JPH0436410A - Complex sintered tungsten alloy - Google Patents
Complex sintered tungsten alloyInfo
- Publication number
- JPH0436410A JPH0436410A JP14286690A JP14286690A JPH0436410A JP H0436410 A JPH0436410 A JP H0436410A JP 14286690 A JP14286690 A JP 14286690A JP 14286690 A JP14286690 A JP 14286690A JP H0436410 A JPH0436410 A JP H0436410A
- Authority
- JP
- Japan
- Prior art keywords
- core
- content
- tungsten alloy
- sintered tungsten
- outer peripheral
- 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
- 229910001080 W alloy Inorganic materials 0.000 title claims abstract description 26
- 230000002093 peripheral effect Effects 0.000 claims abstract description 18
- 239000002131 composite material Substances 0.000 claims description 17
- 229910052721 tungsten Inorganic materials 0.000 claims description 6
- 238000000034 method Methods 0.000 abstract description 11
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 239000011162 core material Substances 0.000 description 38
- 239000002994 raw material Substances 0.000 description 13
- 238000005245 sintering Methods 0.000 description 13
- 229910045601 alloy Inorganic materials 0.000 description 12
- 239000000956 alloy Substances 0.000 description 12
- 230000005484 gravity Effects 0.000 description 11
- 239000007791 liquid phase Substances 0.000 description 11
- 239000000843 powder Substances 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 238000000465 moulding Methods 0.000 description 4
- 238000000280 densification Methods 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 230000002706 hydrostatic effect Effects 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 230000008094 contradictory effect Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000013013 elastic material Substances 0.000 description 2
- 230000035515 penetration Effects 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910003271 Ni-Fe Inorganic materials 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、外周部が心部より高延性を有する複合構造を
有して衝撃的な負荷のかかる徹甲用弾心材やタイルなど
の用途に好適な複合焼結タングステン合金に関する。[Detailed Description of the Invention] [Field of Industrial Application] The present invention is applicable to armor-piercing elastic materials, tiles, etc., which have a composite structure in which the outer peripheral part has higher ductility than the core part and are subjected to impact loads. The present invention relates to a composite sintered tungsten alloy suitable for.
従来、高比重で且つ高延性が要求される弾心材やクイル
などの用途には、Ｗ−Ｎｉ−Ｆｅ系の焼結タングステン
合金が用いられてきたが、同合金における高比重と高延
性とは相反する関係にあり、高比重にすると剛性が向上
する一方で、延性が低下する。このような相反する性能
を満たすものとして、特開昭６２ｗｔ９６３０６号公報
に複合構造の焼結タングステン合金が開示されている。Conventionally, W-Ni-Fe-based sintered tungsten alloys have been used for applications such as elastic core materials and quills that require high specific gravity and high ductility. They have a contradictory relationship; when the specific gravity is increased, the rigidity improves, but the ductility decreases. A sintered tungsten alloy having a composite structure is disclosed in Japanese Patent Application Laid-open No. 62WT96306 as a material that satisfies these contradictory properties.
このものは、Ｗを主成分とし残部がＮｉとＦｅとからな
る焼結タングステン合金において、外周部のＷ含有量を
心部のＷ含有量より高めることにより、心部が外周部よ
り高延性を有するものとした複層構造を備えている。This is a sintered tungsten alloy consisting of W as the main component and the balance being Ni and Fe.By increasing the W content in the outer periphery than in the core, the core has higher ductility than the outer periphery. It has a multilayer structure.
また、この心部より外周部のＷ含有量の方が多い複層構
造を備えた焼結タングステン合金に、加工率５〜２０％
でスェージング加工を施して外周部の硬さを向上させる
ことも示されている。In addition, we have developed a sintered tungsten alloy with a multilayer structure in which the W content is higher in the outer periphery than in the core, with a processing rate of 5 to 20%.
It has also been shown that swaging can be applied to improve the hardness of the outer periphery.
