JP2005036312A - Steel for brake disk, and disk brake unit - Google Patents
Steel for brake disk, and disk brake unit Download PDFInfo
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Description
本発明は、ブレーキディスク用鋼及びディスクブレーキ装置に関し、詳しくは、自動車や鉄道車両などのブレーキディスクに使用される耐摩耗性と靱性とに優れたブレーキディスク用鋼及び上記ブレーキディスク用鋼をブレーキディスクに使用するとともに銅系焼結材料を摩擦材に使用する速度制御性に優れたディスクブレーキ装置、特に２００ｋｍ／時以上の高速走行時の速度制御に好適な耐摩耗性と靱性とに優れたブレーキディスク用鋼及び１６０ｋｍ／時以上の高速走行時の速度制御性に優れたディスクブレーキ装置に関する。 TECHNICAL FIELD The present invention relates to a brake disc steel and a disc brake device. More specifically, the present invention relates to a brake disc steel excellent in wear resistance and toughness used for brake discs of automobiles, railway vehicles, and the like, and brakes the brake disc steel. A disc brake device with excellent speed controllability that uses copper-based sintered material as a friction material as well as a disc, and particularly excellent wear resistance and toughness suitable for speed control at high speeds of 200 km / h or more. The present invention relates to steel for brake discs and a disc brake device excellent in speed controllability at a high speed of 160 km / hour or more.
自動車や鉄道車両などのディスクブレーキ装置は、ブレーキディスクにパッドやライニングと称する摩擦材を圧着させて車輪の回転制動を行う装置である。 A disk brake device such as an automobile or a railway vehicle is a device that performs rotational braking of a wheel by pressing a friction material called a pad or a lining on the brake disk.
ディスクブレーキ装置を構成するブレーキディスクの素材としては、従来一般にJIS G 5501で規定されたＦＣ２５０などの鋳鉄が用いられてきた。しかし、鋳鉄製のブレーキディスクは、鋳鉄に含まれる黒鉛が潤滑作用をもたらし耐摩耗性に優れる一方で、上記黒鉛が熱亀裂発生の起点となるため耐亀裂性に劣り寿命が短い。 Conventionally, cast iron such as FC250 defined by JIS G 5501 has been used as a material for a brake disc constituting a disc brake device. However, cast iron brake discs have excellent wear resistance due to the lubricating action of graphite contained in cast iron. On the other hand, the graphite is inferior in crack resistance and has a short life because the above-mentioned graphite is a starting point for occurrence of thermal cracks.
このため、特許文献１に「耐割損性にすぐれたブレーキディスク用鋼」が、また、特許文献２及び特許文献３に「ディスクブレーキロータ用鋼」が提案されている。 For this reason, Patent Document 1 proposes “brake disc steel excellent in breakage resistance”, and Patent Literature 2 and Patent Literature 3 propose “steel for disc brake rotor”.
本発明の目的は、車両速度が大きくなった場合、特に、２００ｋｍ／時以上で高速走行するような場合でも、耐摩耗性と靱性とに優れるためブレーキディスクの素材として問題なく用いることができるブレーキディスク用鋼を提供することである。本発明のもう１つの目的は、速度制御性に優れた、特に１６０ｋｍ／時以上の高速走行時の速度制御性に優れたディスクブレーキ装置を提供することである。なお、本発明における耐摩耗性と靱性の具体的な目標はそれぞれ、後述の実施例で示すピン試験片に銅系焼結材料を用いたいわゆる「ピンオンディスク摩耗試験」でのディスクの摩耗量が２５０ｍｍ3を下回ること及び、後述の実施例で示すいわゆる「ＣＴ試験片」を用いてASTM E399-83に記載の方法で常温（室温）で行った破壊靱性試験において９３ＭＰａ・ｍ0.5以上の破壊靱性値を有することである。 It is an object of the present invention to provide a brake that can be used without any problem as a material for a brake disk because it has excellent wear resistance and toughness even when the vehicle speed increases, particularly when traveling at a high speed of 200 km / hour or more. It is to provide steel for discs. Another object of the present invention is to provide a disc brake device that is excellent in speed controllability, particularly excellent in speed controllability at a high speed of 160 km / hour or more. The specific goals of wear resistance and toughness in the present invention are the amounts of disk wear in the so-called “pin-on-disk wear test” in which a copper-based sintered material is used for the pin test piece shown in the examples described later. Of less than 250 mm 3 and a fracture of 93 MPa · m 0.5 or more in a fracture toughness test carried out at room temperature (room temperature) by the method described in ASTM E399-83 using a so-called “CT test piece” shown in the examples described later. It has a toughness value.
