JPS6184350A - Sintered hard alloy and its manufacture - Google Patents
Sintered hard alloy and its manufactureInfo
- Publication number
- JPS6184350A JPS6184350A JP59206380A JP20638084A JPS6184350A JP S6184350 A JPS6184350 A JP S6184350A JP 59206380 A JP59206380 A JP 59206380A JP 20638084 A JP20638084 A JP 20638084A JP S6184350 A JPS6184350 A JP S6184350A
- Authority
- JP
- Japan
- Prior art keywords
- hard alloy
- alloy
- carbonitride
- sintered hard
- sintered
- 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.)
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Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、高ａ性かつ耐熱性に優れた高Ｎ３含有の焼結
硬質合金（サーメット合金）お工びその製造方法に関す
る。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a sintered hard alloy (cermet alloy) with high N3 content and high aluminium and excellent heat resistance, and a method for manufacturing the same.
（従来の技術）
近年、Ｔｉｅ基サーメットにＴｉＮ 、 Ｔｉ（ＯＮ）
。(Prior art) In recent years, TiN and Ti(ON) have been added to Tie-based cermets.
.
（ＴｉＭｏＪ （ＯＮ） 、 （Ｔｉｅ） （ＯＮ）等
を添加含有させることにエリ、硬質相粒子を微粒化して
、靭性および耐摩耗性が大巾に向上したサーメット合金
が提案されている。(TiMoJ (ON), (Tie) (ON), etc. are added to the cermet alloy, and the hard phase particles are atomized, thereby greatly improving toughness and wear resistance. Cermet alloys have been proposed.
例えば特公昭５６−５１２０１号公報にアーウィン呻ル
デイによって提案されたサーメット合金の硬質相は、第
２図に示す工うに（ＴｔｘＭｙ）（ＯｕＮＶ） 中に
おけるＹと、■で規定されており、ホｕ （ＴｉＯ，１
１１１ＭＯ，０４） （ＣＯ，４４Ｎｏ、ｓａ入へ１ｊ
（Ｔｉ・、ｓａ Ｍｏ、０４ ）（Ｃｏｊａ ＮＯ＋０
４ ）、 ） ｕ （Ｔｉｏ、ａｏ ＭｏＡｏ） （
００，１１６ＮＯ１１４１ｓ チは（Ｔｉｅ、ｉｏ Ｍ
Ｏ，４０） （ｃｏ、ｇｏＮｏ、ｔｏ ） である〇
ここで、Ｍは、Ｍｏお工び／まｆＣはＷをあられす。な
お第２図は上記の硬質相の範囲をあられすゲラフチ、横
軸ハ（Ｔ’ ｘＭｙ ） （Ｃｕ Ｎｖ ｌ ２ 中に
おけるモル分率Ｙ１また縦軸ハ（ＴｌｘＭｙ）（ＣｕＮ
ｖ）２ 中におけるモル分率Ｖである。For example, the hard phase of a cermet alloy proposed by Irwin Oulday in Japanese Patent Publication No. 56-51201 is defined by Y in TtxMy (OuNV) and ■ as shown in Figure 2, and (TiO,1
111MO, 04) (CO, 44No, enter sa 1j
(Ti・, sa Mo, 04) (Coja NO+0
4), ) u (Tio, ao MoAo) (
00,116NO1141s Tie, io M
O, 40) (co, goNo, to) 〇Here, M is Mo work/MafC is W. In addition, Fig. 2 shows the range of the above-mentioned hard phase, the horizontal axis shows the mole fraction Y1 in (T'
v) is the molar fraction V in 2.
しかしながら、繭記の公報に記載の方法にエリ製造した
サーメット合金は、高温における強度の低下が大きいた
め、重切削や、強い衝撃を受ける切削などには、満足な
使用に期待できない。However, the cermet alloy produced by the method described in Mayuki's publication suffers a large decrease in strength at high temperatures, so it cannot be expected to be used satisfactorily for heavy cutting or cutting that is subjected to strong impact.
本発明の目的は、この工つな現状に鑑み、従来広による
サーメット合金の高温での強度低下の問題を解決して、
高Ｕ性かつ耐熱性に優れたサーメット合金お工びその製
造方法を提供するところにある。In view of this difficult current situation, the purpose of the present invention is to solve the conventional problem of the decrease in strength of cermet alloys at high temperatures.
