JP2001192780A - Martensitic stainless steel for disk brake - Google Patents
Martensitic stainless steel for disk brakeInfo
- Publication number
- JP2001192780A JP2001192780A JP2000001666A JP2000001666A JP2001192780A JP 2001192780 A JP2001192780 A JP 2001192780A JP 2000001666 A JP2000001666 A JP 2000001666A JP 2000001666 A JP2000001666 A JP 2000001666A JP 2001192780 A JP2001192780 A JP 2001192780A
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- Prior art keywords
- cooling
- hardness
- brake
- stainless steel
- martensitic stainless
- Prior art date
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、二輪車やスノーモ
ービルなどのディスクブレーキに使用されるマルテンサ
イト系ステンレス鋼であって、鋼成分を特定し、オース
テナイト化後水冷やガス冷却の種々の冷却速度で冷却し
ても、冷却ままで、ブレーキとして必要な硬さが得ら
れ、かつ靱性にも優れたマルテンサイト系ステンレス鋼
に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a martensitic stainless steel used for disc brakes of motorcycles, snowmobiles, etc., in which the steel component is specified, and various cooling rates of water cooling and gas cooling after austenitization. The present invention relates to a martensitic stainless steel which can provide the required hardness as a brake and has excellent toughness even when cooled by cooling.
【０００２】[0002]
【従来の技術】ディスクブレーキには一般に耐磨耗性が
求められる。ブレーキとパッドの間でいわゆるブレーキ
の鳴きが生じるため、ブレーキの硬さ（ロックウェル硬
さＣスケール：ＨＲＣ）は、３２ＨＲＣ〜３８ＨＲＣが
求められる。二輪車やスノーモービルのようにディスク
ブレーキが直接目に触れる場合は、美観上耐銹性も必要
となる。従って、ディスクブレーキ用材料として、自硬
性と耐銹性に優れたマルテンサイト系ステンレス鋼が開
発されてきた（特開昭５７−１９８２４９号公報）。こ
の鋼は、焼入れままでブレーキとして所望の硬さを安定
して得るため、低Ｃ、低Ｎ化した上、焼入れ性の低下を
主にＭｎを適量添加して補うものである。2. Description of the Related Art Disc brakes generally require wear resistance. Since a so-called brake squeal occurs between the brake and the pad, the hardness of the brake (Rockwell hardness C scale: HRC) is required to be 32 HRC to 38 HRC. When the disc brake is directly visible, as in a motorcycle or a snowmobile, rust resistance is also required from an aesthetic standpoint. Accordingly, a martensitic stainless steel excellent in self-hardening and rust resistance has been developed as a disc brake material (Japanese Patent Laid-Open No. 57-198249). In order to stably obtain a desired hardness as a brake while being quenched, this steel is reduced in C and N and compensates for a decrease in hardenability mainly by adding an appropriate amount of Mn.
【０００３】また、焼入れままだけではなく、使用中の
ブレーキ制動発熱による軟化に対する抵抗を有する鋼も
開示されている（特開平１０−１５２７６０号公報）。
この鋼は、望ましくはＣｕ添加量を１．０％以上とする
ことにより、ブレーキ制動で６００℃にまで加熱される
ような場合でも、ロックウェルＣスケールの硬さの差が
１０未満となり、優れた軟化抵抗を有するものである。[0003] Further, not only as-quenched steel but also steel having resistance to softening due to heat generated by braking during use has been disclosed (Japanese Patent Application Laid-Open No. 10-152760).
This steel preferably has a Cu addition amount of 1.0% or more, so that even if it is heated up to 600 ° C. by brake braking, the hardness difference of the Rockwell C scale is less than 10, and the steel is excellent. It has a softening resistance.
