JPH0716882B2 - Superabrasive Vitrified Wheel with Ceramic Sintering Holder - Google Patents
Superabrasive Vitrified Wheel with Ceramic Sintering HolderInfo
- Publication number
- JPH0716882B2 JPH0716882B2 JP21237188A JP21237188A JPH0716882B2 JP H0716882 B2 JPH0716882 B2 JP H0716882B2 JP 21237188 A JP21237188 A JP 21237188A JP 21237188 A JP21237188 A JP 21237188A JP H0716882 B2 JPH0716882 B2 JP H0716882B2
- Authority
- JP
- Japan
- Prior art keywords
- sintered
- superabrasive
- ceramic
- holder
- layer
- 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.)
- Expired - Lifetime
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は，セラミック焼結保持体部を有する超砥粒ビト
リファイド砥石車などの超砥粒ビトリファイド砥石に関
する。TECHNICAL FIELD The present invention relates to a superabrasive vitrified grinding wheel such as a superabrasive vitrified grinding wheel having a ceramic sintered holder.
（従来の技術） ビトリファイド砥石は砥粒結合剤として磁器質結合剤を
用いこれを融化焼結した砥石であり，ビトリファイド超
砥粒砥石は，一般的に，高価な立方晶形窒化ホウ素，ダ
イヤモンド等の超砥粒を有効に使用できる様に，安価な
セラミック質の保持体の表面に前記超砥粒と磁器質結合
剤から成る比較的薄い超砥粒層を設け一体化された構造
をしている。(Prior art) A vitrified grindstone is a grindstone obtained by fusion-sintering a porcelain binder as an abrasive grain binder. Generally, a vitrified superabrasive grindstone is made of expensive cubic boron nitride, diamond, etc. In order to use the superabrasive grains effectively, a relatively thin superabrasive grain layer composed of the superabrasive grains and a porcelain binder is provided on the surface of an inexpensive ceramic holder to form an integrated structure. .
このような構造のビトリファイド超砥粒砥石として特公
昭52−3147号公報には，セラミック焼結体，アルミナ質
若しくは炭化ケイ素質の砥粒または両者の混合砥粒を骨
材として用いたビトリファイド砥石類似物を保持体とし
予め焼結し，該保持体の表面に等軸晶系窒化ホウ素砥粒
又は等軸晶系窒化ホウ素砥粒と骨材としてのアルミナ
質，結合剤としてホウケイ酸ガラス質原料との混合物を
650〜950℃の比較的低い温度で融化焼結（ビトリファイ
ド）して製造された等軸晶系窒化ホウ素砥粒を含むビト
リファイド超砥粒砥石が記載されている。As a vitrified superabrasive wheel having such a structure, Japanese Patent Publication No. Sho 52-3147 discloses a vitrified grindstone using a ceramic sintered body, an alumina-based or silicon carbide-based abrasive, or a mixed abrasive of both as an aggregate. The material is used as a holder and pre-sintered, and the surface of the holder is equiaxed boron nitride abrasive grains or equiaxed boron nitride abrasive grains and alumina as an aggregate, and borosilicate glass raw material as a binder. A mixture of
A vitrified superabrasive wheel containing equiaxed boron nitride abrasive particles produced by fusion sintering (vitrified) at a relatively low temperature of 650 to 950 ° C is described.
（本発明が解決しようとする問題点） しかし，上記特公昭52−3147号公報に記載の超砥粒ビト
リファイド砥石は，超砥粒層の形状及び寸法精度，保持
体部と超砥粒層との接着力等が十分でなかった。そのた
め，砥石使用時に使用周速度に耐えられず，保持体部か
ら超砥粒層が剥離する場合もあった。このような剥離は
超砥粒層が薄くなるほど顕著であった。(Problems to be Solved by the Present Invention) However, the superabrasive grain vitrified grindstone disclosed in Japanese Patent Publication No. 52-3147 described above has a shape and dimensional accuracy of the superabrasive grain layer, a holding body portion and a superabrasive grain layer. Adhesive strength of was not sufficient. Therefore, when the grindstone was used, it could not withstand the peripheral speed in use, and the superabrasive grain layer sometimes peeled from the holder. Such peeling was more remarkable as the superabrasive layer became thinner.