The purpose of the present invention is to provide a cermet alloy with high U properties and excellent heat resistance, and a method for manufacturing the same.
本発明者らは、サーメット合金の靭性、耐熱性を向上す
べく鋭意研究の結果、これまでに提案されているサーメ
ット合金エリ、さらに装置の窒素を含有させた高Ｎ３含
有サーメット合金が、工９高靭性かつ耐熱性に優れ、上
記の目的を達成できること、さらにこの工うな高Ｎ３含
有サーメット合金の製法を見出し、本発明に到った。As a result of intensive research aimed at improving the toughness and heat resistance of cermet alloys, the present inventors found that the cermet alloys proposed so far, as well as high N3-containing cermet alloys containing nitrogen in the equipment, The inventors have discovered that the cermet alloy has high toughness and heat resistance, can achieve the above objectives, and has also found a method for producing a high N3-containing cermet alloy, leading to the present invention.
すなわち本発明は、Ｔｉを生成分とする炭窒化物の硬質
相と、鉄族金属およびクロム族金属の１８又は２種以上
からなり合金全体の６０〜４０重量％である結合金属と
からなる焼結硬質合金において、該炭窒化物組成が、下
記式
％式％）
（式中、Ｘ＠ ｙｔ’；！金属元素のモル分率、ｕ、
ｙに非金属元素のモル分率、Ｘ ＋ ７ ＝ １．０、
Ｕ＋ｖ＝１．０、ｚは化学量論的パラメーターであり０
．８０≦２≦１．０２である。また、ｙの値は［１０４
からｆ１４０であり、Ｖの値に第１図のイ、口、ハ、二
、に工って限定される。）で表されることを特徴とする
焼結硬質合金を提供する。That is, the present invention provides a sintered material comprising a hard phase of carbonitride containing Ti as a product and a bonding metal consisting of 18 or two or more of iron group metals and chromium group metals and making up 60 to 40% by weight of the entire alloy. In a hardened alloy, the carbonitride composition is expressed by the following formula %) (where X@yt';! Molar fraction of metal element, u,
y is the mole fraction of the nonmetallic element, X + 7 = 1.0,
U+v=1.0, z is the stoichiometric parameter and 0
．． 80≦2≦1.02. Also, the value of y is [104
to f140, and is limited by modifying the value of V to A, C, C, and II in FIG. ) A sintered hard alloy is provided.
また本発明は上記合金においてＪＭＯお工び／又［Ｗｔ
”％ル比でα０１〜［１５０まで’ｒａ 、 Ｎｂ。Further, the present invention provides JMO machining/or [Wt
``%le ratio from α01 to [150'ra, Nb.
Ｚｒ 、 ｖのうち１種又ｒ１２種以上で置換された焼
結硬質合金を提供する。Provided is a sintered hard alloy substituted with one or more of Zr and v or r12 or more.
さらに本発明は上記の焼結硬質合金を製造する方法とし
て、Ｔｉを生成分とする炭窒化物の硬質相と、鉄族金属
お工びクロム族金属の１種又は２種以上からなり合金全
体の３０〜４０重量％である結合金属とからなる焼結硬
質合金であって、該炭窒化物組成が下記式
％式％）
（式中、”ｅ７は金属元素のモル分率、ｕ、 ｖは非金
属元素のモル分率、！＋７＝ｌ、Ｑ、ｕ＋ｖ ＝ １．
０．２は化学緻論的パラメーターであり１８０≦２≦１
，０２である。また、ｙの値は００４から０．４０であ
り、Ｖの値は第１図のイ九口、ハ、二、に工って限定さ
れる。）で表される焼結硬質合金の製造方法であって、
ａ丁（モル比）が［１５以上のＴ１（０ムＮＢ） お
工び／又は、−（モル比）がα３以下で’Ｆ！＋Ｆ（モ
ル比）０＋Ｄ
がＱ、５以上の（Ｔ ｉ ａ （Ｍｏお工び／又’ｄ
” ）ｎ ） （ＯｇＮＦ）の炭窒化物固溶体粉末に、
結合金属として鉄族金属おＬびクロム族金属の１種又は
２種以上を混合した後、所定の形状にブレスし、その後
窒素分圧ｎ１〜５００ ＴＯｒｒの窒素雰囲気中にて、
温度１４００〜１５００℃にて焼結することを特徴とす
る上記焼結硬質合金の製造方法を提供する。Furthermore, the present invention provides a method for producing the above-mentioned sintered hard alloy. A sintered hard alloy consisting of 30 to 40% by weight of a bonding metal, the carbonitride composition of which is expressed by the following formula % (%) (where "e7 is the molar fraction of the metal element, u, v is the mole fraction of nonmetallic elements, !+7=l, Q, u+v = 1.