【０００４】ところが、最近ディスクブレーキヘの要求
特性は多様化し、熱伝導性の良いブレーキが求められる
ようになっている。この要求に対応するためブレーキ加
工メーカーは、Ｃｕをマルテンサイト系ステンレス鋼で
挟んだ３層構造のディスクブレーキを製造している。こ
のブレーキでは、Ｃｕとステンレス鋼の接合は真空中で
ロウ付けで行われる。製造工程省略と酸化防止の目的
で、ロウ付けしたブレーキ素材をそのまま真空中で加熱
・冷却して、いわゆる真空焼入れを行う方法が採られて
いる。However, recently, the characteristics required for a disc brake have been diversified, and a brake having good heat conductivity has been demanded. To meet this demand, brake processing manufacturers have produced disc brakes having a three-layer structure in which Cu is sandwiched between martensitic stainless steels. In this brake, joining of Cu and stainless steel is performed by brazing in a vacuum. For the purpose of omitting the manufacturing process and preventing oxidation, a method has been adopted in which the brazed brake material is directly heated and cooled in vacuum to perform so-called vacuum quenching.
【０００５】このような製造工程を採った場合、従来の
ディスクブレーキ用マルテンサイト系ステンレス鋼では
焼入れ硬さが不十分で、耐磨耗性すなわちブレーキ寿命
が低下する。同時に、十分な焼入れ組織が得られないた
めに、焼入れ後の靱性にも劣るという欠点がある。ま
た、ブレーキ制動発熱による軟化を抑制するために、Ｃ
ｕによる析出硬化を活用する場合は、靱性が著しく低下
する場合がある。When such a manufacturing process is employed, the quench hardness of the conventional martensitic stainless steel for disc brakes is insufficient, and the wear resistance, that is, the brake life is reduced. At the same time, since a sufficient quenched structure cannot be obtained, there is a disadvantage that the toughness after quenching is inferior. In order to suppress softening due to heat generated by braking, C
When utilizing precipitation hardening by u, the toughness may be significantly reduced.
【０００６】[0006]
【発明が解決しようとする課題】本発明の目的は、上記
従来鋼の持つ欠点を有利に克服し、水冷や油冷の冷却速
度のみならず、ガス焼入れの場合のように冷却速度が遅
い場合でも、焼入れままでディスクブレーキとしての好
適な硬さ、３２ＨＲＣ〜３８ＨＲＣが安定して得られ、
併せて熱処理ままや使用中の靱性にも優れたマルテンサ
イト系ステンレス鋼の成分組成を明らかにすることにあ
る。SUMMARY OF THE INVENTION It is an object of the present invention to advantageously overcome the above-mentioned disadvantages of the conventional steel, and not only to a cooling rate of water cooling or oil cooling, but also to a case where the cooling rate is low as in the case of gas quenching. However, it is possible to obtain a stable hardness of 32 HRC to 38 HRC as a hard disk brake as-quenched,
Another object of the present invention is to clarify the component composition of a martensitic stainless steel having excellent toughness during heat treatment or during use.
【０００７】[0007]
【課題を解決するための手段】本発明は、ＣおよびＮ添
加量を限定し、かつ焼入れ性を得るためにＭｎ、Ｎｉ、
Ｃｕを適量添加し、中でもＮｉ添加で、オーステナイト
化後種々の冷却速度で冷却しても所望の硬さになるよう
にすると共に、熱処理ままのみならずＣｕの時効析出後
でも優れた靱性が得られるようにした好適組成で構成さ
れるマルテンサイト系ステンレス鋼である。すなわち、
本発明の骨子とするところは、質量％で、 Ｃ＋Ｎ：０．０５〜０．１％、 Ｓｉ：０．５％以下、 Ｍｎ：０．５〜２．０％、 Ｃｒ：１０〜１５％、 Ｎｉ：０．５〜２．０％、 Ｃｕ：０．５〜２．０％ を含有し、残部がＦｅおよび不可避的不純物からなるデ
ィスクブレーキ用マルテンサイト系ステンレス鋼であ
る。SUMMARY OF THE INVENTION According to the present invention, Mn, Ni, and Ni are added in order to limit the amounts of C and N added and to obtain hardenability.