また，保持体部にはより強度の大きいものが望まれてい
た。特に保持体部が大型のものについてはより一層望ま
れていた。この対策として，例えば外径300mm以上，厚
み30mm以上の大物砥石は，厚み方向で30mm以下の砥石車
を複数個製造し，これを有機接着剤等で厚み方向に接着
し製造していたが，砥石の接着箇所が研削時高速回転に
対し強度的にあるいは動的バランス上不安定でありかつ
接着箇所が外周研削面内に存在するため製造時および使
用前後の研削面の精度自体不十分で長時間の整形工程を
要すると共に，研削面に不均一な領域が存するため研削
に使用した場合高精度加工の弊害となっていた。In addition, the holder has been desired to have higher strength. In particular, the one having a large holder has been desired. As a measure against this, for example, a large wheel with an outer diameter of 300 mm or more and a thickness of 30 mm or more was manufactured by manufacturing a plurality of grinding wheel wheels with a thickness of 30 mm or less and bonding them in the thickness direction with an organic adhesive or the like. Since the bonded part of the grindstone is unstable in terms of strength or dynamic balance against high speed rotation during grinding, and the bonded part exists in the outer peripheral grinding surface, the accuracy of the ground surface during manufacture and before and after use is insufficient and the length is long. In addition to requiring a time shaping process, there is a non-uniform area on the ground surface, which is an obstacle to high-precision machining when used for grinding.
また，従来の方法では超砥粒層の厚さが3mm以上の砥石
しか製造できないので超砥粒を必要以上に使用しなけれ
ばならず，砥石のイニシャルコストを上昇させていた。
例えば厚さ3mmのセンタレス砥石は，寿命が数十年に達
し,1mm以下で十分耐久性があるはずのものである。Moreover, since the conventional method can only manufacture a grindstone having a thickness of the superabrasive grain layer of 3 mm or more, it is necessary to use the superabrasive grains more than necessary, which increases the initial cost of the grindstone.
For example, a centerless grindstone with a thickness of 3 mm should have a service life of several decades and a durability of less than 1 mm should be sufficient.
本発明の目的は，上記従来技術の問題点を解決したセラ
ミック焼結保持体部を有する超砥粒ビトリファイド砥石
を提供することである。An object of the present invention is to provide a superabrasive vitrified grindstone having a ceramic sintered holder that solves the above-mentioned problems of the prior art.
（問題点を解決するための手段） 本発明によれば，無機質固体粒子骨材と磁器質結合剤と
から成るセラミック焼結保持体部と，超砥粒及び磁器質
結合剤から成る焼結超砥粒層との界面に，厚さ５〜15μ
ｍの焼結セラミック質結合剤層を有することを特徴とす
るセラミック焼結保持体部を有する超砥粒ビトリファイ
ド砥石により上記目的が達成できる。前記無機質固体粒
子骨材は最密充填となるよう粒度配合されていることが
好ましい。(Means for Solving the Problems) According to the present invention, a ceramic sintered holding body portion composed of an inorganic solid particle aggregate and a porcelain binder, and a sintered super sintered body composed of a superabrasive grain and a porcelain binder. 5 to 15μ thick at the interface with the abrasive layer
The above object can be achieved by a superabrasive vitrified grindstone having a ceramic sintered holder that is characterized by having a sintered ceramic binder layer of m. It is preferable that the above-mentioned inorganic solid particle aggregates are blended in a particle size so as to be the closest packed.
さらに，無機質固体粒子骨材が,50〜70容積％の粒径30
〜50μｍの粒子と,30〜50容積％の粒径10〜30μｍの粒
子とから成ること，セラミック焼結保持体部が，直径30
0mm以上高さ30mm以上の円筒形であること，焼結超砥粒
層の厚みが1.5mm以下であることはそれぞれ好ましい。Furthermore, the inorganic solid particle aggregate has a particle size of 30 to 50% by volume.
-50 μm particles and 30-50% by volume of 10-30 μm particle size.
It is preferable that the cylindrical shape has a height of 0 mm or more and a height of 30 mm or more, and the thickness of the sintered superabrasive grain layer is 1.5 mm or less.
（好適な実施の態様） 焼結超砥粒層の砥粒は，立方晶窒化ホウ素と同等以上の
硬度を有する超砥粒であり，このような砥粒として立方
晶窒化ホウ素砥粒，人口若しくは天然のダイヤモンド砥
粒等がある。焼結超砥粒層は，砥粒率が25〜55容積％，
気孔率が25〜45容積％，結合剤率が12〜32容積％，集中
度が25〜220であることが好ましい。(Preferred Embodiment) The abrasive grains of the sintered superabrasive grain layer are superabrasive grains having hardness equal to or higher than that of cubic boron nitride, and as such grains, cubic boron nitride abrasive grains, artificial or There are natural diamond abrasives. The sintered superabrasive grain layer has an abrasive grain ratio of 25 to 55% by volume,
It is preferable that the porosity is 25 to 45% by volume, the binder rate is 12 to 32% by volume, and the concentration is 25 to 220.