前述の特許文献１〜３で提案された鋼は、車両のブレーキディスクに適用されているが、最近の２００ｋｍ／時以上の高速走行時の速度制御の場合には、寿命が低下する場合があることが想定される。したがって、寿命を向上させるために、耐摩耗性と耐亀裂性を一層向上させることができる鋼の開発が望まれている。 The steel proposed in Patent Documents 1 to 3 described above is applied to a brake disc of a vehicle, but in the case of speed control at the time of recent high-speed traveling of 200 km / hour or more, the life may be reduced. It is assumed that Therefore, in order to improve the life, development of steel that can further improve the wear resistance and crack resistance is desired.
本発明者らは、このような要望に応えるために、ディスクブレーキ装置のブレーキディスクに用いる鋼の化学組成を種々変えるとともに、摩擦材の材質に銅系焼結材料及びレジン系合成材料を用いて検討を行った。その結果、先ず、下記（ａ）及び（ｂ）の知見を得た。 In order to meet such demands, the present inventors have variously changed the chemical composition of steel used for the brake disc of the disc brake device, and used a copper-based sintered material and a resin-based synthetic material as the friction material. Study was carried out. As a result, first, the following findings (a) and (b) were obtained.
（ａ）ブレーキディスクは摩擦材との摺動により摩耗や熱亀裂を生じるが、高速走行時の車輪の回転制動性、特に１６０ｋｍ／時以上で高速走行するような場合の車輪の回転制動性を高め、更に、耐摩耗性をも高めるためには、摩擦材として銅系焼結材料を用いるのがよい。 (A) Although the brake disk is worn and heat cracked due to sliding with the friction material, the wheel has a rotational braking ability when traveling at a high speed, particularly the rotational braking ability of the wheel when traveling at a high speed of 160 km / hour or more. In order to increase the wear resistance, it is preferable to use a copper-based sintered material as the friction material.
（ｂ）摩擦材に銅系焼結材料を用いた場合に、特定の化学組成からなる鋼を素材とするブレーキディスクの耐摩耗性が大きく向上する。 (B) When a copper-based sintered material is used for the friction material, the wear resistance of a brake disc made of steel having a specific chemical composition is greatly improved.
そこで更に検討を加えたところ、下記（ｃ）〜（ｅ）の知見が得られた。 Therefore, further studies were made, and the following findings (c) to (e) were obtained.
（ｃ）２００ｋｍ／時以上で高速走行する場合、車輪の回転制動のためにブレーキディスクに銅系焼結材料からなる摩擦材が圧着されると、ブレーキディスクと摩擦材の双方とも最表面では１０００℃程度に達し、ブレーキディスクとしては平均３００℃程度に曝される。 (C) When traveling at a high speed of 200 km / hour or more, if a friction material made of a copper-based sintered material is pressure-bonded to the brake disc for rotational braking of the wheels, both the brake disc and the friction material are 1000 on the outermost surface. The brake disk is exposed to an average of about 300 ° C.
（ｄ）素材中に適正量のＣｒ炭化物が存在するブレーキディスクは、こうした高温に曝されても良好な耐摩耗性を示す。 (D) A brake disk having a proper amount of Cr carbide in the material exhibits good wear resistance even when exposed to such high temperatures.
（ｅ）前記のような高温でのブレーキディスクの耐摩耗性は、素材中にＣｒ炭化物だけではなく、適正量のＭｏ炭化物及びＶ炭化物が存在することで一層向上する。特に、Ｃｒ炭化物、Ｍｏ炭化物及びＶ炭化物の存在割合を適正化することで高温での一層良好な耐摩耗性が確保できる。 (E) The wear resistance of the brake disk at a high temperature as described above is further improved by the presence of appropriate amounts of Mo carbide and V carbide as well as Cr carbide in the material. In particular, by optimizing the abundance ratio of Cr carbide, Mo carbide and V carbide, better wear resistance at high temperatures can be ensured.
そこで次に、Ｃ、Ｓｉ及びＭｎの含有量が０．１〜０．６％、０．０１〜１．２％及び０．２〜２．０％である鋼についてＣｒ、Ｍｏ及びＶの含有量を種々変えて、それらの鋼を素材とするブレーキディスクに銅系焼結材料を用いた摩擦材を圧着させた場合について調査した。 Then, next, the content of Cr, Mo and V for steels with C, Si and Mn content of 0.1-0.6%, 0.01-1.2% and 0.2-2.0% We investigated the case where friction materials using a copper-based sintered material were pressure-bonded to brake discs made of those steels with various amounts.