By adding an appropriate amount of Cu, especially Ni, to obtain a desired hardness even when cooled at various cooling rates after austenization, excellent toughness is obtained not only as it is after heat treatment but also after aging precipitation of Cu. Is a martensitic stainless steel having a suitable composition. That is,
In the mass of the present invention, C + N: 0.05 to 0.1%, Si: 0.5% or less, Mn: 0.5 to 2.0%, Cr: 10 to 15% This is a martensitic stainless steel for a disc brake containing 0.5 to 2.0% of Ni and 0.5 to 2.0% of Cu and the balance of Fe and unavoidable impurities.
【０００８】[0008]
【発明の実施の形態】本発明者は、オーステナイト化後
種々の速度による冷却ままで、ディスクブレーキとして
の好適な硬さ、すなわち３２ＨＲＣ〜３８ＨＲＣを有す
る鋼を検討するにあたり、焼入れ性の増大に寄与するオ
ーステナイト形成元素の添加効果を検討した。ＣｒやＭ
ｏも焼入れ性の増大に寄与すると考えられるが、これら
はフェライト形成元素であり、フェライト生成元素の過
度の添加は、オーステナイト化温度域を狭め、結果とし
て熱処理可能な加熱温度域を狭くするので、検討の対象
から外した。Ｃ、Ｎは典型的なオーステナイト形成元素
であるが、添加量により冷却後の硬さが大きく変動する
ので、比較的低廉なオーステナイト形成元素であるＭ
ｎ、Ｃｕ、Ｎｉの効果を検討した。BEST MODE FOR CARRYING OUT THE INVENTION The present inventor has studied hardening steel having a suitable hardness as a disc brake, that is, 32 HRC to 38 HRC, while cooling at various speeds after austenitization, and has contributed to an increase in hardenability. The effect of adding the austenite-forming element to be added was examined. Cr or M
Although o is also considered to contribute to the increase in hardenability, these are ferrite-forming elements, and excessive addition of ferrite-forming elements narrows the austenitizing temperature range and consequently narrows the heating temperature range in which heat treatment can be performed. Removed from consideration. C and N are typical austenite-forming elements, but since the hardness after cooling varies greatly depending on the amount of addition, M is a relatively inexpensive austenite-forming element.
The effects of n, Cu, and Ni were studied.
【０００９】Ｃ＋Ｎ：０．０７２％、Ｃｒ：１２．２％
をべ一スに、 ２．０％Ｍｎ、 １．３％Ｍｎ−１．７％Ｃｕ、 １．３％Ｍｎ−０．８％Ｎｉ を含有する鋼を、１０５０℃×ｌ０min 加熱でオーステ
ナイト化した後、０．０１、０．１、１、ｌ０℃／ｓの
一定の冷却速度で室温まで冷却し、硬さ（ＨＲＣ）を測
定した。結果を図１に示す。C + N: 0.072%, Cr: 12.2%
A steel containing 2.0% Mn, 1.3% Mn-1.7% Cu, 1.3% Mn-0.8% Ni was austenitized by heating at 1050 ° C. × 10 min. Thereafter, the sample was cooled to room temperature at a constant cooling rate of 0.01, 0.1, 1, 10 ° C./s, and the hardness (HRC) was measured. The results are shown in FIG.
【００１０】図１は、オーステナイト化後の冷却ままの
硬さが冷却速度により変化する様子を、２％Ｍｎ、１．
７％Ｃｕ、０．８％Ｎｉ添加鋼についてそれぞれ見たも
のである。図において、Ｎｉの添加により０．０１℃／
ｓからｌ０℃／ｓの非常に広い冷却速度範囲でディスク
ブレーキで要求される３２ＨＲＣ〜３８ＨＲＣを満足す
るので、水冷や油冷の高冷却速度から真空熱処理の低冷
却速度まで、いかなるオーステナイト化後の冷却速度で
も要求硬さ範囲を安定して得られることが分かる。FIG. 1 shows how the hardness as-cooled after austenitization changes with the cooling rate.
