JPH0398768A - Manufacture of metal bonded tool - Google Patents
Manufacture of metal bonded toolInfo
- Publication number
- JPH0398768A JPH0398768A JP23299889A JP23299889A JPH0398768A JP H0398768 A JPH0398768 A JP H0398768A JP 23299889 A JP23299889 A JP 23299889A JP 23299889 A JP23299889 A JP 23299889A JP H0398768 A JPH0398768 A JP H0398768A
- Authority
- JP
- Japan
- Prior art keywords
- alloy powder
- abrasive grains
- grinding
- abrasive grain
- sintering
- 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 39
- 239000002184 metal Substances 0.000 title claims abstract description 37
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 239000000843 powder Substances 0.000 claims abstract description 71
- 239000006061 abrasive grain Substances 0.000 claims abstract description 68
- 239000000956 alloy Substances 0.000 claims abstract description 63
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 57
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 52
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 24
- 229910052742 iron Inorganic materials 0.000 claims abstract description 24
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 23
- 238000000034 method Methods 0.000 claims abstract description 18
- 239000012298 atmosphere Substances 0.000 claims abstract description 14
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 9
- 239000001301 oxygen Substances 0.000 claims abstract description 9
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 9
- 239000002994 raw material Substances 0.000 claims abstract description 9
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims abstract description 5
- 229910003460 diamond Inorganic materials 0.000 claims description 28
- 239000010432 diamond Substances 0.000 claims description 28
- 239000002245 particle Substances 0.000 claims description 27
- 239000011261 inert gas Substances 0.000 claims description 6
- 230000006835 compression Effects 0.000 claims description 4
- 238000007906 compression Methods 0.000 claims description 4
- 229910052582 BN Inorganic materials 0.000 claims description 3
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 3
- 238000005245 sintering Methods 0.000 abstract description 30
- 239000011159 matrix material Substances 0.000 abstract description 29
- 239000007789 gas Substances 0.000 abstract description 6
- 230000001590 oxidative effect Effects 0.000 abstract description 4
- 238000000227 grinding Methods 0.000 description 42
- 230000000052 comparative effect Effects 0.000 description 17
- 238000005261 decarburization Methods 0.000 description 13
- 239000010410 layer Substances 0.000 description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 10
- 230000007423 decrease Effects 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000005507 spraying Methods 0.000 description 7
- 238000005452 bending Methods 0.000 description 6
- 239000000314 lubricant Substances 0.000 description 6
- 229910052786 argon Inorganic materials 0.000 description 5
- 238000010298 pulverizing process Methods 0.000 description 4
- 239000002131 composite material Substances 0.000 description 3
- 238000005461 lubrication Methods 0.000 description 3
- 230000014759 maintenance of location Effects 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- MYMOFIZGZYHOMD-UHFFFAOYSA-N Dioxygen Chemical compound O=O MYMOFIZGZYHOMD-UHFFFAOYSA-N 0.000 description 2
- 229910052581 Si3N4 Inorganic materials 0.000 description 2
- 125000004429 atom Chemical group 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910001882 dioxygen Inorganic materials 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 1
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 239000004215 Carbon black (E152) Substances 0.000 description 1
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229930195733 hydrocarbon Natural products 0.000 description 1
- 150000002430 hydrocarbons Chemical class 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 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
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000001172 regenerating effect Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 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
- 239000000758 substrate Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- -1 vacuum Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052725 zinc Inorganic materials 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
粒との焼結体から或る砥粒層を有するメタルボンド工具
の製造方法に係り、特に焼結性を改善し、焼結時間を短
縮して製造効率を高めるとともに、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 Field of Application) The present invention is directed to an abrasive grain layer formed from a sintered body of a carbon-containing iron-based alloy and abrasive grains having high hardness. This invention relates to a method for manufacturing metal bond tools, and in particular, to a method for manufacturing metal bond tools that improves sinterability, shortens sintering time, increases manufacturing efficiency, and improves matrix strength to increase service life. .
