JP2796894B2 - High speed steel based sintered alloy - Google Patents

High speed steel based sintered alloy

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Publication number
JP2796894B2
JP2796894B2 JP2418060A JP41806090A JP2796894B2 JP 2796894 B2 JP2796894 B2 JP 2796894B2 JP 2418060 A JP2418060 A JP 2418060A JP 41806090 A JP41806090 A JP 41806090A JP 2796894 B2 JP2796894 B2 JP 2796894B2
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Japan
Prior art keywords
sintered alloy
resistance
less
test
effect
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JP2418060A
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Japanese (ja)
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JPH04221042A (en
Inventor
晃 浜田
善雄 片山
淳 船越
秀雄 藤田
Original Assignee
株式会社クボタ
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Description

【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION
【0001】[0001]
【産業上の利用分野】本発明は鋼材圧延用ロール等のよ
うに、耐摩耗性、耐肌荒性、耐焼付性等が要求される部
材の構成材料として有用な高速度鋼系焼結合金に関す
る。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-speed steel-based sintered alloy useful as a constituent material for members requiring wear resistance, surface roughness resistance, seizure resistance, etc., such as rolls for steel rolling. About.
【0002】[0002]
【従来の技術】鋼材の熱間圧延または冷間圧延用ロール
の胴部表面は、耐摩耗性の良いこと、肌荒れ(亀裂、凸
凹、欠け等)を生じ難いこと、被圧延材との焼き付きを
生じ難いこと等が必要である。従来より、熱間圧延用ロ
ールとして鋳鉄ロールが、冷間圧延用ロールとしては鍛
鋼ロールがそれぞれ使用されてきた。近時は、圧延条件
の苛酷化対策・ロール耐用寿命向上策として、熱間等方
圧加圧焼結等により胴部表面に高速度鋼系化学組成を有
する焼結合金層を形成したロールの使用も試みられてい
る(特開昭58−213856号、特開昭63−297
510号等)。
2. Description of the Related Art The surface of a body of a roll for hot rolling or cold rolling of a steel material has good abrasion resistance, is hardly roughened (cracks, unevenness, chipping, etc.), and has seizure with a material to be rolled. It is necessary for things to hardly occur. Conventionally, cast iron rolls have been used as hot rolling rolls, and forged steel rolls have been used as cold rolling rolls. Recently, as a measure to reduce the rolling conditions and to improve the service life of the roll, a roll with a sintered alloy layer having a high-speed steel-based chemical composition formed on the body surface by hot isostatic pressing sintering, etc. It has also been tried for use (JP-A-58-21856, JP-A-63-297).
No. 510).
【0003】[0003]
【発明が解決しようとする課題】高速度鋼系合金は、焼
入れ・焼もどしの調質熱処理が施されてマルテンサイト
またはベイナイト相の硬質の基地に微細な炭化物粒子が
析出分散した金属組織となる。その硬質の基地と、炭化
物粒子の分散強化作用とにより、良好な耐摩耗性や耐肌
荒れ性等を帯有し、これを圧延用ロールに適用すること
によりロール寿命の向上を期待することが可能となる。
本発明は高速度鋼系焼結合金の材料特性を更に改良する
ことを目的としてなされたものである。
The high-speed steel alloy has a metal structure in which fine carbide particles are precipitated and dispersed in a hard matrix of a martensite or bainite phase by performing a tempering heat treatment such as quenching and tempering. . Due to its hard matrix and the effect of strengthening the dispersion of carbide particles, it has good abrasion resistance and rough surface resistance, etc., and it can be expected to improve the roll life by applying it to rolling rolls. Becomes
The present invention has been made to further improve the material properties of a high-speed steel-based sintered alloy.
【0004】[0004]
【課題を解決するための手段および作用】本発明の高速
度鋼系焼結合金は、C:1.7 %を越え,3.5%以下、S
i:0.6 %を越え,3.5%以下、Mn:0.6 %以下、C
r:3〜8%、Mo:3〜9%、W:5〜14%、Co:
7〜14%、V,Ti,Nbの1種ないし2種以上:8%
を越え,11 %以下(合計量) 、およびB: 2%以下,N
i: 3%以下の1種または2種、残部実質的にFeから
なる化学組成を有している。以下、本発明に係る焼結合
金の成分限定理由を説明する。元素含有量を示す%はす
べて重量である。
The high-speed steel-based sintered alloy of the present invention has a C content of more than 1.7% and not more than 3.5%.
i: more than 0.6%, 3.5% or less, Mn: 0.6% or less, C
r: 3 to 8%, Mo: 3 to 9%, W: 5 to 14%, Co:
7-14%, one or more of V, Ti, Nb: 8%
, 11% or less (total amount) , and B: 2% or less, N
i: one or two or less of 3% or less, substantially from Fe
Has the following chemical composition: Hereinafter, the reasons for limiting the components of the sintered alloy according to the present invention will be described. All percentages indicating elemental content are weight percent .