セラミック焼結保持体部は，製造時および使用時の熱的
衝撃に起因する応力をより一層減少ないし緩和のため焼
結超砥粒層と同等の熱膨張係数，即ち焼結超砥粒層に対
して±１×10-6／℃の範囲内の熱膨張係数（焼結後）を
有することが好ましい。例えば300−600℃間の焼結超砥
粒層（焼結後）の熱膨張係数が５×10-6／℃の場合に
は，焼結保持体部の熱膨張係数は５±１×10-6／℃の範
囲内が好ましい。そのため無機質固体粒子骨材としてム
ライト,SiC等を用いることができる。The ceramic sintered holder has a coefficient of thermal expansion equivalent to that of the sintered superabrasive layer, that is, a sintered superabrasive layer, in order to further reduce or alleviate stress caused by thermal shock during manufacturing and use. On the other hand, it is preferable to have a coefficient of thermal expansion (after sintering) within a range of ± 1 × 10 -6 / ° C. For example, when the coefficient of thermal expansion of the sintered superabrasive grain layer (after sintering) between 300 and 600 ° C is 5 × 10 -6 / ° C, the coefficient of thermal expansion of the sintered holder is 5 ± 1 × 10 It is preferably within the range of -6 / ° C. Therefore, mullite, SiC or the like can be used as the inorganic solid particle aggregate.
セラミック焼結保持体部の構成は一例として，砥粒45−
55容積％，磁器質結合剤15〜25容積％，気孔率25−35容
積％とすることが好ましい。As an example of the structure of the ceramic sintered holder, abrasive grains 45-
It is preferable that the content is 55% by volume, the porcelain binder is 15 to 25% by volume, and the porosity is 25 to 35% by volume.
焼結超砥粒層の超砥粒の集中度が高い場合には，焼結保
持体部の無機質固体粒子骨材として超砥粒と同様の熱膨
張係数を示す骨材が，超砥粒層と保持体部との間の応力
緩和または減少のために好ましく，超砥粒が立方晶窒化
ホウ素の場合にはムライト又はSiCが好ましい。When the concentration of superabrasive grains in the sintered superabrasive grain layer is high, the aggregate having the same coefficient of thermal expansion as the superabrasive grains as the inorganic solid particle aggregate in the sintered holder is the superabrasive grain layer. It is preferable to relax or reduce the stress between the carrier and the holder, and when the superabrasive grains are cubic boron nitride, mullite or SiC is preferable.
セラミック焼結保持体部の固体粒子骨材の粒度配合は，
焼結保持体部の強度を最大にするため，固体粒子骨材が
最密充填するように行う。無機質固体粒子骨材は，粒径
30〜50μｍの粒子が50〜70容積％と，粒径10〜30μｍの
粒子が30〜50容積％とから成ることは好ましい。例え
ば，固体粒子骨材がムライトビーズと電融ムライトの場
合には，ムライトビーズより細粒の電融ムライトの粒度
番手がムライトビーズの番手の２〜３倍の粒度番手にな
ることが好ましい。The particle size composition of the solid particle aggregate of the ceramic sintered holder is
In order to maximize the strength of the sinter holder, the solid particle aggregate should be packed closest. Inorganic solid particle aggregate has a particle size
It is preferred that particles of 30 to 50 μm consist of 50 to 70% by volume and particles of 10 to 30 μm in size of 30 to 50% by volume. For example, when the solid particle aggregates are mullite beads and electrofused mullite, it is preferable that the grain size of electrofused mullite, which is finer than that of mullite beads, be 2-3 times the grain size of mullite beads.
セラミック焼結保持体部の超砥粒層を形成すべき研削面
対応面は，必要に応じ，精密加工されている。砥石外周
が研削面となる場合同軸度（ないし円筒度）が，砥石側
面が研削面となる場合には面の平坦度が所定の値以上に
仕上加工されている。その面にセラミック質結合剤層を
接合する。セラミック焼結体保持部の寸法精度は外径と
穴径の同軸度では3/100mm以内に仕上加工されている。The surface of the ceramic sintered holder that corresponds to the grinding surface on which the superabrasive grain layer is to be formed is precision processed as required. When the outer circumference of the grindstone is the grinding surface, the concentricity (or cylindricity) is finished, and when the side surface of the grindstone is the grinding surface, the flatness of the surface is finished to a predetermined value or more. A ceramic binder layer is bonded to the surface. The dimensional accuracy of the ceramic sintered body holding part is finished within 3/100 mm in terms of the coaxiality of the outer diameter and the hole diameter.