（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ボンドダイヤモンド工具が、従
来より広く用いられている。(Conventional technology) Metal-bonded diamond tools that use diamond as 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、アルゴンなどの不活性ガスによる保護
雰囲気において温度８００〜９００℃、圧力２００〜４
００ｋｇ／ｃａｒ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 temperature is 800-900℃ and the pressure is 200-4℃ in a protected atmosphere with an inert gas such as argon.
Hot press is carried out under conditions of about 00kg/car,
Forms an abrasive grain 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、従来のメタルボンド工具の製造方法にお
いては、潤滑材としての炭素を多量に含有した鉄基合金
粉末を原料として使用しているため、焼結性が低いとい
う問題点がある。(Problem to be solved by the invention) However, in the conventional manufacturing method of metal bond tools, iron-based alloy powder containing a large amount of carbon as a lubricant is used as a raw material, so sinterability is low. There is a problem.
すなわち、鉄基合金粉末の表面に多量の炭素粒が析出し
ており、この合金粉末を圧縮成形して焼成する場合、接
触した合金粉末の金属原子の相互拡散が炭素粒によって
阻害されるため焼結が充分に進行しにくい。そのためマ
トリックスの強度が低下し、砥粒および炭素粒の脱落が
多くなり、潤滑機能および研削機能が低下し工具の寿命
が短くなってしまう。In other words, a large amount of carbon grains are precipitated on the surface of the iron-based alloy powder, and when this alloy powder is compression molded and fired, the carbon grains inhibit the interdiffusion of the metal atoms in the alloy powder that come into contact with it. It is difficult for the knot to progress sufficiently. As a result, the strength of the matrix decreases, more abrasive grains and carbon grains fall off, the lubrication function and grinding function deteriorate, and the life of the tool is shortened.
またマトリックスの強度を高くするためには、長時間に
亘る焼結操作が必要となり、メタルボンド工具の生産効
率が低くなる欠点があった。Furthermore, in order to increase the strength of the matrix, a long sintering operation is required, which has the disadvantage of lowering the production efficiency of metal bond tools.
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、合金粉末の焼結性を改善し、焼結時間を短縮して
生産効率を高めるとともに、マトリックスの強度を高く
保持し工具の寿命の延伸を図ることができるメタルボン
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 problems, and it improves the sinterability of alloy powder, shortens the sintering time, increases production efficiency, and maintains high matrix strength to improve tool performance. It is an object of the present invention to provide a method for manufacturing a metal bond tool that can extend its life.
（課題を解決するための手段と作用）
本願発明者等は以上の観点から、焼結性の低下の要因と
なる、合金粉末表面部に析出する炭素粒を低減するため
に種々の処理方法を試行し、またマトリックスの強度を
増加させるために、合金粉末の粒径、砥粒の種類および
粒径との相関関係を調査して種々の砥粒層を形成し、焼
結に要する時間および工具の研磨特性を測定した。(Means and effects for solving the problem) From the above viewpoint, the inventors of the present application have developed various processing methods to reduce the carbon grains precipitated on the surface of the alloy powder, which causes a decrease in sinterability. In order to increase the strength of the matrix, we investigated the correlation between the grain size of the alloy powder, the type of abrasive grains, and the grain size to form various abrasive grain layers, and the time required for sintering and the tooling. The polishing properties were measured.
その結果、酸素を含む不活性ガス雰囲気中で原料となる
鉄基合金粉末を、加熱し、合金粉末表面を脱炭処理した
後に、処理した合金粉末と砥粒との混合物を圧縮成形し
一体に焼結して砥粒層を形成したときに、極めて焼結性
に優れ、また寿命の長いメタルボンド工具を得ることが
できた。As a result, the raw material iron-based alloy powder is heated in an inert gas atmosphere containing oxygen, the surface of the alloy powder is decarburized, and the mixture of the treated alloy powder and abrasive grains is compression molded and integrated. When an abrasive layer was formed by sintering, a metal bond tool with extremely excellent sinterability and a long life could be obtained.
また、砥粒としてダイヤモンドおよび立方晶窒素化硼素
の少なくとも１種を用い、さらにマトリックスとなる合
金粉末の焼結前の平均粒径を、砥粒の平均粒径の１／３
以下に調整したときに、砥粒および潤滑材としての析出
炭素粒の脱落が効果的に抑制され、寿命の長い砥粒層を
得ることができた。In addition, at least one of diamond and cubic boron nitride is used as the abrasive grains, and the average grain size of the alloy powder serving as the matrix before sintering is set to 1/3 of the average grain size of the abrasive grains.
