JPH0398765A - Manufacture of metal bonded tool - Google Patents
Manufacture of metal bonded toolInfo
- Publication number
- JPH0398765A JPH0398765A JP23299589A JP23299589A JPH0398765A JP H0398765 A JPH0398765 A JP H0398765A JP 23299589 A JP23299589 A JP 23299589A JP 23299589 A JP23299589 A JP 23299589A JP H0398765 A JPH0398765 A JP H0398765A
- Authority
- JP
- Japan
- Prior art keywords
- alloy powder
- iron
- carbon
- abrasive grains
- based alloy
- 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
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 49
- 239000002184 metal Substances 0.000 title claims abstract description 49
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 102
- 239000006061 abrasive grain Substances 0.000 claims abstract description 70
- 239000000956 alloy Substances 0.000 claims abstract description 70
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 68
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 66
- 239000000843 powder Substances 0.000 claims abstract description 66
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 63
- 229910052742 iron Inorganic materials 0.000 claims abstract description 51
- 238000001816 cooling Methods 0.000 claims abstract description 32
- 239000000203 mixture Substances 0.000 claims abstract description 14
- 229910003460 diamond Inorganic materials 0.000 claims description 32
- 239000010432 diamond Substances 0.000 claims description 32
- 238000000034 method Methods 0.000 claims description 19
- 229910052710 silicon Inorganic materials 0.000 claims description 19
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 18
- 239000010703 silicon Substances 0.000 claims description 18
- 229910052582 BN Inorganic materials 0.000 claims description 2
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 2
- 238000000227 grinding Methods 0.000 abstract description 46
- 239000011159 matrix material Substances 0.000 abstract description 32
- 238000002844 melting Methods 0.000 abstract description 2
- 230000008018 melting Effects 0.000 abstract description 2
- 239000002245 particle Substances 0.000 description 25
- 239000002244 precipitate Substances 0.000 description 19
- 238000005245 sintering Methods 0.000 description 19
- 230000000052 comparative effect Effects 0.000 description 18
- 239000000463 material Substances 0.000 description 18
- 230000007423 decrease Effects 0.000 description 10
- 238000005507 spraying Methods 0.000 description 9
- 230000014759 maintenance of location Effects 0.000 description 7
- 239000000314 lubricant Substances 0.000 description 6
- 238000005498 polishing Methods 0.000 description 6
- 239000002994 raw material Substances 0.000 description 5
- 229910001567 cementite Inorganic materials 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910002804 graphite Inorganic materials 0.000 description 4
- 239000010439 graphite Substances 0.000 description 4
- 238000002347 injection Methods 0.000 description 4
- 239000007924 injection Substances 0.000 description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000010298 pulverizing process Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910052581 Si3N4 Inorganic materials 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 230000014509 gene expression Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 238000010406 interfacial reaction Methods 0.000 description 2
- 238000005461 lubrication Methods 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 238000007517 polishing process Methods 0.000 description 2
- 238000010583 slow cooling Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 101100474383 Escherichia coli (strain K12) rpsO gene Proteins 0.000 description 1
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 150000002505 iron Chemical class 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000009766 low-temperature sintering Methods 0.000 description 1
- 229910001105 martensitic stainless steel Inorganic materials 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000001172 regenerating effect Effects 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000007514 turning Methods 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Polishing Bodies And Polishing Tools (AREA)
Abstract
Description
【発明の詳細な説明】
〔発明の目的〕
（産業上の利用分野）
本発明は炭素を含有する鉄基合金と、高硬度を有する砥
粒との焼結体から成る砥粒層を有するメタルボンド工具
の製造方法に係り、特に材料中に微小な炭素を均一に分
散させることが可能であり、研削時における潤滑性を高
めるとともに、マトリックスの強度を改善し、寿命の増
大を図ったメタルボンド工具の製造方法に関する。[Detailed Description of the Invention] [Object of the Invention] (Industrial Application Field) The present invention provides a metal having an abrasive grain layer consisting of a sintered body of an iron-based alloy containing carbon and abrasive grains having high hardness. Regarding the manufacturing method of bond tools, in particular, it is possible to uniformly disperse microscopic carbon in the material, which improves lubricity during grinding, improves matrix strength, and extends life. It relates to a method for manufacturing tools.
（従来の技術）
酸化アルミニウム、窒化ケイ素、窒化アルミニウム、炭
化ケイ素などの高硬度ファインセラミックスの研削加工
、仕上加工に使用される研削工具として、砥粒にダイヤ
モンドを使用したメタルポンドダイヤモンド工具が、従
来より広く用いられている。(Prior technology) Metal pound diamond tools that use diamond abrasive grains are conventionally used as grinding tools for grinding and finishing high-hardness fine ceramics such as aluminum oxide, silicon nitride, aluminum nitride, and silicon carbide. more widely used.
またバナジウム（Ｖ）を含む高速度鋼やマルテンサイト
系ステンレス鋼などの難削合金材の研削加工や仕上加工
においては、砥粒として立方晶窒化硼素（以下ｒＣＢＮ
Ｊと略称する。）をマトリックス中に分散させたメタル
ボンド窒化硼素工具が使用されている。In addition, cubic boron nitride (hereinafter referred to as rCBN) is used as an abrasive grain in grinding and finishing of difficult-to-cut alloy materials such as high-speed steel and martensitic stainless steel containing vanadium (V).
It is abbreviated as J. ) dispersed in a matrix have been used.
上記のようなメタルボンド工具のうち、例えば砥粒にダ
イヤモンド粉末を用いるメタルボンドダイヤモンド工具
は、一般に金属粉末および必要により金属化合物を含む
金属粉末とダイヤモンド粉末砥粒とを混合した後に焼結
して形成される。この焼結操作によってマトリックスと
ダイヤモンド粉末砥粒との結合力、機械的強度の向上が
図られ、形成されたメタルボンドダイヤモンド工具は、
適宜ドレッシングによって砥石表面を再生しながら研磨
・研削用工具として使用されている。Among the above-mentioned metal bond tools, for example, metal bond diamond tools that use diamond powder as abrasive grains are generally made by mixing diamond powder abrasive grains with metal powder and metal powder containing a metal compound if necessary, and then sintering the abrasive grains. It is formed. This sintering operation improves the bonding force and mechanical strength between the matrix and the diamond powder abrasive grains, and the resulting metal bonded diamond tool is
It is used as a polishing and grinding tool while regenerating the surface of the whetstone by dressing it appropriately.