0.2 is a chemically precise parameter and 180≦2≦1
,02. Further, the value of y is from 004 to 0.40, and the value of V is limited to A, C, and II in FIG. ) A method for producing a sintered hard alloy,
If a (molar ratio) is [15 or more, T1 (0 mNB) is completed/or - (molar ratio) is α3 or less, 'F! +F (molar ratio)0+D is Q, 5 or more (T i a (Mo work/also'd
” ) n ) (OgNF) carbonitride solid solution powder,
After mixing one or more of iron group metals and chromium group metals as bonding metals, they are pressed into a predetermined shape, and then in a nitrogen atmosphere with a nitrogen partial pressure of n1 to 500 Torr.
Provided is a method for manufacturing the above-mentioned sintered hard alloy, characterized in that sintering is performed at a temperature of 1400 to 1500°C.
本発明者に、サーメット合金の靭性、耐熱性を向上する
べく研究を行った結果、Ｔ１’に生成分とする炭窒化物
の硬質相と鉄族金属お工びクロム族金属の１種又は２種
以上３〜４０重菫チからなる焼結硬質合金において、炭
窒化物に（Ｔｔｘ（”お工び／又ｔＩ′ｓ、Ｗ）ｙ）（
ＣｕＮｖ）ｚであられされ、！、７は金属元素のモル分
率、Ｕ、Ｖは非金属元素のモル分率、ｘ ＋ ｙ ＝
１．０、ｕ＋ｖ＝１．０、Ｚは化学量論パラメーターで
あって（１８０≦２公ｊ、０２で６り、１７ｖｙの値は
１０４から［Ｌ４０であり、■の値は第１図のイロノ＼
二によって限定され、
イに（Ｔｉｏ、９ｓ （Ｍｏ ｊｌ？工び／又は” ）
ｏ、ｏ４） （Ｃ（１，１４Ｎｏ、ａｏ廊・口Ｉ”ｊ
（ＴＩ、、、 （ＭＯお工び／又ｉｆ ）０．０４
ｊ （Ｏ（＋、５６Ｎ０．４４３Ｚ ｓハは（Ｔｉｏ、
ｇｏ （Ｍｏおよび／又Ｕ Ｗ ） ０．４０ ） （
Ｃｏ、ｇｏ Ｎｏ、ａｏ ） Ｚ ％二Ｊｄ （Ｔｉ＠
、−６（Ｍｏお工び／又ｎ Ｗ ） ｏ、ａｏ ） （
ｃｏ、ｉｏ Ｎｏ、ｉｏ ） Ｚ ｓであると、高靭性
で耐熱性にとむサーメット合金になるとの矧見を得友。As a result of research conducted by the present inventor to improve the toughness and heat resistance of cermet alloys, it was found that T1' contains a hard phase of carbonitride as a generated component and one or two types of chromium group metal. In a sintered hard alloy consisting of 3 to 40 violet nitrides, carbonitrides (Ttx("work/also tI's, W)y)(
Hail to CuNv)z! , 7 is the mole fraction of the metal element, U, V are the mole fraction of the nonmetal element, x + y =
1.0, u+v=1.0, Z is the stoichiometric parameter (180≦2 public j, 02 is 6, the value of 17vy is from 104 to [L40, the value of ■ is as shown in Figure 1) Irono＼
limited by two, to i (Tio, 9s (Mo jl?work/or”)
o, o4) (C(1,14No, ao-ro/guchi I"j
(TI,,, (MO work/also if) 0.04
j (O(+, 56N0.443Z s ha (Tio,
go (Mo and/or U W ) 0.40 ) (
Co, go No, ao) Z%2Jd (Ti@
, -6 (Mo work/also n W ) o, ao ) (
co, io No, io) Z s makes a cermet alloy with high toughness and high heat resistance.
