JPH0428840A - Nickel-molybdenum series double boride cermet sintered body and its manufacture - Google Patents
Nickel-molybdenum series double boride cermet sintered body and its manufactureInfo
- Publication number
- JPH0428840A JPH0428840A JP2132502A JP13250290A JPH0428840A JP H0428840 A JPH0428840 A JP H0428840A JP 2132502 A JP2132502 A JP 2132502A JP 13250290 A JP13250290 A JP 13250290A JP H0428840 A JPH0428840 A JP H0428840A
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- powder
- weight
- nickel
- complex boride
- 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
- 239000011195 cermet Substances 0.000 title claims abstract description 27
- DDTIGTPWGISMKL-UHFFFAOYSA-N molybdenum nickel Chemical class [Ni].[Mo] DDTIGTPWGISMKL-UHFFFAOYSA-N 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 7
- 239000000843 powder Substances 0.000 claims abstract description 65
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 32
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 26
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 18
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 14
- 239000002994 raw material Substances 0.000 claims abstract description 14
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 14
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 10
- 239000000956 alloy Substances 0.000 claims abstract description 10
- 229910000990 Ni alloy Inorganic materials 0.000 claims abstract description 8
- 229910000521 B alloy Inorganic materials 0.000 claims abstract 4
- 239000011230 binding agent Substances 0.000 claims description 28
- 238000000034 method Methods 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims 2
- 239000011148 porous material Substances 0.000 abstract description 8
- 239000007787 solid Substances 0.000 abstract 2
- 229910003296 Ni-Mo Inorganic materials 0.000 abstract 1
- 150000001875 compounds Chemical class 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 30
- 230000000052 comparative effect Effects 0.000 description 7
- 239000002245 particle Substances 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 238000005245 sintering Methods 0.000 description 5
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 4
- 230000035939 shock Effects 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910003294 NiMo Inorganic materials 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000007657 chevron notch test Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000003960 organic solvent Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 239000002002 slurry Substances 0.000 description 1
- 229910052723 transition metal Inorganic materials 0.000 description 1
- -1 transition metal nitrides Chemical class 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］
本発明はアルミニウムの押出型やアルミニウムのダイカ
スト型などの用途に適するＮｉ、 Ｍｏ系複硼化物焼結
体、さらに詳しくは強度、硬度および靭性に優れた緻密
なＮｉ、 Ｍｏ系複硼化物サーメット焼結体に関するも
のである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a Ni- and Mo-based complex boride sintered body suitable for use in aluminum extrusion molds, aluminum die-casting molds, etc. This invention relates to a dense Ni, Mo-based complex boride cermet sintered body with excellent properties.
［技術の背景］
先に本発明者らは、強度、硬度、靭性ならびに耐熱衝撃
性に優れたＮｉのＭＯとＷからなる複硼化物焼結体を特
開昭６３−１４３２３６に開示し、さらに６００℃〜１
００℃付近まで高温における強度向上に関して、複硼化
物の成分の一部を４ａ、 ５ａ及び６ａ族の遷移金属窒
化物で置き換える事が特性を改善するのに有効であるこ
とを見出し、特開平１−１３１０７１ （以後、先行発
明という）として開示している。その後の研究の結果、
焼結体の肉厚が３０ｍｍ程度より厚い場合、焼結体の内
部に気孔が残留する傾向を認め、その原因と改善対策を
検討し、複硼化物の一部を置換するために配合した窒化
物一部分が焼結中に分解する傾向があり、生成した窒素
ガスが気孔の残留の原因となっているものと考えた。[Technical background] Previously, the present inventors disclosed a complex boride sintered body made of Ni MO and W that had excellent strength, hardness, toughness, and thermal shock resistance in JP-A-63-143236, and further disclosed 600℃~1
Regarding the improvement of strength at high temperatures up to around 00°C, we discovered that replacing a part of the complex boride components with transition metal nitrides of groups 4a, 5a and 6a is effective in improving the properties, and published JP-A-1 -131071 (hereinafter referred to as prior invention). As a result of subsequent research,
When the wall thickness of the sintered body is thicker than about 30 mm, it is recognized that pores tend to remain inside the sintered body, and the cause and improvement measures were investigated. It was thought that some parts of the material tended to decompose during sintering, and the nitrogen gas produced was the cause of the remaining pores.