その結果、次の事項が明らかになった。 As a result, the following matters became clear.
（ｆ）「ｆｎ１＝１５Ｃ＋１０Ｃｒ＋６Ｍｏ＋２００Ｖ−３５」の式で表されるｆｎ１の値が０以上を満たす場合に高温での良好な耐摩耗性が確保できる。 (F) When the value of fn1 represented by the formula “fn1 = 15C + 10Cr + 6Mo + 200V−35” satisfies 0 or more, good wear resistance at high temperatures can be ensured.
（ｇ）一方、炭化物量が増加すると靱性の低下が大きくなり、熱亀裂が限界長さまで成長すると脆性的な破壊を生じる。 (G) On the other hand, as the amount of carbide increases, the toughness decreases greatly, and when the thermal crack grows to the limit length, brittle fracture occurs.
そこで更に検討を行った結果、下記の事項が判明した。 As a result of further investigation, the following matters were found.
（ｈ）炭化物量が増加した場合でも靱性の低下が抑制され、脆性破壊を生じることを防止するためには、鋼に適正量のＮｉを含有させればよい。 (H) Even when the amount of carbide increases, in order to prevent a decrease in toughness and prevent brittle fracture, the steel may contain an appropriate amount of Ni.
（ｉ）ブレーキディスクが高温に曝されて変形する場合には、素材鋼の７００℃における高温強度を高めればよい。 (I) When the brake disc is deformed by exposure to high temperature, the high temperature strength of the material steel at 700 ° C. may be increased.
（ｊ）素材鋼の７００℃における高温強度を高めるためには、Ｎｉ及びＣｒの含有量を低めに設定すればよい。 (J) In order to increase the high temperature strength of the material steel at 700 ° C., the contents of Ni and Cr may be set lower.
本発明は、上記の知見に基づいて完成されたものである。 The present invention has been completed based on the above findings.
本発明の要旨は、下記（１）及び（２）に示すブレーキディスク用鋼並びに（３）に示すディスクブレーキ装置にある。 The gist of the present invention resides in the brake disc steel shown in the following (1) and (2) and the disc brake device shown in (3).
（１）質量％で、Ｃ：０．１〜０．６％、Ｓｉ：０．０１〜１．２％、Ｍｎ：０．２〜２．０％、Ｎｉ：０．８〜３．０％、Ｃｒ：１．３〜５．０％、Ｍｏ：０．１〜３．０％、Ｖ：０．００５〜０．５％、Ａｌ：０．０６％未満を含有し、残部はＦｅ及び不純物からなり、下記(1)式で表されるｆｎ１の値が０以上であるブレーキディスク用鋼。
ｆｎ１＝１５Ｃ＋１０Ｃｒ＋６Ｍｏ＋２００Ｖ−３５・・・・・(1)
但し、(1)式中の元素記号は、その元素の質量％での鋼中含有量を表す。
(1) By mass%, C: 0.1-0.6%, Si: 0.01-1.2%, Mn: 0.2-2.0%, Ni: 0.8-3.0% , Cr: 1.3-5.0%, Mo: 0.1-3.0%, V: 0.005-0.5%, Al: less than 0.06%, the balance being Fe and impurities A brake disc steel having a fn1 value of 0 or more represented by the following formula (1):
fn1 = 15C + 10Cr + 6Mo + 200V−35 (1)
However, the element symbol in the formula (1) represents the content in steel in mass% of the element.
（２）質量％で、Ｃ：０．１〜０．６％、Ｓｉ：０．０１〜１．０％、Ｍｎ：０．２〜２．０％、Ｎｉ：１．５〜３．０％、Ｃｒ：１．５％を超えて５．０％まで、Ｍｏ：０．１〜３．０％、Ｖ：０．００５〜０．５％、Ａｌ：０．０６％未満を含有し、残部はＦｅ及び不純物からなり、下記(1)式で表されるｆｎ１の値が０以上であるブレーキディスク用鋼。
ｎ１＝１５Ｃ＋１０Ｃｒ＋６Ｍｏ＋２００Ｖ−３５・・・・・(1)
但し、(1)式中の元素記号は、その元素の質量％での鋼中含有量を表す。
(2) By mass%, C: 0.1-0.6%, Si: 0.01-1.0%, Mn: 0.2-2.0%, Ni: 1.5-3.0% , Cr: more than 1.5% to 5.0%, Mo: 0.1-3.0%, V: 0.005-0.5%, Al: less than 0.06%, the balance Is a steel for brake discs, which consists of Fe and impurities, and the value of fn1 represented by the following formula (1) is 0 or more.
n1 = 15C + 10Cr + 6Mo + 200V-35 (1)
However, the element symbol in the formula (1) represents the content in steel in mass% of the element.
