy casing and method for producing same |
| US6511560B2 (en) | 1998-03-26 | 2003-01-28 | Tokyo Seitan Inc. | Thin, forged magnesium alloy casing and method for producing same |
| EP1044742A2 (en) * | 1999-03-29 | 2000-10-18 | Kurimoto Limited | Threaded fastener and a method of making the same |
| US6328657B1 (en) * | 1999-03-29 | 2001-12-11 | Kurimoto, Ltd. | Threaded fastener and a method of making same |
| EP1044742A3 (en) * | 1999-03-29 | 2006-04-19 | Kurimoto Limited | Threaded fastener and a method of making the same |
| JP2008195984A (en) * | 2007-02-09 | 2008-08-28 | Japan Steel Works Ltd:The | Method for producing high strength metallic material |
| JP4693007B2 (en) * | 2007-02-09 | 2011-06-01 | 株式会社日本製鋼所 | Manufacturing method of high strength metal material |
| US20110188967A1 (en) * | 2010-02-03 | 2011-08-04 | Kuo-Chen Hung | Magnesium Nut Manufacturing Method and Magnesium Nut Member Produced Thereby |
| CN103706740A (en) * | 2013-12-06 | 2014-04-09 | 陕西宏远航空锻造有限责任公司 | Forging method of circular GH105 high-temperature alloy forging |
| CN104438996A (en) * | 2014-09-28 | 2015-03-25 | 洛阳镁鑫合金制品有限公司 | ZK61M magnesium alloy slab ingot forging and rolling process |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2763175B2 (en) | 1998-06-11 |
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