When the following adjustment was made, the falling off of the abrasive grains and the precipitated carbon grains as a lubricant was effectively suppressed, and an abrasive grain layer with a long life could be obtained.
本発明は上記の知見に基づいてなされたものである。The present invention has been made based on the above findings.
本発明に係るメタルボンド工具のマトリックス用に使用
する合金粉末としては、Ｆｅを基質金属とし、さらにＮ
ｉ， Ｃｏ， Ｃｕ， Ｚｎ， Ｍｇ，ＡＩｌ，Ｍｎ
，Ｃｒなとの金属元素を所要量添加した鉄基合金粉末が
使用される。特にＮｉ，Ｃｏは焼結を促進する作用およ
びマトリックス中に潤滑材として有用な微細な炭素粒を
析出する作用を有するために１〜１０％程度添加される
。原料となる合金粉末の組成は、必要とされるマトリッ
クスの強度、伝熱性、加工対象の種類等を勘案して決定
されるが、一般に砥粒の保持強度を高くするために、上
記金属元素を添加した鉄基合金材が使用される。The alloy powder used for the matrix of the metal bond tool according to the present invention uses Fe as the substrate metal and further N.
i, Co, Cu, Zn, Mg, Al, Mn
An iron-based alloy powder to which required amounts of metal elements such as , Cr, etc. are added is used. In particular, Ni and Co are added in an amount of about 1 to 10% because they have the effect of promoting sintering and the effect of precipitating fine carbon grains useful as a lubricant in the matrix. The composition of the alloy powder used as the raw material is determined by taking into consideration the required matrix strength, heat conductivity, type of workpiece, etc., but generally the above metal elements are added to increase the retention strength of the abrasive grains. Added iron-based alloy materials are used.
鉄基合金材の炭素含有量は、２．５〜４．５重量％の範
囲に設定することが望ましい。炭素含有量が２．５％未
満では、研削加工時の潤滑作用が低下するとともに、マ
トリックス金属としての強度が小さくなるためである。The carbon content of the iron-based alloy material is desirably set in the range of 2.5 to 4.5% by weight. This is because if the carbon content is less than 2.5%, the lubricating effect during grinding will decrease and the strength as a matrix metal will decrease.
一方、４．５％を超えるとマトリックス金属としての耐
衝撃性が低下し、工具としての強度が低下するため上記
範囲に設定される。On the other hand, if it exceeds 4.5%, the impact resistance as a matrix metal decreases and the strength as a tool decreases, so it is set within the above range.
合金材を粉末化する手段としては、例えば合金材の鋳塊
片をボールミル、スタンプミルによって粉砕する方法や
合金材を溶湯噴霧法等の急冷法を使用して微細化する方
法がある。Examples of means for pulverizing the alloy material include a method of pulverizing an ingot of the alloy material using a ball mill or a stamp mill, and a method of pulverizing the alloy material using a rapid cooling method such as a molten metal spraying method.
上記溶湯噴霧法は、原料の溶湯をガス噴霧、水噴霧、遠
心噴霧によって粉体化する方法であり、噴霧条件により
適当な冷却速度と粉末粒径になるように調整して所望の
原料粉末を得る方法である。The above-mentioned molten metal spraying method is a method in which molten raw material is pulverized by gas spraying, water spraying, or centrifugal spraying, and the desired raw material powder is produced by adjusting the cooling rate and powder particle size to an appropriate level according to the spraying conditions. This is the way to get it.
次に上記のようにして調製された鉄基合金粉末は、酸素
を含有した不活性ガス雰囲気中で加熱され、合金粉末表
面が脱炭処理される。この脱炭処理は、アルゴンなどの
不活性ガスまたは窒素ガスに酸素ガスを混入させて酸化
性雰囲気を形成し、この雰囲気中で合金粉末を７００〜
９００℃に加熱して行なう。Next, the iron-based alloy powder prepared as described above is heated in an oxygen-containing inert gas atmosphere to decarburize the surface of the alloy powder. In this decarburization process, an oxidizing atmosphere is formed by mixing oxygen gas with an inert gas such as argon or nitrogen gas, and in this atmosphere, the alloy powder is
This is done by heating to 900°C.