本発明は上記先行発明による焼結体の優れた強度、硬度
、靭性ならびに耐熱衝撃性を損う事な（、厚肉の焼結体
の焼成不良、特には肉厚３０ｍｍ以上を有する焼結体の
内部に残留する気孔を無くし、より緻密な焼結体を得よ
うとするものである。The present invention is intended to prevent the excellent strength, hardness, toughness, and thermal shock resistance of the sintered body according to the prior invention described above from being impaired (in particular, sintered bodies with a wall thickness of 30 mm or more). The aim is to eliminate the pores remaining inside the sintered body and obtain a denser sintered body.
［発明の構成］
本発明のニッケルモリブデン系複硼化物サーメット焼結
体はＮｉ、 Ｍｏ複硼化物またはＮｉ、Ｍｏ、Ｗ複硼化
物を硬質相とし、結合相が主としてＮｉ。[Structure of the Invention] The nickel-molybdenum complex boride cermet sintered body of the present invention has a hard phase of Ni, Mo complex boride or Ni, Mo, W complex boride, and a binder phase mainly of Ni.
ＭｏまたはＮｉ、Ｍｏ、Ｗからなる合金であり、硬質相
□
および結合相中にＴａおよび／またはＮｂを固溶してお
り、かつ緻密に焼結されていることを特徴とする。本発
明のニッケルモリブデン系複硼化物サーメット焼結体の
好ましい態様では、結合相中におけるＴａの含有率が１
〜２５重量％、Ｎｂの含有率１〜３５重量％であり、更
に好ましくはＴａの含有率が５〜２０重量％、Ｎｂの含
有率が３〜１０重量％である。−本発明のニッケルモリ
ブデン系複硼化物サーメット焼結体の他の好ましい態様
では、焼結体中の結合相が５〜７０重量％である。本発
明のニッケルモリブデン系複硼化物サーメット焼結体の
他の好ましい態様では、焼結体の肉厚が３０ｍｍ以上で
ある。It is an alloy consisting of Mo or Ni, Mo, and W, and is characterized by having Ta and/or Nb dissolved in the hard phase and the binder phase, and being densely sintered. In a preferred embodiment of the nickel-molybdenum complex boride cermet sintered body of the present invention, the Ta content in the binder phase is 1
-25% by weight, Nb content is 1-35% by weight, and more preferably Ta content is 5-20% by weight and Nb content is 3-10% by weight. - In another preferred embodiment of the nickel-molybdenum complex boride cermet sintered body of the present invention, the binder phase in the sintered body is 5 to 70% by weight. In another preferred embodiment of the nickel-molybdenum complex boride cermet sintered body of the present invention, the wall thickness of the sintered body is 30 mm or more.
本発明のＮｉ、Ｍｏ複硼化物またはＮｉ、Ｍｏ、Ｗ複硼
化物を硬質相とし、結合相が主としてＮｉ、Ｍｏまたは
Ｎｉ、Ｍｏ、Ｗからなる合金であるサーメットの焼結体
の製造方法は、硬質相および結合相中に固溶させるＴａ
および／またはＮｂの原料として、Ｔａ粉、Ｎｂ粉、Ｔ
ａ−８合金粉、Ｎｂ−８合金粉、Ｔａ−Ｎｉ合金粉およ
びＮｂ−Ｎｉ合金粉から選ばれる一種以上の粉末を用い
ることを特徴とする。本発明のニッケルモリブデン系複
硼化物サーメット焼結体の製造方法の好ましい態様では
、結合相中におけるＴａの含有率が１〜２５重量％、Ｎ
ｂの含有率が１〜３５重量％となるようにＴａおよび／
またはＮｂの原料を配合する。A method for producing a sintered cermet in which the hard phase is the Ni, Mo complex boride or the Ni, Mo, W complex boride of the present invention, and the binder phase is mainly Ni, Mo or an alloy consisting of Ni, Mo, and W. , Ta dissolved in the hard phase and the binder phase
And/or as a raw material for Nb, Ta powder, Nb powder, T
It is characterized by using one or more types of powder selected from a-8 alloy powder, Nb-8 alloy powder, Ta-Ni alloy powder, and Nb-Ni alloy powder. In a preferred embodiment of the method for producing a nickel-molybdenum-based complex boride cermet sintered body of the present invention, the content of Ta in the binder phase is 1 to 25% by weight, N
Ta and/or so that the content of b is 1 to 35% by weight.
