JP5121276B2 - High-speed steel alloy composite products - Google Patents
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Abstract
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本発明は、耐摩耗性にすぐれる高速度鋼系合金の外周層と、靱性にすぐれる高速度鋼系合金の内周層とを、焼結によって一体化した複合製品に関する。 The present invention relates to a composite product in which an outer peripheral layer of a high-speed steel-based alloy having excellent wear resistance and an inner peripheral layer of a high-speed steel-based alloy having excellent toughness are integrated by sintering.
鋼材の熱間圧延又は冷間圧延用ロール、塑性加工の金型及び部品、プラスチック成形機のスクリュー等は、耐摩耗性、耐肌荒れ性が要求されると共に、耐事故性が要求される。これら用途の材料として、これまで、ＪＩＳに規定された合金工具鋼や高速度鋼が用いられていたが、近年では、高速度鋼系合金の組成を有する合金が使用されている。 Rolls for hot rolling or cold rolling of steel materials, dies and parts for plastic working, screws of plastic molding machines, and the like are required to have wear resistance and rough skin resistance as well as accident resistance. Up to now, alloy tool steels and high-speed steels defined in JIS have been used as materials for these applications, but in recent years, alloys having a composition of high-speed steel-based alloys have been used.
この種用途に用いられる高速度鋼系合金として、質量％にて、Ｃ：１.７〜３.５％、Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、Ｃｒ：３〜８％、Ｍｏ：３〜９％、Ｗ：５〜１４％、Ｃｏ：７〜１４％、Ｖ、Ｔｉ及びＮｂからなる群から選択される少なくとも一種を合計量で８％以下、Ｂ：２％以下及び／又はＮｉ：３％以下、残部Ｆｅ及び不可避的不純物からなるものがある（特許文献１）
また、質量％にて、Ｃ ：１.５〜３.５％、 Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、 Ｃｒ：０.５〜２５％、２Ｍｏ＋Ｗ：１.５〜４５％、 Ｎｉ：３.０％以下、Ｖ、Ｔｉ、Ｎｂ、Ｔａの内の１種以上：総計で０.５〜１２.０％、Ｎ
：０.０５〜０.５％及び残部実質的にＦｅからなるものがある（特許文献２）。
As high-speed steel alloy used for this type application, at mass%, C: 1.7~3.5%, Si : 0.6% or less, Mn: 0.6% or less, Cr:. 3 to 8%, Mo: 3-9%, W: 5-14%, Co: 7-14%, at least one selected from the group consisting of V, Ti and Nb in a total amount of 8% or less, B: 2% And / or Ni: 3% or less, balance Fe and inevitable impurities (Patent Document 1)
Further, in mass%, C: 1.5~3.5%, Si : 0.6% or less, Mn: 0.6% or less, Cr: 0.5~25%, 2Mo + W: 1.5~ 45%, Ni: 3.0% or less, one or more of V, Ti, Nb, Ta: 0.5 to 12.0% in total, N
: 0.05 to 0.5% and the balance substantially consists of Fe (Patent Document 2).
これら特許文献に示された合金は、所定の焼入れ及び焼戻しの調質熱処理を施すことにより、マルテンサイト又はベイナイト相の硬質基地に微細な炭化物粒子が分散した組織を有し、高い硬度(例えばＨＲＣ６５以上)が得られるため、すぐれた耐摩耗性を発揮することができる。しかし、硬度が高くなるほど靱性は低くなる傾向があるため、大きな応力がかかる苛酷な使用環境では靱性が不足し、耐事故性の点では必ずしも十分とは言えなかった。
そこで、靱性にすぐれる合金(例えば、ＳＣＭ材、ＳＣ材、ステンレス鋼等)を内周層材、耐摩耗性にすぐれる合金を外周層材として使用し、これら２種類の合金を複合化するものがある。しかし、外周層を焼結によって内周層と複合化する場合、例えば内周層にＳＣＭ材、外周層に高速度鋼系合金を用いると、代表的なＳＣＭ材の熱膨張係数が１４.２×１０-6／℃（２０〜６００℃）、代表的な高速度鋼系合金の熱膨張係数が１０.８×１０-6／℃（２０〜６００℃）であるから、外周層と内周層の合金の熱膨張率の差が大きく、焼結工程冷却時の収縮率が異なるため、大きな残留応力が発生して割れが生じ易いという問題がある。
このため、外周層と内周層を焼結によって複合化する場合、内周層に用いる材料の成分は、外周層の高速度鋼系合金の成分に近似したものを用いる必要があるが、これまでの高速度鋼系合金では靱性が不十分であるため、高速度鋼系合金どうしの組合せは考えられなかった。
The alloys disclosed in these patent documents have a structure in which fine carbide particles are dispersed in a hard base of martensite or bainite phase by performing a predetermined tempering and tempering heat treatment, and have a high hardness (for example, HRC65 Thus, excellent wear resistance can be exhibited. However, since the toughness tends to decrease as the hardness increases, the toughness is insufficient in a severe use environment where a large stress is applied, and it cannot be said that the accident resistance is sufficient.
Therefore, an alloy having excellent toughness (for example, SCM material, SC material, stainless steel, etc.) is used as an inner peripheral layer material, and an alloy having excellent wear resistance is used as an outer peripheral layer material, and these two kinds of alloys are combined. There is something. However, when the outer peripheral layer is combined with the inner peripheral layer by sintering, for example, when an SCM material is used for the inner peripheral layer and a high-speed steel alloy is used for the outer peripheral layer, the thermal expansion coefficient of a typical SCM material is 14.2. × 10 −6 / ° C. (20 to 600 ° C.) The typical high-speed steel alloy has a thermal expansion coefficient of 10.8 × 10 −6 / ° C. (20 to 600 ° C.). There is a problem that a large difference in thermal expansion coefficient between layers and a different shrinkage ratio during cooling of the sintering process cause a large residual stress to easily cause cracks.
For this reason, when the outer peripheral layer and the inner peripheral layer are combined by sintering, it is necessary to use the material component used for the inner peripheral layer that approximates the component of the high-speed steel alloy of the outer peripheral layer. Since the high-speed steel alloys up to this point have insufficient toughness, combinations of high-speed steel alloys have not been considered.
本発明の目的は、耐摩耗性にすぐれる高速度鋼系合金の外周層と、靱性にすぐれる高速度鋼系合金の内周層とを焼結によって一体化した複合製品を提供することである。 An object of the present invention is to provide a composite product in which an outer peripheral layer of a high-speed steel-based alloy having excellent wear resistance and an inner peripheral layer of a high-speed steel-based alloy having excellent toughness are integrated by sintering. is there.
