JPH0344450A - Sintered compact of cubic boron nitride reinforced high speed tool steel composite and its production - Google Patents
Sintered compact of cubic boron nitride reinforced high speed tool steel composite and its productionInfo
- Publication number
- JPH0344450A JPH0344450A JP1158179A JP15817989A JPH0344450A JP H0344450 A JPH0344450 A JP H0344450A JP 1158179 A JP1158179 A JP 1158179A JP 15817989 A JP15817989 A JP 15817989A JP H0344450 A JPH0344450 A JP H0344450A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- weight
- boron nitride
- tool steel
- cubic boron
- 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
- 229910001315 Tool steel Inorganic materials 0.000 title claims abstract description 54
- 239000002131 composite material Substances 0.000 title claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 229910052582 BN Inorganic materials 0.000 title claims description 57
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 title claims description 57
- 239000000843 powder Substances 0.000 claims abstract description 56
- 238000005245 sintering Methods 0.000 claims abstract description 30
- 239000002245 particle Substances 0.000 claims abstract description 29
- 238000010438 heat treatment Methods 0.000 claims abstract description 20
- 239000000463 material Substances 0.000 claims abstract description 20
- 229910000531 Co alloy Inorganic materials 0.000 claims abstract description 16
- 239000007791 liquid phase Substances 0.000 claims abstract description 15
- 238000002844 melting Methods 0.000 claims abstract description 13
- 230000008018 melting Effects 0.000 claims abstract description 13
- 239000000203 mixture Substances 0.000 claims abstract description 13
- 238000002156 mixing Methods 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 6
- 229910000990 Ni alloy Inorganic materials 0.000 claims abstract 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 31
- 229910045601 alloy Inorganic materials 0.000 claims description 16
- 239000000956 alloy Substances 0.000 claims description 16
- 229910052759 nickel Inorganic materials 0.000 claims description 15
- 239000011812 mixed powder Substances 0.000 claims description 10
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 6
- 239000010941 cobalt Substances 0.000 claims description 5
- 229910017052 cobalt Inorganic materials 0.000 claims description 5
- 238000010304 firing Methods 0.000 claims description 4
- 150000004767 nitrides Chemical class 0.000 claims description 3
- 229910021332 silicide Inorganic materials 0.000 claims description 3
- FVBUAEGBCNSCDD-UHFFFAOYSA-N silicide(4-) Chemical compound [Si-4] FVBUAEGBCNSCDD-UHFFFAOYSA-N 0.000 claims description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims 1
- 229910052796 boron Inorganic materials 0.000 claims 1
- -1 cubic BN Inorganic materials 0.000 abstract description 3
- 239000002994 raw material Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 5
- 238000000465 moulding Methods 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- MENXHHBNZPFGKB-UHFFFAOYSA-N [Fe].[Si].[B].[C] Chemical compound [Fe].[Si].[B].[C] MENXHHBNZPFGKB-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000007790 solid phase Substances 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000011888 foil Substances 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- 229910052721 tungsten Inorganic materials 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〕
本発明の製造法によって製造した立方晶窒化硼素複合高
速度工具鋼焼結体は工具用材料として・利用される材料
である。[Detailed Description of the Invention] [Industrial Application Field] The cubic boron nitride composite high-speed tool steel sintered body produced by the production method of the present invention is a material used as a tool material.
在来の立方晶窒化硼素工具材は高い硬度を備えているが
其の製造原価が高いために利用範囲が制限されており、
高速度工具鋼工具材は製造原価は安いが硬度が低いため
に利用範囲が制限されている。Conventional cubic boron nitride tool materials have high hardness, but their use is limited due to their high manufacturing costs.
High-speed tool steel has low manufacturing costs, but its low hardness limits its range of use.
従来の立方晶窒化硼素焼結体は立方晶窒化硼素粉末を焼
結する結合材としてニッケル粉末またはコバルト粉末を
使用しているが、ニッケルは其の融点が１，４５５℃で
あ？て、この温度に対する立方晶窒化硼素の安定領域に
おける圧力は４５，２６０Ｋｆ／ｃｔｌとなり、コバル
トは其の融点が１，４９０℃であって、゛この温度に対
する立方晶窒化硼素の安定領域における圧力は４６，３
６０Ｋｇ／ｃｍ２であって、斯る高圧力を発生し得るプ
レス装置は特殊構造の装置となり、其の装置の償却費と
共に其の運転費も高くなるので、立方晶窒化硼素焼結体
の製造原価は高いものとなっている。Conventional cubic boron nitride sintered bodies use nickel powder or cobalt powder as a binder for sintering cubic boron nitride powder, but nickel has a melting point of 1,455°C. Therefore, the pressure in the stable region of cubic boron nitride at this temperature is 45,260 Kf/ctl, and the melting point of cobalt is 1,490°C, so the pressure in the stable region of cubic boron nitride at this temperature is 46,3
The press equipment that can generate such a high pressure of 60 kg/cm2 has a special structure, and the depreciation cost and operating cost of the equipment are high, so the manufacturing cost of the cubic boron nitride sintered body is low. is expensive.