焼結セラミック質結合剤層のセラミック質結合剤は，砥
石として要求される所定の強度でセラミック焼結保持体
部及び焼結超砥粒層と焼結するものであればセラミック
焼結保持体部及び焼結超砥粒層の結合剤と異なっても良
いが，セラミック焼結保持体部及び焼結超砥粒層の磁器
質結合剤と同一又は類似の結合剤であることが好まし
い。The ceramic binder of the sintered ceramic binder layer is a ceramic sintered holder as long as it can be sintered with the ceramic sintered holder and the sintered superabrasive grain layer with a predetermined strength required as a grindstone. The binder may be different from the binder of the sintered superabrasive grain layer, but is preferably the same as or similar to the ceramic binder of the ceramic sintered holder and the sintered superabrasive layer.
焼結セラミック質結合剤層は，焼結保持体部と焼結超砥
粒層との界面に設けられ一体化されている。焼結セラミ
ック質結合剤層は，砥石として要求される所定の強度を
発揮できる範囲の量で設ける。無機固形分換算で３×10
-2〜７×10-2g/cm2の範囲が好ましい。この範囲より少
ない場合には，焼結セラミック質結合剤層を設けたこと
による接合強度が十分発揮されず，またこの範囲より多
い場合には，焼結保持体部と焼結超砥粒層との接合強度
が低下する。The sintered ceramic binder layer is provided and integrated at the interface between the sintered holder and the sintered superabrasive layer. The sintered ceramic binder layer is provided in an amount within a range capable of exhibiting a predetermined strength required as a grindstone. 3 x 10 in terms of inorganic solids
The range of −2 to 7 × 10 −2 g / cm 2 is preferable. If it is less than this range, the bonding strength due to the provision of the sintered ceramic binder layer is not sufficiently exerted, and if it is more than this range, the sintered holder and the sintered superabrasive layer are The joint strength of is reduced.
セラミック焼結保持体部と焼結超砥粒層との界面にセラ
ミック質結合剤層を設けて成る一体成形体は，セラミッ
ク質結合剤層の厚さが５〜15μｍとなるようにセラミッ
ク質結合剤層を介在させる。厚み５μｍ未満では接合力
が不十分であり,15μｍをこえるとやはり十分な接合力
が生じない。The integrally formed body having the ceramic binder layer provided at the interface between the ceramic sintered holder and the sintered superabrasive grain layer is ceramic bonded so that the thickness of the ceramic binder layer is 5 to 15 μm. The agent layer is interposed. If the thickness is less than 5 μm, the joining force is insufficient, and if it exceeds 15 μm, sufficient joining force is not generated.
熱膨張係数を考慮して，一体成形体を構成するセラミッ
ク焼結保持体部の無機質固体粒子骨材の材質としてはム
ライト又はSiCが好ましい。Considering the coefficient of thermal expansion, mullite or SiC is preferable as the material of the inorganic solid particle aggregate of the ceramic sintered holder that constitutes the integrally formed body.
本発明の砥石は，焼結超砥粒層の厚みが1.5mm以下はも
ちろん1mm以下，さらに0.5mm以下のものを高精度に有す
ることができ，かつセラミック焼結保持体部との間に高
い接合力をもっている。The grindstone of the present invention can have a sintered superabrasive grain layer with a thickness of 1.5 mm or less as well as 1 mm or less, and even 0.5 mm or less with high accuracy, and is high between it and the ceramic sintered holder. Has a bonding power.
（実施例） 図面の第１図及び第２図に基づいて次の実施例１及び２
の超砥粒ビトリファイド砥石を説明する。(Embodiment) The following Embodiments 1 and 2 will be described based on FIGS. 1 and 2 of the drawings.
The superabrasive grain vitrified grindstone will be described.
実施例１ 円筒形状であって、その円筒の軸方向に孔を有するセラ
ミック焼結保持体部（１）は，ムライトビーズ（＃60）
（JISR6001をセラミック原料に転用した），電融ムライ
ト（＃180）及び第１表の磁器質結合剤から成る。焼結
セラミック質結合剤層（２）は，前記セラミック焼結保
持体部（１）の磁器質結合剤と同一組成であり，前記セ
ラミック焼結保持体部（１）の外周面と焼結超砥粒層
（３）との界面に15μｍの厚さで存在する。前記焼結超
砥粒層（３）は，立方晶窒化ホウ素砥粒（＃80），及び
前記セラミック焼結保持体部（１）の磁器質結合剤と同
一組成の磁器質結合剤から成り，前記焼結セラミック質
結合剤層（２）を介して前記セラミック焼結保持体部
（１）と強力に接合する。Example 1 A ceramic sintered holder (1) having a cylindrical shape and having a hole in the axial direction of the cylinder was a mullite bead (# 60).