ここで第１図は、本発明の焼結硬質合金の硬質相の炭窒
化物組成の範囲を示すグラフであって、横軸［（ＴｉＸ
（Ｍｏおよび／また［Ｗ）ｙ）（ＯｕＮｖ）ｚ中におけ
るモル分率ｙ１縦軸ｔｄ （Ｔｉｘ（Ｍ。Here, FIG. 1 is a graph showing the range of carbonitride composition of the hard phase of the sintered hard alloy of the present invention, with the horizontal axis [(TiX
Mole fraction y1 in (Mo and/or [W)y)(OuNv)z Vertical axis td (Tix(M.
および／またはＷ ）ｙ） （ＯｕＮｖ）ｚ中における
モル分率Ｖを示し、線イロノにお工び線イロノ為二に工
り囲まれる範囲が本発明の合金の硬質相の範囲である。and/or W ) y) (OuNv) The range surrounded by the line Irono and Irono Tameji is the range of the hard phase of the alloy of the present invention.
本発明の合金の硬質の炭窒化物において、ｙｉｎ０４か
らα４であって、ｙが０．０４工Ｖ小であると強度が大
巾に低下して欠けやすぐなり、また０４０を越えると耐
摩耗性が劣る結果となる。In the hard carbonitride of the alloy of the present invention, if y is from 04 to α4 and y is less than 0.04 mm, the strength will be greatly reduced and will be easily chipped, and if it exceeds 040, the wear resistance will be reduced. This results in inferior performance.
’Ｉｔ ｆｃＺ ｒＪ、０．８０ ｕ 上１−０２ ｍ
下テアッテ、ｚが（１８０エリ小さいと合金中に脆化相
が多くなり欠は易くなり、又１．０２エリ大きいと遊離
炭素が存在し強度が低下する。'It fcZ rJ, 0.80 u upper 1-02 m
If z is smaller by 180 el, there will be more embrittlement phases in the alloy, making it easier to chip, and if it is larger by 1.02 el, free carbon will be present and the strength will decrease.
また第１図の線イニ以上に窒素を含有させると炭窒化物
中の窒素分解圧が高くなり、焼結中に窒素ガスが分解し
、合金中に巣を残し、強度不足となる。さらに線ロバ以
下の窒累倉であると、高温での強度低下、お工び刃先の
塑性変形が大となる。Furthermore, if nitrogen is contained above the line in FIG. 1, the nitrogen decomposition pressure in the carbonitride increases, and the nitrogen gas decomposes during sintering, leaving voids in the alloy, resulting in insufficient strength. Furthermore, if the nitrogen storage is smaller than a wire rod, the strength will decrease at high temperatures and the plastic deformation of the machining cutting edge will be large.
炭窒化物を結合する金属に、鉄族金属お工びり日ム族金
属の１種又は２種以上からなるが、３重ｔチェリ少ない
と強度が低下し、４０重鎗チを越えると、耐摩耗性が大
巾に低下するので、５〜４０重量−が好ましい。The metal that binds the carbonitrides is composed of one or more of the iron group metals, but if there is less 3-layer metal, the strength will decrease, and if it exceeds 40-layer metal, the resistance will decrease. The weight range is preferably 5 to 40% by weight, since the abrasion properties are greatly reduced.
本発明の焼結硬質合金は、上記の炭窒化物が、ＭＯお工
び／又ｔｌＷをモル比でα０１〜Ｑ、５０まで、Ｔａ
、 Ｎｂ ＊ ｚｒ ＊ ｖのうちの１種又は２種以上
で置換することができ、この↓うな置換に１って靭性お
工び耐熱性を向上できるが、モル比がα０１工９少ない
とその効果はな（、（１５０を越えると耐摩耗性に劣る
結果となる。The sintered hard alloy of the present invention is characterized in that the above-mentioned carbonitride has a molar ratio of α01 to Q, 50 to MO and tlW, and Ta
, Nb * zr * v, and this substitution can improve toughness and heat resistance, but if the molar ratio is less α01, the If it exceeds 150, the wear resistance will be poor.
本発明のサーメット合金の製造法としては、Ｔｉｅ 、
ＴｉＮ を添加混合する従来法によっても可能であ
るが、スが発生して焼結しにくい場合もある。The method for producing the cermet alloy of the present invention includes Tie,
Although it is possible to use the conventional method of adding and mixing TiN, sintering may be difficult due to the generation of gas.