この加熱処理によって合金粉末表面部に析出した炭素粒
は酸素によって酸化され、炭酸ガスとなって放逐される
。そのため合金粉末表面には中心部と比較して炭素分が
少ないフエライト層が形或される。Through this heat treatment, the carbon grains deposited on the surface of the alloy powder are oxidized by oxygen and are emitted as carbon dioxide gas. Therefore, a ferrite layer containing less carbon than the center portion is formed on the surface of the alloy powder.
ここで雰囲気中の酸素ガス濃度は０．１〜２ｖａ ｌ，
％に設定される。濃度がＱ， ｌｙｏｌ、％未満の場
合は脱炭効果が少なく、一方２ｖｏｌ．％を超える場合
は合金粉末の深部まで酸化が進行し、マトリックスの強
度が急激に低下するためである。Here, the oxygen gas concentration in the atmosphere is 0.1 to 2 val,
Set to %. When the concentration is less than Q, lyol,%, the decarburization effect is small; on the other hand, when the concentration is less than 2vol. %, oxidation progresses deep into the alloy powder and the strength of the matrix decreases rapidly.
次に脱炭処理された合金粉末は、砥粒と均一に混合され
た後に、圧縮成形され、真空、アルゴンなどの不活性ガ
ス、水素・分解アンモニアガス・変成炭化水素ガスなど
の保護雰囲気において一体に焼結されて砥粒層を形威す
る。脱炭処理された合金粉末の表層部には析出炭素粒が
少ないため、焼結時における金属原子の相互拡散が円滑
に進行し、短時間内に焼結が完結し、真密度に近い焼結
体を形成することができる。Next, the decarburized alloy powder is uniformly mixed with abrasive grains, and then compression molded and integrated in a protective atmosphere such as vacuum, inert gas such as argon, hydrogen, decomposed ammonia gas, modified hydrocarbon gas, etc. It is sintered to form an abrasive grain layer. Since there are few precipitated carbon particles in the surface layer of the decarburized alloy powder, mutual diffusion of metal atoms during sintering progresses smoothly, sintering is completed within a short time, and sintering close to true density is achieved. can form a body.
この場合、焼結操作前の金属粉末の平均粒径は砥粒の平
均粒径の１／３以下に設定することが好ましい。これは
粒径比が１７３を超えると、砥粒の分布が不均一となり
、砥粒の表面近傍に金属粉を均一に配置することが不可
能であり、砥粒同士が接する部分が増大し、成形性を劣
化させるばかりでなく、研削中の砥粒の脱落を招き、工
具としての研削・研磨能力が低下するためである。In this case, it is preferable that the average particle size of the metal powder before the sintering operation is set to 1/3 or less of the average particle size of the abrasive grains. This is because when the particle size ratio exceeds 173, the distribution of the abrasive grains becomes uneven, making it impossible to uniformly arrange the metal powder near the surface of the abrasive grains, and the area where the abrasive grains come into contact with each other increases. This is because not only the formability is deteriorated, but also the abrasive grains fall off during grinding, and the grinding/polishing ability of the tool is reduced.
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、８５００．５１００ｋｇ／
ｓ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ＣＢＮ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 8500.5100kg/
All have extremely high hardness of s or more, and are useful as abrasive grains for processing difficult-to-grind materials. In particular, CBN abrasive grains have excellent heat resistance, so their use as abrasive grains for dry machining without using a coolant is rapidly expanding.
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、予め
酸化性雰囲気で加熱し、合金粉末表面を脱炭処理してお
り、粉末表面のＦｅ分を相対的に高めているため、焼結
性が極めて優れている。すなわち、短時間で焼結が完結
するのでメタルボンド工具の生産効率を大幅に改善する
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 heated in advance in an oxidizing atmosphere to decarburize the alloy powder surface. Since the content is relatively high, the sinterability is extremely excellent. That is, since sintering is completed in a short time, the production efficiency of metal bond tools can be greatly 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拉層を形成している
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。In addition, since the abrasive layer is formed by firmly bonding the metal powder that forms the matrix and the high-hardness abrasive grains made of at least one of diamond and CBN through sintering, 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.