発明者らは、硬度と靱性が相反する性質であることに着目し、内周層に用いる高速度鋼系合金について、合金基地(マトリックス)中のＣ量、及びＣｒ、Ｍｏ、Ｗ、Ｖ、Ｔｉ、Ｎｂ、Ｔａからなる炭化物生成元素の量を制御することにより、熱処理時のオーステナイトからマルテンサイト変態量を、最低限の耐摩耗性を確保できる程度に、少なく抑えて合金の高硬度化を抑制することにより、所定の靱性を得られるようにした。
また、内周層のマルテンサイト変態量を少なく抑えることにより、複合製品製作の焼結及び熱処理工程において、内周層の変態応力に起因する両層境界部での割れ発生を防止できることを見出した。
The inventors pay attention to the fact that hardness and toughness are contradictory properties, and for the high-speed steel alloy used for the inner circumferential layer, the amount of C in the alloy matrix (matrix), and Cr, Mo, W, V, By controlling the amount of carbide-forming elements composed of Ti, Nb, and Ta, the amount of martensite transformation from austenite during heat treatment is suppressed to a level that can ensure the minimum wear resistance, thereby increasing the hardness of the alloy. By suppressing it, predetermined toughness was obtained.
In addition, it has been found that by suppressing the amount of martensite transformation in the inner circumferential layer to a small extent, it is possible to prevent the occurrence of cracks at the boundary between the two layers due to the transformation stress of the inner circumferential layer in the sintering and heat treatment processes of composite product manufacture. .
本発明の複合製品は、耐摩耗性にすぐれる高速度鋼系合金の外周層と、靱性にすぐれる高速度鋼系合金の内周層を焼結によって一体化したもので、外周層の高速度鋼系合金の硬度はＨＲＣ６３以上であり、内周層の高速度鋼系合金は、質量％にて、Ｃ：０.５％以上、１.５％未満、Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、Ｃｒ：０.５〜１０.０％、Ｍｏ：０.５〜１５％、Ｗ：０.５〜２０％、Ｖ：０.５〜２０％、残部Ｆｅ及び不可避的不純物からなり、Ｃｂａｌが−１.５以上、−０.５以下の範囲、好ましくは−１.０以上、−０.５以下の範囲にあることを特徴とするものである。ここで、Ｃｂａｌ＝Ｃ−Ｃｓｔｉｃであり、Ｃｓｔｉｃ＝０.０６Ｃｒ＋０.０６３Ｍｏ＋０.０３３Ｗ＋０.２４Ｖであって、Ｃｓｔｉｃは、炭化物の形成に必要なＣの量を表し、Ｃｂａｌはマトリックスに残るＣの量を表している。
本発明の複合製品の内周層の高速度系合金は、必要に応じて、Ｔｉ、Ｎｂ及びＴａからなる群から選択される少なくとも一種をＶとの合計量で０.５〜２０％含むことができる。具体的には、質量％にて、Ｃ：０.５％以上、１.５％未満、Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、Ｃｒ：０.５〜１０.０％、Ｍｏ：０.５〜１５％、Ｗ：０.５〜２０％、Ｔｉ、Ｎｂ及びＴａからなる群から選択される少なくとも一種とＶとの合計量：０.５〜２０％、残部Ｆｅ及び不可避的不純物からなり、Ｃ ｂａｌ が−１.５以上、−０.５以下の範囲、好ましくは−１.０以上、−０.５以下の範囲にある。ここで、Ｃ ｂａｌ ＝Ｃ−Ｃ ｓｔｉｃ であり、Ｃ ｓｔｉｃ ＝０.０６Ｃｒ＋０.０６３Ｍｏ＋０.０３３Ｗ＋０.２４Ｖ＋０.２５Ｔｉ＋０.１３Ｎｂ＋０.０６６Ｔａである。
前記内周層の高速度鋼系合金は、必要に応じて、Ｎｉ：０.５〜３％及び／又はＮ：０.１〜０.５％を含むことができるし、また、Ｃｏ：７〜２０％を含むこともできる。
The composite product of the present invention is obtained by integrating the outer peripheral layer of a high-speed steel alloy excellent in wear resistance and the inner peripheral layer of a high-speed steel alloy excellent in toughness by sintering. hardness speed steel alloy is at HRC63 or more, high speed steel alloy of the inner peripheral layer, at mass%, C: 0.5% to less than 1.5%, Si: 0.6% or less Mn: 0.6% or less, Cr: 0.5-10.0%, Mo: 0.5-15%, W: 0.5-20%, V : 0.5-20%, balance Fe and It consists of inevitable impurities, and Cbal is in the range of -1.5 or more and -0.5 or less, preferably in the range of -1.0 or more and -0.5 or less. Here, C bal = C−C stic , C stic = 0.06Cr + 0.063Mo + 0.033W + 0.24 V , C stic represents the amount of C required for carbide formation, and C bal is the matrix Represents the amount of C remaining.
The high-speed alloy of the inner peripheral layer of the composite product of the present invention contains 0.5 to 20% of the total amount of V and at least one selected from the group consisting of Ti, Nb and Ta, if necessary. Can do. Specifically, in mass%, C: 0.5% or more and less than 1.5%, Si: 0.6% or less, Mn: 0.6% or less, Cr: 0.5 to 10.0% , Mo: 0.5 to 15%, W: 0.5 to 20%, total amount of at least one selected from the group consisting of Ti, Nb and Ta and V: 0.5 to 20%, balance Fe and It consists of inevitable impurities, and Cbal is in the range of -1.5 or more and -0.5 or less, preferably in the range of -1.0 or more and -0.5 or less. Here, C bal = C−C stic and C stic = 0.06Cr + 0.063Mo + 0.033W + 0.24V + 0.25 Ti + 0.13Nb + 0.066Ta.
The high-speed steel-based alloy of the inner peripheral layer may contain Ni: 0.5-3% and / or N: 0.1-0.5% as necessary, and Co: 7 It can also contain ~ 20%.
外周層は、ＨＲＣ６３以上の硬度を得られる高速度鋼系合金であれば特定の合金に限定されるものではない。
外周層合金として、例えば、質量％にて、Ｃ：１.５〜３.５％、Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、Ｃｒ：０.５〜２５％、Ｍｏ：０.５〜１０％、Ｗ：０.５〜２０％、Ｖ、Ｔｉ、Ｎｂ及びＴａからなる群から選択される少なくとも一種を合計量で０.５〜１５％、残部Ｆｅ及び不可避的不純物からなる合金が挙げられる。なお、この合金は、所望により、Ｃｏ：５〜２０％、Ｂ：２％以下、Ｎｉ：３％以下、Ｎ：０.０５〜０.５％の少なくとも一種を含むことができる。
The outer peripheral layer is not limited to a specific alloy as long as it is a high-speed steel alloy capable of obtaining a hardness of HRC 63 or higher.