したがって本発明のサーメット合金は’ Ａ＋Ｂ（モル
比）が（１５以上のＴｉ （ＯＡＮＢ） のＴ１炭窒
化物粉末および／又ｒｘ Ｏ＋Ｄ （モル比）がα３以
下で古（モル比）が［１５以上の（Ｔｔｏ（Ｍｏお工び
／又はｗ）ＤＨａ、ｎ−の炭窒化物固溶体粉末を用いる
ことに工って、炭窒化物の焼結時の窒素分解圧が低下し
、合金中の巣が生じにくく１９、好適に製造できる。Therefore, the cermet alloy of the present invention is a T1 carbonitride powder of Ti (OANB) with an A + B (molar ratio) of (15 or more) and/or a T1 carbonitride powder of Ti (OANB) with a (molar ratio) of By using (Tto(Mo)/or w) DHa, n- carbonitride solid solution powder, the nitrogen decomposition pressure during sintering of carbonitride is reduced, and the voids in the alloy are reduced. It is less likely to occur19 and can be manufactured suitably.
以上のごときＴ１炭窒化物、Ｔ１炭窒化物同溶体を用い
た場合、真空焼結でも目的とするサーメット合金は可能
であるが、さらに、α１〜５００’ｒｏｒｒ の窒素
分圧で焼結すると、焼結時における合金の表面、内部の
脱窒を防ぐことが可能であり好ましい。When using T1 carbonitride or T1 carbonitride isosolver as described above, it is possible to form the desired cermet alloy by vacuum sintering, but furthermore, if sintered at a nitrogen partial pressure of α1 to 500'rorr, This is preferable since it is possible to prevent denitrification on the surface and inside of the alloy during sintering.
Ｔ１（ＣＡＮＢ ） 中ノＡ＋ Ｂが（Ｌ５ｊｅ）少
ないと、合金中に窒素全多量に含有することができない
。T1(CANB) If the amount of A+B in the alloy is small (L5je), a large amount of nitrogen cannot be contained in the alloy.
また（ Ｔｉ Ｏ（Ｍｏお工び／又はＷ）Ｄ）（Ｏ□Ｎ
、）中の缶が０．３を越えると、ＭｏｚＣ，Ｗｅが析出
したり、高窒素を含有させることができない。Also (Ti O(Mo work/or W)D)(O□N
, ), if the content of the can exceeds 0.3, MozC and We will precipitate and it will not be possible to contain a high nitrogen content.
さらにに＋ｔｌ’ がα５エリ少ないと、合金中に窒
素を多量に含有することができない。Furthermore, if +tl' is less than α5, a large amount of nitrogen cannot be contained in the alloy.
窒素雰囲気にて焼結する際の窒素分圧がα１Ｔｏｒｒ工
９小さいと、脱窒しやすくなり、５００Ｔｏｒｒ ｋ越
えると合金中に巣が生じ、強度低下をきたしたり、表面
に炭窒化物のｌ１ｉｌｉ金生じることに、Ｃり％衣表面
脆くなる。If the nitrogen partial pressure during sintering in a nitrogen atmosphere is small, denitrification will occur easily, and if it exceeds 500 Torr, cavities will form in the alloy, resulting in a decrease in strength, or carbonitrides on the surface. As a result, the coating surface becomes brittle.
焼結温度は１４００〜１５００℃が好ましく、１４００
’Ｃ以下では合金中に巣を生じて強度が低下し、また１
５００℃を越えると、結合金属の鉄族・クロム族金属が
合金中から揮散するため、所期を工９少なくなってしま
う。The sintering temperature is preferably 1400 to 1500°C, and 1400°C
Below 'C, cavities are formed in the alloy and the strength decreases, and
If the temperature exceeds 500°C, iron group metals and chromium group metals, which are bonding metals, will volatilize from the alloy, resulting in less than the expected amount.
以下実施例を挙げて説明する。 This will be explained below with reference to examples.
実施例１
原料粉末として、ＴｉＯ、ＴｉＮ 、 Ｔｉ（Ｃｏ、ｓ
Ｎｏ、ｓ ）ｔＴｉ （ｃｏ、ａ Ｎｏ、ａ ） ｅ
（Ｔｉｅ、ｙＷｏ、ｍ ） （Ｏｏ、ｓ Ｎ６．ｓ）
ｅ （Ｔｉｏ、ｔ Ｗｏ、冨１’！ＯｏＪ ） （０
０，、Ｎ（１，７）、 ’ｒａａ 、 Ｎ’ｉ＋Ｏ、Ｚ
ｒＯ、ＶＣ、Ｃｏ 、 Ｎｉ 。Example 1 As raw material powders, TiO, TiN, Ti(Co, s
No, s ) tTi (co, a No, a ) e
(Tie,yWo,m) (Oo,s N6.s)
e (Tio, t Wo, Tomi 1'!OoJ) (0
0,, N(1,7), 'raa, N'i+O, Z
rO, VC, Co, Ni.