This is a view of each of the steels containing 7% Cu and 0.8% Ni. In the figure, 0.01 ° C /
Since it satisfies 32 HRC to 38 HRC required for a disc brake in a very wide cooling rate range from 10 ° C./s to 10 ° C./s, any austenitizing from high cooling rate of water cooling or oil cooling to low cooling rate of vacuum heat treatment can be performed. It can be seen that the required hardness range can be stably obtained even at the cooling rate.
【００１１】Ｍｎを増やした２．０％Ｍｎ鋼は、冷却速
度が０．１℃／ｓまで低下すると硬さの下限を外れてし
まう。Ｃｕを添加した１．３％Ｍｎ−１．７％Ｃｕ鋼で
は、高冷速側では硬さが高過ぎ、低冷速の０．１℃／ｓ
では硬さが低すぎる。さらに冷却速度が０．０１℃／ｓ
まで低下すると再び硬さが上昇するが、これは冷却中に
Ｃｕが析出したことによるものである。いずれにして
も、ＭｎやＣｕの添加量を増して、種々の冷却速度で３
２ＨＲＣ〜３８ＨＲＣの硬さ範囲に収めるのは困難であ
る。The 2.0% Mn steel with increased Mn falls below the lower limit of hardness when the cooling rate is reduced to 0.1 ° C./s. In the case of 1.3% Mn-1.7% Cu steel to which Cu is added, the hardness is too high on the high cooling speed side and 0.1 ° C./s at the low cooling speed.
Then the hardness is too low. Furthermore, the cooling rate is 0.01 ° C / s
When the hardness is lowered, the hardness increases again, which is due to the precipitation of Cu during cooling. In any case, the addition amount of Mn or Cu is increased to increase the cooling rate at various cooling rates.
It is difficult to fall within the hardness range of 2 HRC to 38 HRC.
【００１２】これに対して、Ｎｉを添加した１．３％Ｍ
ｎ−０．８％Ｎｉ鋼は、０．０１℃／ｓから１０℃／ｓ
に至る広い冷却速度範囲で、安定して３２ＨＲＣ〜３８
ＨＲＣの硬さ範囲が達成できる。すなわち、Ｎｉ添加に
より水冷や油冷の高冷却速度から真空熱処理の低冷却速
度まで、いかなる冷却速度でもディスクブレーキで要求
される硬さ範囲を安定して得られることを知見した。On the other hand, 1.3% M containing Ni
n-0.8% Ni steel is 0.01 ° C / s to 10 ° C / s
32HRC-38 in a wide cooling rate range up to
A hardness range of HRC can be achieved. In other words, it has been found that the hardness range required for the disc brake can be stably obtained by adding Ni at any cooling rate from a high cooling rate of water cooling or oil cooling to a low cooling rate of vacuum heat treatment.
【００１３】次に、本発明者らは表１に化学組成を示す
種々の鋼（本発明鋼１〜１０）を実験室で溶製して、オ
ーステナイト化−冷却後、ならびに更に５５０℃で焼戻
しを行った後の２mmＶノッチシャルピー衝撃値を測定し
た。結果を表２に示す。０．５５％から１．８５％のＮ
ｉ添加（本発明鋼１〜６）で、冷却ままで１００J/cm2
以上の衝撃値を有し、マルテンサイト系ステンレス鋼と
しては優れた衝撃値を示す。また、一般にマルテンサイ
ト系ステンレス鋼は５５０℃程度で焼き戻すとＣｒの炭
化物の析出により衝撃値が低下することが知られている
が、これらの鋼では焼戻し後も少なくとも６０J/cm2 の
衝撃値を有し、靱性に優れることを確認した。Next, the present inventors melted various steels (inventive steels 1 to 10) having the chemical compositions shown in Table 1 in a laboratory, austenitized and cooled, and further tempered at 550 ° C. , A 2 mm V notch Charpy impact value was measured. Table 2 shows the results. 0.55% to 1.85% N
i addition (inventive steels 1-6), 100 J / cm 2 while cooling
It has the above impact value, and shows an excellent impact value as a martensitic stainless steel. It is generally known that, when tempered at about 550 ° C., martensitic stainless steels have a reduced impact value due to precipitation of Cr carbide, but these steels have an impact value of at least 60 J / cm 2 even after tempering. And excellent toughness.