ところで、切込み深さが大きい重研削加工に適したメタ
ルボンドダイヤモンド工具の場合、マトリックスの原料
としては、炭素含有量が大きな鉄基合金鋳造材の切粉を
、ボールミルまたはスタンプ法などで粉砕した粉末が使
用される。この高炭素鉄基合金粉末にダイヤモンド砥粒
を均一に混合し、真空またはアルゴンなどの不活性ガス
による保護雰囲気において例えば温度８００〜９００’
Ｃ、圧力２００〜４００ｋｇ／ｃｆｌ程度の条件でホッ
トプレスを行ない、砥粒層を形成している。砥粒の周囲
には炭素粒子が分散するように固定される。この炭素粒
子は研削対象物との研削抵抗を低減する潤滑材として働
く一方、マトリックスはダイヤモンド砥粒を支持固定す
る保持材として機能する。By the way, in the case of metal-bonded diamond tools that are suitable for heavy-duty grinding with large depths of cut, the raw material for the matrix is powder obtained by pulverizing chips of iron-based alloy casting material with a high carbon content using a ball mill or stamping method. is used. Diamond abrasive grains are uniformly mixed with this high carbon iron-based alloy powder, and the mixture is heated to a temperature of 800 to 900' in a vacuum or in a protected atmosphere with an inert gas such as argon.
C. Hot pressing is performed at a pressure of about 200 to 400 kg/cfl to form an abrasive layer. Carbon particles are fixed and dispersed around the abrasive grains. The carbon particles act as a lubricant that reduces grinding resistance with the object to be ground, while the matrix acts as a holding material that supports and fixes the diamond abrasive grains.
（発明が解決しようとする課題）
しかしながら、従来の製造方法で合金鋳造材の切粉を粉
砕して得られた鉄基合金粉末は、鋳造時の冷却速度が小
さいため炭素の析出物の大きさが数十μｍないし数百μ
ｍと砥粒の平均粒径（数μｍ〜１００μｍ）に比較して
大きく、また形状的にも不均一であり、マトリックス中
に微細に分散した組織になっていない。(Problems to be Solved by the Invention) However, iron-based alloy powder obtained by crushing chips of alloy casting materials using conventional manufacturing methods has a low cooling rate during casting, so the size of carbon precipitates is small. is several tens of μm to several hundred μm
It is larger than the average particle size of the abrasive grains (several μm to 100 μm), and is non-uniform in shape, and does not have a finely dispersed structure in the matrix.
そのため粉砕操作によって粉末中に保持されていた炭素
粒子の脱落が起り易く、粉末中の炭素の分布および形状
が不均一になる。そしてこの鉄基合金粉末によりマトリ
ックスを形成した工具材料では、炭素析出物の径が大き
いことから、研削中に炭素析出物が脱落し易く、また脱
落によって形成された窪みに削り屑や磨き屑が堆積して
目詰りの原因となり、さらに目詰りは焼き付きによるマ
トリックスの破損や塑性変形を生起する。Therefore, the carbon particles held in the powder are likely to fall off during the crushing operation, resulting in uneven distribution and shape of carbon in the powder. In tool materials whose matrix is formed from this iron-based alloy powder, the diameter of carbon precipitates is large, so carbon precipitates tend to fall off during grinding, and shavings and polishing debris are deposited in the depressions formed by the falling off. This builds up and causes clogging, which further causes damage to the matrix and plastic deformation due to seizure.
また砥粒の近傍に窪みが形成されることによって砥粒の
保持強度が急減し、ダイヤモンド砥粒の脱落が急増して
研削、研磨効率の低下を招き、さらに高い仕上げ精度が
得られないという問題があった。In addition, due to the formation of depressions near the abrasive grains, the retention strength of the abrasive grains rapidly decreases, and diamond abrasive grains rapidly fall off, leading to a decrease in grinding and polishing efficiency, and furthermore, high finishing accuracy cannot be obtained. was there.
また従来のメタルボンドダイヤモンド工具の製造工程に
おいては、グラフアイトなどの炭素粉末を添加して圧縮
成形後、焼結操作を行なうことによって焼結体中に炭素
粒を分散させる方法を採用しているが、砥粒層全体に微
小な炭素粒を均一に分散させることが困難であった。そ
のため炭素析出物および砥粒の脱落が多く、これにより
研削・研磨加工の効率が低下し、高い仕上げ精度が得ら
れない上に砥石自体の寿命が短いという根本的な問題点
があった。In addition, in the conventional manufacturing process for metal-bonded diamond tools, carbon particles such as graphite are added, compression molded, and then sintered to disperse carbon particles in the sintered body. However, it has been difficult to uniformly disperse fine carbon grains throughout the abrasive grain layer. As a result, many carbon precipitates and abrasive grains fall off, which reduces the efficiency of grinding and polishing processes, making it impossible to obtain high finishing accuracy, and posing the fundamental problem that the life of the grinding wheel itself is short.
本発明は上記の問題点を解決するためになされたもので
あり、材料中に微小な炭素粒子を均一に分散させ、研削
時における潤滑性を高めるとともに、マトリックスの強
度を高め砥粒および潤滑材としての炭素粒の脱落が少な
く、高い効率で研削・研磨加工を実施することが可能で
あり、寿命が長い経済的なメタルボンド工具を製造し得
るメタルボンド工具の製造方法を提供することを目的と
する。The present invention was made to solve the above-mentioned problems, and by uniformly dispersing fine carbon particles in the material, it improves lubricity during grinding, increases the strength of the matrix, and improves the abrasive grains and lubricant. The purpose of the present invention is to provide a method for manufacturing a metal bond tool that can produce an economical metal bond tool that has a long lifespan, has less carbon particles falling off, and can perform grinding and polishing processes with high efficiency. shall be.
（課題を解決するための手段と作用）
本願発明者等は、従来の問題点がマトリックス中の炭素
の形態に起因することを見い出し、研削時における炭素
による潤滑作用を保持しつつ、寿命の長いメタルボンド
工具を得ることを目的にして、マトリックス材料中に微
細な炭素粒子を分散させる方法を研究し、さらに砥粒層
の研磨特性に及ぼす砥石の種類の影響を研究した。(Means and effects for solving the problem) The inventors of the present application discovered that the conventional problem was caused by the form of carbon in the matrix. Aiming to obtain a metal-bonded tool, a method of dispersing fine carbon particles in the matrix material was investigated, and the influence of the type of grinding wheel on the polishing properties of the abrasive layer was also studied.
その結果、原料となる鉄基合金を溶融し、得られた溶湯
を粉化すると同時に毎秒１０℃以上の冷却速度で２００
℃以下の温度まで冷却し、しかる後に得られた鉄基合金
粉末と砥粒との混合物を一体に焼結して砥粒層を形成し
たときに、従来と比較して、研削特性が格段に優れた長
寿命のメタルボンド工具を得ることができた。As a result, the iron-based alloy that is the raw material is melted, the resulting molten metal is powdered, and at the same time the cooling rate is 200°C or higher at a cooling rate of 10°C or more per second.