Alternatively, a raw material for Nb is blended.
即ち本発明は、Ｎｉ、Ｍｏ複硼化物（ＭｏＪｉ Ｂ２）
またはＮｉ、Ｍｏ、Ｗ複硼化物 （（ＭＯ＋−Ｊｘ）Ｊ
ｉＢｚ）を硬質相とし、結合相が主としてＮｉ、Ｍｏあ
るいはＮｉ、Ｍｏ、Ｗからなるサーメット焼結体におい
て、硬質相及び結合相中にＴａ、Ｎｂの中から選ばれる
１種類以上の元素を固溶せしめることにより得られる高
強度、高硬度、高靭性で耐熱衝撃性にすぐれ、緻密かつ
焼結性の良好なサーメット焼結体を提供するものである
。That is, the present invention provides Ni, Mo complex boride (MoJi B2)
or Ni, Mo, W complex boride ((MO+-Jx)J
iBz) as a hard phase and a binder phase mainly composed of Ni, Mo or Ni, Mo, and W, in which one or more elements selected from Ta and Nb are solidified in the hard phase and binder phase. The object of the present invention is to provide a cermet sintered body which is obtained by melting and has high strength, high hardness, high toughness, excellent thermal shock resistance, and is dense and has good sinterability.
本発明のサーメット焼結体を得るには、例えばＭｏＢ、
ＷＢ、 Ｍｏ、 Ｎｉの各粉末及びＴａ粉、Ｎｂ粉、
ｌ’ａ−８合金粉、Ｎｂ−８合金粉、Ｔａ−Ｎｉ合金粉
、Ｎｂ−Ｎｉ合金粉の中から選ばれる１種類以上の粉末
を秤量し、回転ボールミルや振動ボールミル等を用いて
、エタノール等の有機溶媒中で混合粉砕し、乾燥後、金
型ブレスやラバープレス等を用いて加圧成形し、通常は
真空中等の減圧雰囲気中において、１１０（１℃〜１５
００℃程度の温度で焼結する。用いる原料粉末は必ずし
も上記のＭｏＢ粉、ＷＢ粉、ＭＯ粉、Ｎｉ粉の形である
必要はなく、例えばＮ１−８合金粉とＭＯ粉、Ｗ粉及び
Ｎｉ粉との組合せ、あるいは予めアトマイズ法やその他
の方法で合成したＭＯ２ＮＩＢ２粉末や （Ｍｏ＋−Ｊ
ｘ）ＪｉＢｚ粉末とＮｉ粉末、Ｍｏ粉末等との組合せ、
更にはＮｉＭｏ、 Ｗ等の単体の金属粉末とＢ粉末の組
合せ等でもよ（、これらの組合せの原料粉末にＴａ粉、
Ｎｂ粉、Ｔａ−Ｂ粉、Ｎｂ−Ｂ粉、Ｔａ−Ｎｉ粉、Ｎｂ
−Ｎｉ粉の中から選ばれる１種類以上の粉末を所定量配
合すればよい。−船釣にこれ等の原料粉末は出来る限り
純度が高く微細である方が優れた特性を有するサーメッ
ト焼結体を得る上で有利である事は言うまでもない。In order to obtain the cermet sintered body of the present invention, for example, MoB,
WB, Mo, Ni powder, Ta powder, Nb powder,
One or more types of powder selected from l'a-8 alloy powder, Nb-8 alloy powder, Ta-Ni alloy powder, and Nb-Ni alloy powder are weighed, and ethanol is added using a rotary ball mill, vibrating ball mill, etc. After drying, the powder is mixed and pulverized in an organic solvent such as the
It is sintered at a temperature of about 00°C. The raw material powder used does not necessarily have to be in the form of the above-mentioned MoB powder, WB powder, MO powder, or Ni powder. MO2NIB2 powder synthesized by other methods and (Mo+-J
x) Combination of JiBz powder, Ni powder, Mo powder, etc.