As peripheral layer alloy, for example, by mass%, C: 1.5~3.5%, Si : 0.6% or less, Mn: 0.6% or less, Cr: 0.5 to 25%, Mo : 0.5 to 10%, W: 0.5 to 20%, at least one selected from the group consisting of V, Ti, Nb and Ta in a total amount of 0.5 to 15%, the remaining Fe and inevitable impurities The alloy which consists of is mentioned. In addition, this alloy can contain at least 1 type of Co: 5-20%, B: 2% or less, Ni: 3% or less, N: 0.05-0.5% depending on necessity.
内周層と外周層とは、ＨＩＰ等の焼結によって一体化される。
外周層と焼結する前に、内周層は予め丸棒状に形成されるが、焼結(ＨＩＰ等)に限らず、鋳造又は熱間押出等により形成することもできる。
内周層と外周層の一体化は、内周層の周囲に所定空間を存して包囲するカプセル(例えば炭素鋼製)を準備し、カプセル内の前記空間に外周層の合金粉末(例えば、粒径５００μｍ以下)を充填し、脱気密封した後、ＨＩＰ処理によって行なうことができる。ＨＩＰ処理は、好適には、温度約９００〜１２００℃、加圧力約５００〜１５００気圧、処理時間約２〜４時間の条件で行なうことができる。これにより、外周層と内周層が境界面で強固に一体化した焼結複合品が得られる。
The inner peripheral layer and the outer peripheral layer are integrated by sintering such as HIP.
Before sintering with the outer peripheral layer, the inner peripheral layer is formed in a round bar shape in advance. However, the inner peripheral layer is not limited to sintering (HIP or the like), but can be formed by casting or hot extrusion.
Integration of the inner peripheral layer and the outer peripheral layer is to prepare a capsule (for example, made of carbon steel) that surrounds the inner peripheral layer with a predetermined space, and the outer layer alloy powder (for example, It can be carried out by HIP treatment after filling with a particle size of 500 μm or less and degassing and sealing. The HIP treatment can be performed preferably under conditions of a temperature of about 900 to 1200 ° C., a pressure of about 500 to 1500 atm, and a treatment time of about 2 to 4 hours. Thereby, a sintered composite product in which the outer peripheral layer and the inner peripheral layer are firmly integrated at the interface is obtained.
焼結複合品は、必要に応じて、所定形状に機械加工が施される。
機械加工の後、所定の熱処理を施すことにより、外周層に高耐摩耗性、内周層に高靱性が付与された複合製品が形成される。
なお、この明細書で用いる「複合製品」という語は、内周層と外周層を有する中空状又は中実状のあらゆる形状の製品を意味するものとする。
The sintered composite product is machined into a predetermined shape as necessary.
After machining, a predetermined heat treatment is performed to form a composite product in which the outer peripheral layer has high wear resistance and the inner peripheral layer has high toughness.
In addition, the term “composite product” used in this specification means a product having any shape of a hollow shape or a solid shape having an inner peripheral layer and an outer peripheral layer.
熱処理は、約１１００〜１２００℃の温度で加熱した後、強制空冷による焼入れ又は不活性ガス(窒素ガス等)を冷媒とする焼入れを行ない、次に、焼戻しを約５００〜６００℃の温度で２〜４回繰り返す。外周層と内周層は、同じ材料系の高速度鋼系合金であるから、外周層と内周層を同じ条件で熱処理を行なうことができる。この熱処理を施すことにより、外周層の硬度がＨＲＣ６３以上、内周層のシャルピー衝撃強さが３０×１０4Ｊ／ｍ2以上の特性を得ることができる。
なお、複合製品が、内周層に耐摩耗性が必要とされる中空状製品の場合は、内周層の硬度はＨＲＣ５０〜６２であることが好ましく、ＨＲＣ５０〜６０であることがより好ましく、ＨＲＣ５５〜６０であることがさらに好ましい。
In the heat treatment, after heating at a temperature of about 1100 to 1200 ° C., quenching by forced air cooling or quenching using an inert gas (nitrogen gas or the like) as a refrigerant is performed, followed by tempering at a temperature of about 500 to 600 ° C. Repeat ~ 4 times. Since the outer peripheral layer and the inner peripheral layer are high-speed steel alloys of the same material system, the outer peripheral layer and the inner peripheral layer can be heat-treated under the same conditions. By performing this heat treatment, it is possible to obtain characteristics in which the hardness of the outer peripheral layer is HRC 63 or higher and the Charpy impact strength of the inner peripheral layer is 30 × 10 4 J / m 2 or higher.
In addition, when the composite product is a hollow product in which wear resistance is required for the inner circumferential layer, the hardness of the inner circumferential layer is preferably HRC 50 to 62, more preferably HRC 50 to 60, More preferably, it is HRC55-60.
本発明の複合製品の内周層に用いられる高速度鋼系合金の成分限定理由及びＣbalの意義について、以下に説明する。 The reasons for limiting the components of the high-speed steel alloy used in the inner peripheral layer of the composite product of the present invention and the significance of Cbal will be described below.
Ｃ：０.５％以上、１.５％未満
Ｃは、炭化物形成元素であり、Ｖ、Ｔｉ、Ｎｂ、Ｔａ、Ｗ、Ｍｏ、Ｃｒ等と結合して、ＭＣ型、Ｍ2Ｃ型、Ｍ6Ｃ型の硬質炭化物を形成し、合金の耐摩耗性を高める。このため、少なくとも０.５％以上含有させる。しかし、Ｃを多量に含有すると、靱性が悪化し、欠け割れが発生し易くなる。従って、上限を１.５％未満とする。
C: 0.5% or more and less than 1.5% C is a carbide forming element, which is combined with V, Ti, Nb, Ta, W, Mo, Cr, and the like to form MC type, M 2 C type, M 6 Forms C-type hard carbide to increase the wear resistance of the alloy. For this reason, it is made to contain at least 0.5% or more. However, when a large amount of C is contained, the toughness is deteriorated and cracking is likely to occur. Therefore, the upper limit is made less than 1.5%.