またマトリックスを形或する鉄基合金粉末の平均粒径を
、砥粒の平均粒径に対して１／３以下に調整しているた
め、潤滑材としての炭素粒および砥粒の支持材となる鉄
基合金粉末を、砥粒の周辺に均一に分散配置することが
できる。In addition, the average particle size of the iron-based alloy powder that forms the matrix is adjusted to 1/3 or less of the average particle size of the abrasive grains, so it serves as a support material for the carbon grains and abrasive grains as a lubricant. The iron-based alloy powder can be uniformly distributed around the abrasive grains.
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
実施例１〜３として、第１表に示すように炭素３．０％
、Ｓｉ１％、残部Ｆｅから成り、平均粒径が１５μｍで
ある鉄基合金粉末を溶湯噴霧法によって調製した。さら
に得られた合金粉末を、酸素濃度をそれぞれ０． １
， ０． ５． １． ５▼ｏｆ．％含有した
アルゴンガス雰囲気に置き、温度７００℃で１０分間加
熱して脱炭処理を実施した。Examples 1 to 3 and Comparative Examples 4 to 6 As Examples 1 to 3, as shown in Table 1, 3.0% carbon
An iron-based alloy powder consisting of 1% Si and the balance Fe and having an average particle size of 15 μm was prepared by a molten metal spraying method. Furthermore, the obtained alloy powder was adjusted to an oxygen concentration of 0. 1
, 0. 5. 1. 5▼of. % in an argon gas atmosphere, and was heated at a temperature of 700° C. for 10 minutes to carry out decarburization treatment.
次に脱炭処理した鉄基合金粉末８０％に対して、第１表
に示すように、平均粒径５０μｍで鋭いプロッキーな稜
線形状を有するダイヤモンド粉末を２０％を均一に混合
した。Next, to 80% of the decarburized iron-based alloy powder, 20% of diamond powder having an average particle size of 50 μm and a sharp proky ridgeline shape as shown in Table 1 was uniformly mixed.
次に上記組戊の混合物を外径８０ｍｍ，内径１５■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、３００ｋｇ／ｃｒｒｒの加圧力
を作用させた状態で９００℃に昇温し、１５分間保持し
た後に加工を施し、幅１０ｍｍのダイヤモンド砥石を形
成した。Next, the mixture of the above molds was filled into a mold space having an outer diameter of 80 mm and an inner diameter of 15 cm, and sintering was carried out in a vacuum by a hot press method. In the sintering operation, the temperature was raised to 900° C. while applying a pressure of 300 kg/crrr, held for 15 minutes, and then processed to form a diamond grindstone 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
金組成を有する原料で、脱炭処理を行なわない合金粉末
８０重量％に対して、ダイヤモンド砥粒２０重量％を混
合したものについて、温度９００℃においてそれぞれ１
５分、３０分、６０分焼結した後に加工を施し、外径８
０ｍｍ，内径１５閣、幅１０ｍｍのダイヤモンド砥石と
した。In addition, as Comparative Examples 4 and 5.6, 20% by weight of diamond abrasive grains were mixed with 80% by weight of alloy powder that was not subjected to decarburization using raw materials having the same alloy composition as Examples 1 to 3. 1 at a temperature of 900°C.
After sintering for 5 minutes, 30 minutes, and 60 minutes, it is processed to an outer diameter of 8.
A diamond whetstone with a diameter of 0 mm, an inner diameter of 15 mm, and a width of 10 mm was used.
こうして得られた実施例１〜３および比較例４〜６のダ
イヤモンド砥石の抗折強度を測定するとともに各ダイヤ
モンド砥石を使用してビッカース硬度１７００のＳｉ３
Ｎ４の研削加工を行なった。研削加工条件は、回転数３
００Ｏｒｐｍ，送り速度５ｍ／ｍｉｎ，研削幅１０ｍｍ
，切込み深さは、０．２５ｍに設定した。The bending strength of the diamond grinding wheels of Examples 1 to 3 and Comparative Examples 4 to 6 thus obtained was measured, and each diamond grinding wheel was used to measure Si3 with a Vickers hardness of 1700.