Furthermore, it is also possible to use a combination of single metal powder such as NiMo, W, etc. and B powder (Ta powder, Ta powder,
Nb powder, Ta-B powder, Nb-B powder, Ta-Ni powder, Nb
- A predetermined amount of one or more types of powder selected from Ni powder may be blended. - It goes without saying that it is advantageous for these raw material powders for boat fishing to be as pure and fine as possible in order to obtain a cermet sintered body with excellent properties.
これ等原料を用いた成形体を焼結する際、昇温過程で成
形体中の各成分が反応してＭ３Ｂ２（Ｍは主としてＭｏ
、ＮｉあるいはＭｏ、 Ｗ、 Ｎｉでありこれに固溶す
る副成分としてＴａおよび／またはＮｂを含む）タイプ
の複硼化物を形成し、次にこの複硼化物とＮｉ、Ｍｏあ
るいはＮｉ、Ｍｏ、Ｗを主成分とし副成分とし、Ｔａま
たは／およびＮｂを含有する残りの相が共晶反応を起し
液相を生ずる。成形体はこの液相焼結により相対密度が
ほぼ１００％の緻密な焼結体となる。本発明によるサー
メット焼結体では、先行発明によるサーメット焼結体の
ように、窒化物を添加していないので、先行発明による
サーメット焼結体にみられた、窒化物の一部分が分解し
て発生する窒素ガスを原因とする気孔の形成もなく、緻
密で特性の優れたサーメット焼結体となり、特に焼結体
の肉厚が３０ｍｍを超えても、内部まで緻密な焼結体と
なる。When sintering a molded body using these raw materials, each component in the molded body reacts during the temperature rising process, resulting in M3B2 (M is mainly Mo).
, Ni or Mo, W, Ni containing Ta and/or Nb as a solid solution subcomponent) type complex boride is formed, and then this complex boride and Ni, Mo or Ni, Mo, The remaining phase containing W as the main component and subcomponents and Ta and/or Nb undergoes a eutectic reaction to produce a liquid phase. Through this liquid phase sintering, the compact becomes a dense sintered body with a relative density of approximately 100%. In the cermet sintered body according to the present invention, unlike the cermet sintered body according to the prior invention, nitrides are not added. There is no formation of pores caused by nitrogen gas, resulting in a cermet sintered body that is dense and has excellent properties.In particular, even if the thickness of the sintered body exceeds 30 mm, the sintered body is dense to the inside.
本発明において、結合相及び硬質相中に固溶させる金属
元素としてＴａおよび／またはＮｂを選ぶのは、Ｔａや
Ｎｂが結合相中に固溶するときの固溶強化能が大きく、
焼結体の強度向上に寄与する効果が大きいためである。In the present invention, Ta and/or Nb are selected as the metal elements to be dissolved in the binder phase and the hard phase because they have a large solid solution strengthening ability when Ta and Nb are dissolved in the binder phase.
This is because it has a large effect of contributing to improving the strength of the sintered body.