前項にて説明したように、従来製造されている立方晶窒
化硼素工具材および高速度工具鋼工具材において、立方
晶窒化硼素工具材は高い硬度を備えていて工具材として
は優れているが其の製造原価が著しく高いために利用範
囲が制約されている。また、高速度工具鋼工具材は其の
製造原価は高くないが硬度が低いために其の利用範囲が
制約されている。従って硬度が高速度工具鋼工具材より
も高く、立方晶窒化硼素工具材に近く、更に其の製造原
価が立方晶窒化硼素工具材より著しく安い工具材が開発
されていないことが問題点である。As explained in the previous section, among conventionally manufactured cubic boron nitride tool materials and high-speed tool steel tool materials, cubic boron nitride tool materials have high hardness and are excellent as tool materials. Its range of use is limited due to its extremely high manufacturing cost. Furthermore, although the production cost of high-speed tool steel is not high, its range of use is restricted due to its low hardness. Therefore, the problem is that no tool material has been developed whose hardness is higher than that of high-speed tool steel, close to cubic boron nitride tool material, and whose manufacturing cost is significantly lower than cubic boron nitride tool material. .
前項に説明した問題点を解決するための手段として、立
方晶窒化硼素粒子における立方晶結晶が焼結作業の時間
内では、六方晶結晶へ転移することのない１，３５０℃
以下の温度であって、且つ、高速度工具鋼粉末が焼結す
るに適した温度である１、２００℃乃至１，２５０℃を
含めた１、３５０℃以下の温度で立方晶窒化硼素粉末と
高速度工具鋼粉末との複合焼結作業を行うことを問題解
決の手段とするものである。複合焼結作業を１，３５０
℃以下の温度で行うときに使用する焼結作業用装置とし
ては、ピストンシリンダ型のホットプレス装置を使用す
ることができる。ピストンシリンダ型のホットプレス装
置は設備が安く、且つ関連装置の設備費も安くつき、更
に其の運転費も安くできるので其の製造原価を安くする
ことができる。また焼結作業用装置に冷間静水圧プレス
装置と熱間静水圧プレス装置を使用することもできるが
、其の静水圧プレス装置は一般作業の静水圧プレス装置
を使用することができるから其の静水圧プレス装置を使
用する場合も製造原価を安くすることができる。As a means to solve the problems explained in the previous section, we have developed a method of heating the cubic boron nitride particles at a temperature of 1,350°C, at which the cubic crystals in the cubic boron nitride particles do not transform into hexagonal crystals during the sintering process.
Cubic boron nitride powder at a temperature of 1,350°C or less, including 1,200°C to 1,250°C, which is a temperature suitable for sintering high-speed tool steel powder. The solution is to perform a composite sintering operation with high-speed tool steel powder. 1,350 yen for composite sintering work
A piston cylinder type hot press device can be used as the sintering device used when performing the sintering operation at a temperature of 0.degree. C. or lower. The piston-cylinder type hot press equipment is inexpensive, and the equipment cost of related equipment is also low, and its operating cost is also low, so that its manufacturing cost can be reduced. In addition, a cold isostatic press device and a hot isostatic press device can be used as the sintering device, but since the isostatic press device can be used for general work, Manufacturing costs can also be reduced when using a hydrostatic press device.
斯様に製造原価を安くすることができる焼結作業用プレ
ス装置を使用することによって、製造原価の安い立方晶
窒化硼素複合高速度工具鋼焼結体を製造するので、問題
点を解決することができる。By using a press device for sintering work that can reduce manufacturing costs in this way, a cubic boron nitride composite high-speed tool steel sintered body with low manufacturing costs is manufactured, thereby solving the problem. I can do it.
以上に説明したように、本発明の製造法によって製造す
る立方晶窒化硼素複合高速度工具鋼焼結体に関する作用
については、始めに特許請求範囲（１）、（３）に関す
る作用について説明する。As explained above, regarding the effects related to the cubic boron nitride composite high-speed tool steel sintered body produced by the production method of the present invention, the effects related to claims (1) and (3) will first be explained.