Ｓｉ：０.６％以下
Ｓｉは脱酸作用を有する。しかし、多量に含有すると材料を脆化させるため、上限は０.６％とする。
Si: 0.6% or less Si has a deoxidizing action. However, the upper limit is made 0.6% because the material becomes brittle if contained in large amounts.
Ｍｎ：０.６％以下
Ｍｎは脱酸作用を有する。しかし、多量に含有すると材料を脆化させるため、上限は０.６％とする。
Mn: 0.6% or less Mn has a deoxidizing action. However, the upper limit is made 0.6% because the material becomes brittle if contained in large amounts.
Ｃｒ：０.５〜１０.０％
Ｃｒは、Ｍ6Ｃ型の炭化物を生成し、耐摩耗性を向上させるので少なくとも０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は１０.０％に規定する。好ましくは４〜７％である。
Cr: 0.5 to 10.0%
Cr produces M 6 C type carbide and improves wear resistance, so it is contained at least 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is specified at 10.0%. Preferably it is 4 to 7%.
Ｍｏ：０.５〜１５％
Ｍｏは、Ｍ2Ｃ型炭化物を生成し、耐摩耗性を向上させるので少なくとも０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は１５％に規定する。好ましくは１〜１０％であり、さらに好ましくは１.５〜５％である。
Mo: 0.5 to 15%
Mo generates M 2 C type carbide and improves wear resistance, so it is contained at least 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is defined as 15%. Preferably it is 1 to 10%, and more preferably 1.5 to 5%.
Ｗ：０.５〜２０％
Ｗは、Ｍ2Ｃ型炭化物を生成し、耐摩耗性を向上させるので少なくとも０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は２０％に規定する。好ましくは３〜６％である。
W: 0.5-20%
W forms M 2 C type carbide and improves wear resistance, so it is contained at least 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is defined as 20%. Preferably it is 3 to 6%.
Ｖ、Ｔｉ、Ｎｂ、Ｔａのうちの少なくとも一種：合計量で０.５〜２０％
Ｖ、Ｔｉ、Ｎｂ、Ｔａは、ＭＣ型炭化物を生成し、耐摩耗性には、ＭＣ型炭化物が顕著な効果を奏するので、これら元素の少なくとも一種を合計量で０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は合計量で２０％に規定する。好ましくは０.５〜６％である。
At least one of V, Ti, Nb, Ta: 0.5 to 20% in total
V, Ti, Nb, and Ta produce MC type carbides, and MC type carbides have a remarkable effect on wear resistance. Therefore, at least one of these elements is contained in a total amount of 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is defined as 20% in total. Preferably it is 0.5 to 6%.
Ｃbal：−１.５以上、−０.５以下
前述したように、本発明の複合製品の内周層用高速度鋼系焼結合金は、合金基地(マトリックス)中のＣ量を制御することにより、熱処理時のマルテンサイト変態量を抑制するものである。
Ｃは、一般的に、炭化物形成に１００％使用されるわけではなく、マトリックスに分散して残存する。マトリックスに残ったＣは、熱処理時にオーステナイトから硬質のマルテンサイトへの変態を促し、合金の高硬度化をすすめ、その一方で靱性を低下させる。
そこで、合金設計上のＣ量と、他の元素と炭化物を形成する理論上のＣ量(Ｃstic)との差から、マトリックスに残る理論上のＣ量(Ｃbal)を算出し、Ｃbalを−１.５以上、−０.５以下の範囲に規定した。Ｃbal値が−(マイナス)を示しているが、これは理論上の値であり、Ｃbalが計算上この範囲にあっても、実際の合金においてはマトリックス中にＣが残存する。
Ｃbalが−１.５より小さいとマルテンサイト化が少なくなり、合金に必要な硬度が得られない。一方、Ｃbalが−０.５より大きいとマルテンサイト化が進みすぎて硬度が高くなり、本発明の目的にあった靱性を得ることができない。
なお、Ｃsticは、炭化物形成元素の種類に応じて次式で与えられる。
Ｃstic＝０.０６Ｃｒ＋０.０６３Ｍｏ＋０.０３３Ｗ＋０.２４Ｖ＋０.２５Ｔｉ＋０.１３Ｎｂ＋０.０６６Ｔａ
本発明の複合製品の内周層を構成する高速度鋼系焼結合金は、Ｃbalが−１.５以上、−０.５以下の範囲となるように、Ｃ、Ｃｒ、Ｍｏ、Ｗ、Ｖ、Ｔｉ、Ｎｂ、Ｔａの量を調整することにより、熱処理での焼入れ性能を低下させるようにした。これにより、一般的な高速度鋼と同じ条件の熱処理を施しても、得られる硬度は比較的低い範囲(ＨＲＣ５０〜６２)であり、高い靱性を得ることができる。
Cbal : -1.5 or more, -0.5 or less As mentioned above, the high-speed steel-based sintered alloy for the inner peripheral layer of the composite product of the present invention controls the amount of C in the alloy matrix (matrix). This suppresses the amount of martensitic transformation during heat treatment.
C is generally not used 100% for carbide formation but remains dispersed in the matrix. C remaining in the matrix promotes transformation from austenite to hard martensite during the heat treatment, and promotes higher hardness of the alloy while reducing toughness.
Therefore, the theoretical C amount (C bal ) remaining in the matrix is calculated from the difference between the C amount in the alloy design and the theoretical C amount (C stic ) that forms carbide with other elements, and C bal Was specified in the range of -1.5 or more and -0.5 or less. Although the C bal value indicates − (minus), this is a theoretical value, and even if C bal is within this range, C remains in the matrix in an actual alloy.
When Cbal is less than -1.5, martensite formation is reduced, and the hardness required for the alloy cannot be obtained. On the other hand, if C bal is larger than −0.5, the martensite is excessively advanced and the hardness becomes high, and the toughness suitable for the purpose of the present invention cannot be obtained.
C stic is given by the following equation according to the type of carbide forming element.
C stic = 0.06Cr + 0.063Mo + 0.033W + 0.24V + 0.25Ti + 0.13Nb + 0.066Ta
The high-speed steel-based sintered alloy constituting the inner peripheral layer of the composite product of the present invention has C, Cr, Mo, W, Cbal so that Cbal is in the range of -1.5 or more and -0.5 or less. By adjusting the amounts of V, Ti, Nb, and Ta, the quenching performance in the heat treatment was lowered. Thereby, even if it heat-processes on the same conditions as general high speed steel, the hardness obtained is a comparatively low range (HRC50-62), and high toughness can be acquired.