When the resulting mixture of iron-based alloy powder and abrasive grains is cooled to a temperature below ℃ and then sintered together to form an abrasive layer, the grinding properties are significantly improved compared to conventional methods. We were able to obtain a metal bond tool with excellent long life.
また鉄基合金粉末中の硅素含有量（Ａｗｔ％）と炭素含
有量（Ｂｗｊ％）との配合量を、２．５≦Ｂ≦４．５
３≦Ｂ＋Ａ／３≦５
の関係式を満たすように設定したときに、特に微細な炭
素粒がマトリックス中に形成され、潤滑作用が優れた長
寿命の砥粒層を得ることができた。In addition, the blending amount of silicon content (Awt%) and carbon content (Bwj%) in the iron-based alloy powder should be adjusted to satisfy the following relational expressions: 2.5≦B≦4.5 3≦B+A/3≦5 When the setting was set to
本発明は上記知見に基づいてさなれたものである。本発
明方法において使用する鉄基合金粉末としては、Ｆｅを
基材として他に潤滑剤となる炭素や炭素の析出を促進さ
せる硅素などの元素を添加した合金材が使用される。The present invention has been made based on the above findings. As the iron-based alloy powder used in the method of the present invention, an alloy material is used in which Fe is used as a base material and elements such as carbon, which serves as a lubricant, and silicon, which promotes the precipitation of carbon, are added.
鉄基合金粉末は鉄基合金を一旦加熱溶融させ、これを粉
化させると同時に冷却して調製される。Iron-based alloy powder is prepared by heating and melting an iron-based alloy, pulverizing it, and cooling it at the same time.
鉄基合金を粉末化し、冷却する手段としては、一般に溶
湯を水中に滴下して粉末にする方法や半溶融状態に加熱
して急速攪拌する方法などがあるが、上記方法で得られ
る原料粉末は２５０μｍ程度の大きな粒子となり、形状
も複雑で酸化物の量も多くなるため、次に述べる溶湯噴
霧法（アトマイズ法）を用いることが望ましい。Generally, there are methods for powdering and cooling iron-based alloys, such as dropping molten metal into water and turning it into powder, or heating it to a semi-molten state and rapidly stirring it, but the raw material powder obtained by the above method is Since the particles are large, about 250 μm in size, have a complicated shape, and contain a large amount of oxide, it is desirable to use the molten metal spraying method (atomization method) described below.
この溶湯噴霧法は鉄基合金の溶湯を、例えばアルミナ製
の噴射ノズルから２〜１０気圧の圧縮空気、不活性ガス
等の粉化用気体を吹き込んで粉化し、ノズル下部に配設
した水槽中に集積させる方法であり、ノズルの開口量、
溶湯の注入速度、粉化用気体の圧力および温度などを調
節することによって、粉末の粒径・粒径分布および冷却
速度を変えることが可能であり、所望の粒度、結晶組織
を有する原料粉末を得る方法である。In this molten metal spraying method, molten metal of iron-based alloy is pulverized by blowing compressed air of 2 to 10 atm, inert gas, or other pulverizing gas through an alumina injection nozzle, and the molten metal is pulverized into a water tank located below the nozzle. It is a method of accumulating in the nozzle opening amount,
By adjusting the injection rate of the molten metal, the pressure and temperature of the powdering gas, etc., it is possible to change the particle size, particle size distribution, and cooling rate of the powder, allowing raw material powder with the desired particle size and crystal structure to be produced. This is the way to get it.
本発明方法においては鉄基合金を粉末化すると同時に毎
秒１０℃以上の冷却速度で２００℃以下の温度まで急速
に冷却する。冷却速度が毎秒１０℃未満の緩速冷却であ
ると炭素の析出物が粗大化し、工具として使用した場合
に潤滑剤としての機能が低下する一方、砥粒の脱落が頻
発し研削研磨効率の低下を招き、また高い仕上げ精度が
得られない。In the method of the present invention, the iron-based alloy is pulverized and simultaneously cooled rapidly to a temperature of 200°C or less at a cooling rate of 10°C or more per second. Slow cooling at a cooling rate of less than 10 degrees Celsius per second will cause carbon precipitates to become coarser, reducing its function as a lubricant when used as a tool, while abrasive grains will frequently fall off, reducing grinding and polishing efficiency. In addition, high finishing accuracy cannot be obtained.
一方、毎秒１０℃以上で急速に冷却すると、炭素の微小
な析出物が合金粉末内に均一に分散されるため、砥粒の
保持強度の低下もなく、寿命の長い工具を形成すること
ができる。On the other hand, when rapidly cooled at 10°C or more per second, minute carbon precipitates are evenly dispersed within the alloy powder, making it possible to form a tool with a long life without reducing the retention strength of the abrasive grains. .
また溶湯噴霧後の合金粉末は、２００℃以下の温度まで
充分冷却することが必要である。２００℃を超える温度
まで冷却された高温状態においては、まだ粉末内の元素
の拡散移動が活発であり、炭素の析出物の粗大化が進行
してしまうからである。Further, the alloy powder after being sprayed with the molten metal needs to be sufficiently cooled to a temperature of 200° C. or lower. This is because, in a high temperature state where the powder is cooled to a temperature exceeding 200° C., the elements within the powder are still actively diffusing and moving, and the coarsening of carbon precipitates progresses.
さらに調製する合金粉末の平均粒径は１５０μｍ以下で
、かつ砥粒の平均粒径の１／３以下のものが好ましい。Further, the average particle size of the alloy powder to be prepared is preferably 150 μm or less and 1/3 or less of the average particle size of the abrasive grains.
平均粒径が１５０μｍを超え、また砥粒の平均粒径の１
／３を超える場合は、マトリックス中の砥粒の分布が均
一となり、砥粒の保持強度も低下し、工具としての研削
研磨能力が低下する傾向があるからである。The average particle size exceeds 150 μm, and the average particle size of the abrasive grains exceeds 150 μm.
This is because if it exceeds /3, the distribution of abrasive grains in the matrix becomes uniform, the retention strength of the abrasive grains also decreases, and the grinding and polishing ability of the tool tends to decrease.