Consists of JIS R6001 (used as a ceramic raw material), electrofused mullite (# 180), and the porcelain binder shown in Table 1. The sintered ceramic binder layer (2) has the same composition as the porcelain binder of the ceramic sintered holder part (1), and the sintered ceramic binder layer (2) and the sintered surface of the ceramic sintered holder part (1). It exists at a thickness of 15 μm at the interface with the abrasive grain layer (3). The sintered superabrasive grain layer (3) is composed of cubic boron nitride abrasive grains (# 80) and a porcelain binder having the same composition as the porcelain binder of the ceramic sintered holder (1). It is strongly bonded to the ceramic sintered holder part (1) through the sintered ceramic binder layer (2).
実施例２ 円筒形状であって，その円筒の軸方向に孔を有するセラ
ミック焼結保持体部（21）は，ムライトビーズ（＃6
0），電融ムライト（＃180）及び第１表の磁器質結合剤
から成る。焼結セラミック質結合剤層（22）は前記セラ
ミック焼結保持体部の磁器質結合剤と同一組成であり，
前記セラミック焼結保持体部（21）の平坦な側面と焼結
超砥粒層（23）との界面に５μｍの厚さで存在する。前
記焼結超砥粒層（23）は，立方晶窒化ホウ素砥粒（＃8
0），及び前記セラミック焼結保持体部（21）の磁器質
結合剤と同一組成の磁器質結合剤から成り，前記焼結セ
ラミック質結合剤層（22）を介して前記セラミック焼結
保持体部（21）と強力に接合する。 Example 2 A ceramic sintered holder (21) having a cylindrical shape and having a hole in the axial direction of the cylinder was made of mullite beads (# 6).
0), fused mullite (# 180) and the porcelain binder of Table 1. The sintered ceramic binder layer (22) has the same composition as the ceramic binder of the ceramic sintered holder.
It exists at a thickness of 5 μm at the interface between the flat side surface of the ceramic sintered holder (21) and the sintered superabrasive grain layer (23). The sintered superabrasive grain layer (23) is a cubic boron nitride abrasive grain (# 8).
0) and a porcelain binder having the same composition as the porcelain binder of the ceramic sinter holder (21), and the ceramic sinter holder via the sinter ceramic binder layer (22). Strongly joins the part (21).
（製造例） 製造例１ 骨材としてムライトビーズ＃60を34容量部及び電融ムラ
イト＃180を22容量部，セラミック質結合剤としてMgO−
CaO−BaO−Li2O−ZrO2−P2O5を含むSiO2−Al2O3−B2O3
の組成が第１表の磁器質結合剤を16容量部，からなる外
径349mm,厚み100mm,穴径150mm,同軸度3/100mm以内であ
るセラミック焼結保持体部の外周面（研削面に対応する
表面）に厚み10μｍのセラミック質結合剤層を設ける。
この外周面に超砥粒として立方晶窒化ホウ素砥粒（＃8
0）55容量部，第１表の組成の磁器質結合剤16容量部，
から成る厚さ1mmの超砥粒層を設け，外径351mm,厚み100
mm,穴径150mmの一体成形体を得る。この一体成形体を窒
素雰囲気中900℃で40時間焼成し，セラミック焼結保持
体部を有する超砥粒ビトリファイド砥石を製造した。１
年間研削加工に使用しているが，焼結超砥粒層の剥離，
変形，亀裂は発生していない。(Production Example) Production Example 1 34 parts by volume of mullite beads # 60 and 22 parts by volume of electrofused mullite # 180 as an aggregate, MgO-as a ceramic binder
SiO 2 -Al 2 O 3 -B 2 O 3 containing CaO-BaO-Li 2 O- ZrO 2 -P 2 O 5
The composition consists of 16 parts by volume of the porcelain binder shown in Table 1 and has an outer diameter of 349 mm, thickness of 100 mm, hole diameter of 150 mm, and concentricity within 3/100 mm. A 10 μm thick ceramic binder layer is provided on the corresponding surface).
Cubic boron nitride abrasive grains (# 8
0) 55 parts by volume, 16 parts by volume of the porcelain binder having the composition shown in Table 1,
1mm thick super-abrasive grain layer consisting of 351mm outer diameter and 100mm thickness
mm to obtain an integrally molded body with a hole diameter of 150 mm. This integrally molded body was fired in a nitrogen atmosphere at 900 ° C for 40 hours to manufacture a superabrasive vitrified grindstone having a ceramic sintered holder. 1
It has been used for annual grinding processing, but peeling of the sintered superabrasive layer,
No deformation or cracks have occurred.