本発明の複合製品の内周層用高速度鋼系合金は、上記成分を含有し、残部Ｆｅ及び不可避の不純物からなるが、所望により、Ｎｉ、Ｎ及びＣｏをさらに含有させることもできる。 The high-speed steel-based alloy for the inner peripheral layer of the composite product of the present invention contains the above components and consists of the balance Fe and inevitable impurities, but may further contain Ni, N, and Co if desired.
Ｎｉ：０.５〜３％
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り靱性の向上に寄与する。また、耐食性を改善する元素でもある。このため、少なくとも０.５％以上含有させることが好ましい。一方、含有量が３％を越えると焼入れ性を著しく低下させるため、上限は３％に規定する。
Ni: 0.5 to 3%
Ni is an austenite phase stabilizing element and contributes to the improvement of toughness by increasing the amount of retained austenite. It is also an element that improves corrosion resistance. For this reason, it is preferable to contain at least 0.5% or more. On the other hand, if the content exceeds 3%, the hardenability is remarkably lowered, so the upper limit is defined as 3%.
Ｎ：０.１〜０.５％
Ｎは、Ｎｉと同様、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り靱性の向上に寄与すると共に耐食性を改善する。このため、少なくとも０.１％以上含有させることが好ましい。一方、含有量が０.５％を越えると焼入れ性を著しく低下を招くため、上限は０.５％に規定する。
なお、ＮはＮｉの約５倍の含有効果を有する。このため、ＮとＮｉを両方含有する場合は、Ｎｉ＋５Ｎを、０.５〜３％の範囲で含有することが好ましい。
N: 0.1-0.5%
N, like Ni, is an austenite phase stabilizing element and contributes to the improvement of toughness by increasing the amount of retained austenite and also improves the corrosion resistance. For this reason, it is preferable to contain at least 0.1% or more. On the other hand, if the content exceeds 0.5%, the hardenability is remarkably reduced, so the upper limit is specified to 0.5%.
N has a content effect about five times that of Ni. For this reason, when both N and Ni are contained, it is preferable to contain Ni + 5N in the range of 0.5 to 3%.
Ｃｏ：７〜２０％
Ｃｏはマトリックスに固溶してマトリックスを強化し、高温における耐力を著しく向上させる。このため、高温に曝される部材の材料にはＣｏを少なくとも７％以上含有させることが好ましく、８％以上含有させることがより好ましい。一方、あまりに多く含有すると靱性の低下を招く。このため、上限は２０％とするが、１２％以下がより好ましい。
Co: 7-20%
Co dissolves in the matrix and strengthens the matrix, significantly improving the yield strength at high temperatures. For this reason, it is preferable to contain at least 7% or more Co in the material of the member exposed to high temperature, and it is more preferable to contain 8% or more. On the other hand, when it contains too much, the toughness will be reduced. For this reason, although an upper limit is 20%, 12% or less is more preferable.
次に本発明の具体的実施例を掲げて説明する。
＜内周層の高速度鋼系合金の特性＞
表１に示す合金成分(質量％)の高速度鋼系合金粉末(粒径約３００μｍ以下)を原料粉末として使用し、ＨＩＰ処理を施して丸棒状の焼結合金(外径５０ｍｍ、長さ１５０ｍｍ)を得た。ＨＩＰ処理条件は、温度：１１５０℃、加圧力：１０００気圧、保持時間：３時間である。但し、No.１０４は、鋳造により調製した合金である。
次にこれら合金に焼入れ焼戻し熱処理を施して供試材を作製した。焼入れは、真空焼入れ炉にて１２００℃に１時間保持後、常温常圧の窒素ガスを導入し、ガス冷却することにより行なった。焼戻しは、５４０℃に５時間保持した後放冷するヒートパターンを３回繰り返した。
Next, specific examples of the present invention will be described.
<Characteristics of high-speed steel-based alloy for inner circumference layer>
High-speed steel alloy powder of alloy compositions shown in Table 1 (mass%) (hereinafter particle size of about 300 [mu] m) was used as raw material powder, the sintered alloy of the round bar is subjected to HIP treatment (outer diameter 50 mm, length 150 mm). The HIP treatment conditions are as follows: temperature: 1150 ° C., applied pressure: 1000 atm, and holding time: 3 hours. However, No. 104 is an alloy prepared by casting.
Next, these alloys were subjected to quenching and tempering heat treatments to prepare test materials. Quenching was performed by holding nitrogen gas at normal temperature and pressure after holding at 1200 ° C. for 1 hour in a vacuum quenching furnace and cooling the gas. For tempering, a heat pattern of holding for 5 hours at 540 ° C. and then allowing to cool was repeated three times.
各供試材について、硬度測定、摩耗試験及びシャルピー衝撃試験を行なった。
硬度はロックウエル硬度計のＣスケールで測定した。
摩耗試験は、大越式摩耗試験機を使用し、比摩耗量(１０-14ｍｍ2／Ｎ)を測定した。試験条件は、回転輪材質：ＳＵＪ２(ＨＲＣ６０)、摩耗速度：３.３８ｍ／ｓ、摩耗距離：４００ｍ、最終荷重６０Ｎにて行なった。
シャルピー衝撃試験は、５ｍｍ×５ｍｍ×５５ｍｍ、ノッチ無しの試験片を用い、常温で実施した。吸収エネルギー(Ｊ)を断面積(ｍ2)で除した値(Ｊ／ｍ2)を比較した。
試験結果を表１に示す。
Each specimen was subjected to hardness measurement, wear test and Charpy impact test.
The hardness was measured with a C scale of a Rockwell hardness tester.
In the abrasion test, a specific abrasion amount (10 −14 mm 2 / N) was measured using an Ogoshi type abrasion tester. The test conditions were as follows: rotating wheel material: SUJ2 (HRC60), wear rate: 3.38 m / s, wear distance: 400 m, and final load 60 N.
The Charpy impact test was performed at room temperature using a 5 mm × 5 mm × 55 mm, non-notched test piece. Absorbing energy (J) was compared by dividing the value (J / m 2) by the cross-sectional area (m 2).
The test results are shown in Table 1.