【００１４】本発明者らは、靱性に及ぼすＮｉ添加の効
果は１％以上のＣｕを添加して、Ｃｕの析出により５５
０℃の焼戻し（ブレーキ制動発熱による焼戻しを想定）
に対する軟化抵抗を持たせた場合にも有利に発揮される
ことを知見した。表１の本発明鋼７〜ｌ０のようにＣｕ
を１．２５〜１．８５％含有し、５５０℃の焼戻し後で
もＣｕの析出で３２ＨＲＣ以上の硬さを維持する場合で
も、表２に示すように衝撃値は非常に優れることを知見
した。The present inventors have found that the effect of the addition of Ni on the toughness is as follows.
0 ° C tempering (assuming tempering due to brake braking heat)
It has been found that it is also advantageously exerted when softening resistance is provided. As shown in Table 1, the steels 7 to 10 of the present invention have Cu
1.25 to 1.85%, and even after tempering at 550 ° C., even when the hardness of 32 HRC or more is maintained by precipitation of Cu, the impact value was found to be extremely excellent as shown in Table 2.
【００１５】本発明者らは、上述の知見に基づき合金設
計することにより、本発明を完成するに至った。以下
に、本発明の成分限定理由を述べる。The present inventors have completed the present invention by designing an alloy based on the above findings. The reasons for limiting the components of the present invention are described below.
【００１６】ＣおよびＮは、マルテンサイトの硬さを高
め耐磨耗性を得るのに有効な元素である。本発明の構成
成分組成において、焼入れままでディスクブレーキとし
て所望の最低の硬さ３２ＨＲＣを得るために、Ｃ＋Ｎの
下限を０．０５％とする。一方、Ｃ＋Ｎの上限は、ディ
スクブレーキとして所望の最高の硬さ３８ＨＲＣに収め
るために、０．１０％とする。C and N are effective elements for increasing the hardness of martensite and obtaining abrasion resistance. In the composition of the present invention, the lower limit of C + N is set to 0.05% in order to obtain a desired minimum hardness of 32 HRC as a disc brake while quenching. On the other hand, the upper limit of C + N is set to 0.10% in order to achieve the desired maximum hardness of 38 HRC as a disc brake.
【００１７】Ｓｉは、脱酸元素が残存したものであり、
過度に添加すると非金属介在物が鋼中に残存して靱性低
下等の弊害をもたらすため、０．５％を上限に添加す
る。Si is the one in which the deoxidizing element remains,
If added excessively, non-metallic inclusions remain in the steel and cause adverse effects such as a decrease in toughness. Therefore, 0.5% is added to the upper limit.
【００１８】Ｍｎは、脱酸と焼入れ可能温度域を拡大す
るために０．５％以上添加する。しかし、多量に添加す
ると鋼中にＭｎＳが多量に残存し、発銹起点となって耐
銹性を劣化させるので、上限を２．０％とする。Mn is added in an amount of 0.5% or more to extend the temperature range in which deoxidation and quenching are possible. However, when added in a large amount, a large amount of MnS remains in the steel and becomes a rusting point to deteriorate the rust resistance. Therefore, the upper limit is set to 2.0%.
【００１９】Ｃｒは、耐食性を確保するため最低１０％
以上を必要とする。しかし、１５％を超えるとフェライ
ト主体の組織となり、所望の硬さが得られなくなるの
で、上限を１５％とする。Cr is at least 10% in order to secure corrosion resistance.
Need more. However, if it exceeds 15%, the structure becomes mainly ferrite, and the desired hardness cannot be obtained, so the upper limit is made 15%.