次に固溶させるＴａやＮｂの供給原料としてＴａ粉、Ｎ
ｂ粉、Ｔａ−Ｂ粉、Ｎｂ−Ｂ粉、Ｔａ−Ｎｉ粉、Ｎｂ−
Ｎｉ粉の中から選ばれる１種類以上の粉末を選ぶ理由Ｌ
′ｉ、これらの原料がＭｏＢ、 ＷＢ、 Ｎｉ、 Ｍｏ
等の他の原料粉末と比較的反応しやすく、結合相や硬質
相中に溶は込みやすいこと、および先行発明で用いられ
た窒化物と異なり焼結時に気孔の原因となるようなガス
の放出が少ないことなどが挙げられる。Next, Ta powder and Nb are used as raw materials for solid solution of Ta and Nb.
b powder, Ta-B powder, Nb-B powder, Ta-Ni powder, Nb-
Reasons for choosing one or more types of Ni powder
'i, these raw materials are MoB, WB, Ni, Mo
It is relatively easy to react with other raw material powders such as, and easily penetrates into the binder phase and hard phase, and unlike the nitride used in the prior invention, it releases gas that causes pores during sintering. For example, there are few
結合相中でのＴａおよび／またはＮｂの含有量を各々１
〜２５重量％、１〜３５重量％とするのは、これらの量
より含有量が少ないと強度向上効果が充分得られず、ま
たこれらの量より含有量が多いと逆に強度の低下が認め
られるためである。The content of Ta and/or Nb in the bonded phase is 1
~25% by weight and 1 to 35% by weight because if the content is less than these amounts, the strength improvement effect will not be obtained sufficiently, and if the content is more than these amounts, a decrease in strength will be observed. This is so that you can be saved.
得られる焼結体の物性から見て、結合相中でのＴａおよ
び／またはＮｂの含有率は各々５〜２０重量％、３〜１
０重量％とするのがより好ましい。In view of the physical properties of the obtained sintered body, the content of Ta and/or Nb in the binder phase is 5 to 20% by weight and 3 to 1% by weight, respectively.
More preferably, it is 0% by weight.
更に好ましくは、ＴａやＮｂと同時に結合相中に含有さ
れるＭｏあるいはＭＯとＷの合計量を１０〜３５重量％
とすると、Ｔａおよび／またはＮｂによる固溶強化の効
果がより高まり、強度や靭性が更に向上する。More preferably, the total amount of Mo or MO and W contained in the binder phase at the same time as Ta and Nb is 10 to 35% by weight.
In this case, the effect of solid solution strengthening by Ta and/or Nb is further enhanced, and the strength and toughness are further improved.
原料中に配合されたＭｏとＷは、本発明の複硼化物サー
メット焼結体では、先ず優先的に複硼化物の生成に利用
され、余剰のＭＯとＷが結合相中に固溶するという傾向
を有している。結合相中にＭｏとＷが１０〜３５重量％
固溶されている場合、ＭｏとＷの好ましい固溶割合はＭ
ｏが７０〜９５重量％、Ｗが５〜３０重量％である。複
硼化物サーメット焼結体中のＷの含有量を余りに増すこ
とは、焼結体の比重を大きくすることになり、この点か
らはＷの含有量は余り多くないほうが良い。In the complex boride cermet sintered body of the present invention, Mo and W blended in the raw materials are first used preferentially for the production of complex boride, and excess MO and W are solid-solved in the binder phase. It has a tendency. 10-35% by weight of Mo and W in the binder phase
In the case of solid solution, the preferable solid solution ratio of Mo and W is M
O is 70 to 95% by weight, and W is 5 to 30% by weight. Excessively increasing the W content in the complex boride cermet sintered body increases the specific gravity of the sintered body, and from this point of view, it is better that the W content is not too large.
焼結体中に占める結合相の割合を５〜７０重量％とする
のは、結合相の量が５重量％より少ないと強度や靭性、
特に靭性の低下が著しくなるためであり、また結合相の
割合が７０重量％を越えると硬度の低下が大きくなるた
めである。The reason why the proportion of the binder phase in the sintered body is set to 5 to 70% by weight is that if the amount of the binder phase is less than 5% by weight, the strength and toughness will deteriorate.
This is because the decrease in toughness becomes particularly significant, and when the proportion of the binder phase exceeds 70% by weight, the decrease in hardness becomes large.
本発明による複硼化物ザーメットの焼成は、好ましくは
１０−”ｔｏｒｒ以下の真空中で行う。このことは焼結
の初期において粉末に吸着されてぃるガス成分等の放出
に都合が良（、緻密な焼結体で得易い他、アルゴンなど
のガスを消費しない点でも好ましいためである。The sintering of the complex boride cermet according to the present invention is preferably carried out in a vacuum of 10-'' torr or less. This is because it is easy to obtain a dense sintered body and is also preferable because it does not consume gas such as argon.