表１を参照すると、No.１〜No.１９は本発明の複合製品の内周層を構成する高速度鋼系合金の実施例であり、No.１０１〜No.１０９は比較例である。
発明例No.１〜No.１９は、比較例(No.１０３とNo.１０９を除く)と比べて、靱性(シャルピー衝撃値)にすぐれることがわかる。
比較例中、No.１０１及びNo.１０２は、Ｃの含有量が多く、靱性に劣る結果を示している。No.１０４〜No.１０８は、Ｃbalの値が大きく、熱処理時のマルテンサイト変態量が多すぎて、高硬度化を十分に抑えることができず、靱性を向上させることができなかったためと考えられる。
なお、No.１０３及びNo.１０９は、靱性にすぐれるが、硬度が不足し、耐摩耗性が著しく劣る。No.１０３は、Ｎｉの含有量が多すぎるため、オーステナイトが安定化して残留オーステナイト量が増加し、高硬度化がさらに抑えられたためと考えられる。また、No.１０９は、Ｃbalの値が小さく、マトリックスに残存するＣが少なすぎるため、十分な硬度が得られなかったものと考えられる。
Referring to Table 1, No. 1 to No. 19 are examples of high-speed steel alloys constituting the inner peripheral layer of the composite product of the present invention, and No. 101 to No. 109 are comparative examples.
It can be seen that Invention Examples No. 1 to No. 19 are superior in toughness (Charpy impact value) compared to Comparative Examples (excluding No. 103 and No. 109).
In the comparative examples, No. 101 and No. 102 have a high C content and are inferior in toughness. No. 104 to No. 108 had a large value of C bal, and the amount of martensite transformation at the time of heat treatment was too large, so that the increase in hardness could not be sufficiently suppressed and the toughness could not be improved. Conceivable.
Although No. 103 and No. 109 are excellent in toughness, the hardness is insufficient and the wear resistance is remarkably inferior. In No. 103, since the Ni content is too large, austenite is stabilized, the amount of retained austenite is increased, and the increase in hardness is further suppressed. In No. 109, it is considered that sufficient hardness was not obtained because the value of C bal was small and the amount of C remaining in the matrix was too small.
＜複合製品の製作＞
発明例及び比較例の複合製品を構成する外周層と内周層の合金成分を表２に示す。比較例１の内周層は、Ｃbalの値が本発明の範囲よりも大きい例である。比較例２の内周層はNo.１０１(表１参照)の合金であり、Ｃの含有量が本発明の範囲よりも多い例である。比較例３の内周層はNo.１０４(表１参照)の合金(ＳＫＨ５１相当材)でＣbalの値が本発明の範囲よりも大きい例である。比較例４の内周層は、ＳＫＤ１１相当材で、Ｃ、Ｃｒ、Ｖの含有量が本発明の範囲から逸脱し、Ｃbalの値が本発明の範囲よりも大きい。
まず、内周層の高速度系合金の粉末(粒径約３００μｍ以下)を、実施例１と同じ条件でＨＩＰ処理を施して丸棒状の焼結合金(外径５０ｍｍ、長さ１５０ｍｍ)を得た。なお、比較例３と比較例４の内周層は鋳造合金(外径５０ｍｍ、長さ１５０ｍｍ)である。
次に、得られた丸棒状の焼結合金又は鋳造合金を芯金として使用し、その周囲に所定空間を存して包囲する炭素鋼カプセルを準備し、カプセル内の前記空間に外周層の合金粉末(粒径約３００μｍ以下)を充填し、脱気密封した後、ＨＩＰ処理を施して、内周層と外周層を有する焼結複合品(内周層外径５０ｍｍ、外周層外径１２０ｍｍ、長さ１５０ｍｍ)を作製した。ＨＩＰ処理は、温度１１５０℃、加圧力１０００気圧、保持時間３時間の条件で行なった。
<Production of composite products>
Table 2 shows the alloy components of the outer peripheral layer and the inner peripheral layer constituting the composite product of the inventive example and the comparative example. The inner peripheral layer of Comparative Example 1 is an example in which the value of C bal is larger than the range of the present invention. The inner peripheral layer of Comparative Example 2 is an alloy of No. 101 (see Table 1), and is an example in which the C content is larger than the range of the present invention. The inner peripheral layer of Comparative Example 3 is an example of No. 104 (see Table 1) alloy (SKH51 equivalent material), and the C bal value is larger than the range of the present invention. The inner peripheral layer of Comparative Example 4 is an SKD11 equivalent material, and the contents of C, Cr, and V deviate from the scope of the present invention, and the value of Cbal is larger than the scope of the present invention.
First, a high-speed alloy powder (particle size of about 300 μm or less) in the inner peripheral layer is subjected to HIP treatment under the same conditions as in Example 1 to obtain a round bar-like sintered alloy (outer diameter 50 mm, length 150 mm). It was. In addition, the inner peripheral layer of Comparative Example 3 and Comparative Example 4 is a cast alloy (outer diameter 50 mm, length 150 mm).
Next, the obtained round bar-like sintered alloy or cast alloy is used as a core metal, and a carbon steel capsule is prepared surrounding the space with a predetermined space around it. Filled with powder (particle size of about 300 μm or less), degassed and sealed, then subjected to HIP treatment, and a sintered composite product having an inner peripheral layer and an outer peripheral layer (an outer peripheral layer outer diameter of 50 mm, an outer peripheral layer outer diameter of 120 mm, 150 mm in length) was produced. The HIP treatment was performed under conditions of a temperature of 1150 ° C., a pressure of 1000 atm, and a holding time of 3 hours.
焼結複合品に焼入れ及び焼戻し熱処理を施した。焼入れは、真空焼入れ炉にて１２００℃に１時間保持後、常温常圧の窒素ガスを導入し、ガス冷却することにより行なった。焼戻しは、５４０℃に５時間保持した後放冷するヒートパターンを３回繰り返した。 The sintered composite article was subjected to quenching and tempering heat treatment. Quenching was performed by holding nitrogen gas at normal temperature and pressure after holding at 1200 ° C. for 1 hour in a vacuum quenching furnace and cooling the gas. For tempering, a heat pattern of holding for 5 hours at 540 ° C. and then allowing to cool was repeated three times.
熱処理後、焼結複合品を切断し、接合状態を検査すると共に、外周層及び内周層からワイヤーカットにより夫々の試験片を切り出し、硬度測定、摩耗試験及びシャルピー衝撃試験を行なった。測定及び試験の条件及び要領は実施例１と同じである。
硬度測定、摩耗試験及び衝撃試験の結果を表２に示している。
After the heat treatment, the sintered composite product was cut to inspect the bonding state, and each test piece was cut out from the outer peripheral layer and the inner peripheral layer by wire cutting, and a hardness measurement, a wear test, and a Charpy impact test were performed. The conditions and procedures for measurement and testing are the same as in Example 1.
The results of hardness measurement, wear test and impact test are shown in Table 2.