製造例２ 製造例１の磁器質結合剤の代りに,MgO−CaO−Li2Oを含
むSiO2−Al2O3−B2O3−ZnO−PbOの組成が第１表である
磁器質結合剤を使用した一体成形体を750℃×30時間で
焼成した以外は製造例１と同一のセラミック焼結保持体
部を有する超砥粒ビトリファイド砥石を製造した。１年
間研削加工に使用しているが，焼結超砥粒層の剥離，変
形，亀裂は起こっていない。Production Example 2 Instead of the porcelain binder of Production Example 1, the composition of SiO 2 —Al 2 O 3 —B 2 O 3 —ZnO—PbO containing MgO—CaO—Li 2 O is as shown in Table 1. A superabrasive vitrified grindstone having the same ceramic sintered holder as in Production Example 1 was produced except that the integrally formed body using the binder was fired at 750 ° C. for 30 hours. It has been used for grinding for one year, but no peeling, deformation, or cracking of the sintered superabrasive layer has occurred.
（接合強度比較試験） テストピース 実験例Ａ 製造例１と同様の製造方法により,4mm×6mm×20mmの直
方体の焼結保持体部の4mm×6mmの面の一方と,4mm×6mm
×20mmの直方体の超砥粒層の（横）4mm×（縦）6mmの面
の一方とが塗付量1.0×10-2g/cm2のセラミック質結合剤
層を介して一体化し焼結して成るテストピースＡ。(Joint strength comparison test) Test piece Experimental example A By the same manufacturing method as in Manufacturing example 1, one of the 4 mm × 6 mm faces of the 4 mm × 6 mm × 20 mm rectangular parallelepiped sintered holding body and 4 mm × 6 mm
One of the (horizontal) 4 mm × (longitudinal) 6 mm surfaces of the × 20 mm rectangular parallelepiped superabrasive grain layer is integrated and sintered through a ceramic binder layer with a coating amount of 1.0 × 10 -2 g / cm 2. Test piece A made up of.
実験例Ｂ 前記テストピースＡにおいて，セラミック結合剤層の塗
付量を5.0×10-2g/cm2として焼結して成るテストピース
Ｂ。Experimental Example B A test piece B obtained by sintering the test piece A with the coating amount of the ceramic binder layer being 5.0 × 10 −2 g / cm 2 .
実験例Ｃ 前記テストピースＡにおいて，セラミック結合剤層の塗
付量を10.0×10-2g/cm2として焼結して成るテストピー
スＣ。Experimental Example C A test piece C obtained by sintering the test piece A with the coating amount of the ceramic binder layer being 10.0 × 10 −2 g / cm 2 .
実験例Ｄ ムライトビーズ＃60を電融ムライト＃180に代えた（骨
材の粒度配合がない）以外は前記製造例１と同様の製造
により,4mm×6mm×20mmの直方体の焼結保持体部の4mm×
6mmの面の一方と,4mm×6mm×20mmの直方体の超砥粒層の
（横）4mm×（縦）6mmの面の一方とが塗付量5.0×10-2g
/cm2のセラミック質結合剤層を介して一体化し焼結して
成るテストピースＤ。Experimental Example D 4 mm × 6 mm × 20 mm rectangular parallelepiped sintered holder part was manufactured in the same manner as in Manufacturing Example 1 except that the mullite beads # 60 was replaced with the electromelting mullite # 180 (there was no aggregate particle size composition). 4mm ×
Coating amount 5.0 × 10 -2 g on one side of the 6 mm surface and on the other side of the 4 mm × 6 mm × 20 mm rectangular parallelepiped superabrasive layer (horizontal) 4 mm × (vertical) 6 mm
A test piece D formed by integrating and sintering via a ceramic binder layer of / cm 2 .
比較実験例１ 前記テストピースＡと同一形状，寸法および組成である
が，セラミック質結合剤層を有さない焼結テストピー
ス。Comparative Experimental Example 1 A sintered test piece having the same shape, size and composition as the test piece A, but having no ceramic binder layer.
試験方法 前記各テストピースの接合部分に縦（6mm）の方向にス
パン30mmで荷重を加え界面が剥離する時の荷重を測定し
接着強度を求めた。Test Method A bond strength was obtained by applying a load with a span of 30 mm in the longitudinal direction (6 mm) to the joint part of each test piece and measuring the load when the interface peels.
試験結果 試験結果を第３図に示す。第３図により，従来技術と同
様の比較実験例１に較べ，本発明の実験例は2.5〜４倍
程度の接合力を示す。Test Results The test results are shown in FIG. As shown in FIG. 3, the experimental example of the present invention shows about 2.5 to 4 times the joining force as compared with the comparative experimental example 1 similar to the prior art.