Ｗ、Ｍｏ、Ｏｒ粉末を用い、本発明に従い所定の割合に
混合し、本発明の合金ａ〜ｆｆ製造した。Alloys a to ff of the present invention were manufactured by mixing W, Mo, and Or powders in a predetermined ratio according to the present invention.
それぞれの硬質相（モル比）、結合相（重量％）、焼結
条件、原料を表１にまとめて示す。Table 1 summarizes the hard phase (molar ratio), binder phase (wt%), sintering conditions, and raw materials for each.
また従来、分類の合金ｊ −ｙ ｍを製造し比較例とし
たが、仁れについても、同様に表１に示す。In addition, conventionally, alloys j - y m of classification were manufactured and used as comparative examples, and the pitting is also shown in Table 1.
以上の合金ａ〜ｍについて、以下硬度（ＨＶ）、抗折力
（ｋｌｉ＋／、、” ）を試験し、さらに次の切削試験
を行った。The above alloys a to m were tested for hardness (HV) and transverse rupture strength (kli+/, ''), and were further subjected to the following cutting test.
■ 逃げ面摩耗１（、、＋）
切削条件 被削材：８０Ｍ４５５
切削速度： １８ Ｇ ｍ／ｍｉｎ
送 ０ ： α５ ６ ｍ／ ｒｅＶ切込み：２．Ｏ
ｗｏａ
切削時間：２０分
■ 欠損発生時の送０（■／ｒｅＶ）
切削条件 被削材：８０Ｍ４５５（溝付主材）切削速
度：１５０ｍ／ｍｉｎ
送 ９：変化（漸次上げて、
欠損したときの送り
を確認）
切込み：２．Ｏｍ
切削時間： １ ｍｉｎ
■ 熱亀裂発生本数
切削条件（フライス試験）
被剛材：８０Ｍ４５５
切削速度： ２００ ｒｎ／ ｍｉｎ
送 リ ：（Ｌ２Ｇ、／刃
切込み：２．０ＩＩＩＩ＋
切削時間： ４０ ｍｉｎ
以上の試験結果を表２にまとめて示す。表２から明らか
な工うに、本発明合金は従来の合金に比べ、重切削が可
能で、耐熱性に優れることがわかる。■ Flank wear 1 (,, +) Cutting conditions Work material: 80M455 Cutting speed: 18 G m/min Feed 0: α5 6 m/reV Depth of cut: 2. O
woa Cutting time: 20 minutes■ Feed at the time of fracture 0 (■/reV) Cutting conditions Work material: 80M455 (grooved main material) Cutting speed: 150 m/min Feed 9: Change (gradually increase, (Check feed) Depth of cut: 2. Om Cutting time: 1 min ■ Cutting conditions for number of thermal cracks (milling test) Rigid material: 80M455 Cutting speed: 200 rn/min Feed rate: (L2G, /blade depth of cut: 2.0III+ Cutting time: 40 min or more test) The results are summarized in Table 2. It is clear from Table 2 that the alloy of the present invention is capable of heavy cutting and has superior heat resistance compared to conventional alloys.
〔発明の効果〕
以上説明の如く、本発明は従来に比して、工９多量の窒
素を含有する高Ｎ、含有サーメット合金でありエリ高靭
性かつ耐熱性が向上した優れた焼結硬質合金お工びその
製造法であり、高温での強度低下が少なく重切削や強い
衝撃全骨ける切削に使用可能な焼結硬質合金を提供でき
る。[Effects of the Invention] As explained above, the present invention is a high N-containing cermet alloy that contains a large amount of nitrogen, and is an excellent sintered hard alloy with high toughness and improved heat resistance. This manufacturing method allows us to provide a sintered hard alloy that can be used for heavy cutting and strong impact cutting with little loss of strength at high temperatures.