また本発明においては、マトリックスを形成する鉄基合
金粉末中の炭素は２．５重量％以上、４．５重量％以下
に設定される。これは炭素量が２．５％未満では自己潤
滑性の低下を招き、またマトリックス金属としての強度
が低下し、さらに砥粒であるダイヤモンドが鉄基材中に
溶出してしまうからである。Further, in the present invention, the carbon content in the iron-based alloy powder forming the matrix is set at 2.5% by weight or more and 4.5% by weight or less. This is because if the carbon content is less than 2.5%, self-lubricating properties will be reduced, the strength as a matrix metal will be reduced, and diamond, which is an abrasive grain, will be eluted into the iron base material.
一方、炭素含有量が４．５重量％を超えると、工具とし
ての強度が低下するため、炭素含有量（Ｂｗｊ％）は２
．５≦Ｂ≦４．５の範囲に定められる。On the other hand, if the carbon content exceeds 4.5% by weight, the strength as a tool decreases, so the carbon content (Bwj%) is
．． It is set in the range of 5≦B≦4.5.
このように本発明において用いる鉄基合金としては、荊
述した範囲の炭素を含有するものであればよく、粉化冷
却工程において、冷却速度を所定値以上に設定し、この
炭素の析出物の大きさを制御することにより本発明の効
果が得られるのであって、通常の工具のマトリックスに
用いられるような鉄基合金であれば、Ｍｎ，Ｍｇ等の不
可避的不純物を含んでいても良く、その組成は問われな
い。As described above, the iron-based alloy used in the present invention may be one containing carbon within the range described above. The effects of the present invention can be obtained by controlling the size, and as long as it is an iron-based alloy that is used for the matrix of ordinary tools, it may contain inevitable impurities such as Mn and Mg. Its composition does not matter.
しかしながらこの合金組成として硅素を用い、さらにマ
トリックス中の硅素を重量比でＡ％、炭素をＢ％とした
時、３≦（Ｂ＋Ａ／３）≦５の範囲で添加すると、硅素
が基質のセメンタイトを不安定にして炭素（黒鉛）を生
じ易くさせて、より細かい炭素析出物が形威され、マト
リックスの強度および潤滑性を高めることができる。However, when silicon is used as the alloy composition, and silicon is added in a weight ratio of A% and carbon is B% in the matrix, if it is added in the range of 3≦(B+A/3)≦5, silicon will absorb the cementite matrix. It is destabilized to facilitate the formation of carbon (graphite), forming finer carbon precipitates, which can increase the strength and lubricity of the matrix.
上記関係式の範囲未満であると、炭素の析出の効果が少
なく、基質がセメンタイト化し易くなる。If it is less than the range of the above relational expression, the effect of carbon precipitation will be small and the substrate will be likely to become cementite.
またこの範囲を超えると焼結性が低下してしまう。Moreover, if it exceeds this range, sinterability will deteriorate.
この硅素量は１，Ｏｗｌ％〜３． ５ｗｊ％が好まし
い。硅素量が１．０％未満では、炭素の析出および粒径
が不均一となると同時に、工具としての十分な強度が得
にくい。一方、硅素量が３．５％を超えると、マトリッ
クス金属の主な部分を占めるフエライト相が変態、硬化
することにより焼結性が低下し強度が小さくなり易いか
らである。This amount of silicon is 1.Owl% to 3.0%. 5wj% is preferable. If the amount of silicon is less than 1.0%, carbon precipitation and grain size become non-uniform, and at the same time, it is difficult to obtain sufficient strength as a tool. On the other hand, if the amount of silicon exceeds 3.5%, the ferrite phase that occupies the main part of the matrix metal is transformed and hardened, resulting in a decrease in sinterability and a tendency to reduce strength.
また砥粒としては、ダイヤモンド粉末の他にＣＢＮを混
合して使用することもできる。ダイヤモンドおよびＣＢ
Ｎのヌープ硬さはそれぞれ、８５０ ０． ５ １
０ ０ｋｇ／ｍｔＡ以上といずれも極めて高い硬度を有
し、難研削材の加工用砥粒として有用である。特にＣＢ
Ｎ砥粒は、耐熱性に優れているため、冷却材を使用しな
い乾式加工用砥粒として急速に用途を拡大している。Further, as the abrasive grains, CBN may be mixed in addition to diamond powder. diamond and cb
The Knoop hardness of N is 850 0. 5 1
All have extremely high hardness of 0.0 kg/mtA or more, and are useful as abrasive grains for processing difficult-to-grind materials. Especially CB
Since N abrasive grains have excellent heat resistance, their use is rapidly expanding as abrasive grains for dry machining that do not use a coolant.
前記のように、微小な炭素を均一に析出させた鉄基合金
粉末と、砥粒として用いるダイヤモンドおよび／または
ＣＢＮとを均一に混合した混合物を一体に焼結して砥粒
層が形威され、その砥粒層と合金部とを接合してメタル
ボンド工具が製造される。As mentioned above, an abrasive grain layer is formed by sintering a mixture of an iron-based alloy powder in which fine carbon is uniformly precipitated and diamond and/or CBN used as abrasive grains. , a metal bond tool is manufactured by joining the abrasive grain layer and the alloy part.
焼結操作は非酸化性雰囲気中で１０００〜１■８０℃程
度で実施すると良い。焼結温度が１０００℃未満ではＦ
ｅ中にＳｉ，Ｃを拡散させるために長時間を要し、十分
な強度を有する砥粒層が得にくい。一方１１８０℃を超
えると液相を生じ、砥粒との界面反応を生じ、砥粒層の
強度低下を招き易い。The sintering operation is preferably carried out in a non-oxidizing atmosphere at about 1000-180°C. F when the sintering temperature is less than 1000℃
It takes a long time to diffuse Si and C in e, making it difficult to obtain an abrasive grain layer with sufficient strength. On the other hand, if the temperature exceeds 1180°C, a liquid phase is generated, which causes an interfacial reaction with the abrasive grains, which tends to cause a decrease in the strength of the abrasive grain layer.
その点から、加圧焼結を用いると、上記常圧焼結と比較
して、８５０℃以上での低温焼結が可能となり、界面反
応が起こりにくい。さらに焼結体の寸法変化が少なく、
ツルーイングを簡素化できる。From this point of view, when pressure sintering is used, low-temperature sintering at 850° C. or higher is possible, and interfacial reactions are less likely to occur, compared to the above-mentioned normal pressure sintering. Furthermore, there is little dimensional change in the sintered body,
Truing can be simplified.
加圧力は、成形性および焼結時の相互拡散を促進させる
ために５ ０ ｋｇ ／ ｃ／以上に設定される。しか
し加圧焼結を行なう場合においても、焼結温度が８５０
℃未満では鉄基材中に硅素、炭素を拡散させるために長
時間を要し、十分な強度が得にくい。したがって加圧焼
結温度は８５０〜１１８００Ｃの範囲に設定される。The pressing force is set to 50 kg/c/ or more in order to promote formability and mutual diffusion during sintering. However, even when pressure sintering is performed, the sintering temperature is 850°C.