【００２０】Ｎｉは、Ｍｎと同様焼入れ可能温度域を広
げるだけでなく、水冷や油冷の高冷却速度から真空熱処
理の低冷却速度までオーステナイト化後のいかなる冷却
速度でも、ディスクブレーキで要求される硬さ範囲を安
定して得るためと、熱処理まま（焼入れ処理）ならびに
焼戻し後の優れた靱性を得るために、０．５％以上添加
する。しかし、Ｎｉは高価である上、過度に添加すると
冷却後に室温で残留するオーステナイト量が増大し、硬
さが低下する場合があるので、上限を２．０％とする。Ni, like Mn, not only widens the quenching temperature range, but is also required for disc brakes at any cooling rate after austenitization from a high cooling rate of water cooling or oil cooling to a low cooling rate of vacuum heat treatment. In order to stably obtain a hardness range and to obtain excellent toughness after heat treatment (quenching treatment) and tempering, 0.5% or more is added. However, Ni is expensive, and if added excessively, the amount of austenite remaining at room temperature after cooling increases and the hardness may decrease, so the upper limit is made 2.0%.
【００２１】Ｃｕは、焼入れ可能温度域を拡大するため
０．５％以上添加する。また、Ｃｕはブレーキ制動発熱
による軟化を抑制するのにも効果的で、制動発熱が６０
０℃まで高くなるような場合には、望ましくは１．０％
以上を添加する。しかし、過度に添加すると熱間加工性
を低下させるし、Ｃｕの析出で靱性が低下するので、上
限を２．０％とする。Cu is added in an amount of 0.5% or more in order to expand the quenching temperature range. Cu is also effective in suppressing softening due to brake braking heat.
If the temperature rises to 0 ° C., it is desirable that the
Add the above. However, if added excessively, the hot workability is lowered, and the toughness is lowered by the precipitation of Cu, so the upper limit is made 2.0%.
【００２２】[0022]
【実施例】表１に示す成分の鋼を実験室で溶製し、イン
ゴットを作製した。実験室で熱間圧延後熱処理用のサン
プルを切り出し、熱処理を行った。熱処理は、１０５０
℃にｌ０分間加熱してオーステナイト化後、窒素ガスで
室温まで冷却した。サンプルの温度を熱電対で測定しな
がら、ｌ０℃／ｓおよび０．１℃／ｓの一定の冷却速度
で冷却した。冷却ままのサンプルについて、ロックウェ
ルＣスケールの硬さを測定した。硬さは、ディスクブレ
ーキで一般に要求される３２ＨＲＣ〜３８ＨＲＣを満た
す必要がある。EXAMPLES Steels having the components shown in Table 1 were melted in a laboratory to produce ingots. A sample for heat treatment was cut out in the laboratory after hot rolling, and heat treatment was performed. Heat treatment is 1050
After heating to 10 ° C. for 10 minutes to austenitize, the mixture was cooled to room temperature with nitrogen gas. The sample was cooled at a constant cooling rate of 10 ° C./s and 0.1 ° C./s while measuring the temperature of the sample with a thermocouple. The hardness of the Rockwell C scale was measured for the as-cooled sample. Hardness must meet 32 HRC to 38 HRC generally required for disc brakes.
【００２３】また、１／４サブサイズの２mmＶノッチシ
ャルピー衝撃試験片を作製し、０℃の衝撃値を測定し
た。試験数は３で、フルサイズの試験片に換算した平均
の衝撃値を求めた。また上記の熱処理（冷却速度はｌ０
℃／ｓ）後さらに５５０℃で３０分間加熱後空冷する焼
戻しを行い、同様に硬さ並びに衝撃値の測定を行った。
結果を表２に示す。A 1/4 sub-size 2 mm V notch Charpy impact test piece was prepared, and the impact value at 0 ° C. was measured. The number of tests was 3, and the average impact value converted into a full-size test piece was determined. The above heat treatment (cooling rate is 10
After heating at 550 ° C. for 30 minutes, tempering was performed by air cooling, and the hardness and impact value were measured in the same manner.
Table 2 shows the results.