全ての発明例は、外周層と内周層の境界部に割れ(クラック)は認められず、接合状態は良好であった。また、使用した合金の特性に基づいて、外周層は高硬度及び高耐摩耗性を有し、内周層は高硬度化が抑えられて、高い靱性を有することを示している。 In all the inventive examples, no crack was observed at the boundary between the outer peripheral layer and the inner peripheral layer, and the bonding state was good. In addition, based on the characteristics of the alloy used, the outer peripheral layer has high hardness and high wear resistance, and the inner peripheral layer has high toughness with high hardness suppressed.
比較例１及び比較例３は、外周層と内周層の境界部に割れが認められた。これら比較例の内周層は、Ｃbalの値が本発明の規定よりも大きいため、内周層は、熱処理時のマルテンサイト変態による膨張量が多く、ＨＩＰ焼結又は熱処理の冷却時のマルテンサイト変態応力が大きくなり、割れが発生したものと考えられる。また、内周層は、高硬度化のために靱性に劣ることを示している。 In Comparative Example 1 and Comparative Example 3, cracks were observed at the boundary between the outer peripheral layer and the inner peripheral layer. Since the inner peripheral layer of these comparative examples has a C bal value larger than that of the present invention, the inner peripheral layer has a large amount of expansion due to martensitic transformation during heat treatment, and the martens during cooling of HIP sintering or heat treatment. It is considered that the site transformation stress increased and cracking occurred. Moreover, it has shown that an inner peripheral layer is inferior to toughness for high hardness.
比較例４も、外周層と内周層の境界部に割れが認められた。比較例４の内周層は、Ｃbalの値が本発明の範囲から外れているが、硬度はＨＲＣ６１.０であり、あまり高くはないのでマルテンサイト変態応力はあまり大きくなかったと考えられる。しかし、炭化物生成元素であるＣｒ、Ｍｏ、Ｗ、Ｖの含有量が外周層の含有量とはかなり異なっているため、外周層と内周層との熱膨張率の差によって生じた残留応力も複合的に作用して割れに至ったものと考えられる。 In Comparative Example 4 as well, cracks were observed at the boundary between the outer peripheral layer and the inner peripheral layer. The inner peripheral layer of Comparative Example 4 has a C bal value that is out of the range of the present invention, but the hardness is HRC 61.0, which is not so high, so it is considered that the martensitic transformation stress was not so large. However, since the content of Cr, Mo, W, and V, which are carbide generating elements, is significantly different from the content of the outer peripheral layer, the residual stress caused by the difference in thermal expansion coefficient between the outer peripheral layer and the inner peripheral layer is also It is thought that the combined action led to cracking.
比較例２は、外周層と内周層の境界部に割れの発生は認められなかった。比較例２の内周層はＣbalの値が本発明の範囲内にあり、内周層のマルテンサイト変態による変態応力の発生は小さく抑えられたためと考えられる。しかし、Ｃを多量に含有したことにより、靱性が劣るため、内周層側に大きな応力がかかる苛酷な環境で使用される場合には靱性が不足する可能性がある。 In Comparative Example 2, no crack was observed at the boundary between the outer peripheral layer and the inner peripheral layer. This is probably because the inner peripheral layer of Comparative Example 2 had a Cbal value within the range of the present invention, and the generation of transformation stress due to martensitic transformation in the inner peripheral layer was suppressed to a small level. However, since the toughness is inferior due to containing a large amount of C, the toughness may be insufficient when used in a severe environment where a large stress is applied to the inner peripheral layer side.
次に、具体的な複合製品の製作例を挙げる。なお、以下に記載する複合製品は単なる例示であって、本発明の複合製品をこれらの例に限定することを企図するものではない。 Next, a specific example of manufacturing a composite product will be given. The composite products described below are merely examples, and are not intended to limit the composite products of the present invention to these examples.
＜プラスチック成形機のスクリュー＞
カプセルの中に発明例１の内周層と同じ成分の粉末を入れ、脱気密封した後、ＨＩＰ処理を施すことにより、外径３０ｍｍ、長さ６０ｍｍの丸棒を作る。この丸棒周囲に所定空間を存して包囲するカプセルを準備し、カプセル内の前記空間に、発明例１の外周層の合金粉末を充填し、脱気密封した後、ＨＩＰ処理を施して、内周層外径(外周層内径)３０ｍｍ、外周層外径６５ｍｍ、長さ６０ｍｍのスクリュー用素材を作る。
次に、内周層にインボリュート加工、キー加工を施して軸孔を形成すると共に、外周層に螺旋状加工を施して羽根を形成することにより、プラスチック成形機のスクリューが作製される。図１はプラスチック成形機のスクリューの斜視図であり、(1)は内周層、(2)は外周層である。得られたスクリューは、内径２０ｍｍ、内周層(1)の外径(外周層内径)３０ｍｍ、外周層(2)の最大外径６０ｍｍ、軸方向長さ５０ｍｍである。
<Plastic molding machine screw>
A powder having the same composition as that of the inner peripheral layer of Invention Example 1 is put in a capsule, degassed and sealed, and then subjected to HIP treatment to produce a round bar having an outer diameter of 30 mm and a length of 60 mm. Prepare a capsule surrounding the round bar with a predetermined space, fill the space in the capsule with the alloy powder of the outer peripheral layer of Invention Example 1, deaerate and seal, and then perform HIP treatment, A screw material having an inner peripheral layer outer diameter (outer peripheral layer inner diameter) of 30 mm, an outer peripheral layer outer diameter of 65 mm, and a length of 60 mm is made.
Next, involute processing and key processing are performed on the inner peripheral layer to form a shaft hole, and a spiral processing is performed on the outer peripheral layer to form blades, thereby producing a screw for a plastic molding machine. FIG. 1 is a perspective view of a screw of a plastic molding machine, where (1) is an inner peripheral layer and (2) is an outer peripheral layer. The obtained screw has an inner diameter of 20 mm, an outer diameter of the inner peripheral layer (1) (outer peripheral layer inner diameter) of 30 mm, a maximum outer diameter of the outer peripheral layer (2) of 60 mm, and an axial length of 50 mm.