〔発明が解決しようとする課題］
しかし、弾心材やタイルでは、実使用時の衝撃的な負荷
による破壊が心部ではなく外周部の表面から生じる。し
たがって、心部より外周部の方の延性を高くした方が実
際的であり、より効果的である。ところが上記従来例の
複合焼結タングステン合金にあっては、「心部が外周部
より高延性を有する」ため、複合構造とした効果が殆ど
発揮されないという問題点があった。[Problems to be Solved by the Invention] However, in elastic core materials and tiles, breakage due to impact loads during actual use occurs not from the core but from the surface of the outer periphery. Therefore, it is more practical and more effective to make the outer periphery more ductile than the core. However, the conventional composite sintered tungsten alloy has a problem in that "the core has higher ductility than the outer circumference", so that the effect of having a composite structure is hardly exhibited.
また、スェージング加工による加工硬化を利用して硬度
の向上を図っているが、その加工率が２０％を越えるス
ェージング加工を施すと割れが発生し易くなり、弾心材
やタイルに負荷される衝撃的な負荷に耐え得る程の高硬
度を獲得することは難しいという問題点があった。In addition, hardness is improved by using work hardening due to swaging, but if the swaging process has a processing rate of more than 20%, cracks are likely to occur, and impact loads on elastic materials and tiles are likely to occur. There was a problem in that it was difficult to obtain a hardness high enough to withstand heavy loads.
そこで本発明の目的とするところは、弾心材やタイルの
衝撃的な負荷による破壊の実状況に即し、外周部が心部
より高延性を有する複合焼結タングステン合金を提供す
ることにより、上記従来の問題点を解決することにある
。Therefore, an object of the present invention is to provide a composite sintered tungsten alloy in which the outer peripheral part has higher ductility than the core part, in accordance with the actual situation of fracture of elastic core materials and tiles due to impact loads. The purpose is to solve conventional problems.
〔課題を解決するための手段〕
本発明は、Ｗを主成分とし残部がＮｉとＦｅとからなる
焼結タングステン合金であって、心部のＷ含有量を９３
〜９８−ｔ％とし、外周部のＷ含有量を８０〜９２ｗｔ
％とした外周部が心部より高延性を有する複合焼結タン
グステン合金である。[Means for Solving the Problems] The present invention provides a sintered tungsten alloy consisting of W as the main component and the balance being Ni and Fe, the W content in the core being 93%.
~98-t%, and the W content in the outer periphery is 80-92wt.
This is a composite sintered tungsten alloy whose outer periphery has higher ductility than the core.
また、上記複合焼結タングステン合金に加工率２５〜７
０％のスェージング加工を施して、Ｈｖ５００以上の硬
度を有するものとすることができる。In addition, the processing rate of 25 to 7 is applied to the above composite sintered tungsten alloy.
It can be subjected to 0% swaging processing to have a hardness of Hv500 or more.
本発明者らは高延性と高比重とを兼備した焼結タングス
テン合金について研究を重ねた結果、焼結タングステン
合金全体の高延性化と高比重化に関して外周部の延性が
支配因子であることを見出した。本発明はこの知見に基
づいてなされたもので、外周部のＷ含有量は心部より少
ない複層構造としたため、外周部が高延性で、心部は高
比重。As a result of repeated research on sintered tungsten alloys that have both high ductility and high specific gravity, the present inventors have found that the ductility of the outer periphery is the controlling factor in increasing the ductility and specific gravity of the entire sintered tungsten alloy. I found it. The present invention was made based on this knowledge, and since the outer periphery has a multilayer structure with a lower W content than the core, the outer periphery has high ductility and the core has high specific gravity.
高剛性となり、衝撃的な負荷による破壊が外周部の表面
から生じる弾心材やタイル等の用途に最適なものとなっ
た。It has high rigidity, making it ideal for applications such as elastic core materials and tiles, where breakage due to impact loads occurs from the outer peripheral surface.
また、外周部を高延性としたため割れを生じることなく
高加工率のスェージング加工を施すことが可能となり、
加工硬化させて衝撃的な負荷に耐え得る程の高硬度を有
する合金を得ることができる。In addition, since the outer periphery is made highly ductile, it is possible to perform swaging processing at a high processing rate without causing cracks.
By work hardening, an alloy with high hardness that can withstand impact loads can be obtained.
以下、更に詳細に説明する。This will be explained in more detail below.