高速度工具鋼粉末を５０重量多乃至９０重重量％と、立
方晶窒化硼素粉末を３０Ｍ量伜乃至５重量多と、立方晶
窒化硼素の安定温度領域における温度である１、３５０
℃以下の低い溶融温度を有しているニッケル系合金粉末
またはコバルト系合金粉末を２０重量多乃至５重量肇と
、の割合範囲内より選定した割合にて混合した混合粉末
を焼結用原料とし、其の焼結用原料をピストンシリンダ
型のホットプレス装置にて５００Ｋｙ／ｌ＃ｉ乃至１０
，０００Ｋｐ／ｃｍ２の範囲内より選定した圧力にて加
圧成形すると同時に９００℃乃至１，３５０℃の範囲内
より選定した温度にて加熱焼成して焼結体を生成するか
、または、焼結用原料を通常のプレス装置にて５００Ｋ
ｇ／ｃｍ２乃至１０，０ＯＯＫｖ／ｄの範囲内より選定
した圧力にて加圧成形し、其の成形体を真空炉にて８０
０℃乃至１，０００℃の範囲内の温度にて真空焼結して
其の真空焼結体を熱間静水圧プレス装置にて５００ Ｋ
９／ｃｍ２乃至２，０００助／ｃｆｌの範囲内の、圧力
にて加圧成形すると同時に９００℃乃至１，３５０℃の
範囲内より選定した温度にて加熱焼成して焼結体を生成
する。この加圧加熱作業において、高速度工具鋼粒子の
多数個と立方晶窒化硼素粒子の多数個との混合物と溶融
ニッケル系合金または溶融コバルト系合金が液相焼結し
て液相焼結体を生威し、次いで、生成した液相焼結体□
加えていた圧力は保持したままで加熱のみを停止し、更
に外部より冷却して固相焼結体を生威し、次いで、保持
していた圧力を常圧にもどして安定した複合焼結組織体
を構成している立方晶窒化硼素複合高速度工具鋼焼結体
を生成する。The temperature in the stable temperature range of cubic boron nitride is 1,350 when the high-speed tool steel powder is added in an amount of 50% to 90% by weight and the cubic boron nitride powder is added in an amount of 30M to 5% by weight.
A mixed powder obtained by mixing nickel-based alloy powder or cobalt-based alloy powder having a low melting temperature of ℃ or less in a proportion selected from a proportion range of 20 to 5 weight is used as a raw material for sintering. , the raw material for sintering is heated to 500 Ky/l #i to 10 using a piston-cylinder type hot press device.
,000 Kp/cm2, and simultaneously heat and sinter at a temperature selected from 900°C to 1,350°C to produce a sintered body, or sintering. 500K using normal press equipment.
Pressure molding is performed at a pressure selected from the range of g/cm2 to 10,0 OOKv/d, and the molded product is heated to 80°C in a vacuum furnace.
Vacuum sintering is performed at a temperature within the range of 0°C to 1,000°C, and the vacuum sintered body is heated at 500 K using a hot isostatic press machine.
The sintered body is formed by pressure molding at a pressure in the range of 9/cm2 to 2,000 cm/cfl and simultaneously heated and fired at a temperature selected from the range of 900° C. to 1,350° C. to produce a sintered body. In this pressurizing and heating operation, a mixture of a large number of high-speed tool steel particles and a large number of cubic boron nitride particles and a molten nickel-based alloy or a molten cobalt-based alloy undergo liquid phase sintering to form a liquid phase sintered body. The liquid phase sintered body produced
Only the heating is stopped while the applied pressure is maintained, and the solid-phase sintered body is formed by cooling from the outside.Then, the maintained pressure is returned to normal pressure to create a stable composite sintered structure. A cubic boron nitride composite high-speed tool steel sintered body is produced.
次いで、特許請求範囲（２）、（４）に関する作用につ
いて説明する。高速度工具鋼粉末を５０重量多乃至９０
重量多と、。立方晶窒化硼素粉末を２０重量多乃至５重
量多と、硬質炭化物・硬質理化物・硬質窒化物・硬質珪
化物・硬質酸化物のうちより選択した硬質物の粉末を１
０重量多乃至２重量多と、立方晶窒化硼素の安定温度領
域における温度である１、３５０℃以下の低い溶融温度
を有しているニッケル系合金粉末またはコバルト系合金
粉末を２０重量嘩乃至３重量多と、の割合範囲内より選
定した割合にて混合した混合粉末を焼結用原料とし、斯
様に配合した焼結用原料を５００Ｋｙ ／ｃｍ２以上の
圧力にて加圧成形すると共に、９００℃乃至１，３５０
℃の範囲内より選定した温度にて加熱焼成して焼結体を
生成する。Next, effects related to claims (2) and (4) will be explained. High speed tool steel powder from 50% to 90% by weight
With a lot of weight. 20 to 5 weight cubic boron nitride powder and 1 hard powder selected from hard carbide, hard physic, hard nitride, hard silicide, and hard oxide.
0 to 2 parts by weight, and 20 to 3 parts by weight of nickel-based alloy powder or cobalt-based alloy powder having a low melting temperature of 1,350°C or less, which is the temperature in the stable temperature range of cubic boron nitride. The raw material for sintering is a mixed powder mixed in a ratio selected from within the range of weight and weight. °C to 1,350
A sintered body is produced by heating and firing at a temperature selected within the range of °C.