If it is less than 0.degree. C., it takes a long time to diffuse silicon and carbon into the iron base material, making it difficult to obtain sufficient strength. Therefore, the pressure sintering temperature is set in the range of 850 to 11,800C.
このように本発明に係るメタルボンド工具の製造方法に
よれば、マトリックスを形成する鉄基合金粉末を一旦溶
融せしめ、得られた溶湯を粉化すると同時に毎秒１０℃
以上の冷却速度で急速に冷却して鉄基合金粉末を調製し
ている。そのため合金粉末内には微小な炭素の析出物を
均一に分散させることができる。したがってマトリック
スによる砥粒の保持強度の低下がなく、潤滑性も十分に
保持することが可能となり、工具の寿命を著しく延伸す
ることができる。As described above, according to the method for manufacturing a metal bond tool according to the present invention, the iron-based alloy powder forming the matrix is once melted, and the resulting molten metal is pulverized at a rate of 10°C per second.
Iron-based alloy powder is prepared by rapid cooling at the above cooling rate. Therefore, fine carbon precipitates can be uniformly dispersed within the alloy powder. Therefore, there is no reduction in the retention strength of the abrasive grains by the matrix, and it is possible to maintain sufficient lubricity, and the life of the tool can be significantly extended.
また急速冷却後における合金粉末の温度は２００℃以下
に設定されているため、冷却後における合金構成元素の
拡散は少なく、炭素の析出物の粗大化を防止することが
できる。Further, since the temperature of the alloy powder after rapid cooling is set to 200° C. or lower, diffusion of alloy constituent elements after cooling is small, and coarsening of carbon precipitates can be prevented.
またセメンタイトを不安定にして黒鉛の析出物を生じ易
くする硅素を添加することにより、合金粉末中に、より
安定した微細な炭素析出物を均一に形成することが可能
となり、ボンド材の強度および砥粒との界面結合力を向
上させることができる。Additionally, by adding silicon, which destabilizes cementite and makes graphite precipitates more likely to form, it becomes possible to uniformly form more stable and fine carbon precipitates in the alloy powder, increasing the strength of the bond material. The interfacial bonding force with the abrasive grains can be improved.
また、マトリックスを形成する金属粉末と、ダイヤモン
ドおよびＣＢＮの少なくとも一方から成る高硬度の砥粒
とを焼結によって強固に結合して砥粒層を形成している
ため、砥粒の保持力が大きく、良好な研削仕上面が得ら
れるとともに工具の寿命を延伸することができる。なお
砥粒としてダイヤモンドおよびＣＢＮを併用することに
より研削対象範囲を広くすることができる。In addition, the metal powder that forms the matrix and the highly hard abrasive grains made of at least one of diamond and CBN are firmly bonded by sintering to form the abrasive grain layer, so the retention force of the abrasive grains is large. , it is possible to obtain a good ground surface and extend the life of the tool. Note that by using diamond and CBN together as abrasive grains, the range to be ground can be widened.
またマトリックスを形成する鉄基合金粉末の中に予め微
細な炭素析出物が均一に分散されるため、焼結後におい
ても、潤滑材としての炭素粒を、砥粒の周辺に均一に分
散配置することができる。In addition, since fine carbon precipitates are uniformly dispersed in advance in the iron-based alloy powder that forms the matrix, even after sintering, the carbon grains as a lubricant are uniformly distributed around the abrasive grains. be able to.
したがって、研削加工時の潤滑機能が充分に発揮される
とともに、支持材としてのマトリックスの強度が充分確
保され、砥粒の脱落が抑制される結果、常に高い研削効
率を維持できる上に砥粒層の寿命を大幅に延伸させるこ
とができる。Therefore, the lubrication function during grinding is fully demonstrated, the strength of the matrix as a supporting material is ensured sufficiently, and abrasive grains are prevented from falling off. As a result, it is possible to maintain high grinding efficiency at all times, and the abrasive grain layer The lifespan of can be significantly extended.
（実施例）
次に本発明について以下に示す実施例を参照して、より
具体的に説明する。(Examples) Next, the present invention will be described in more detail with reference to the following examples.
実施例１〜３および比較例４〜６
まず実施例１〜３として、鉄基合金を加熱して溶湯を形
成し、この溶湯を溶湯鳴霧装置の噴射ノズルから粉化用
圧縮空気と共に噴出させて粉化すると同時に２００℃ま
で急冷し、第１表に示すように炭素３．０重量％、硅素
１．５重量％、残部鉄から成り、平均粒径が３０μｍの
鉄基合金粉末を得た。このとき冷却速度はそれぞれ１０
，２０，３０°Ｃ／ｓｅｅであった。Examples 1 to 3 and Comparative Examples 4 to 6 First, as Examples 1 to 3, an iron-based alloy was heated to form a molten metal, and this molten metal was jetted together with compressed air for powdering from an injection nozzle of a molten metal spray device. At the same time, the powder was pulverized and rapidly cooled to 200°C to obtain an iron-based alloy powder consisting of 3.0% by weight of carbon, 1.5% by weight of silicon, and the balance iron, with an average particle size of 30 μm, as shown in Table 1. . At this time, the cooling rate is 10
,20,30°C/see.
次に上記溶湯噴霧処理によって得られた鉄基合金粉末８
０重量％に対して平均粒径１００μｍのダイヤモンド砥
粒を２０重量％を均一に混合した。Next, iron-based alloy powder 8 obtained by the above molten metal spraying treatment
20% by weight of diamond abrasive grains having an average particle diameter of 100 μm were uniformly mixed with 0% by weight.
さらに上記組成の混合物を外径８０ｍｍ，内径１５闘の
金型空間に充填し、真空中でホットプレス法により焼結
を行なった。焼結操作は、４００ｋｇ／ｃｔｌの加圧力
を作用させた状態で９００℃に昇温し、３０分間保持し
た後に加工を施し、幅１０ｍｍのダイヤモンド工具を形
成した。Furthermore, a mold space having an outer diameter of 80 mm and an inner diameter of 15 mm was filled with the mixture having the above composition, and sintering was performed in a vacuum by a hot press method. In the sintering operation, the temperature was raised to 900° C. while applying a pressure of 400 kg/ctl, and after holding for 30 minutes, processing was performed to form a diamond tool with a width of 10 mm.