本発明のタングステン焼結合金の主成分はＷでで、残部
がＮｉとＦｅである。Ｗ含有量は、成形体の心部と外周
部とで異なっており、合金全量に対して心部では９３〜
９８−ｔ％であるのに対し、外周部は８０〜９２−ｔ％
とより少なくしている。The main component of the tungsten sintered alloy of the present invention is W, with the remainder being Ni and Fe. The W content differs between the core and the outer periphery of the molded body, and the W content in the core is 93~93% relative to the total amount of alloy.
98-t%, while the outer periphery is 80-92-t%
and less.
これにより、より高比重の心部を、より高延性の外周部
が取り巻く複合構造としている。Ｗ含有量が心部で９３
−ｔ％未満、外周部で８０ｅｖｔ％未満の場合には所定
の高比重を満足する合金を得ることができない。一方、
Ｗ含有量が心部で９８−ｔ％を越え、外周部で９２ｗｔ
％を越える場合には所定の高延性を満足する合金を得る
ことができない。This creates a composite structure in which a core with higher specific gravity is surrounded by an outer peripheral part with higher ductility. W content is 93 in the core
If the content is less than -t% or less than 80evt% at the outer periphery, an alloy satisfying a predetermined high specific gravity cannot be obtained. on the other hand,
W content exceeds 98-t% in the core and 92wt in the outer periphery
%, it is impossible to obtain an alloy that satisfies the predetermined high ductility.
ＮｉとＦｅは、タングステン焼結合金を製造する際の液
相焼結工程において液相を発生して高密度化を促進し、
かつ合金の延性を高める結合材として添加される。その
添加量は、合金全量に対して心部では２〜７ｗｔ％、外
周部で８〜２０ｗｔ％である。２ｗｔ％未満では十分な
液相が発生せず、完全に緻密化した合金組織を得ること
ができない。Ni and Fe generate a liquid phase in the liquid phase sintering process when producing tungsten sintered alloys to promote densification.
It is also added as a binder to increase the ductility of the alloy. The amount added is 2 to 7 wt% in the core and 8 to 20 wt% in the outer periphery, based on the total amount of the alloy. If it is less than 2 wt%, a sufficient liquid phase will not be generated and a completely densified alloy structure cannot be obtained.
心部で７ｔｍｔ％を越えるとＷ量が少なくなり過ぎて所
定の比重を得ることができない。外周部では８ｗｔ％未
満では所定の延性が得られず、２０ｗｔ％を越えると、
所定の比重が得られなくなる。又、ＮｉとＦｅの重量比
率は、液相生成温度を下げて効果的な液相焼結を実施す
るために、Ｎｉ：Ｆｅ＝０．５〜４の範囲内にすること
が好ましい。If it exceeds 7tmt% in the core, the amount of W becomes too small and a predetermined specific gravity cannot be obtained. At the outer periphery, if it is less than 8 wt%, the desired ductility cannot be obtained, and if it exceeds 20 wt%,
Predetermined specific gravity cannot be obtained. Further, the weight ratio of Ni and Fe is preferably within the range of Ni:Fe=0.5 to 4 in order to lower the liquid phase generation temperature and carry out effective liquid phase sintering.
本発明の複合焼結タングステン合金の製造は、原料粉末
の混合、成形、焼結、熱処理等の工程を経て行う。混合
工程で、Ｗ粉末８０〜９２ｗｔに。The composite sintered tungsten alloy of the present invention is manufactured through steps such as mixing raw material powder, molding, sintering, and heat treatment. In the mixing process, W powder becomes 80-92wt.
残部がＮｉとＦｅの各粉末（Ｎｉ；Ｆｅ＝０．５〜４重
量比）からなる心部配合原料と、Ｗ粉末９３〜９８−ｔ
％、残部がＮｉとＦｅの各粉末（同上重量比）からなる
外周部配合原料とを、それぞれ別にミキサーで均一に混
合する。A core compound raw material with the remainder consisting of Ni and Fe powders (Ni; Fe = 0.5 to 4 weight ratio) and W powder 93 to 98-t
%, the balance being Ni and Fe powders (same weight ratios as above) and the outer peripheral part compound raw materials are uniformly mixed separately using a mixer.