なお，一般に磁器質結合剤を用いた砥石をエポキシ系接
着剤で（保持体に相当する）支持体に接着した場合，支
持体（鋼，ビトリファイド砥石）に対する剥離を生ずる
接着強度は200kgf/cm2程度である。本発明によれば200k
gf/cm2をはるかに越えて400kgf/cm2レベル以上の接合強
度が得られる。Generally, when a grindstone using a porcelain binder is adhered to a support (corresponding to a holder) with an epoxy adhesive, the adhesive strength that causes peeling from the support (steel, vitrified grindstone) is 200 kgf / cm 2 It is a degree. 200k according to the invention
Bonding strength of 400kgf / cm 2 level or more can be obtained, far exceeding gf / cm 2 .
（作用及び効果） 本発明において，セラミック焼結保持体部の無機質固体
粒子が最密充填する粒子形状，大きさ，含有率等を有す
る場合は，該骨材とセラミック質結合剤層とから成るセ
ラミック焼結保持体の強度が大きくなり，砥石を大型化
でき，また，形成されるセラミック焼結保持体部が緻密
になり精密な表面加工が可能となるので，均一かつ精密
な厚さの焼結セラミック質結合剤層と焼結超砥粒層とを
有し得る。(Operation and effect) In the present invention, when the inorganic solid particles of the ceramic sintered holder have the shape, size, content, etc. of the closest packed particles, the particles are composed of the aggregate and the ceramic binder layer. The strength of the ceramic sinter holder is increased, the grindstone can be made larger, and the formed ceramic sinter holder can be made more precise and precise surface processing is possible. It may have a ceramic binder layer and a sintered superabrasive layer.
セラミック焼結保持体部と焼結超砥粒層との界面に存在
する焼結セラミック質結合剤層は，セラミック焼結保持
体部と焼結超砥粒層とを強力に接合するので，本発明の
砥石は，使用時にセラミック焼結保持体部から焼結超砥
粒層が剥離しない。Since the sintered ceramic binder layer existing at the interface between the ceramic sintered holder and the sintered superabrasive layer strongly bonds the ceramic sintered holder and the sintered superabrasive layer, In the grindstone of the invention, the sintered superabrasive grain layer does not peel off from the ceramic sintered holder during use.
本発明の超砥粒ビトリファイド砥石においてセラミック
焼結保持体部の無機質固体粒子を最密充填する場合は，
保持体部の強度が大きく外径300mm以上，厚み30mm以上
の一体構造の超砥粒ビトリファイド砥石を可能とし，か
つその外径と穴径の同軸度が3/100mm以内の高精度仕上
げをも可能とする。本発明の超砥粒ビトリファイド砥石
は，焼結超砥粒層の厚みが1.5mm以下（さらに1mm以下）
にしても使用時に保持体部から剥離したり亀裂等も発生
しない。さらに，焼結超砥粒層が均一な厚みの砥石にで
きるので，高価な超砥粒の余分な使用を削減でき，超砥
粒砥石のイニシャルコストを低減できる。In the superabrasive vitrified grindstone of the present invention, when the inorganic solid particles of the ceramic sinter holder are closely packed,
The strength of the holder is large and it is possible to use a super-abrasive grain vitrified grindstone with an outer diameter of 300 mm or more and a thickness of 30 mm or more, and it is also possible to perform high-precision finishing with the outer diameter and hole diameter coaxiality within 3/100 mm. And The superabrasive vitrified grindstone of the present invention has a sintered superabrasive layer with a thickness of 1.5 mm or less (further 1 mm or less).
However, neither peeling nor cracking occurs from the holder during use. Furthermore, since the sintered superabrasive grain layer can be made into a grindstone with a uniform thickness, the excess use of expensive superabrasive grains can be reduced, and the initial cost of the superabrasive grain grindstone can be reduced.
また，本発明の超砥粒ビトリファイド砥石は，砥石外径
は510mm程度まで可能であり，軸方向厚みは技術的には
制限されず，例えば200mm程度のものも一体構造にでき
る。Further, the superabrasive vitrified grindstone of the present invention can have a grindstone outer diameter of up to about 510 mm, and its axial thickness is not technically limited, and for example, a grindstone with a diameter of about 200 mm can be integrated.