第１図は本発明サーメットの硬質相である炭窒化物の組
成範囲を示すグラフである。
第２図は特公昭５６−５１２０１号公報記載のサーメッ
トの炭窒化物相組成範囲の１例を示すグラフである。FIG. 1 is a graph showing the composition range of carbonitride, which is the hard phase of the cermet of the present invention. FIG. 2 is a graph showing an example of the carbonitride phase composition range of the cermet described in Japanese Patent Publication No. 56-51201.
Claims (4)
属およびクロム族金属の１種又は２種以上からなり合金
全体の３０〜４０重量％である結合金属とからなる焼結
硬質合金において、該炭窒化物組成が、下記式 ｛Ｔｉ＿ｘ（Ｍｏおよび／又はＷ）＿ｙ｝（Ｃ＿ｕＮ＿
ｖ）＿ｚ（式中、ｘ、ｙは金属元素のモル分率、ｕ、ｖ
は非金属元素のモル分率、ｘ＋ｙ＝１．０、ｕ＋ｖ＝１
．０、ｚは化学量論的パラメーターであり０．８０≦ｚ
≦１．０２である。また、ｙの値は０．０４から０．４
０であり、ｖの値は第１図のイ、ロ、ハ、ニ、によつて
限定される。）で表されることを特徴とする焼結硬質合
金。(1) Sintering consisting of a hard carbonitride phase containing Ti as a product and a bonding metal consisting of one or more of iron group metals and chromium group metals and making up 30 to 40% by weight of the entire alloy. In the hard alloy, the carbonitride composition is expressed by the following formula {Ti_x(Mo and/or W)_y}(C_uN_
v)_z (where x, y are the molar fraction of the metal element, u, v
is the molar fraction of nonmetallic elements, x+y=1.0, u+v=1
．． 0, z are stoichiometric parameters and 0.80≦z
≦1.02. Also, the value of y is from 0.04 to 0.4
0, and the value of v is limited by A, B, C, and D in FIG. ) A sintered hard alloy characterized by:
おいて、（Ｍｏおよび／又はＷ）をモル比で０．０１〜
０．５０までＴａ、Ｎｂ、Ｚｒ、Ｖのうちの１種又は２
種以上で置換したことを特徴とする上記焼結硬質合金。(2) In the sintered hard alloy according to claim (1), the molar ratio of (Mo and/or W) is from 0.01 to
One or two of Ta, Nb, Zr, V up to 0.50
The above-mentioned sintered hard alloy, characterized in that it is substituted with at least one species.
属およびクロム族金属の１種又は２種以上からなり合金
全体の３０〜４０重量％である結合金属とからなる焼結
硬質合金であつて、該炭窒化物組成が、下記式 ｛Ｔｉ＿ｘ（Ｍｏおよび／又はＷ）＿ｙ｝（Ｃ＿ｕＮ＿
ｖ）＿ｚ（式中、ｘ、ｙは金属元素のモル分率、ｕ、ｖ
は非金属元素のモル分率、ｘ＋ｙ＝１．０、ｕ＋ｖ＝１
．０、ｚは化学量論的パラメーターであり０．８０≦ｚ
≦１．０２である。また、ｙの値は０．０４から０．４
０であり、ｖの値は第１図のイ、ロ、ハ、ニ、によつて
限定される。）で表される焼結硬質合金の製造方法であ
つて、Ｂ／（Ａ＋Ｂ）（モル比）が０．５以上のＴｉ（
Ｃ＿ＡＮ＿Ｂ）および／又は、Ｄ／（Ｃ＋Ｄ）（モル比
）が０．３以下で、Ｆ／（Ｅ＋Ｆ）（モル比）が０．５
以上の｛Ｔｉ＿Ｃ（Ｍｏおよび／又はＷ）＿Ｄ｝（Ｃ＿
ＥＮ＿Ｆ）の炭窒化物固溶体粉末に、結合金属として鉄
族金属およびクロム族金属の１種又は２種以上を混合し
た後、所定の形状にプレスし、その後窒素分圧０．１〜
５００Ｔｏｒｒの窒素雰囲気中にて、温度１４００〜１
５００℃にて焼結することを特徴とする上記焼結硬質合
金の製造方法。(3) Sintering consisting of a hard carbonitride phase containing Ti as a product and a bonding metal consisting of one or more of iron group metals and chromium group metals and making up 30 to 40% by weight of the entire alloy. It is a hard alloy, and the carbonitride composition is expressed by the following formula {Ti_x(Mo and/or W)_y}(C_uN_
v)_z (where x, y are the molar fraction of the metal element, u, v
is the molar fraction of nonmetallic elements, x+y=1.0, u+v=1
．． 0, z are stoichiometric parameters and 0.80≦z
≦1.02. Also, the value of y is from 0.04 to 0.4
0, and the value of v is limited by A, B, C, and D in FIG. ) is a method for producing a sintered hard alloy represented by Ti(
C_AN_B) and/or D/(C+D) (molar ratio) is 0.3 or less and F/(E+F) (molar ratio) is 0.5
{Ti_C(Mo and/or W)_D}(C_
EN_F) carbonitride solid solution powder is mixed with one or more of iron group metals and chromium group metals as bonding metals, then pressed into a predetermined shape, and then nitrogen partial pressure is 0.1~
In a nitrogen atmosphere of 500 Torr, at a temperature of 1400 to 1
The method for producing the sintered hard alloy described above, characterized by sintering at 500°C.