【0005】C: 1.7 %を超え、3.5 %以下 Cは炭化物形成元素であり、V,Ti,Nb,W,M
o,Cr等と結合して、MC型、M6 C型、M2 C型等
の炭化物を形成し、合金の硬度を高める。この効果を十
分ならしめるため、含有量を1.7 %超とする。しかし、
Cの増量は反面において、炭化物の過剰析出や粗大化等
による合金の靱性劣化および加工性の低下等の原因とな
る。このため、3.5 %を上限とした。
C: more than 1.7% and not more than 3.5% C is a carbide forming element , and V, Ti, Nb, W, M
By combining with o, Cr, etc., carbides such as MC type, M 6 C type, M 2 C type are formed, and the hardness of the alloy is increased. In order to make this effect sufficient, the content is made more than 1.7%. But,
On the other hand, an increase in the amount of C, on the other hand, causes deterioration of the alloy toughness and workability due to excessive precipitation and coarsening of carbides. Therefore, the upper limit was 3.5%.
【0006】Si:0.6%を越え、3.5%以下 Siは脱酸作用、および焼入れ性改善効果を有し、また
耐食性、殊に孔食抵抗性を高める。焼入れ性改善効果
は、0.6%以下の添加でも認められるが、耐食性改善
効果を確保するためには0.6%を越える添加を必要と
する。また、Siの一部はMC型炭化物のM元素(W
等)と置換し、M元素の節減を可能とする。添加増量に
よりこれらの効果を増すが、反面炭化物の析出量の増加
に伴い合金の脆化を招くので、3.5%を上限とする。
Si: more than 0.6% and not more than 3.5% Si has a deoxidizing effect and an effect of improving hardenability, and also enhances corrosion resistance, especially pitting resistance. The effect of improving hardenability is observed even when the addition is 0.6% or less, but in order to secure the effect of improving corrosion resistance, the addition needs to exceed 0.6%. In addition, part of Si is an M element of M 6 C-type carbide (W element).
, Etc.) to save M elements. Although these effects are increased by increasing the amount of addition, the alloy is embrittled with an increase in the amount of carbide precipitation, so the upper limit is 3.5%.
【0007】Mn:0.6%以下 Mnは脱酸作用を有し、また焼入性の改善効果を有す
る。この効果を得るための添加量は0.6%までで十分
であり、多量の添加は高温におけるオーステナイト粒の
粗大化を招き、合金の脆化の原因となる。このため、
0.6%を上限とした。好ましくは、0.2〜0.4%
である。
Mn: 0.6% or less Mn has a deoxidizing effect and an effect of improving hardenability. The addition amount for obtaining this effect is sufficient up to 0.6%, and a large amount of addition causes coarsening of austenite grains at a high temperature and causes embrittlement of the alloy. For this reason,
The upper limit was 0.6%. Preferably, 0.2-0.4%
It is.
【0008】Cr:3〜8% Crは合金の焼入性改善元素であり、また耐食性の向上
に寄与する。この効果を得るには少なくとも3%を必要
とする。添加増量に伴って効果を増すが、焼入れ性改善
効果は約5%までの添加で十分に得られる。耐食性改善
効果は5%を越える添加により顕著となり、特に耐孔食
性の強化に奏効する。しかし、多量添加に伴って衝撃特
性の低下や高温での軟化抵抗性の低下を生じるので、8
%を上限とする。
[0008] Cr: 3 to 8% Cr is an element for improving the hardenability of the alloy and contributes to the improvement of corrosion resistance. This effect requires at least 3%. The effect increases as the amount of addition increases, but the effect of improving hardenability can be sufficiently obtained by adding up to about 5%. The effect of improving corrosion resistance becomes remarkable when added over 5%, and is particularly effective in enhancing pitting corrosion resistance. However, the addition of a large amount causes a decrease in impact characteristics and a decrease in softening resistance at high temperatures.
% As the upper limit.