【００２４】本発明の条件に従う鋼の場合、オーステナ
イト化後の冷却ままで、冷却速度が異なっても、３２Ｈ
ＲＣ〜３８ＨＲＣを満足し、所望の硬さが得られる。ま
たオーステナイト化後の冷却まま、ならびに更に５５０
℃で焼戻しを行った後も優れた衝撃値を有している。特
に、Ｃｕを１％以上添加して５５０℃の焼戻し後も３２
ＨＲＣを維持する場合、Ｃｕによる析出硬化が生じてい
ても良好な靱性を保つことができる。In the case of the steel according to the conditions of the present invention, 32H
Satisfies RC to 38 HRC, and a desired hardness is obtained. In addition, the cooling after austenitization, and further 550
It has excellent impact value even after tempering at ℃. In particular, even after adding 1% or more of Cu and tempering at 550 ° C.,
When HRC is maintained, good toughness can be maintained even when precipitation hardening due to Cu occurs.
【００２５】しかし、本発明の条件にない比較鋼におい
ては、比較鋼１、２、３は冷却速度０．１℃／ｓのとき
の硬さが低く、さらにＮｉは添加せずにＭｎ＋Ｃｕを添
加した比較鋼２は、冷却速度１０℃／ｓのとき硬さが高
過ぎてしまう。また比較鋼１、２、３ではオーステナイ
ト化後冷却ままの衝撃値は、本発明鋼のそれに比べて相
対的に低い。さらに比較鋼２、３では焼戻し後の衝撃値
が顕著に低下する。比較鋼４では冷却速度に依らずオー
ステナイト化後の冷却ままで、硬さは所望の範囲を満足
するが、焼戻しを行った場合Ｃｕ析出による衝撃値の低
下が著しい。However, in the comparative steels not satisfying the conditions of the present invention, the comparative steels 1, 2, and 3 have low hardness at a cooling rate of 0.1 ° C./s, and do not add Ni but add Mn + Cu. The comparative steel 2 obtained has too high hardness at a cooling rate of 10 ° C./s. In Comparative Steels 1, 2, and 3, the impact value of the steel after cooling after austenitization was relatively lower than that of the steel of the present invention. Further, in Comparative Steels 2 and 3, the impact value after tempering is significantly reduced. In Comparative Steel 4, the hardness satisfies the desired range with cooling after austenitization irrespective of the cooling rate, but when tempering is performed, the impact value is significantly reduced due to precipitation of Cu.
【００２６】[0026]
【表１】 [Table 1]
【００２７】[0027]
【表２】 [Table 2]
【００２８】[0028]
【発明の効果】本発明により、オーステナイト化後水冷
やガス冷却の種々の冷却速度で冷却しても、冷却まま
で、ブレーキとして必要な硬さが得られ、かつ靱性にも
優れたディスクブレーキ用マルテンサイト系ステンレス
鋼が提供できるため、工業的効果は非常に大きい。Industrial Applicability According to the present invention, a disc brake excellent in toughness and having the required hardness as a brake while cooling at various cooling rates such as water cooling and gas cooling after austenitization. Since martensitic stainless steel can be provided, the industrial effect is very large.
【図１】２％Ｍｎ、１．７％Ｃｕ、０．８％Ｎｉ添加鋼
について、オーステナイト化後の冷却ままの硬さが冷却
速度により変化する状況を示す図。FIG. 1 is a view showing a state in which the hardness of a steel after addition of austenitizing while being cooled changes with the cooling rate for 2% Mn, 1.7% Cu, and 0.8% Ni added steel.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 天藤 雅之 富津市新富20−１ 新日本製鐵株式会社技 術開発本部内 Ｆターム(参考） 3J058 BA46 BA61 CB11 EA04 EA09 EA17 EA37 EA40 FA02 ────────────────────────────────────────────────── ─── Continuing on the front page (72) Inventor Masayuki Amatou 20-1 Shintomi, Futtsu-shi F-term in the Technology Development Division, Nippon Steel Corporation (reference) 3J058 BA46 BA61 CB11 EA04 EA09 EA17 EA37 EA40 FA02
Claims (1)
ィスクブレーキ用マルテンサイト系ステンレス鋼。C + N: 0.05 to 0.1%, Si: 0.5% or less, Mn: 0.5 to 2.0%, Cr: 10 to 15%, Ni: 0. Martensitic stainless steel for disc brakes containing 5 to 2.0%, Cu: 0.5 to 2.0%, and the balance being Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000001666A JP4283405B2 (en) | 2000-01-07 | 2000-01-07 | Martensitic stainless steel for disc brakes |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000001666A JP4283405B2 (en) | 2000-01-07 | 2000-01-07 | Martensitic stainless steel for disc brakes |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2001192780A true JP2001192780A (en) | 2001-07-17 |