N4 grinding was performed. The grinding conditions are rotation speed 3.
00Orpm, feed speed 5m/min, grinding width 10mm
The cutting depth was set to 0.25 m.
こうして得られた試験結果を第１表の実施例１〜３、比
較例４〜６に対応する右欄に示す。ここで第１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 test results thus obtained are shown in the right column corresponding to Examples 1 to 3 and Comparative Examples 4 to 6 in Table 1. The grinding ratio shown in Table 1 is expressed as the ratio of the amount of material to be ground removed to the amount of wear on the grinding wheel.
第１表の結果からわかるように脱炭処理を実施した合金
粉末を使用した実施例１〜３のダイヤモンド砥石は、脱
炭処理を実施しない比較例４と比べて抗折強度が大きく
、焼結性が極めて良好になり、また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, the diamond grinding wheels of Examples 1 to 3, which used alloy powders that were decarburized, had higher bending strength than Comparative Example 4, which did not undergo decarburization. It can be seen that the grinding ratio is extremely good, the grinding ratio is high in all cases, and the product has a long life.
また比較例５，６に示すように、焼結を長時間実施すれ
ば、研削比をある程度高めることは可能であるが、製造
効率が大幅に低下してしまう問題点がある。また長時間
にわたり焼結するとマトリックス金属組織の粗大化を招
き、研削比が逆に低下する場合がある。Further, as shown in Comparative Examples 5 and 6, if sintering is carried out for a long time, it is possible to increase the grinding ratio to some extent, but there is a problem in that the manufacturing efficiency is significantly reduced. Moreover, if sintered for a long time, the matrix metal structure may become coarser, and the grinding ratio may decrease.
また脱炭処理時の酸素濃度は、実施例の範囲０．ｌ〜２
％においては、合金粉末表面の性状および研削特性に及
ぼす影響も少ない。In addition, the oxygen concentration during decarburization was within the range of 0. l~2
%, there is little effect on the surface properties and grinding characteristics of the alloy powder.
実施例７および比較例８〜９
次に実施例７として、炭素２．５％、Ｎｉｌ．０％、Ｃ
ｏ０．５％、残部鉄から戊り、平均粒径が２５μｍの合
金粉末を、酸素を０． ２ｖｏｌ，含有するアルゴン
雰囲気中で温度９００℃に昇熱して１０分間保持し脱炭
処理を行なった。処理した合金粉末８０重量％に対して
平均粒径８８μｍ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
結温度条件で２０分間焼結し、外径８０ｍｍ，内径１５
ｍｍ，幅１０ｍｍのＣＢＮ砥石を形成した。Example 7 and Comparative Examples 8 to 9 Next, as Example 7, carbon 2.5%, Nil. 0%, C
0.5%, the balance was removed from iron, and alloy powder with an average particle size of 25 μm was mixed with 0.5% oxygen. The temperature was raised to 900° C. and held for 10 minutes in an argon atmosphere containing 2 vol to perform decarburization treatment. CBN with an average particle size of 88 μm was added at a ratio of 20% by weight to 80% by weight of the treated alloy powder,
The homogeneously mixed mixture was sintered for 20 minutes under the same sintering temperature conditions as in Examples 1 to 3, and the outer diameter was 80 mm and the inner diameter was 15 mm.
A CBN grindstone with a width of 10 mm and a width of 10 mm was formed.
また比較例８として実施例７における脱炭処理を行なわ
ず、また焼結時間を６０分とした焼結体でＣＢＮ砥石を
製造した。さらに比較例９として脱炭処理を行なわずに
、実施例７と同一条件で焼結加工して同一形状のＣＢＮ
砥石を形成した。Further, as Comparative Example 8, a CBN grindstone was manufactured using a sintered body in which the decarburization treatment in Example 7 was not performed and the sintering time was 60 minutes. Furthermore, as Comparative Example 9, CBN of the same shape was sintered under the same conditions as Example 7 without performing decarburization treatment.
A grindstone was formed.