【0009】Mo:3〜9% Moは、焼入れ性改善に著効に奏し、かつ焼もどし軟化
抵抗性の向上に寄与する。また、MC型炭化物として
微細析出し二次硬化をもたらす。これらの効果は3%以
上の添加により確保される。しかし、9%を越えると効
果はほぼ飽和する。
Mo: 3 to 9% Mo is remarkably effective in improving hardenability and contributes to improvement in temper softening resistance. In addition, it precipitates finely as an M 2 C-type carbide and causes secondary hardening. These effects are ensured by adding 3% or more. However, if it exceeds 9%, the effect is almost saturated.
【0010】W:5〜14% Wは、焼入れのためのオーステナイト化時に固溶して焼
入れ性を高める効果を有する。またWは強力な炭化物形
成元素であり、焼もどし処理により、MC型炭化物と
して微細析出し顕著な二次硬化をもたらす。また、焼も
どし軟化抵抗性を示す。添加量の下限を5%としたの
は、その炭化物の析出による十分な二次硬化を得るため
である。添加増量により、その効果を増すが、反面析出
炭化物の粗大化による靭性等の低下をみるので、14%
を上限とした。
W: 5 to 14% W has the effect of forming a solid solution at the time of austenitization for quenching to enhance quenchability. W is a strong carbide-forming element, and is finely precipitated as M 6 C-type carbide by tempering to bring about remarkable secondary hardening. In addition, it shows tempering softening resistance. The lower limit of the addition amount is set to 5% in order to obtain sufficient secondary hardening due to precipitation of the carbide. The effect is increased by increasing the amount of addition, but on the other hand, a decrease in toughness and the like due to coarsening of precipitated carbides is observed.
Was set as the upper limit.
【0011】V、Ti、Nb:8%を越え、11%以下 V、Ti、Nbは、焼入れ後の焼もどし処理により、微
細なMC型炭化物として析出し顕著な二次硬化をもたら
す。この効果を十分ならしめるため、添加量は8%超
(2種以上の場合はその合計量)とする。しかし、あま
り多く添加すると炭化物の過剰析出により、合金の靭性
低下を伴い、また加工性が悪くなるので、11%を上限
とする。
V, Ti, Nb: more than 8%, not more than 11% V, Ti, Nb are precipitated as fine MC type carbides by tempering after quenching and bring about remarkable secondary hardening. In order to sufficiently enhance this effect, the addition amount is set to more than 8% (the total amount in the case of two or more types). However, if too much is added, excessive precipitation of carbides causes a decrease in the toughness of the alloy, and the workability deteriorates. Therefore, the upper limit is 11%.
【0012】Co:7〜14% Coは、焼入れ性を高め、また基地に固溶して耐熱性を
高め、高温強度の改善に寄与する。これらの効果は7%
以上の添加により得られる。しかし、約14%をこえる
と効果はほぼ飽和するので、14%を上限とする。
Co: 7-14% Co enhances hardenability and increases the heat resistance by forming a solid solution with the matrix, thereby contributing to improvement in high-temperature strength. These effects are 7%
It is obtained by the above addition. However, if the ratio exceeds about 14%, the effect is almost saturated. Therefore, the upper limit is set to 14%.
【0013】本発明の焼結合金は上記諸元素とともに、
2%以下のB、および3%以下のNiの1種または2種
の元素を含有している。
[0013] The sintered alloy of the present invention, together with the above elements,
Contains one or two elements of up to 2% B and up to 3% Ni .
【0014】B: 2%以下 Bは、C代替元素であり、化物を形成して耐摩耗性の
向上に寄与する。2%のBは1%のCに等価である。ま
た基地中に固溶して基地を強化する。しかし、多量の添
加は、合金の融点を下げ、強度の低下の原因となるの
で、2%を上限とする。好ましくは、0.2 〜1%であ
る。
[0014] B: 2% or less B, and C alternate element, which contributes to the improvement of wear resistance by forming the boron compound. 2% B is equivalent to 1% C. In addition, solid solution in the base strengthens the base. However, the addition of a large amount lowers the melting point of the alloy and lowers the strength, so the upper limit is 2%. Preferably, it is 0.2-1%.