［実施例］ 以下、実施例により本発明を更に詳細に説明する。[Example] Hereinafter, the present invention will be explained in more detail with reference to Examples.
実施例Ｉ
ＭｏＢ粉末（Ｂ含有量１Ｏ１３％、平均粒径４．５μｍ
）４７重量％、ＷＢ粉末（Ｂ含有量５．５％、平均粒径
３．５μｍ）８重量％、ＭＯ粉末（純度９９．９％、平
均粒径０．８μｒｒｌ）７重量％、Ｎｉ粉末（純度９９
．６％、平均粒径２．８μｍ）３３重量％、Ｔａ粉末（
純度９９．７％、平均粒径１５μｍ）５重量％を秤量し
て合わせ、振動ミルを用いてエタノール媒体中で２４時
間混合粉砕した。スラリーを取り出して減圧下で乾燥後
２ ｔｏｎ／ｃｍ２の圧力で静水圧プレス成形を行い、
これを約１０−”ｔｏｒｒの真空中に於いて１２７５℃
の温度で１時間焼成し５０ｍｍＸ５０ｍｍＸ ５０ｎｏ
ｎの立方体形状の焼結体を得た。得られた焼結体の相対
密度は９９．９％であった。この焼結体の中央部から３
ｍｍＸ ３ ｍｍＸ ３０ｍｍの曲げ試験片を切出し
、室温における３点曲げ強度を測定したところ１９５ｋ
ｇ／ｍｍ”であった。また、焼結体の中央部から切り出
した３ Ｘ ３ Ｘ ３０ｍｍの試験片でシェブロンノ
ツチ法により破壊靭性値を測定したところ、１８ＭＮ／
ｍ””であり、ビッカース硬さは１０００ｋｇ／ｍｍ”
であった。Example I MoB powder (B content 1O13%, average particle size 4.5 μm
) 47% by weight, WB powder (B content 5.5%, average particle size 3.5μm) 8% by weight, MO powder (purity 99.9%, average particle size 0.8μrrl) 7% by weight, Ni powder ( Purity 99
．． 6%, average particle size 2.8 μm) 33% by weight, Ta powder (
5% by weight (purity 99.7%, average particle size 15 μm) were weighed and combined, and mixed and ground for 24 hours in an ethanol medium using a vibration mill. The slurry was taken out, dried under reduced pressure, and then subjected to isostatic press molding at a pressure of 2 ton/cm2.
This was heated to 1275°C in a vacuum of about 10-”torr.
Bake for 1 hour at a temperature of 50 mm x 50 mm x 50 no.
A cubic-shaped sintered body of n was obtained. The relative density of the obtained sintered body was 99.9%. 3 from the center of this sintered body
A bending test piece measuring 3 mm x 3 mm x 30 mm was cut out and its 3-point bending strength at room temperature was measured to be 195k.
When the fracture toughness value was measured using the chevron notch method using a 3 x 3 x 30 mm test piece cut out from the center of the sintered body, it was found to be 18 MN/mm.
m"" and Vickers hardness is 1000 kg/mm"
Met.
実施例２〜１６、比較例１〜５
ＴａやＮｂの供給原料の種類及び配合量を変え、焼結体
の寸法以外の処方については実施例１と同様の条件で焼
結体を作製して特性を調べたところ、第２表に示す結果
を得た。また、用いた原料粉末の組成と平均粒径を第１
表にまとめて示した。Examples 2 to 16, Comparative Examples 1 to 5 Sintered bodies were produced under the same conditions as Example 1, except for the dimensions of the sintered body, with the types and blending amounts of Ta and Nb feedstocks changed. When the properties were investigated, the results shown in Table 2 were obtained. In addition, the composition and average particle size of the raw material powder used were
They are summarized in the table.