焼結作業は、特許請求範囲（１）、（３）の場合の説明
と同様な焼結作業を行って成る焼結体において、高速度
工具鋼粒子の多数個と立方晶窒化硼素粒子の多数個なら
び□硬質物粒子の多数個との混合物と溶融ニッケル系合
金または溶融コバルト系合金とが液相焼結して液相焼結
体を生威し、次いで、生成した液相焼結体に加えていた
圧力を保持したままで加熱のみを停止し、更に外部より
冷却して固相焼結体を生威し、次いで、保持していた圧
力を常圧にもどして安定した複合焼結組織体を構成して
いる立方晶窒化硼素複合高速度工具鋼焼結体を生成する
。In the sintering process, a large number of high-speed tool steel particles and a large number of cubic boron nitride particles are formed in a sintered body obtained by performing the same sintering process as described in claims (1) and (3). A mixture of a large number of hard material particles and a molten nickel-based alloy or a molten cobalt-based alloy is liquid-phase sintered to produce a liquid-phase sintered body, and then the resulting liquid-phase sintered body is Only the heating is stopped while the applied pressure is maintained, and the solid phase sintered body is formed by cooling from the outside.Then, the maintained pressure is returned to normal pressure to create a stable composite sintered structure. A cubic boron nitride composite high-speed tool steel sintered body is produced.
以上に説明した作業において立方晶窒化硼素粉末に加え
る温度を１，３５０℃以下としたことは、プレス装置の
中に装填されている立方晶窒化硼素結晶の安定温度領域
が１，３５０℃以下であると一般的に認められているこ
とによるものである。In the work explained above, the temperature applied to the cubic boron nitride powder was set to 1,350°C or less because the stable temperature range of the cubic boron nitride crystal loaded in the press equipment was 1,350°C or less. This is because it is generally accepted that there is.
尚、本発明においては、高速度工具鋼粉末を使用した場
合についてのみ述べたが、タングステン工具鋼・炭素工
具鋼等の工具鋼の粉末を使用した場合においても、高速
度工具鋼を使用した場合と類似した焼結体を得ることが
できる。In the present invention, only the case where high-speed tool steel powder is used has been described, but even when powder of tool steel such as tungsten tool steel or carbon tool steel is used, the case where high-speed tool steel is used A sintered body similar to can be obtained.
実施例 １゜
高速度工具！ｉｌ （５ＫＨ９）粉末を６０重重量％と
、粒径１０ミクロンの立方晶窒化硼素粉末を２０重重量
％と、溶融温度が１．１５０℃であってニッケＮの含有
割合が８９．９４重量予てアルニッケル系合金にッケル
ー硼素−シリコンー鉄−炭素）粉末（補出金属箔粉社製
）を２０重重量％と、の割合にて混合した混合粉末を焼
結用原料とした。斯様に配合した焼結用原料を、ピスト
ンシリンダ型のホットプレス装置を用いて８００ＫＬｉ
／ｉの圧力にて加圧成形すると同時に１，２３０℃の温
度にて加熱焼成し、次いで、加えていた圧力は保持した
ままで加熱のみを停止し、更□外部より冷却して加熱室
内の温度が３００℃にまで降温した後に、保持していた
圧・力を常圧□もどして生成した焼結組織体を取り出し
た。得た焼結組織体は、高速度工具鋼粒子の多数個と立
方晶窒化硼素粒子の多数個との混合物とニッケル系合金
が液相焼結して安定した複合焼結組織体を構成している
立方晶窒化硼素複合高速度工具鋼焼結体であった。Example 1゜High speed tool! il (5KH9) powder is 60% by weight, cubic boron nitride powder with a particle size of 10 microns is 20% by weight, the melting temperature is 1.150°C, and the content of nickel N is 89.94% by weight. A mixed powder obtained by mixing an alnickel alloy with 20% by weight of Kkeru boron-silicon-iron-carbon powder (manufactured by Shushu Metal Foil Co., Ltd.) was used as a raw material for sintering. The raw materials for sintering blended in this way were heated to 800KLi using a piston-cylinder type hot press device.
Pressure molding is performed at a pressure of /i, and at the same time, heating and baking are performed at a temperature of 1,230°C.Then, only the heating is stopped while maintaining the applied pressure, and then the inside of the heating chamber is cooled from the outside. After the temperature was lowered to 300° C., the pressure and force that had been maintained were returned to normal pressure and the generated sintered tissue was taken out. The obtained sintered structure is composed of a mixture of a large number of high-speed tool steel particles and a large number of cubic boron nitride particles and a nickel-based alloy that are liquid-phase sintered to form a stable composite sintered structure. It was a cubic boron nitride composite high speed tool steel sintered body.