【0015】Ni:3%以下 Niは、オーステナイト相安定化元素であり、残留オー
ステナイト量の増加による靭性の改善に奏効する。しか
し、オーステナイト量の増加は、反面において機械加工
の困難化を招くので、3%を越えてはならない。好まし
くは0.1%〜2.5%とする。
Ni: 3% or less Ni is an austenite phase stabilizing element, and is effective in improving toughness by increasing the amount of retained austenite. However, the increase in the amount of austenite, on the other hand, causes difficulty in machining, so that it should not exceed 3%. Preferably, it is 0.1% to 2.5%.
【0016】本発明の焼結合金を製造するための焼結手
法は任意であるが、好ましくは熱間等方圧加圧焼結法
(HIP焼結法)が適用される。HIP焼結法によれ
ば、高加圧力の均一な作用下に高緻密質の焼結合金を得
ることができるからである。
The sintering method for producing the sintered alloy of the present invention is arbitrary, but preferably a hot isostatic pressing sintering method (HIP sintering method) is applied. According to the HIP sintering method, a high-density sintered alloy can be obtained under a uniform action of a high pressing force.
【0017】本発明の焼結合金は各種用途に供される
が、耐摩耗性や耐肌荒れ性等は部材の表面の問題である
ので、例えば圧延用ロールの胴部に本発明の焼結合金を
適用する場合には、適当な金属材料(例えば、JIS
G 4105 のCr−Mo系合金鋼、同4103のC
r−Ni−Mo系合金鋼等)からなる中空もしくは中実
形状の円柱体を基材とし、その外周を本発明の焼結合金
で被覆した積層構造を有するロール胴部を形成するとよ
い。
The sintered alloy of the present invention is used in various applications. However, wear resistance and rough surface resistance are problems of the surface of the member. When applying a suitable metal material (for example, JIS
Cr-Mo alloy steel of G 4105, C of 4103
It is preferable to form a roll body having a laminated structure in which a hollow or solid cylindrical body made of an r-Ni-Mo alloy steel or the like is used as a base material and the outer periphery thereof is coated with the sintered alloy of the present invention.
【0018】本発明の焼結合金を以て金属基材の表面を
被覆した複合部材(例えば圧延用ロール)の製造工程に
ついて説明すると、まず金属基材の周囲を適当なカプセ
ル材(例えば、炭素鋼製円筒体)で囲包し、これに焼結
原料として所定の化学組成を有する合金粉末(ガスアト
マイズ粉等、粒径 例えば500μm以下)をを充填
し、その粉末充填層を脱気し、密封したうえ、熱間等方
圧加圧焼結に付して焼結合金層を形成する。焼結合金粉
末が比較的多量の酸化皮膜を付随するものである場合
は、粉末充填層内に水素含有ガス等の還元ガスを導入し
加熱下に酸化皮膜を還元除去したのち、脱気密封して焼
結処理を行えばよい。焼結処理は、温度:900〜12
00℃、加圧力:約500〜1500kgf/cm
適当時間(約2〜4Hr)を保持することにより好適に
達成される。その焼結過程において焼結合金層と金属基
材との界面には強固な密着結合関係が形成される。焼結
完了後、機械加工によりカプセル材の除去および必要な
形状修正を行う。
The manufacturing process of a composite member (for example, a roll for rolling) in which the surface of a metal substrate is coated with the sintered alloy of the present invention will be described. First, a suitable encapsulant (for example, carbon steel And filled with an alloy powder having a predetermined chemical composition as a sintering raw material (gas atomized powder or the like, particle size of, for example, 500 μm or less), and the powder-filled layer is degassed and sealed. And hot isostatic pressing to form a sintered alloy layer. If the sintered alloy powder is accompanied by a relatively large amount of oxide film, a reducing gas such as a hydrogen-containing gas is introduced into the powder packed layer, the oxide film is reduced and removed under heating, and then degassed and sealed. Sintering may be performed. The sintering process is performed at a temperature of 900 to 12
It is preferably achieved by maintaining a suitable time (about 2 to 4 hours) at 00 ° C. and a pressure of about 500 to 1500 kgf / cm 2 . During the sintering process, a strong close bonding relationship is formed at the interface between the sintered alloy layer and the metal substrate. After the completion of sintering, the capsule material is removed by machining and the necessary shape is corrected.