実施例１〜１６はＴａやＮｂの供給原料としてＴａやＮ
ｂの窒化物を使用していないことにより、５０ｍｍＸ
５０ｍｍＸ ５０ｍｍの厚肉ブロックを焼結しても内部
に気孔が残留せず、相対密度はいずれの焼結体も９９．
９％以上となり、これら焼結体の中央部から切り出した
試験片について強度、硬度および靭性を測定した所いず
れも高い値が得られた。In Examples 1 to 16, Ta and Nb were used as feed materials for Ta and Nb.
By not using nitride of b, 50mmX
Even when a thick block of 50 mm x 50 mm is sintered, no pores remain inside, and the relative density of each sintered body is 99.
The strength, hardness, and toughness of test pieces cut out from the center of these sintered bodies were measured and high values were obtained.
比較例１はＴａやＮｂを結合相中に含有しない試料であ
る。この場合の相対密度は９９９％以上であり、中央部
まで緻密に焼結されているが、強度、硬度、靭性の測定
値はいずれも低い値を示した。Comparative Example 1 is a sample that does not contain Ta or Nb in the binder phase. In this case, the relative density was 999% or more, and the material was densely sintered to the center, but the measured values of strength, hardness, and toughness all showed low values.
比較例２及び３はＴａＮの形でＴａを添加した試料の薄
肉品と厚肉品の特性を示しているが、比較例２の薄肉品
の場合と比べると比較例３の厚肉品の強度、硬度、靭性
の差が著しいことがわかる。比較例４はＮｂＮ０形でＮ
ｂを添加した試料であるが、相対密度が低（十分な強度
、硬度、靭性が得られていない。Comparative Examples 2 and 3 show the characteristics of thin-walled products and thick-walled products of samples with Ta added in the form of TaN, but the strength of the thick-walled product of Comparative Example 3 is lower than that of the thin-walled product of Comparative Example 2. It can be seen that there are significant differences in hardness and toughness. Comparative example 4 is NbN0 type
Although this is a sample to which b is added, the relative density is low (sufficient strength, hardness, and toughness are not obtained).
比較例５は、結合層中のＮｂの重量％を多（した場合で
あるが曲げ強度と靭性が相対的に小さくなっている。In Comparative Example 5, although the weight percentage of Nb in the bonding layer was increased, the bending strength and toughness were relatively low.
以上の様に本発明のニッケルモリブデン系複硼化物サー
メット焼結体では、肉厚が３０ｍｍ以上ある焼結体の場
合にも、窒化物の形でＴａやＮｂを添加した焼結体（先
行発明による焼結体）と比較して焼結体中央部での気孔
の残留がなく均質であり、高い強度と硬度及び靭性を保
有している。したがってアルミニウムの押出し成形用ダ
イスやアルミニウムのダイカスト成形用金型等の金型類
など、大型で厚肉の素材を必要としさらに高強度、高硬
度、高靭性が要求される用途に於いて優れた性能と耐久
性のある材料を提供するものであり、その産業上の利用
効果は多大である。As described above, in the nickel-molybdenum complex boride cermet sintered body of the present invention, even in the case of a sintered body with a wall thickness of 30 mm or more, a sintered body to which Ta or Nb is added in the form of nitride (prior invention The sintered body is homogeneous with no residual pores in the center, and has high strength, hardness, and toughness. Therefore, it is excellent in applications that require large, thick-walled materials and require high strength, hardness, and toughness, such as aluminum extrusion molding dies and aluminum die-casting molds. It provides a material with high performance and durability, and its industrial application effects are significant.
Claims (7)
物を硬質相とし、結合相が主としてＮｉ、ＭｏまたはＮ
ｉ、Ｍｏ、Ｗからなる合金であり、硬質相および結合相
中にＴａおよび／またはＮｂを固溶しており、かつ緻密
に焼結されていることを特徴とするニッケルモリブデン
系複硼化物サー メット焼結体。(1) The hard phase is Ni, Mo complex boride or Ni, Mo, W complex boride, and the binder phase is mainly Ni, Mo or N.