実施例 ２゜
高速度工具鋼（ＳＫＨＩＯ）粉末を６０重量優と、粒径
１０ミクロンの立方晶窒化硼素粉末を２０重量多と、溶
融温度が１，２００℃であってコーバルトの含有割合が
５０．８重量蝿であるコバル） 系合金（コバルト−ク
ロム−硼素−ニッケルータングステン−シリコン−炭素
）粉末にクロブレイズ社製）を２０重重量％と、の割合
にて混合した混合粉末を焼結用原料とした。斯様に配合
した焼結用原料を通常の加圧プレス装置を用いて７，０
００Ｋｇ／ｃｍ２の圧力にて加圧成形し、其の成形体を
真空炉を用いて９００℃に加熱して真空焼結して予備焼
結体を生成し、次いで、其の予備焼結体を熱間静水圧プ
レス装置を用いて１，２００Ｋｇ／ｃｍ２の圧力こて加
圧すると同時に１，２５０℃の温度にて加熱焼成した。Example 2 60% high speed tool steel (SKHIO) powder, 20% cubic boron nitride powder with a particle size of 10 microns, melting temperature 1,200°C, cobalt content 50% A mixed powder of 20% by weight of Cobalt alloy (cobalt-chromium-boron-nickel-tungsten-silicon-carbon) powder (manufactured by Cloblaze) was sintered. It was used as a raw material for The raw materials for sintering blended in this way are 7.0
Pressure molding is performed at a pressure of 00 kg/cm2, and the molded body is heated to 900°C using a vacuum furnace and vacuum sintered to produce a pre-sintered body. A pressure trowel of 1,200 Kg/cm2 was applied using a hot isostatic press device, and at the same time, the product was heated and fired at a temperature of 1,250°C.
次いで、加えていた圧力は保持したままで加熱のみを停
止し、更に冷却して加熱室内の温度が３００ ’ＣｔＣ
まで降温した後に、保持していた圧力を常圧にもどして
生成した焼結組織体を取り出した。Next, only the heating was stopped while maintaining the applied pressure, and the temperature in the heating chamber was further cooled to 300'CtC.
After the temperature was lowered, the pressure that had been maintained was returned to normal pressure and the generated sintered tissue was taken out.
得た焼結組織体は、高速度工具鋼粒子の多数個と立方晶
窒化硼素粒子の多数個との混合物とコバルト系合金が液
相焼結して安定した複合焼結組織体を構成している立方
晶窒化硼素複合高速度工具鋼焼結体であった。The obtained sintered structure is a stable composite sintered structure formed by liquid phase sintering of a cobalt-based alloy and a mixture of a large number of high-speed tool steel particles and a large number of cubic boron nitride particles. It was a cubic boron nitride composite high speed tool steel sintered body.
実施例 ３゜
高速度工具鋼（ＳＫ）（９）粉末を６５重量褒と、粒径
１０ミクロンの立方晶窒化硼素粉末を１５重量多と、炭
化タングステン粉末を５重量優と、溶融温度が１，１５
０℃であってニッケルの含有割合が８９．９４重量俸で
ある二ｙｌフルＪ 合金にッケルー硼素−シリコンー鉄
−炭素）粉末（補出金属箔粉社製）を１５重量多と、の
割合にて混合した混合粉末な焼結用原料とした。斯様に
配合した焼結用原料を、ピストンシリンダ型のホットプ
レス装置を用いて、８００Ｋｇ／ｉの圧力にて加圧成形
すると同時に１，２３０℃の温度にて加熱焼成し、次い
で、加えていた圧力は保持したままで加熱のみを停止し
、更に外部より冷却して加熱室内の温度が３００℃にま
で降温した後に、保持していた圧力を常圧にもどして生
成した焼結組織体を取り出した。得た焼結組織体は、高
速度工具鋼粒子の多数個と立方晶窒化硼素粒子の多数個
と炭化タングステン粒子の多数個との混合物とニッケル
系合金が液相焼結して安定した複合焼結組織体を構成し
ている立方晶窒化硼素複合高速度工具鋼焼結体であった
。Example 3 65 parts by weight of high-speed tool steel (SK) (9) powder, 15 parts by weight of cubic boron nitride powder with a grain size of 10 microns, 5 parts by weight of tungsten carbide powder, and the melting temperature is 1. ,15
At 0°C, 15% of Kkeru boron-silicon-iron-carbon powder (manufactured by Shushu Metal Foil Powder Co., Ltd.) was added to a 2yl full J alloy with a nickel content of 89.94% by weight. This was used as a mixed powder raw material for sintering. The raw materials for sintering blended in this manner were press-formed at a pressure of 800 kg/i using a piston-cylinder type hot press device, simultaneously heated and fired at a temperature of 1,230°C, and then added. The heating was stopped while the pressure was maintained, and the temperature inside the heating chamber was lowered to 300°C by cooling from the outside, and then the maintained pressure was returned to normal pressure to produce a sintered structure. I took it out. The obtained sintered structure is a stable composite sintered body obtained by liquid-phase sintering of a mixture of many high-speed tool steel particles, many cubic boron nitride particles, and many tungsten carbide particles, and a nickel-based alloy. It was a cubic boron nitride composite high-speed tool steel sintered body constituting a tissue body.