【0019】上記のように金属基材の表面に焼結合金層
を形成した後、焼結合金層に調質熱処理(焼入れ・焼も
どし)を行う。その焼入れ・焼もどし処理は常法に従っ
て行えばよく、焼入れ温度は約1050〜1250℃、
好ましくは1100〜1200℃であり、同温度からの
冷却は、油浴、塩浴等を使用することも可能ではある
が、熱応力に起因する焼結合金層の亀裂・割れ等の防止
のために、ガス(Nガス等)を冷媒とし、略常圧、ま
たは加圧(例えば3〜7kgf/cm)雰囲気中にお
いて制御された冷却速度(例えば5〜20℃/分)で冷
却するとよい。
After forming the sintered alloy layer on the surface of the metal substrate as described above, the tempered heat treatment (quenching / tempering) is performed on the sintered alloy layer. The quenching / tempering treatment may be performed according to a conventional method, and the quenching temperature is about 1050 to 1250 ° C.
Preferably, the temperature is from 1100 to 1200 ° C. For cooling from the same temperature, an oil bath, a salt bath, or the like can be used, but in order to prevent cracking and cracking of the sintered alloy layer due to thermal stress. to, may gas (N 2 gas) as a refrigerant, cooled substantially at atmospheric pressure or pressure (e.g. 3~7kgf / cm 2) cooling at a controlled rate in an atmosphere, (e.g., 5 to 20 ° C. / min) .
【0020】焼入れにつづく焼もどし処理は、約500
〜600℃好ましくは520〜580℃に加熱保持した
のち、徐冷(例えば空冷)する操作を1回、または複数
回(例えば2〜4回)実施することにより達成される。
The tempering treatment following the quenching is about 500
After heating and maintaining the temperature at 徐 600 ° C., preferably 520-580 ° C., the operation is gradually cooled (for example, air-cooled) once or a plurality of times (for example, 2 to 4 times).
【0021】本発明の焼結合金は、焼入れ・焼もどし処
理により、マルテンサイトもしくはベイナイト相、また
はこれらの相を主相とし少量の残留オーステナイト相が
混在しているマトリックスに、炭化物が微細に析出分散
した金属組織が与えられる。その析出炭化物は面積率で
約25〜45%を占め、一般の溶製材における炭化物量
(通常、約10〜15%)に比し豊富であり、かつ均一
に分散している。本発明の焼結合金は、前記化学組成と
金属組成とによって、圧延用ロールの胴部構成材料等と
して望まれる改良された耐摩耗性、耐肌荒性、耐焼付
性、耐腐食性等を備えている。
In the sintered alloy of the present invention, carbide is finely precipitated by quenching and tempering on a martensite or bainite phase or a matrix containing these phases as a main phase and a small amount of a retained austenite phase. A distributed metallographic structure is provided. The precipitated carbides occupy about 25 to 45% in area ratio, and are abundant and uniformly dispersed as compared with the amount of carbides (usually about 10 to 15%) in general ingots. The sintered alloy of the present invention has improved abrasion resistance, skin roughness resistance, seizure resistance, corrosion resistance, etc., which are desired as a material for the body of a rolling roll, etc., by the chemical composition and the metal composition. Have.
【0022】図1は本発明に係る焼結合金の用途の具体
例として、円筒形状の金属基材(11)の外周面に焼結
合金層(12)を形成した積層構造を有する円筒体の断
面構造を模式的に示している。この複合部材(10)
は、例えばその中空孔内に別途用意したアーバー(2
0)を嵌着して圧延用ロールとして使用される。図の例
では、一定の層厚を有する焼結合金層(12)を基材
(11)の外周面の全体に亘って形成しているが、必ず
しもそうである必要はなく、例えば丸鋼仕上圧延ロール
等のカリバーを有するロールでは、その円周溝面にのみ
焼結合金層を形成し、他の部分は基材の表面が露出した
ままの部分複合構造としてよいことはいうまでもない。
焼結合金層(12)の層厚は特に限定されないが、圧延
用ロールの場合は、あまり薄いと、圧延荷重による剪断
応力の作用で焼結合金層の剥離を生じ易くなるので、約
3mm以上の層厚であるので好ましい。もっとも、あま
り厚くすると、熱応力による亀裂を生じ易くなるので、
約25mmまでとするのが適当である。
FIG. 1 shows, as a specific example of the use of the sintered alloy according to the present invention, a cylindrical body having a laminated structure in which a sintered alloy layer (12) is formed on the outer peripheral surface of a cylindrical metal substrate (11). 2 schematically shows a cross-sectional structure. This composite member (10)
Is, for example, an arbor (2) prepared separately in the hollow hole.
0) is used as a roll for rolling. In the example shown in the figure, the sintered alloy layer (12) having a constant layer thickness is formed over the entire outer peripheral surface of the base material (11). In a roll having a caliber such as a rolling roll, a sintered alloy layer may be formed only on the circumferential groove surface, and the other portion may have a partial composite structure in which the surface of the base material is exposed.