また比較例４． ５． ６として実施例１〜３と同
一の合金組戊を有する原料を使用し、溶湯噴霧装置を運
転し、冷却速度をそれぞれ３°Ｃ／ｓｅｃ，７℃／ ｓ
ｅ ｃに設定し温度２００℃まで急冷したもの（比較
例４，５）および冷却速度２０℃／ｓｅｃで温度３００
℃まで急冷したもの（比較例６）をダイヤモンド砥粒と
混合して焼結後、加工して外径８０鴫、内径１５肺、幅
１０閣のダイヤモンド工具とした。Also, Comparative Example 4. 5. As for 6, raw materials having the same alloy structure as in Examples 1 to 3 were used, the molten metal spraying device was operated, and the cooling rate was set to 3°C/sec and 7°C/s, respectively.
The temperature was rapidly cooled to 200°C at a cooling rate of 20°C/sec (Comparative Examples 4 and 5), and the
The material rapidly cooled to ℃ (Comparative Example 6) was mixed with diamond abrasive grains, sintered, and processed into a diamond tool with an outer diameter of 80 mm, an inner diameter of 15 mm, and a width of 10 mm.
こうして得られた実施例１〜３および比較例４〜６のダ
イヤモンド工具を使用してビッカース硬度工７００のＳ
ｉ３Ｎ４の研削加工を行なった。Using the diamond tools of Examples 1 to 3 and Comparative Examples 4 to 6 thus obtained, Vickers hardness machining of 700 S
Grinding of i3N4 was performed.
研削加工条件は、回転数３００Ｏｒｐｍ，送り速度５ｍ
／ｍｉｎ，研削幅１０ｍｍ，切込み深さは、０．２５ｍ
ｍに設定した。Grinding conditions are rotation speed 300 rpm, feed speed 5 m.
/min, grinding width 10mm, cutting depth 0.25m
It was set to m.
こうして得られた研削試験結果を第ｔ表の実施例１〜３
、比較例４〜６に対応する右欄に示す。The grinding test results obtained in this way are shown in Examples 1 to 3 in Table t.
, shown in the right column corresponding to Comparative Examples 4 to 6.
ここで第↑表に示す研削比は、砥石損耗量に対する被研
削材の除去量の比で表わしている。The grinding ratio shown in Table ↑ is expressed as the ratio of the amount of material removed to the amount of wear on the grinding wheel.
第１表の結果からわかるように溶湯噴霧処理において、
冷却速度を１０℃／ｓｅｃ以上に設定して調製された鉄
基合金粉末中の析出炭素は極めて微細であり、マトリッ
クス中に均一に分散するため、この合金粉末を使用した
実施例１〜３のダイヤモンド砥石は、冷却速度を１０℃
／ｓｅｃ未満で処理した比較例４．５と比べて研削比が
いずれも高く、長寿命を有することがわかる。As can be seen from the results in Table 1, in the molten metal spraying process,
The precipitated carbon in the iron-based alloy powder prepared by setting the cooling rate to 10°C/sec or higher is extremely fine and is uniformly dispersed in the matrix. Diamond whetstone has a cooling rate of 10℃
It can be seen that the grinding ratios are higher in all cases than in Comparative Example 4.5, which was processed at less than /sec, indicating that the grinding ratios are longer.
一方比較例４，５に示す合金粉末は、冷却速度が緩速で
あるため、炭素析出物の粗大化が進み、研削比が低下す
る傾向が観察される。On the other hand, since the alloy powders shown in Comparative Examples 4 and 5 have a slow cooling rate, it is observed that the carbon precipitates tend to become coarser and the grinding ratio decreases.
また比較例６に示すように、冷却速度を２０℃／ｓｅｅ
に設定しても、冷却後の温度を３００℃と高値にした場
合、粉末内部における元素の拡散が冷却後においても進
行し、析出炭素が粗大化するため、研削比がやや低下す
ることがわかる。In addition, as shown in Comparative Example 6, the cooling rate was set to 20°C/see.
It can be seen that even if the temperature after cooling is set to a high value of 300°C, the diffusion of elements inside the powder will continue even after cooling, and the precipitated carbon will become coarser, resulting in a slight decrease in the grinding ratio. .
実施例７〜１０および比較例１１〜１４次に実施例７〜
１０および比較例１１〜１４として、鉄基合金を溶融し
、得られた溶湯を溶湯噴霧装置に供して粉化すると同時
に温度】。８０’Ｃまで急冷した。このときの冷却速度
は２０°（：：／ｓｅＣであった。Examples 7-10 and Comparative Examples 11-14 Next, Examples 7-10
10 and Comparative Examples 11 to 14, an iron-based alloy was melted, and the obtained molten metal was subjected to a molten metal spraying device to be powdered, and at the same time, the temperature was adjusted to 1. It was rapidly cooled to 80'C. The cooling rate at this time was 20° (::/secC).
この溶湯噴霧処理によって第１表左欄に示すような組成
を有する平均粒径が３０μｍの鉄基合金粉末を得た。By this molten metal spraying treatment, an iron-based alloy powder having a composition shown in the left column of Table 1 and having an average particle size of 30 μm was obtained.
次に得られた鉄基合金粉末８０重量％に対して平均粒径
１００μｍのＣＢＮを２０重量％の割合で加え、均一に
混合した混合物を前記実施例１〜３と同様な焼結加工条
件で焼結し、外径８０ｍｍ，内径↓５ｍｍ，幅１０ｍｍ
のＣＢＮ砥石を形成した。Next, 20% by weight of CBN with an average particle size of 100 μm was added to 80% by weight of the obtained iron-based alloy powder, and the uniformly mixed mixture was sintered under the same conditions as in Examples 1 to 3. Sintered, outer diameter 80mm, inner diameter ↓5mm, width 10mm
A CBN grinding wheel was formed.
上記実施例７〜１０および比較例１１〜１４によって得
られたＣＢＮ砥石を使用して、実施例１〜３と同様な加
工条件で超硬合金の研削加工を実施し、研削比を測定し
、炭素および硅素の添加量の大小が研削特性に及ぼす影
響を調査した。研削試験結果は第１表の対応する右欄に
示す。Using the CBN grindstones obtained in Examples 7 to 10 and Comparative Examples 11 to 14, grinding of cemented carbide was carried out under the same processing conditions as in Examples 1 to 3, and the grinding ratio was measured. The influence of the amount of carbon and silicon added on the grinding properties was investigated. The grinding test results are shown in the corresponding right column of Table 1.