次に成形工程では、上記の混合した心部配合原料を所定
の成形型の心部に、外周部配合原料をその周囲に、両者
が混ざり合わないようにして二層に充填した後、静水圧
圧縮成形する。静水圧の大きさは１〜４ｔｏｎ／ｃｊと
する。１ｔｏｎ／ｃＩＩ未満の圧力では液相焼結を行っ
ても２〜３％の気孔が残留し、成形体の密度が小さすぎ
て完全には緻密化できずに延性が低下する。一方、４ｔ
ｏｎ／ｄ越える成形では、逆に密度あが高（なりすぎて
成形体中にクローズドボアが生じ、結局完全な緻密化が
できない。加圧に際して通常の一軸圧縮ではなく静水圧
を用いるのは、四方から万遍なく加圧することにより、
合金の均質性を高め、ひいては延性を高めるためである
。Next, in the molding process, the mixed core raw material is filled into the core of a predetermined mold, and the outer peripheral raw material is filled around it in two layers so that the two do not mix, and then hydrostatic pressure is applied. Compression mold. The magnitude of the hydrostatic pressure is 1 to 4 ton/cj. At a pressure of less than 1 ton/cII, 2 to 3% of pores remain even if liquid phase sintering is performed, and the density of the compact is too small to be completely densified, resulting in a decrease in ductility. On the other hand, 4t
On the contrary, when molding exceeds on/d, the density increases (so much so that closed bores occur in the molded product, and complete densification cannot be achieved.When pressurizing, hydrostatic pressure is used instead of normal uniaxial compression. By applying pressure evenly from all sides,
This is to improve the homogeneity of the alloy and thus its ductility.
上記の成形工程における心細配合原料と外周部配合原料
との比率で、本複合焼結タングステン合金の外周部と心
部との比率が定まる。この比率は、Ｗ含有量がより少な
い外周部が増えるにつれて延性が高くなり、反対にＷ含
有量のより多い心部が増えるにつれて比重が高くなるが
、粉末充填上の制約のため、例えば棒状成形体であれば
径に対して外周部二心部＝８：２〜２：８を限度とし、
好ましくは外周部二心部＝６：４〜４：６の範囲である
。The ratio between the outer periphery and the core of the present composite sintered tungsten alloy is determined by the ratio of the fine blended raw material and the outer periphery blended raw material in the above forming process. This ratio increases as the periphery with lower W content increases, while the specific gravity increases as the core with higher W content increases, but due to powder filling constraints, e.g. If it is a body, the limit is 8:2 to 2:8 for the diameter of the outer peripheral part,
Preferably, the ratio of the outer peripheral portion to the two core portions is in the range of 6:4 to 4:6.
焼結工程では、Ｈ２気流中でＮｉ、Ｆｅ成分が液相を生
成する１４３０°Ｃ以上の温度に加熱して液相焼結する
。液相焼結時間は、完全に緻密化が進行するに必要な２
０分間以上を要し、また焼結中に粗大ポロシティを生じ
させないためには６０分間以下が望ましい。液相焼結の
終了後の熱処理工程は、上記焼結体に望ましい延性を付
与するために行うもので、真空中で７００〜１４００°
Ｃの温度で２〜１０時間加熱保持し、その後急冷する。In the sintering process, liquid phase sintering is performed by heating the Ni and Fe components to a temperature of 1430° C. or higher to form a liquid phase in an H2 gas flow. The liquid phase sintering time is 2 times the time required for complete densification.
The sintering time is preferably 60 minutes or less in order to prevent coarse porosity from occurring during sintering. The heat treatment step after the completion of liquid phase sintering is carried out in order to impart desired ductility to the sintered body, and is performed at 700 to 1400° in vacuum.
The mixture is heated and maintained at a temperature of C for 2 to 10 hours, and then rapidly cooled.
これにより焼結工程で焼結体中に固溶した過剰の水素が
低減されると共に、Ｗ粒界への析出物の生成が防止され
て延性の向上が図れる。This reduces the excess hydrogen solidly dissolved in the sintered body during the sintering process, and prevents the formation of precipitates at W grain boundaries, thereby improving ductility.