The thickness of the sintered alloy layer (12) is not particularly limited, but in the case of a roll for rolling, if it is too thin, the sintered alloy layer is likely to peel off due to the action of shear stress due to the rolling load. It is preferable because the layer thickness is However, if it is too thick, cracks due to thermal stress tend to occur,
Suitably it is up to about 25 mm.
【0023】[0023]
【実施例】所定の化学組成に調製された金属粉末(平均
粒径:200μm)を焼結原料とし、熱間等方圧加圧焼
結を行い、ついでその焼結合金ブロックに焼入れ・焼も
どし処理を行って供試焼結合金を得た。但し、焼結処理
は、温度:1150℃、加圧力:1000kgf/cm
、保持時間:3Hrの条件で行い、焼入れ処理は、真
空焼入れチャンバー内で、1200℃に1時間保持後、
ガス(常温・常圧)を導入してガス冷却することに
より行い、焼もどし処理は540℃に5時間加熱保持し
て放冷するヒートパターンを3回反復した。
EXAMPLE A metal powder (average particle size: 200 μm) prepared to a predetermined chemical composition is used as a sintering material, hot isostatic pressing and sintering, and then quenched and tempered in the sintered alloy block. By performing the treatment, a test sintered alloy was obtained. However, the sintering process was performed at a temperature of 1150 ° C. and a pressure of 1000 kgf / cm.
2. Holding time: performed under the condition of 3Hr, and the quenching treatment was performed at 1200 ° C for 1 hour in a vacuum quenching chamber.
Heating was performed by introducing N 2 gas (normal temperature and normal pressure) and gas cooling, and the tempering treatment was repeated three times in a heat pattern of heating and holding at 540 ° C. for 5 hours and allowing to cool.
【0024】表1に供試焼結合金の化学組成を示す。各
供試焼結合金について、硬度(Hs)測定、および摩耗
試験、耐食試験、焼付性試験、熱衝撃試験、曲げ試験を
行って表2に示す結果を得た。供試No.1〜6 は発明例、
No.101〜105 は比較例である。
Table 1 shows the chemical composition of the test sintered alloy. For each of the test sintered alloys, a hardness (Hs) measurement, a wear test, a corrosion resistance test, a seizure test, a thermal shock test, and a bending test were performed, and the results shown in Table 2 were obtained. Test Nos. 1 to 6 are invention examples,
Nos. 101 to 105 are comparative examples.
【0025】(1)摩耗試験 大越式迅速摩耗試験により比摩耗量Ws(mm/kg
f)を測定 (i)回転輪:SUJ2:硬度(HRC)60、回転輪
幅3.0mm (ii)摩耗速度:3.4m/sec (iii)摩耗距離:200m (iv)最終荷重:16.8kg・f
(1) Wear test The specific wear amount Ws (mm 2 / kg)
f) measuring (i) rotating ring: SUJ2: hardness (H RC) 60, the rotation wheel width 3.0 mm (ii) the wear rate: 3.4m / sec (iii) Wear distance: 200 meters (iv) final load: 16 .8kg ・ f
【0026】(2)腐食試験 試験片(試験面積35×35,mm)を塩水(約800
cc+NaCl69.5g,濃度8%)に24時間浸漬
し、大気中で24時間放置乾燥する処理を、5回反復実
施し、試験片の孔食発生状況を肉眼観察する。表2中
「孔食数」欄の数値は、試験片表面に発生した孔食によ
る微小凹孔の個数を示している。
(2) Corrosion test A test piece (test area 35 × 35, mm) was subjected to salt water (about 800
(cc + NaCl 69.5 g, concentration 8%) for 24 hours, and left to dry in the air for 24 hours. The numerical value in the column of "number of pits" in Table 2 indicates the number of micro-pits due to pitting generated on the surface of the test piece.
【0027】(3)耐焼付性試験 ファレックス型焼付試験(押付荷重;150kg)によ
り、試験片表面に相手材(SUS304ステンレス鋼)
を押付けて回転トルクを測定し、トルクの異常変動の有
無により試験片と相手材との摺接面間の焼付の有無を判
定する(試験時間:5分)。表1中、「耐焼付性」欄の
「〇」は焼付き無し(トルク低位安定)、「×」は焼付
き発生(トルク異常変動)を意味している。
(3) Seizure resistance test According to a Falex type seizure test (pressing load: 150 kg), a mating material (SUS304 stainless steel) was applied to the surface of the test piece.