＜圧延用ロール＞
カプセルの中に発明例６の内周層と同じ成分の粉末を入れ、脱気密封した後、ＨＩＰ処理を施すことにより、外径３００ｍｍ、長さ４５０ｍｍの棒状体を作る。この棒状体周囲に所定空間を存して包囲するカプセルを準備し、カプセル内の前記空間に、発明例６の外周層の合金粉末を充填し、脱気密封した後、ＨＩＰ処理を施して、内周層外径(外周層内径)３００ｍｍ、外周層外径４２０ｍｍ、長さ４５０ｍｍのロール用素材を作る。
次に、内周層に軸孔加工、外周層に仕上げ加工を施して、複合スリーブ圧延ロールが作製される。図２は、圧延ロールの断面図であり、(1)は内周層、(2)は外周層である。得られた圧延用ロールは、内径２００ｍｍ、内周層(1)の外径(外周層(2)内径)３００ｍｍ、外周層(2)の外径４００ｍｍ、軸方向長さ４００ｍｍである。
<Roll for rolling>
A powder having the same composition as that of the inner peripheral layer of Invention Example 6 is put in the capsule, deaerated and sealed, and then subjected to HIP treatment to produce a rod-like body having an outer diameter of 300 mm and a length of 450 mm. A capsule surrounding the rod-like body with a predetermined space is prepared, and the space in the capsule is filled with the alloy powder of the outer peripheral layer of Invention Example 6, deaerated and sealed, and then subjected to HIP treatment. A roll material having an inner peripheral layer outer diameter (outer peripheral layer inner diameter) of 300 mm, an outer peripheral layer outer diameter of 420 mm, and a length of 450 mm is made.
Next, shaft hole processing is performed on the inner peripheral layer, and finishing processing is performed on the outer peripheral layer, so that a composite sleeve rolling roll is manufactured. FIG. 2 is a cross-sectional view of the rolling roll, in which (1) is an inner circumferential layer and (2) is an outer circumferential layer. The obtained rolling roll has an inner diameter of 200 mm, an outer diameter of the inner peripheral layer (1) (outer diameter of the outer peripheral layer (2)) of 300 mm, an outer diameter of the outer peripheral layer (2) of 400 mm, and an axial length of 400 mm.
＜プレス機械用パンチ＞
カプセルの中に発明例７の内周層と同じ成分の粉末を入れ、脱気密封した後、ＨＩＰ処理を施すことにより、上側が小径、下側が大径の段付棒状体を作る。得られた段付棒状体は、小径部の外径が８０ｍｍ、大径部の外径が１００ｍｍ、長さ２００ｍｍである。内径が１００ｍｍより僅かに大きいカプセルの中にこの棒状体を入れ、小径部とカプセル内の空間に、発明例７の外周層の合金粉末を充填し、脱気密封した後、ＨＩＰ処理を施して、パンチ用素材を作る。
次に、内周層に軸孔加工、外周層に仕上げ加工を施して、プレス機械用パンチが作製される。図３は、プレス機械用パンチの断面図であり、(1)は内周層、(2)は外周層である。得られたパンチは、内径５０ｍｍ、内周層(1)のの小径部外径(外周層(2)内径)８０ｍｍ、外周層(2)外径９０ｍｍ、軸方向長さ１８０ｍｍである。
<Punch for press machine>
A powder having the same component as that of the inner peripheral layer of Invention Example 7 is put in the capsule, degassed and sealed, and then subjected to HIP treatment to form a stepped rod-like body having a small diameter on the upper side and a large diameter on the lower side. The obtained stepped rod-shaped body has an outer diameter of the small diameter portion of 80 mm, an outer diameter of the large diameter portion of 100 mm, and a length of 200 mm. This rod-shaped body is put in a capsule whose inner diameter is slightly larger than 100 mm, the alloy powder of the outer peripheral layer of Invention Example 7 is filled in the small diameter portion and the space in the capsule, and after deaeration and sealing, HIP treatment is performed. Make punch materials.
Next, a punch for a press machine is produced by subjecting the inner peripheral layer to shaft hole processing and the outer peripheral layer to finish processing. FIG. 3 is a cross-sectional view of a punch for a press machine, where (1) is an inner peripheral layer and (2) is an outer peripheral layer. The obtained punch has an inner diameter of 50 mm, an outer diameter (outer layer (2) inner diameter) of 80 mm, an outer layer (2) outer diameter of 90 mm, and an axial length of 180 mm.
上記の如く、本発明の複合製品は、外周層は高硬度で耐摩耗性にすぐれ、内周層は靱性にすぐれている。
従って、外周層に耐摩耗性、内周層に靱性が要求される鋼材の熱間圧延又は冷間圧延用ロール、塑性加工用金型及び部品、プラスチック成形機のスクリュー等の製品として有用である。
As described above, in the composite product of the present invention, the outer peripheral layer has high hardness and excellent wear resistance, and the inner peripheral layer has excellent toughness.
Therefore, it is useful as a product such as a roll for hot rolling or cold rolling of steel materials requiring wear resistance for the outer peripheral layer and toughness for the inner peripheral layer, molds and parts for plastic working, screws for plastic molding machines, etc. .
(1) 内周層
(2) 外周層
(1) Inner layer
(2) Outer layer
Claims (8)
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| CN109825773A (en) * | 2019-04-10 | 2019-05-31 | 安徽环渤湾高速钢轧辊有限公司 | Wear-resisting collars of heavy wall high-speed steel and preparation method thereof |
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| JP5522854B2 (en) * | 2011-06-01 | 2014-06-18 | 株式会社日本製鋼所 | Cold tool steel and manufacturing method thereof |
| JP6304466B1 (en) * | 2016-09-02 | 2018-04-04 | Ｊｆｅスチール株式会社 | Roll outer layer material for rolling and composite roll for rolling |
| CN114058947B (en) * | 2021-10-15 | 2022-10-21 | 首钢集团有限公司 | Multi-element composite high-carbon low-alloy tool steel and preparation method and application thereof |
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| JP2796896B2 (en) * | 1990-12-19 | 1998-09-10 | 株式会社クボタ | High speed steel based sintered alloy |
| JP3357953B2 (en) * | 1991-10-25 | 2002-12-16 | 株式会社クボタ | Excellent plastic parts for plastic molding machines with excellent wear resistance |
| JPH05163551A (en) * | 1991-12-11 | 1993-06-29 | Hitachi Metals Ltd | Powder high-speed tool steel |
| JP2972033B2 (en) * | 1992-06-16 | 1999-11-08 | 株式会社クボタ | High speed steel based sintered alloy |
| JPH0971848A (en) * | 1995-09-01 | 1997-03-18 | Kubota Corp | High speed steel base powder alloy excellent in corrosion resistance |
| JP3275727B2 (en) * | 1996-09-18 | 2002-04-22 | 三菱マテリアル株式会社 | Method for producing two-layer valve seat made of Fe-based sintered alloy with excellent wear resistance |
| JP2005240059A (en) * | 2004-02-24 | 2005-09-08 | Sumitomo Denko Shoketsu Gokin Kk | Method for producing composite sintered component and composite sintered component obtained by the method |
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