第１表に示す結果から理解されるように、ＣＢＮ砥粒を
使用した場合においても、炭素を２．５〜４．５重量％
、硅素を１．０〜３．５重量％の範囲で含有する鉄基合
金粉末を使用した実施例７〜１０の方が、上記範囲を外
れる比較例１１〜１４よりも研削比が優れている。比較
例ｌ１〜１４においては、急速冷却によって鉄基合金粉
末を調整しているため、いずれも合金中の析出炭素の粒
径は微細であるが、炭素または硅素の過不足によってマ
トリックスの強度が低下するため、研削比が低下する傾
向が伺える。As can be understood from the results shown in Table 1, even when CBN abrasive grains are used, the carbon content is 2.5 to 4.5% by weight.
, Examples 7 to 10 using iron-based alloy powder containing silicon in the range of 1.0 to 3.5% by weight have better grinding ratios than Comparative Examples 11 to 14, which are outside the above range. . In Comparative Examples 11 to 14, the iron-based alloy powder was adjusted by rapid cooling, so the particle size of the precipitated carbon in the alloy was fine, but the strength of the matrix decreased due to excess or deficiency of carbon or silicon. Therefore, there is a tendency for the grinding ratio to decrease.
実施例１５および比較例１６
次に実施例１５は、炭素３．６％、硅素１．１％、残部
鉄から成る鉄基合金を加熱溶融し、得られた溶湯を溶湯
噴霧装置に注入し、噴射ノズルから圧縮空気と共に噴出
せしめ、粉化すると同時に冷却速度４０℃／ｓｅｃで１
５０℃まで急速冷却したものである。Example 15 and Comparative Example 16 Next, in Example 15, an iron-based alloy consisting of 3.6% carbon, 1.1% silicon, and the balance iron was heated and melted, and the resulting molten metal was injected into a molten metal spraying device. It is ejected from the injection nozzle together with compressed air, and at the same time it is pulverized and cooled at a cooling rate of 40°C/sec.
It was rapidly cooled to 50°C.
得られた鉄基合金粉末は第１表に示すように炭素３．５
％、硅素１．０％、残部鉄から成り、平均粒径が２８μ
ｍであった。The obtained iron-based alloy powder has carbon 3.5 as shown in Table 1.
%, silicon 1.0%, balance iron, average grain size 28μ
It was m.
こうして得られた鉄基合金粉末７５重量％に対して、砥
粒としてダイヤモンド砥粒（平均粒径１００μｍ）およ
びＣＢＮ砥粒（平均粒径１００μｍ）を重量比で９＝１
の割合、すなわち２２．５重量％、２．５重量％ずつ混
合し、得られた混合粉末を実施例１〜３と同様な焼結加
工を施して、ダイヤモンドＣＢＮ複合砥石を形成したも
のである。Diamond abrasive grains (average particle size 100 μm) and CBN abrasive grains (average particle size 100 μm) were added as abrasive grains at a weight ratio of 9=1 to 75% by weight of the thus obtained iron-based alloy powder.
The proportions of 22.5% by weight and 2.5% by weight were mixed, and the obtained mixed powder was subjected to the same sintering process as in Examples 1 to 3 to form a diamond CBN composite grindstone. .
また比較例１６は実施例１５で得た鉄基合金粉末と同様
の組成を有する鋳造材をスタンプ法によって２８μｍま
で粉砕して得た合金粉末を使用し、同様な焼結体組成、
焼結条件でダイヤモンドＣＢＮ複合砥石を形成した。In Comparative Example 16, an alloy powder obtained by crushing a cast material having the same composition as the iron-based alloy powder obtained in Example 15 to 28 μm by a stamping method was used, and a similar sintered body composition,
A diamond CBN composite grindstone was formed under sintering conditions.
実施例１５および比較例１６で得られたダイヤモンドＣ
ＢＮ複合砥石を使用して、実施例１〜３と同様な加工条
件でＳｉ３Ｎ４の研削加工試験を実施したところ下記第
１表の右欄に示す結果を得た。Diamond C obtained in Example 15 and Comparative Example 16
When a Si3N4 grinding test was carried out using a BN composite grindstone under the same processing conditions as in Examples 1 to 3, the results shown in the right column of Table 1 below were obtained.
第ｌ表の結果からわかるようにダイヤモンド砥粒とＣＢ
Ｎ砥粒との混合砥粒を使用した場合においても、溶湯噴
霧法によって形成した鉄基合金粉末を使用した実施例１
５の工具は合金中の析出炭素の粒径が微細である。した
がって研削面粗さは小さく、良好な加工仕上げを行なう
ことが可能であり、特に高い研削比を確保することがで
きる。As can be seen from the results in Table I, diamond abrasive grains and CB
Example 1 using iron-based alloy powder formed by molten metal spraying even when mixed abrasive grains with N abrasive grains are used
In tool No. 5, the grain size of precipitated carbon in the alloy is fine. Therefore, the roughness of the ground surface is small, it is possible to perform a good finish, and it is possible to ensure a particularly high grinding ratio.
一方実施例１５と同一の組成を有する合金，粉末であっ
ても、従来法による鋳造材をスタンプ法で粉砕して得た
鉄基合金粉末を使用した比較例１６においては、冷却速
度が遅いため、炭素粒径が粗大になり、充分な研削比が
得られないことがわかる。On the other hand, even though the alloy and powder have the same composition as Example 15, the cooling rate was slow in Comparative Example 16, which used iron-based alloy powder obtained by crushing a conventionally cast material by stamping. It can be seen that the carbon particle size becomes coarse and a sufficient grinding ratio cannot be obtained.
以上説明の通り本発明に係るメタルボンドエ具の製造方
法によれば、マトリックスを形成する鉄基合金粉末を一
旦溶融せしめ、得られた溶湯を粉化すると同時に毎秒１
０℃以上の冷却速度で急速に冷却して鉄基合金粉末を調
製している。そのため合金粉末内には微小な炭素の析出
物を均一に分散させることができる。したがってマトリ
ックスによる砥粒の保持強度の低下がなく、潤滑性も十
分に保持することが可能となり、研削比が大きく工具の
寿命を著しく延伸することができる。As explained above, according to the method for manufacturing a metal bonded tool according to the present invention, the iron-based alloy powder forming the matrix is once melted, and the resulting molten metal is powdered and at the same time
Iron-based alloy powder is prepared by rapid cooling at a cooling rate of 0° C. or higher. Therefore, fine carbon precipitates can be uniformly dispersed within the alloy powder. Therefore, there is no reduction in the retention strength of the abrasive grains due to the matrix, it is possible to maintain sufficient lubricity, and the grinding ratio is large, making it possible to significantly extend the life of the tool.