| JP4283405B2 JP4283405B2 (en) | 2009-06-24 |
Family
ID=18530868
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2000001666A Expired - Lifetime JP4283405B2 (en) | 2000-01-07 | 2000-01-07 | Martensitic stainless steel for disc brakes |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4283405B2 (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003013185A (en) * | 2001-06-27 | 2003-01-15 | Nisshin Steel Co Ltd | Fe-Cr-Ni-Cu ALLOY FOR SLIDING MEMBER |
| JP2003027133A (en) * | 2001-07-19 | 2003-01-29 | Nisshin Steel Co Ltd | Method for producing alloy for sliding member |
| JP2003073743A (en) * | 2001-08-31 | 2003-03-12 | Kawasaki Steel Corp | Method for manufacturing hot-rolled sheet of low- carbon martensitic stainless steel superior in punching property |
| JP2005133204A (en) * | 2003-10-08 | 2005-05-26 | Jfe Steel Kk | Brake disk having excellent temper softening resistance, and its production method |
| JP2006291240A (en) * | 2005-04-06 | 2006-10-26 | Jfe Steel Kk | Brake disk with excellent temper softening resistance and toughness |
| JP2014208911A (en) * | 2008-07-28 | 2014-11-06 | エイティーアイ・プロパティーズ・インコーポレーテッド | Thermal mechanical treatment of ferrous alloys, and related alloys and articles |
| JP2017190525A (en) * | 2016-04-07 | 2017-10-19 | エイ・フィンクル・アンド・サンズ・カンパニー | Precipitation hardened martensitic stainless steel and reciprocating pump manufactured therewith |
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2000
- 2000-01-07 JP JP2000001666A patent/JP4283405B2/en not_active Expired - Lifetime
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003013185A (en) * | 2001-06-27 | 2003-01-15 | Nisshin Steel Co Ltd | Fe-Cr-Ni-Cu ALLOY FOR SLIDING MEMBER |
| JP2003027133A (en) * | 2001-07-19 | 2003-01-29 | Nisshin Steel Co Ltd | Method for producing alloy for sliding member |
| JP2003073743A (en) * | 2001-08-31 | 2003-03-12 | Kawasaki Steel Corp | Method for manufacturing hot-rolled sheet of low- carbon martensitic stainless steel superior in punching property |
| JP2005133204A (en) * | 2003-10-08 | 2005-05-26 | Jfe Steel Kk | Brake disk having excellent temper softening resistance, and its production method |
| JP4496908B2 (en) * | 2003-10-08 | 2010-07-07 | Ｊｆｅスチール株式会社 | Brake disc excellent in tempering softening resistance and manufacturing method thereof |
| JP2006291240A (en) * | 2005-04-06 | 2006-10-26 | Jfe Steel Kk | Brake disk with excellent temper softening resistance and toughness |
| JP4569360B2 (en) * | 2005-04-06 | 2010-10-27 | Ｊｆｅスチール株式会社 | Brake disc with excellent temper softening resistance and toughness |
| JP2014208911A (en) * | 2008-07-28 | 2014-11-06 | エイティーアイ・プロパティーズ・インコーポレーテッド | Thermal mechanical treatment of ferrous alloys, and related alloys and articles |
| JP2017190525A (en) * | 2016-04-07 | 2017-10-19 | エイ・フィンクル・アンド・サンズ・カンパニー | Precipitation hardened martensitic stainless steel and reciprocating pump manufactured therewith |
| JP7133288B2 (en) | 2016-04-07 | 2022-09-08 | エイ・フィンクル・アンド・サンズ・カンパニー | Precipitation hardening martensitic stainless steel and reciprocating pumps made therefrom |
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