Is pressed to measure the rotational torque, and the presence or absence of seizure between the sliding contact surface of the test piece and the mating material is determined based on the presence or absence of abnormal fluctuation in torque (test time: 5 minutes). In Table 1, “〇” in the “seizure resistance” column means no seizure (low torque stability), and “×” means seizure occurrence (abnormal torque fluctuation).
【0028】(4)熱衝撃試験 試験片(Φ25×t5,mm)を900℃に1Hr加熱
したのち、水中に投入する加熱・急冷のヒートサイクル
を反復。試験片表面のクラック発生の有無をダイチェッ
クにより判定。表2中、「熱衝撃性」欄の数値は、割れ
発生までのヒートサイクル反復回数を示し、○マーク
は、20回の反復経過時点で割れの発生がなかったこと
を表している。
(4) Thermal Shock Test A heat cycle of heating and quenching, in which a test piece (Φ25 × t5, mm) is heated to 900 ° C. for 1 hour and then put into water, is repeated. The presence or absence of cracks on the test piece surface was determined by die check. In Table 2, the values in the column of "thermal shock resistance" indicate the number of heat cycle repetitions up to the occurrence of cracks, and the mark "O" indicates that no cracks occurred after the repetition of 20 times.
【0029】(5)曲げ試験 3点曲げ法により曲げ強さ(kgf/mm)を測定。
試験片サイズ:3×4×50,mm、スパン距離:30
mm。
(5) Bending test The bending strength (kgf / mm 2 ) was measured by a three-point bending method.
Test piece size: 3 x 4 x 50, mm, span distance: 30
mm.
【0030】[0030]
【表1】 [Table 1]
【0031】[0031]
【表2】 [Table 2]
【0032】上記実施例の試験結果は、発明例の焼結合
金は、従来の高速度鋼系焼結合金を凌ぐ改良された耐摩
耗性、強度、耐食性、耐肌荒れ性、耐熱衝撃性等を備え
ていることを示している。
The test results of the above examples are based on the fire bond of the invention examples .
Gold has been shown to have improved wear resistance, strength, corrosion resistance, surface roughness resistance, thermal shock resistance, etc., over conventional high speed steel-based sintered alloys.
【0033】[0033]
【発明の効果】本発明の焼結合金は、その化学組成と金
属組織とにより、すぐれて安定した耐摩耗性、強度、耐
食性、耐肌荒れ性、耐焼付性等を具備しているので、例
えば、金属円筒体の表面を本発明の焼結合金で被覆して
圧延用ロールの胴部材として使用することにより、ロー
ル寿命の向上、ロールメンテナンスの軽減等の効果が得
られ、またその胴部表面状態が安定していることによ
り、被圧延材の品質改善にも大きな効果が得られる。な
お、本発明焼結合金は、そのほか軸受、シリンダ等の耐
摩耗性等を必要とする構造部材の表面改質材料等として
も有用である。
The sintered alloy of the present invention has excellent and stable wear resistance, strength, corrosion resistance, rough surface resistance, seizure resistance, etc. due to its chemical composition and metal structure. By coating the surface of the metal cylinder with the sintered alloy of the present invention and using it as a body member of a rolling roll, effects such as improvement of roll life, reduction of roll maintenance, etc. are obtained, and the body surface When the state is stable, a great effect can be obtained in improving the quality of the material to be rolled. In addition, the sintered alloy of the present invention is also useful as a surface modification material for structural members requiring wear resistance such as bearings and cylinders.
【図面の簡単な説明】[Brief description of the drawings]
【図1】本発明の焼結合金を金属基材の表面に適用した
例を示す断面説明図である。
FIG. 1 is an explanatory sectional view showing an example in which a sintered alloy according to the present invention is applied to a surface of a metal substrate.