また急速冷却後における合金粉末の温度は２００℃以下
に設定されているため、冷却後における合金構成元素の
拡散は少なく、炭素の析出物の粗大化を防止することが
できる。Further, since the temperature of the alloy powder after rapid cooling is set to 200° C. or lower, diffusion of alloy constituent elements after cooling is small, and coarsening of carbon precipitates can be prevented.
さらにセメンタイトを不安定にして黒鉛の析出物を生じ
易くする硅素を添加することにより、合金粉末中に、よ
り安定した微細な炭素析出物を均一に形成することが可
能となり、ボンド材の強度および砥粒との界面結合力を
向上させることができる。Furthermore, by adding silicon, which destabilizes cementite and facilitates the formation of graphite precipitates, it becomes possible to uniformly form more stable and fine carbon precipitates in the alloy powder, improving the strength of the bond material. The interfacial bonding force with the abrasive grains can be improved.
また、マトリックスを形威する金属粉末と、ダイヤモン
ドおよびＣＢＮの少なくとも一方から成る高硬度の砥粒
とを焼結によって強固に結合して砥粒層を形成している
ため、砥粒の保持力が大きく、良好な研削仕上面が得ら
れるとともに工具の寿命を延伸することができる。なお
砥粒としてダイヤモンドおよびＣＢＮを併用することに
より研削対象範囲を広くすることができる。In addition, since the abrasive layer is formed by firmly bonding the metal powder that forms the matrix and the highly hard abrasive grains made of at least one of diamond and CBN through sintering, the retention force of the abrasive grains is increased. A large and good ground surface can be obtained, and the life of the tool can be extended. Note that by using diamond and CBN together as abrasive grains, the range to be ground can be widened.
またマトリックスを形成する鉄基合金粉末中に予め微細
な炭素析出物が均一に分散されるため、焼結後において
も、潤滑材としての炭素粒を、砥粒の周辺に均一に分散
配置することができる。In addition, since fine carbon precipitates are uniformly dispersed in advance in the iron-based alloy powder that forms the matrix, even after sintering, the carbon grains as a lubricant can be uniformly distributed around the abrasive grains. I can do it.
したがって、研削加工時の潤滑機能が充分に発揮される
とともに、支持材としてのマトリックスの強度が充分確
保され、砥粒の脱落が抑制される結果、研削比が従来の
ものと比較して格段に増大化するため砥粒層の寿命を大
幅に延伸させることができる。Therefore, the lubrication function during grinding is fully demonstrated, the strength of the matrix as a support material is ensured, and the falling off of abrasive grains is suppressed, resulting in a significantly higher grinding ratio compared to conventional methods. Because of this increase, the life of the abrasive layer can be significantly extended.
Claims (1)
成る砥粒層を備えたメタルボンド工具の製造方法におい
て、鉄基合金を溶融し、得られた溶湯を粉化すると同時
に毎秒１０℃以上の冷却速度で２００℃以下の温度まで
冷却し、しかる後に得られた鉄基合金粉末と砥粒との混
合物を一体に焼結して砥粒層を形成することを特徴とす
るメタルボンド工具の製造方法。 ２、鉄基合金粉末中の硅素含有量（Ａ重量％）炭素含有
量（Ｂ重量％）としたとき、 ２．５≦Ｂ≦４．５ ３≦Ｂ＋Ａ／３≦５ の関係を満たすことを特徴とする請求項１記載のメタル
ボンド工具の製造方法。 ３、砥粒としてダイヤモンドおよび立方晶窒化硼素の少
なくとも一種を用いることを特徴とする請求項１記載の
メタルボンド工具の製造方法。[Claims] 1. In a method for manufacturing a metal bond tool having an abrasive grain layer made of a sintered body of carbon-containing iron-based alloy powder and abrasive grains, At the same time as the molten metal is powdered, it is cooled to a temperature of 200°C or less at a cooling rate of 10°C or more per second, and then the resulting mixture of iron-based alloy powder and abrasive grains is sintered together to form an abrasive grain layer. A method for manufacturing a metal bond tool, characterized by: 2. When silicon content (A weight %) and carbon content (B weight %) in iron-based alloy powder, satisfy the following relationships: 2.5≦B≦4.5 3≦B+A/3≦5 The method for manufacturing a metal bond tool according to claim 1. 3. The method for manufacturing a metal bond tool according to claim 1, wherein at least one of diamond and cubic boron nitride is used as the abrasive grain.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23299589A JPH0398765A (en) | 1989-09-11 | 1989-09-11 | Manufacture of metal bonded tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23299589A JPH0398765A (en) | 1989-09-11 | 1989-09-11 | Manufacture of metal bonded tool |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0398765A true JPH0398765A (en) | 1991-04-24 |
Family
ID=16948153
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23299589A Pending JPH0398765A (en) | 1989-09-11 | 1989-09-11 | Manufacture of metal bonded tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0398765A (en) |
-
1989
- 1989-09-11 JP JP23299589A patent/JPH0398765A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US8882868B2 (en) | Abrasive slicing tool for electronics industry | |
| KR100224290B1 (en) | Metal bonded, metal abrasive articles, and grinding method | |
| JP5226522B2 (en) | Cubic boron nitride compact | |
| CN107739950A (en) | A kind of WC Co cBN composite hard alloys and preparation method thereof | |
| US6617271B1 (en) | Tungsten carbide cutting tool materials | |
| CN107531578B (en) | Polycrystalline abrasive structure | |
| US4832707A (en) | Metal-bonded tool and method of manufacturing same | |
| JPH0398765A (en) | Manufacture of metal bonded tool | |
| JP3513547B2 (en) | Grinding stone for polishing single crystal diamond or diamond sintered body and polishing method thereof | |
| CN113319742A (en) | Preparation method of abrasive with grinding and polishing functions | |
| JPH04152068A (en) | Metal bond tool and manufacture thereof | |
| JPH0398766A (en) | Manufacture of metal bonded tool | |
| JPH04152069A (en) | Metal bond tool and manufacture thereof | |
| JPS6158432B2 (en) | ||
| JPH0543463B2 (en) | ||
| JPH03149186A (en) | Metal bond tool | |
| JPH04152066A (en) | Metal bond tool | |
| JPH0224061A (en) | Polishing molded body and manufacture thereof | |
| JP2004107154A (en) | Tool material and tool for cutting | |
| SU1722803A1 (en) | Abrasive body for manufacturing tools | |
| JPH0398768A (en) | Manufacture of metal bonded tool | |
| JPH0398767A (en) | Manufacture of metal bonded tool | |
| KR810001998B1 (en) | Method producing a sintered diamond compact | |
| JPS6038458B2 (en) | Ceramic sintered body for cutting tools | |
| JPS62264868A (en) | Metal bonded grinding stone |