実施例 ４゜
高速度工具鋼（ＳＫＨＩＯ）粉末を６５重量肇と、粒径
が１０ミクロンの立方晶窒化硼素粉末を１５重量多と、
硼化チタン粉末を５重量多と、溶融温度が１，２００℃
であってコバルトの含有割合が５０．８重量多であるコ
バルト系１ｉ−（コバルト−クロム−硼素−ニッケルー
タングステン−シリコン−炭素）粉末にグロプレイズ社
製）を１５重量傅と、の割合にて混合した混合粉末を焼
結用原料とした。Example 4 65 parts by weight of high-speed tool steel (SKHIO) powder, 15 parts by weight of cubic boron nitride powder with a particle size of 10 microns,
When titanium boride powder is added by 5 weight, the melting temperature is 1,200℃.
Cobalt-based 1i (cobalt-chromium-boron-nickel-tungsten-silicon-carbon) powder with a cobalt content of 50.8% by weight and 15% by weight of Gropleys Co., Ltd. The mixed powder was used as a raw material for sintering.
斯様に配合した焼結用原料を通常の加圧プレス装置を用
いて７，０００Ｋｇ／ｃｔＡの圧力にて加圧成形し、其
の成形体を真空炉を用いて９００℃に加熱して真空焼結
して予備焼結体を生威し、次いで、其の予備焼結体を熱
間静水圧プレス装置を用いて１．２００ Ｋｆ／ ｃｆ
ｌの圧力にて加圧すると同時に１，２５０℃の温度にて
加熱焼成した。次いで、加えていた圧力は保持したまま
で加熱のみを停止し、更に冷却して加熱室内の温度が３
００℃にまで降温した後に保持していた圧力を常圧にも
どして生成した焼結組織体を取り出した。得た焼結組織
体は高速度工具鋼粒子の多数個と立方晶窒化硼素粒子の
多数個と硼化チタン粒子の多数個との混合物とコバルト
系合金が液相焼結して安定〔
した複合焼結組織体を構成している立方晶窒化硼素複合
高速度工具鋼焼結体であった。The raw materials for sintering blended in this way are pressure-formed at a pressure of 7,000 kg/ctA using a normal pressure press device, and the molded body is heated to 900°C using a vacuum furnace and vacuum-filled. Sinter to produce a pre-sintered body, and then press the pre-sintered body to 1.200 Kf/cf using a hot isostatic press device.
The material was pressurized at a pressure of 1,250° C. and fired at a temperature of 1,250° C. at the same time. Next, only the heating is stopped while maintaining the applied pressure, and the temperature inside the heating chamber is reduced to 3.
After the temperature was lowered to 00° C., the pressure that had been maintained was returned to normal pressure and the generated sintered tissue was taken out. The obtained sintered structure is a stable composite obtained by liquid phase sintering of a mixture of a large number of high-speed tool steel particles, a large number of cubic boron nitride particles, and a large number of titanium boride particles, and a cobalt-based alloy. The sintered body was a cubic boron nitride composite high-speed tool steel sintered body.
発明の効果〕
以上略説明したように、本発明の製造法によって製造し
た立方晶窒化硼素複合高速度工具鋼焼結体は、高価な特
殊構造の超高圧高温発生装置を使用することなく、通常
構造のピストンシリンダ型のホットプレス装置、または
通常構造の加圧プレス装置と真空炉と一般用として設け
られている熱間静水圧プレス装置と、を使用して５００
に９／ｃｍ２以上の圧力にて加圧成形すると共ＶＣ９０
０℃乃至１，３５０℃の範囲内より選定した温度にて加
熱焼成する方法によって製造する立方晶窒化硼素複合高
速度工具鋼焼結体であるので、償却費の負担額が安くて
すみ、従って立方晶窒化硼素複合高速度工具鋼焼結体の
製造原価を安くする効果が得られる。更に、従来の高速
度工具鋼よりも硬度が高く切削能力の高い工具材を得る
ことができる。斯様な理由によって、本発明の立方晶窒
化硼素複合高速度工具鋼焼結体は安価でしかも利用分野
が広い工具材としての効果を奏することができるもので
ある。[Effects of the Invention] As briefly explained above, the cubic boron nitride composite high-speed tool steel sintered body produced by the production method of the present invention can be produced without using an expensive specially constructed ultra-high pressure and high temperature generator. 500 using a piston-cylinder type hot press device with a structure, or a pressure press device with a normal structure, a vacuum furnace, and a hot isostatic press device provided for general use.