複合焼結タングステン合金を例えば徹甲弾に使用する場
合などは、貫徹力を向上させるべく外周部の硬さを向上
させるのに、熱処理後にスェージング加工を施すと良い
。その場合、スェージング加工率は２５〜７０％とし、
これにより成形体の合金硬度をＨｖ５００以上にする。When a composite sintered tungsten alloy is used, for example, in an armor-piercing bullet, it is recommended to perform a swaging process after heat treatment to improve the hardness of the outer periphery in order to improve the penetration force. In that case, the swaging rate should be 25-70%,
As a result, the alloy hardness of the compact is set to Hv500 or higher.
加工率が２５％未満では外周部の硬度をＨｖ５００以上
にすることができず、貫徹力の向上が果たせない。一方
、７０％を越えると心部まで加工硬化して合金の延性が
低下する。If the processing rate is less than 25%, the hardness of the outer peripheral portion cannot be increased to Hv500 or more, and the penetration force cannot be improved. On the other hand, if it exceeds 70%, work hardening occurs to the core, reducing the ductility of the alloy.
以下、本発明の詳細な説明する。 The present invention will be explained in detail below.
Ｗ、Ｎｉ、Ｆｅの各原料粉末を心細配合原料と外周部配
合原料とそれぞれ別々に■型ミキサーで均一に混合して
、種々の配合の配合原料を調整した。次に冷間静水圧プ
レスを用い、２ｔｏｎ／ｃｆｆｌの圧力で外径１８ｍ、
長さ１５０閣の成形体を成形した。この成形に際して、
成形型の外周部には均一に混合した外周部配合原料を、
成形型の心部には均一に混合した心細配合原料を互いに
混ざり合うことなく二層に充填して加圧成形した。心部
と外周部とのＷ量の重量比率および直径の割合は表１に
示すように構成した。Raw material powders of W, Ni, and Fe were uniformly mixed separately with a core blend raw material and an outer peripheral blend raw material using a ■-type mixer to prepare blended raw materials with various blends. Next, using a cold isostatic press, the outer diameter was 18 m at a pressure of 2 tons/cffl.
A molded body with a length of 150 mm was molded. During this molding,
The outer periphery of the mold is filled with uniformly mixed raw materials.
The core of the mold was filled with two layers of uniformly mixed raw materials without mixing with each other, and pressure molded. The weight ratio of the W amount and the diameter ratio between the core and the outer periphery were configured as shown in Table 1.
こうして得た成形体を、ブツシャ一連続焼結炉を用いて
Ｈ２気流中で焼結温度１５００″Ｃ２焼結時間６０分間
で液相焼結し、冷却した。次いで、真空度１０−’Ｔｏ
ｒ ｒＯ下で１２００°Ｃ，２時間の真空熱処理を行
ない、その後Ａｒガスにより２０℃／ｍｊｎの冷却速度
で冷却し複数個の被試験体を得た。更に、スェージング
加工の効果を確認するため、複数の被試験体に異なる加
工率でスェージング加工を施した。The thus obtained compact was liquid-phase sintered in a H2 gas flow at a sintering temperature of 1500''C2 for 60 minutes using a continuous sintering furnace, and then cooled.
A vacuum heat treatment was performed at 1200°C for 2 hours under r rO, and then cooling was performed with Ar gas at a cooling rate of 20°C/mjn to obtain a plurality of specimens. Furthermore, in order to confirm the effect of swaging, multiple test specimens were subjected to swaging at different processing rates.
表１に被試験体の組成（心部と外周部とのＷ成分の重量
比率）とスェージング加工の加工率を示す。Ｎｏ、 １
〜１０は本発明の実施例であり、これに対してＮｏ、１
１〜１６は比較例である。Table 1 shows the composition of the test object (the weight ratio of the W component between the core and the outer periphery) and the processing rate of the swaging process. No. 1
-10 are examples of the present invention, whereas No. 1
1 to 16 are comparative examples.
このように形成した複数種の被試験体のそれぞれにつき
、加工後の状態、比重、抗折力、及び心部と外周部との
硬度（Ｈｖ３゜）を測定し、試験結果を表１に併記した
。なお、抗折力は被試験体を支点闇路Ｈ１００ＩＩＩ１
１１で水平に支持し、その中間に反対側からアムスラー
万能試験機を用いて荷重を負荷する３点曲げ試験を行っ
て求めた値である。For each of the multiple types of test specimens formed in this way, the state after processing, specific gravity, transverse rupture strength, and hardness (Hv3°) of the core and outer periphery were measured, and the test results are also listed in Table 1. did. In addition, the transverse rupture force is determined by using the test object as the fulcrum dark road H100III1.