【符号の説明】[Explanation of symbols]
11 金属基材 12 焼結合金層 11 Metal substrate 12 Sintered alloy layer
フロントページの続き (72)発明者 片山 善雄 兵庫県尼崎市西向島町64番地株式会社ク ボタ尼崎工場内 (56)参考文献 特開 平1−225747(JP,A) 特開 平1−155242(JP,A) 特開 昭63−297510(JP,A) 特開 平4−72042(JP,A) (58)調査した分野(Int.Cl.6,DB名) C22C 38/00 304Continuation of the front page (72) Inventor Yoshio Katayama 64, Nishimukaijima-cho, Amagasaki-shi, Hyogo Prefecture Kubota Amagasaki Plant Co., Ltd. (56) References JP-A-63-297510 (JP, A) JP-A-4-72042 (JP, A) (58) Fields investigated (Int. Cl. 6 , DB name) C22C 38/00 304

Claims (3)

    (57)【特許請求の範囲】(57) [Claims]
  1. 【請求項1】 C:1.7 %を越え,3.5%以下、Si:0.
    6 %を越え,3.5%以下、Mn:0.6 %以下、Cr:3〜
    8%、Mo:3〜9%、W:5〜14%、Co:7〜14
    %、V, Ti,Nbの1種ないし2種以上:8%を越
    え,11 %以下、B:2%以下、残部実質的にFeからな
    る高速度鋼系焼結合金。
    1. C: Exceeding 1.7%, 3.5% or less, Si: 0.
    Over 6%, 3.5% or less, Mn: 0.6% or less, Cr: 3 ~
    8%, Mo: 3-9%, W: 5-14%, Co: 7-14
    %, One or more of V, Ti, and Nb: more than 8%, 11% or less, B: 2% or less, the balance being a high-speed steel-based sintered alloy consisting essentially of Fe.
  2. 【請求項2】 C:1.7 %を越え,3.5%以下、Si:0.
    6 %を越え,3.5%以下、Mn:0.6 %以下、Cr:3〜
    8%、Mo:3〜9%、W:5〜14%、Co:7〜14
    %、V, Ti, Nbの1種ないし2種以上:8%を越
    え,11 %以下、Ni:3%以下、残部実質的にFeから
    なる高速度鋼系焼結合金。
    2. C: more than 1.7%, not more than 3.5%, Si: 0.
    Over 6%, 3.5% or less, Mn: 0.6% or less, Cr: 3 ~
    8%, Mo: 3-9%, W: 5-14%, Co: 7-14
    %, One or more of V, Ti, and Nb: more than 8%, 11% or less, Ni: 3% or less, and a high-speed steel-based sintered alloy consisting essentially of Fe.
  3. 【請求項3】 C:1.7 %を越え,3.5%以下、Si:0.
    6 %を越え,3.5%以下、Mn:0.6 %以下、Cr:3〜
    8%、Mo:3〜9%、W:5〜14%、Co:7〜14
    %、V, Ti, Nbの1種ないし2種以上:8%を越
    え,11 %以下、Ni:3%以下、B:2%以下、残部実
    質的にFeからなる高速度鋼系焼結合金。
    3. C: more than 1.7%, not more than 3.5%, Si: 0.
    Over 6%, 3.5% or less, Mn: 0.6% or less, Cr: 3 ~
    8%, Mo: 3-9%, W: 5-14%, Co: 7-14
    %, One or more of V, Ti, Nb: more than 8%, 11% or less, Ni: 3% or less, B: 2% or less, balance: Fe-based high-speed steel-based sintered alloy .
JP2418060A 1990-12-19 1990-12-19 High speed steel based sintered alloy Expired - Lifetime JP2796894B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
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Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2418060A JP2796894B2 (en) 1990-12-19 1990-12-19 High speed steel based sintered alloy

Publications (2)

Publication Number Publication Date
JPH04221042A JPH04221042A (en) 1992-08-11
JP2796894B2 true JP2796894B2 (en) 1998-09-10

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102994692B (en) * 2012-12-01 2014-02-26 云南昆钢重型装备制造集团有限公司 Smelting process of high-boron high-speed steel roller material
CN103757556B (en) * 2014-01-24 2015-11-11 东北大学 A kind of Roller of High material for powder ore and roll surface preparation method

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH075934B2 (en) * 1987-05-29 1995-01-25 株式会社クボタ Composite member having excellent wear resistance, seizure resistance, and rough skin resistance, and method for manufacturing the same
JPH01152242A (en) * 1987-12-10 1989-06-14 Sanyo Special Steel Co Ltd High-toughness and high-speed steel by powder metallurgy
JPH01225747A (en) * 1988-03-03 1989-09-08 Sumitomo Metal Ind Ltd Manufactured article of high-speed steel having excellent surface treatability and its manufacture
JPH0472042A (en) * 1990-07-09 1992-03-06 Hitachi Metals Ltd Powdery high speed tool steel having high hardness and high wear resistance

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