．５０までＴａ、Ｎｂ、Ｚｒ、Ｖのうちの１種又は２種
以上で置換した特許請求の範囲第（３）項に記載の焼結
硬質合金の製造方法。(4) (Mo and/or W) in a molar ratio of 0.01 to 0
．． The method for producing a sintered hard alloy according to claim 3, wherein up to 50% of the sintered hard alloy is replaced with one or more of Ta, Nb, Zr, and V.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59206380A JPS6184350A (en) | 1984-10-03 | 1984-10-03 | Sintered hard alloy and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59206380A JPS6184350A (en) | 1984-10-03 | 1984-10-03 | Sintered hard alloy and its manufacture |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6184350A true JPS6184350A (en) | 1986-04-28 |
| JPH0471986B2 JPH0471986B2 (en) | 1992-11-17 |
Family
ID=16522378
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP59206380A Granted JPS6184350A (en) | 1984-10-03 | 1984-10-03 | Sintered hard alloy and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6184350A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62170452A (en) * | 1986-01-22 | 1987-07-27 | Hitachi Carbide Tools Ltd | Ticn-base cermet |
| JPS6357732A (en) * | 1986-08-27 | 1988-03-12 | Sumitomo Electric Ind Ltd | Cermet sintering method |
| JPH0273945A (en) * | 1988-09-08 | 1990-03-13 | Toyo Kohan Co Ltd | Cermet tool for drawing-ironing can forming |
| CN109053191A (en) * | 2018-08-17 | 2018-12-21 | 中南大学 | A kind of soap-free emulsion polymeization phase base titanium carbonitride and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5146509A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | Niobu ofukumu chokoshitsugokin |
| JPS5146508A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | |
| JPS5146510A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | Banajiumu ofukumu chokoshitsugokin |
| JPS5146511A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | |
| JPS613853A (en) * | 1984-06-18 | 1986-01-09 | Sumitomo Electric Ind Ltd | Manufacture of sintered hard alloy |
-
1984
- 1984-10-03 JP JP59206380A patent/JPS6184350A/en active Granted
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5146509A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | Niobu ofukumu chokoshitsugokin |
| JPS5146508A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | |
| JPS5146510A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | Banajiumu ofukumu chokoshitsugokin |
| JPS5146511A (en) * | 1974-10-18 | 1976-04-21 | Sumitomo Electric Industries | |
| JPS613853A (en) * | 1984-06-18 | 1986-01-09 | Sumitomo Electric Ind Ltd | Manufacture of sintered hard alloy |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62170452A (en) * | 1986-01-22 | 1987-07-27 | Hitachi Carbide Tools Ltd | Ticn-base cermet |
| JPS6357732A (en) * | 1986-08-27 | 1988-03-12 | Sumitomo Electric Ind Ltd | Cermet sintering method |
| JPH0273945A (en) * | 1988-09-08 | 1990-03-13 | Toyo Kohan Co Ltd | Cermet tool for drawing-ironing can forming |
| CN109053191A (en) * | 2018-08-17 | 2018-12-21 | 中南大学 | A kind of soap-free emulsion polymeization phase base titanium carbonitride and preparation method thereof |
| CN109053191B (en) * | 2018-08-17 | 2021-11-30 | 中南大学 | Titanium carbonitride based cermet without binder phase and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0471986B2 (en) | 1992-11-17 |
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