上記実施例７および比較例８〜９のＣＢＮ砥石の抗折強
度を測定するとともに、各ＣＢＮ砥石を使用して、実施
例１〜３と同様の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、焼結時間の長短および脱炭処理の
有無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。The bending strength of the CBN grinding wheels of Example 7 and Comparative Examples 8 to 9 was measured, and cemented carbide was ground using each CBN grinding wheel under the same processing conditions as Examples 1 to 3. We measured the grinding ratio and investigated the effects of sintering time and the presence or absence of decarburization on the grinding characteristics. The grinding test results are shown in the corresponding right column of Table 1.
第１表の結果から理解されるように、実施例７と比較例
８とを比較すると、脱炭処理を行なった実施例７では焼
結性が良好であり高い抗折強度および研削比が得られ、
焼結時間も、比較例８と比べ大幅に短縮することができ
る。As can be understood from the results in Table 1, when comparing Example 7 and Comparative Example 8, Example 7, which was subjected to decarburization, had good sinterability and a high flexural strength and grinding ratio. is,
The sintering time can also be significantly shortened compared to Comparative Example 8.
一方比較例９のように脱炭処理を行なわずに実施例７と
同一の焼結時間で焼結を行なった場合は焼結が充分進行
しないため、マトリックスの強度が充分得られず、抗折
強度および研削比が小さくなっている。On the other hand, when sintering was carried out for the same sintering time as in Example 7 without decarburization as in Comparative Example 9, sintering did not proceed sufficiently, and the matrix did not have sufficient strength, resulting in Strength and grinding ratio are reduced.
実施例１０〜１１および比較例１２〜１４実施例１０〜
１１は炭素３．５％、Ｎｉ２％、Ｃｏｌ％、残部鉄から
成り、粒径をそれぞれ６．１５μｍに設定した合金粉末
を、酸素を１▼ｏｆ．％含有するアルゴンガス雰囲気中
で、温度８５０℃に昇熱し、１５分間保持して脱炭処理
を行なったものである。処理した合金粉末７５重量％に
対して、砥粒としてダイヤモンド砥粒（平均粒径５５μ
ｍ）およびＣＢＮ砥粒（平均粒径５５μｍ）を重量比で
９＝１の割合、すなわちそれぞれ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
石を形或したものである。Examples 10-11 and Comparative Examples 12-14 Example 10-
No. 11 is an alloy powder consisting of 3.5% carbon, 2% Ni, Col%, and the balance iron, each having a particle size of 6.15 μm, and oxygen of 1▼of. % in an argon gas atmosphere, the temperature was raised to 850° C. and held for 15 minutes to perform decarburization treatment. Diamond abrasive grains (average particle size 55μ
m) and CBN abrasive grains (average particle size 55 μm) in a weight ratio of 9=1, that is, 22.5% by weight, respectively.
Examples 1 to 3 of the mixed powder obtained by mixing 5% by weight each
A diamond CBN composite grindstone was formed by performing the same sintering process as described above.
また比較例１２〜１４は、実施例１０〜１１と同一の合
金組戊を有する合金粉末の平均粒径を２５〜９０μｍの
範囲で変え、砥粒の平均粒径（５５μｍ）に対する粒径
比を０．４５〜１．６４まで変化させてその研削性能に
及ぼす影響を調査した。In addition, in Comparative Examples 12 to 14, the average particle size of the alloy powder having the same alloy composition as in Examples 10 to 11 was changed in the range of 25 to 90 μm, and the particle size ratio to the average particle size of the abrasive grains (55 μm) was changed. The influence on grinding performance was investigated by changing the grinding temperature from 0.45 to 1.64.
実施例１０〜１１および比較例１２〜１４で得られたダ
イヤモンドＣＢＮ複合砥石の抗折強度を測定することと
もに、各ダイヤモンドＣＢＮ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。In addition to measuring the bending strength of the diamond CBN composite grinding wheels obtained in Examples 10 to 11 and Comparative Examples 12 to 14, each diamond CBN composite grinding wheel was used under the same processing conditions as Examples 1 to 3. When a grinding test was conducted on Si3N4, the results shown in the right column of Table 1 below were obtained.