A nickel-molybdenum complex boride cermet, which is an alloy consisting of i, Mo, and W, has Ta and/or Nb dissolved in the hard phase and binder phase, and is densely sintered. Sintered body.
率が１〜２５重量％、Ｎｂの含有率が１〜３５重量％で
あるニッケルモリブデン系複硼化物サーメット焼結体。(2) The nickel-molybdenum complex boride cermet sintered body according to claim 1, wherein the content of Ta in the binder phase is 1 to 25% by weight and the content of Nb is 1 to 35% by weight.
率が５〜２０重量％、Ｎｂの含有率が３〜１０重量％で
あるニッケルモリブデン系複硼化物サーメット焼結体。(3) The nickel-molybdenum complex boride cermet sintered body according to claim 2, wherein the content of Ta in the binder phase is 5 to 20% by weight and the content of Nb is 3 to 10% by weight.
の結合相が５〜７０重量％であるニッケルモリブデン系
複硼化物サーメット焼結 体。(4) The nickel-molybdenum complex boride cermet sintered body according to any one of claims 1 to 3, wherein the binder phase in the sintered body is 5 to 70% by weight.
肉厚が３０ｍｍ以上であるニッケルモリブデン系複硼化
物サーメット焼結体。(5) The nickel-molybdenum complex boride cermet sintered body according to any one of claims 1 to 4, wherein the sintered body has a wall thickness of 30 mm or more.
物を硬質相とし、結合相が主としてＮｉ、ＭｏまたはＮ
ｉ、Ｍｏ、Ｗからなる合金であるサーメットの焼結体を
製造するに際し、硬質相および結合相中に固溶させるＴ
ａおよび／またはＮｂの原料として、Ｔａ粉、Ｎｂ粉、
Ｔａ−Ｂ合金粉、Ｎｂ−Ｂ合金粉、Ｔａ−Ｎｉ合金粉お
よびＮｂ−Ｎｉ合金粉から選ばれる一種以上の粉末を用
いることを特徴とするニッケルモリブデン系複硼化物サ
ーメット焼結体の製造方法。(6) Ni, Mo complex boride or Ni, Mo, W complex boride is used as a hard phase, and the binder phase is mainly Ni, Mo or N.
When producing a sintered body of cermet, which is an alloy consisting of i, Mo, and W, T is dissolved in the hard phase and the binder phase.
As raw materials for a and/or Nb, Ta powder, Nb powder,
A method for producing a nickel-molybdenum complex boride cermet sintered body, characterized by using one or more powders selected from Ta-B alloy powder, Nb-B alloy powder, Ta-Ni alloy powder, and Nb-Ni alloy powder. .
率が１〜２５重量％、Ｎｂの含有率が１〜３５重量％と
なるようにＴａおよび／またはＮｂの原料を配合するニ
ッケルモリブデン系複硼化物サーメット焼結体の製造方
法。(7) In claim 6, a nickel-molybdenum system in which Ta and/or Nb raw materials are blended so that the Ta content in the binder phase is 1 to 25% by weight and the Nb content is 1 to 35% by weight. A method for manufacturing a complex boride cermet sintered body.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2132502A JP2534159B2 (en) | 1990-05-24 | 1990-05-24 | Ni-Mo-W system double boride cermet sintered body and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2132502A JP2534159B2 (en) | 1990-05-24 | 1990-05-24 | Ni-Mo-W system double boride cermet sintered body and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0428840A true JPH0428840A (en) | 1992-01-31 |
| JP2534159B2 JP2534159B2 (en) | 1996-09-11 |
Family
ID=15082866
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2132502A Expired - Fee Related JP2534159B2 (en) | 1990-05-24 | 1990-05-24 | Ni-Mo-W system double boride cermet sintered body and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2534159B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5406825A (en) * | 1993-04-28 | 1995-04-18 | Asahi Glass Company Ltd. | Forging die |
-
1990
- 1990-05-24 JP JP2132502A patent/JP2534159B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5406825A (en) * | 1993-04-28 | 1995-04-18 | Asahi Glass Company Ltd. | Forging die |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2534159B2 (en) | 1996-09-11 |
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