Pressure molded at a pressure of 9/cm2 or more and VC90
Since it is a cubic boron nitride composite high-speed tool steel sintered body manufactured by heating and firing at a temperature selected within the range of 0°C to 1,350°C, the burden of depreciation costs is low. The effect of lowering the manufacturing cost of the cubic boron nitride composite high-speed tool steel sintered body can be obtained. Furthermore, a tool material with higher hardness and higher cutting ability than conventional high-speed tool steel can be obtained. For these reasons, the cubic boron nitride composite high-speed tool steel sintered body of the present invention can be effective as a tool material that is inexpensive and can be used in a wide range of fields.
Claims (4)
、立方晶窒化硼素粉末を３０重量％乃至５重量％と、立
方晶窒化硼素の安定温度領域における温度である１，３
５０℃以下の低い溶融温度を有しているニッケル系合金
粉末またはコバルト系合金粉末を２０重量％乃至５重量
％と、の割合範囲内より選定した割合にて混合した混合
粉末を５００Ｋｇ／ｃｍ＾２以上の圧力にて加圧成形す
ると共に９００℃乃至１，３５０℃の範囲内より選定し
た温度にて加熱焼結して成る焼結体において、高速度工
具鋼粒子の多数個と立方晶窒化硼素粒子の多数個との混
合物と溶融ニッケル合金または溶融コバルト合金が液相
焼結して焼結組織体を構成していることを特徴とする立
方晶窒化硼素複合高速度工具鋼焼結体。(1) The temperature in the stable temperature range of cubic boron nitride is 1,3 when the high speed tool steel powder is 50% to 90% by weight and the cubic boron nitride powder is 30% to 5% by weight.
500 kg/cm^ of mixed powder made by mixing nickel-based alloy powder or cobalt-based alloy powder having a low melting temperature of 50°C or less at a ratio selected from within the ratio range of 20% by weight to 5% by weight. In a sintered body formed by pressure forming at a pressure of 2 or more and heating and sintering at a temperature selected from the range of 900°C to 1,350°C, a large number of high-speed tool steel particles and cubic nitridation are formed. A cubic boron nitride composite high-speed tool steel sintered body, characterized in that a mixture with a large number of boron particles and a molten nickel alloy or a molten cobalt alloy are liquid-phase sintered to constitute a sintered structure.
、立方晶窒化硼素粉末を２０重量％乃至５重量％と、硬
質炭化物・硬質硼化物・硬質窒化物・硬質珪化物・硬質
酸化物のうちより選択した硬質物の粉末を１０重量％乃
至２重量％と、立方晶窒化硼素の安定温度領域における
温度である１，３５０℃以下の低い溶融温度を有してい
るニッケル系合金粉末またはコバルト系合金粉末を２０
重量％乃至３重量％と、の割合範囲内より選定した割合
にて混合した混合粉末を５００Ｋｇ／ｃｍ＾２以上の圧
力にて加圧成形すると共に９００℃乃至１，３５０℃の
範囲内より選定した温度にて加熱焼成して成る焼結体に
おいて、高速度工具鋼粒子の多数個と立方晶窒化硼素粒
子の多数個及び硬質物粒子の多数個との混合物と溶融ニ
ッケル系合金または溶融コバルト系合金が液相焼結して
焼結組織体を構成していることを特徴とする立方晶窒化
硼素複合高速度工具鋼焼結体。(2) 50% to 90% by weight of high speed tool steel powder, 20% to 5% by weight of cubic boron nitride powder, hard carbide, hard boride, hard nitride, hard silicide, hard oxide A nickel-based alloy powder containing 10% to 2% by weight of a powder of a hard material selected from among the above, and having a low melting temperature of 1,350°C or less, which is the temperature in the stable temperature range of cubic boron nitride. Or 20% cobalt alloy powder
A mixed powder mixed in a ratio selected from within the range of weight% to 3% by weight is press-molded at a pressure of 500Kg/cm^2 or more and at a temperature selected from within the range of 900℃ to 1,350℃. In the sintered body formed by heating and firing at a temperature of A cubic boron nitride composite high-speed tool steel sintered body, characterized in that the alloy is liquid-phase sintered to form a sintered structure.
、立方晶窒化硼素粉末を３０重量％乃至５重量％と、立
方晶窒化硼素の安定温度領域における温度である１，３
５０℃以下の低い溶融温度を有しているニッケル系合金
粉末またはコバルト系合金粉末を２０重量％乃至５重量
％と、の割合範囲内より選定した割合にて混合した混合
粉末を５００Ｋｇ／ｃｍ＾２以上の圧力にて加圧成形す
ると共に９００℃乃至１，３５０℃の範囲内より選定し
た温度にて加熱焼成して成る高速度工具鋼粒子の多数個
と立方晶窒化硼素粒子の多数個との混合物と溶融ニッケ
ル系合金または溶融コバルト系合金が液相焼結して焼結
組織体を生成することを特徴とする立方晶窒化硼素複合
高速度工具鋼焼結体の製造法。(3) The temperature in the stable temperature range of cubic boron nitride is 1,3 when the high speed tool steel powder is 50% to 90% by weight and the cubic boron nitride powder is 30% to 5% by weight.