This value was obtained by performing a three-point bending test in which the sample was supported horizontally at a point 11 and a load was applied from the opposite side in the middle using an Amsler universal testing machine.
表１より、本発明の実施例である階１〜１０の複合焼結
タングステン合金は、比較例のものに比べて抗折力が格
段に大きく衝撃的な荷重に対する優れた抵抗力を有して
いることが明らかである。From Table 1, the composite sintered tungsten alloys of grades 1 to 10, which are examples of the present invention, have significantly higher transverse rupture strengths and excellent resistance to impact loads than those of comparative examples. It is clear that there are
更に、高加工率のスェージング加工を施した場合は、顕
著な抗折力とＨｖ５００以上の硬度が得られ弾心材に好
適である。Furthermore, when swaging processing is performed at a high processing rate, remarkable transverse rupture strength and hardness of Hv500 or more are obtained, making it suitable for elastic core materials.
以上説明したように、本発明によれば、複合焼結タング
ステン合金の外周部のＷ含有量を心細のＷ含有量より高
めることにより、心細が外周部より高延性を有するもの
とし、また必要に応じて２５〜７０％のスェージング加
工を施し硬度をＨｖ５００以上にした。As explained above, according to the present invention, by increasing the W content in the outer peripheral part of the composite sintered tungsten alloy than the W content in the thin core, the fine core has higher ductility than the outer peripheral part. Accordingly, a swaging process of 25 to 70% was performed to increase the hardness to Hv500 or higher.
Claims (2)
タングステン合金であって、心部のＷ含有量を９３〜９
８ｗｔ％とし、外周部のＷ含有量を８０〜９２ｗｔ％と
した外周部が心部より高延性を有することを特徴とする
複合焼結タングステン合金。(1) A sintered tungsten alloy consisting of W as the main component and the balance being Ni and Fe, with a core W content of 93 to 9
A composite sintered tungsten alloy characterized in that the outer peripheral part has higher ductility than the core part, and the W content in the outer peripheral part is 80 to 92 wt%.
加工率２５〜７０％のスエージング加工を施してなるＨ
ｖ５００以上の硬度を有することを特徴とする複合焼結
タングステン合金。(2) H obtained by subjecting the composite sintered tungsten alloy according to claim (1) to swaging processing at a processing rate of 25 to 70%.
A composite sintered tungsten alloy characterized by having a hardness of v500 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14286690A JPH0436410A (en) | 1990-05-31 | 1990-05-31 | Complex sintered tungsten alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14286690A JPH0436410A (en) | 1990-05-31 | 1990-05-31 | Complex sintered tungsten alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0436410A true JPH0436410A (en) | 1992-02-06 |
Family
ID=15325427
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14286690A Pending JPH0436410A (en) | 1990-05-31 | 1990-05-31 | Complex sintered tungsten alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0436410A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04333534A (en) * | 1991-05-09 | 1992-11-20 | Japan Steel Works Ltd:The | Production of sintered w alloy |
| KR100375944B1 (en) * | 2000-07-08 | 2003-03-10 | 한국과학기술원 | Process for Making Oxide Dispersion Strengthened Tungsten Heavy Alloy by Mechanical Alloying |
| CN111394603A (en) * | 2020-04-14 | 2020-07-10 | 东莞市金材五金有限公司 | Production process method of powder metallurgy W-Ni-Fe tungsten-nickel-iron alloy |
-
1990
- 1990-05-31 JP JP14286690A patent/JPH0436410A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04333534A (en) * | 1991-05-09 | 1992-11-20 | Japan Steel Works Ltd:The | Production of sintered w alloy |
| KR100375944B1 (en) * | 2000-07-08 | 2003-03-10 | 한국과학기술원 | Process for Making Oxide Dispersion Strengthened Tungsten Heavy Alloy by Mechanical Alloying |
| CN111394603A (en) * | 2020-04-14 | 2020-07-10 | 东莞市金材五金有限公司 | Production process method of powder metallurgy W-Ni-Fe tungsten-nickel-iron alloy |
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