第１図及び第２図は，本発明のセラミック焼結保持体部
を有する超砥粒ビトリファイド砥石の実施例を示す図で
ある。第３図は接合強度比較試験の試験結果を示す図で
ある。 1,21…セラミック焼結保持体部 2,22…焼結セラミック質結合剤層 3,23…焼結超砥粒層1 and 2 are views showing an embodiment of a superabrasive vitrified grindstone having a ceramic sintered holder of the present invention. FIG. 3 is a diagram showing test results of a joint strength comparison test. 1,21… Sintered ceramic holder 2,22… Sintered ceramic binder layer 3,23… Sintered superabrasive layer
Claims (5)
成るセラミック焼結保持体部と，超砥粒及び磁器質結合
剤から成る焼結超砥粒層との界面に，厚さ５〜15μｍの
焼結セラミック質結合剤層を有することを特徴とするセ
ラミック焼結保持体部を有する超砥粒ビトリファイド砥
石。1. A thickness of 5 at the interface between a ceramic sintered holder comprising an inorganic solid particle aggregate and a porcelain binder and a sintered superabrasive layer comprising a superabrasive and a porcelain binder. A superabrasive vitrified grindstone having a ceramic sintered holder portion, which has a sintered ceramic binder layer of ˜15 μm.
度配合からなる請求項１記載の超砥粒ビトリファイド砥
石。2. The superabrasive vitrified grindstone according to claim 1, wherein the aggregate of the inorganic solid particles has a particle size composition that provides the closest packing.
の粒径30〜50μｍの粒子と,30〜50容積％の粒径10〜30
μｍの粒子とから成ることを特徴とする請求項２記載の
ビトリファイド砥石。3. The inorganic solid particle aggregate is 50 to 70% by volume.
Particle size of 30 to 50 μm and particle size of 30 to 50% by volume of 10 to 30
The vitrified grindstone according to claim 2, wherein the vitrified grindstone is composed of particles having a diameter of μm.
m以上高さ30mm以上の円筒形であることを特徴とする請
求項１ないし３の一に記載の砥石。4. The ceramic sintered holder has a diameter of 300 m.
4. The grindstone according to claim 1, wherein the grindstone has a cylindrical shape with a height of m or more and a height of 30 mm or more.
ることを特徴とする請求項１又は４記載の砥石。5. The grindstone according to claim 1, wherein the sintered superabrasive grain layer has a thickness of 1.5 mm or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21237188A JPH0716882B2 (en) | 1988-08-29 | 1988-08-29 | Superabrasive Vitrified Wheel with Ceramic Sintering Holder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21237188A JPH0716882B2 (en) | 1988-08-29 | 1988-08-29 | Superabrasive Vitrified Wheel with Ceramic Sintering Holder |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0265974A JPH0265974A (en) | 1990-03-06 |
| JPH0716882B2 true JPH0716882B2 (en) | 1995-03-01 |
Family
ID=16621458
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21237188A Expired - Lifetime JPH0716882B2 (en) | 1988-08-29 | 1988-08-29 | Superabrasive Vitrified Wheel with Ceramic Sintering Holder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0716882B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6846233B2 (en) | 2002-02-12 | 2005-01-25 | Noritake Co., Limited | Segmental type grinding wheel |
| US8617273B2 (en) | 2009-10-08 | 2013-12-31 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| US8721751B2 (en) | 2009-12-02 | 2014-05-13 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| US8784521B2 (en) | 2009-12-02 | 2014-07-22 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| CN108908141A (en) * | 2018-08-23 | 2018-11-30 | 沈阳中科超硬磨具磨削研究所 | A kind of preparation method of vitrified bond |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2835425B2 (en) * | 1995-03-27 | 1998-12-14 | 大阪ダイヤモンド工業株式会社 | Grinding wheel base, superabrasive grindstone, and methods for producing them |
| WO1998021009A1 (en) * | 1996-11-13 | 1998-05-22 | Rappold International Sales Ag | Abrasive body and process for manufacturing the same |
| CN103624696B (en) * | 2013-12-16 | 2015-09-16 | 珠海市钜鑫科技开发有限公司 | The manufacture method of vitrified bond, preparation method and vitrified bonded grinding tool |
| CN109759963B (en) * | 2019-02-13 | 2021-04-02 | 苏州远东砂轮有限公司 | Ceramic microcrystalline grinding wheel for grinding cobalt-chromium-nickel alloy sealing block and preparation method thereof |
-
1988
- 1988-08-29 JP JP21237188A patent/JPH0716882B2/en not_active Expired - Lifetime
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6846233B2 (en) | 2002-02-12 | 2005-01-25 | Noritake Co., Limited | Segmental type grinding wheel |
| US8617273B2 (en) | 2009-10-08 | 2013-12-31 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| US8999026B2 (en) | 2009-10-08 | 2015-04-07 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| US8721751B2 (en) | 2009-12-02 | 2014-05-13 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| US8784521B2 (en) | 2009-12-02 | 2014-07-22 | Saint-Gobain Abrasives, Inc. | Bonded abrasive article and method of forming |
| CN108908141A (en) * | 2018-08-23 | 2018-11-30 | 沈阳中科超硬磨具磨削研究所 | A kind of preparation method of vitrified bond |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0265974A (en) | 1990-03-06 |
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