500 kg/cm^ of mixed powder made by mixing nickel-based alloy powder or cobalt-based alloy powder having a low melting temperature of 50°C or less at a ratio selected from within the ratio range of 20% by weight to 5% by weight. A large number of high-speed tool steel particles and a large number of cubic boron nitride particles formed by pressure forming at a pressure of 2 or more and heating and baking at a temperature selected from a range of 900°C to 1,350°C. A method for producing a cubic boron nitride composite high-speed tool steel sintered body, characterized in that a mixture of the above and a molten nickel-based alloy or a molten cobalt-based alloy are sintered in a liquid phase to produce a sintered structure.
、立方晶窒化硼素粉末を２０重量％乃至５重量％と、硬
質炭化物・硬質硼化物・硬質窒化物、硬質珪化物・硬質
酸化物のうちより選択した硬質物の粉末を１０重量％乃
至２重量％と、立方晶窒化硼素粉末の安定温度領域にお
ける温度である１，３５０℃以下の低い溶融温度を有し
ているニッケル系合金粉末またはコバルト系合金粉末を
２０重量％乃至３重量％と、の割合範囲内より選定した
割合にて混合した混合粉末を５００Ｋｇ／ｃｍ＾２以上
の圧力にて加圧成形すると共に９００℃乃至１，３５０
℃の範囲内より選定した温度にて加熱焼成して成る高速
度工具鋼粒子の多数個と立方晶窒化硼素粒子の多数個と
硬質物粒子の多数個との混合物と溶融ニッケル系合金ま
たは溶融コバルト系合金が液相焼結して焼結組織体を生
成することを特徴とする立方晶窒化硼素複合高速度工具
鋼焼結体の製造法。(4) 50% to 90% by weight of high speed tool steel powder, 20% to 5% by weight of cubic boron nitride powder, hard carbide, hard boride, hard nitride, hard silicide, hard oxide A nickel-based alloy containing 10% by weight to 2% by weight of a hard material powder selected from among the above, and having a low melting temperature of 1,350°C or less, which is the temperature in the stable temperature range of cubic boron nitride powder. A mixed powder prepared by mixing powder or cobalt-based alloy powder at a ratio selected from within the ratio range of 20% by weight to 3% by weight is press-molded at a pressure of 500 kg/cm^2 or more and at 900°C to 1%. ,350
A mixture of a large number of high-speed tool steel particles, a large number of cubic boron nitride particles, and a large number of hard material particles, and a molten nickel-based alloy or molten cobalt formed by heating and firing at a temperature selected within the range of °C. A method for manufacturing a cubic boron nitride composite high-speed tool steel sintered body, characterized in that a system alloy is liquid-phase sintered to produce a sintered structure.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6213289 | 1989-03-16 | ||
| JP1-62132 | 1989-03-16 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0344450A true JPH0344450A (en) | 1991-02-26 |
Family
ID=13191246
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1158179A Pending JPH0344450A (en) | 1989-03-16 | 1989-06-22 | Sintered compact of cubic boron nitride reinforced high speed tool steel composite and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0344450A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000319705A (en) * | 1999-04-07 | 2000-11-21 | Sandvik Ab | Manufacture of cutting tool insert of polycrystalline cubic boron nitride, and body of this polycrystalline cubic boron nitride |
| US11707784B2 (en) | 2019-10-15 | 2023-07-25 | King Fahd University Of Petroleum And Minerals | Spark plasma sintered cBN and Ni-cBN bearing steel |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59118852A (en) * | 1982-12-27 | 1984-07-09 | Tatsuro Kuratomi | Composite high speed steel of sintered hard alloy and its production |
| JPS6289843A (en) * | 1985-10-14 | 1987-04-24 | Kobe Steel Ltd | Sintered tool steel |
| JPS63159692A (en) * | 1986-12-23 | 1988-07-02 | Toshiba Corp | Blade for rotary compressor |
-
1989
- 1989-06-22 JP JP1158179A patent/JPH0344450A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59118852A (en) * | 1982-12-27 | 1984-07-09 | Tatsuro Kuratomi | Composite high speed steel of sintered hard alloy and its production |
| JPS6289843A (en) * | 1985-10-14 | 1987-04-24 | Kobe Steel Ltd | Sintered tool steel |
| JPS63159692A (en) * | 1986-12-23 | 1988-07-02 | Toshiba Corp | Blade for rotary compressor |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000319705A (en) * | 1999-04-07 | 2000-11-21 | Sandvik Ab | Manufacture of cutting tool insert of polycrystalline cubic boron nitride, and body of this polycrystalline cubic boron nitride |
| US11707784B2 (en) | 2019-10-15 | 2023-07-25 | King Fahd University Of Petroleum And Minerals | Spark plasma sintered cBN and Ni-cBN bearing steel |
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