第１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、合金粉末の粒径を砥粒の
平均粒径の１／３以下に設定した実施例１０〜１１にお
いては、抗折強度がいずれも大きく、良好な加工仕上げ
を行なうことが可能であり、併せて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 1, diamond abrasive grains and CB
In Examples 10 to 11, in which mixed abrasive grains with N abrasive grains were used and the grain size of the alloy powder was set to 1/3 or less of the average grain size of the abrasive grains, the bending strength was high and good. Machining and finishing can be performed, and a high grinding ratio can also be ensured.
しかし比較例１２〜１４で示すように、マトリックスと
なる金属粉末の平均粒径が砥粒の平均粒径の１／３を超
える場合は、砥粒の脱落が増加し、研削比が逆に低下す
る。したがってマトリックスを構成する金属粉末の平均
粒径は砥粒の平均粒径の１／３以下に設定することが必
要となる。However, as shown in Comparative Examples 12 to 14, when the average particle size of the metal powder serving as the matrix exceeds 1/3 of the average particle size of the abrasive grains, the shedding of the abrasive grains increases and the grinding ratio decreases. do. Therefore, it is necessary to set the average particle size of the metal powder constituting the matrix to 1/3 or less of the average particle size of the abrasive grains.
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、
予め酸化性雰囲気で加熱し、合金粉末表面を脱炭処理し
ており、粉末表面のＦｅ分を相対的に高めているため、
焼結性が極めて優れている。すなわち、抗折強度が大き
く高い研削比が得られるとともに、短時間で焼結が完結
するのでメタルボンド工具の生産効率を大幅に改善する
ことができる。As explained 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
The alloy powder surface is decarburized by heating in an oxidizing atmosphere in advance, and the Fe content on the powder surface is relatively high.
Excellent sinterability. That is, not only can a high bending strength and a high grinding ratio be obtained, but also sintering can be completed in a short time, so that the production efficiency of metal bond tools can be greatly 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。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.
またマトリックスを形成する鉄基合金粉末の平均粒径を
、砥粒の平均粒径に対して１／３以下に調整しているた
め、潤滑材としての炭素粒および砥粒の支持材となる鉄
基合金粉末を、砥粒の周辺に均一に分散配置することが
できる。In addition, the average particle size of the iron-based alloy powder that forms the matrix is adjusted to 1/3 or less of the average particle size of the abrasive grains, so carbon grains serve as a lubricant and iron as a support material for the abrasive grains. The base alloy powder can be uniformly distributed around the abrasive grains.
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.
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、酸素を含む不活性ガス雰囲気中で原料となる鉄基合
金粉末を加熱し、合金粉末表面を脱炭処理した後に、処
理した合金粉末と砥粒との混合物を圧縮成形し一体に焼
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、合金粉末の平均粒径は、砥粒の平均粒径の１／３以
下に設定した請求項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１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, the raw material is heated in an oxygen-containing inert gas atmosphere. After heating the iron-based alloy powder and decarburizing the surface of the alloy powder, the mixture of the treated alloy powder and abrasive grains is compression molded and sintered together to form an abrasive grain layer. A method for manufacturing metal bond tools. 2. The method for manufacturing a metal bond tool according to claim 1, wherein the average particle size of the alloy powder is set to 1/3 or less of the average particle size of the abrasive grains. 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 |
|---|---|---|---|
| JP23299889A JPH0398768A (en) | 1989-09-11 | 1989-09-11 | Manufacture of metal bonded tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23299889A JPH0398768A (en) | 1989-09-11 | 1989-09-11 | Manufacture of metal bonded tool |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0398768A true JPH0398768A (en) | 1991-04-24 |
Family
ID=16948204
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23299889A Pending JPH0398768A (en) | 1989-09-11 | 1989-09-11 | Manufacture of metal bonded tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0398768A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08335736A (en) * | 1995-06-07 | 1996-12-17 | Nec Corp | Discharge electrode for excimer laser and its production |
-
1989
- 1989-09-11 JP JP23299889A patent/JPH0398768A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08335736A (en) * | 1995-06-07 | 1996-12-17 | Nec Corp | Discharge electrode for excimer laser and its production |
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