（３）摩擦材をブレーキディスクに圧着させて車輪の回転制動を行うディスクブレーキ装置であって、前記摩擦材が銅系焼結材料からなり、前記ブレーキディスクが上記（１）又は（２）に記載のブレーキディスク用鋼からなるディスクブレーキ装置。 (3) A disk brake device that presses a friction material against a brake disk to perform rotational braking of a wheel, wherein the friction material is made of a copper-based sintered material, and the brake disk is in the above (1) or (2) Disc brake device made of steel for brake disc as described.
以下、上記（１）及び（２）のブレーキディスク用鋼に係る発明並びに（３）のディスクブレーキ装置に係る発明を、それぞれ「（１）の発明」〜「（３）の発明」という。また、総称して「本発明」ということがある。 Hereinafter, the invention relating to the steel for brake discs of (1) and (2) and the invention relating to the disc brake device of (3) are referred to as “the invention of (1)” to “the invention of (3)”, respectively. Also, it may be collectively referred to as “the present invention”.
本発明のブレーキディスク用鋼は耐摩耗性と靱性とに優れるため、車両速度が大きくなって２００ｋｍ／時以上で高速走行するような場合のブレーキディスクの素材として用いることができる。また、本発明のディスクブレーキ装置は１６０ｋｍ／時以上の高速走行の場合にも速度制御性に優れるので、高速走行用車両のディスクブレーキ装置として好適である。 Since the brake disc steel of the present invention is excellent in wear resistance and toughness, it can be used as a material for a brake disc when the vehicle speed increases and the vehicle travels at a high speed of 200 km / hour or more. Further, the disc brake device of the present invention is excellent in speed controllability even at a high speed of 160 km / hour or more, and is therefore suitable as a disc brake device for a high speed vehicle.
以下、本発明の各要件について詳しく説明する。なお、各元素の含有量の「％」表示は「質量％」を意味する。 Hereinafter, each requirement of the present invention will be described in detail. In addition, "%" display of the content of each element means "mass%".
（Ａ）ブレーキディスク用鋼の化学組成
Ｃ：０．１〜０．６％
Ｃは、鋼の焼入れ性を高めて靱性を向上させる。更に、ＣがＣｒ、Ｍｏ及びＶと結合したＣｒ炭化物、Ｍｏ炭化物及びＶ炭化物は、銅系焼結材料からなる摩擦材が圧着された場合の摩耗を防ぐのに有効である。しかし、Ｃの含有量が０．１％未満では添加効果に乏しく、０．６％を超えると却って靱性の低下を招く。したがって、Ｃの含有量を０．１〜０．６％とした。なお、炭化物析出による耐摩耗性向上及び靱性向上の点から、Ｃの含有量は、０．２５〜０．５５％とすることが好ましく、０．２７〜０．５％とすれば一層好ましい。一方、Ｃ含有量が高い場合には、Ａｃ３変態点以上に上昇したブレーキディスク表面が急冷されることで、ブレーキディスクに割れを生じることがあり、こうした割れの発生を低減させるには、Ｃの含有量は０．１５〜０．２７％とすることが好ましい。
(A) Chemical composition of steel for brake disc C: 0.1 to 0.6%
C improves the toughness by increasing the hardenability of the steel. Further, Cr carbide, Mo carbide and V carbide in which C is combined with Cr, Mo and V are effective in preventing wear when a friction material made of a copper-based sintered material is pressed. However, if the C content is less than 0.1%, the effect of addition is poor, and if it exceeds 0.6%, the toughness is reduced. Therefore, the content of C is set to 0.1 to 0.6%. In addition, from the viewpoint of improving wear resistance and toughness due to carbide precipitation, the C content is preferably 0.25 to 0.55%, and more preferably 0.27 to 0.5%. On the other hand, when the C content is high, the brake disc surface that has risen above the Ac3 transformation point is rapidly cooled, which may cause cracks in the brake disc. To reduce the occurrence of such cracks, The content is preferably 0.15 to 0.27%.
Ｓｉ：０．０１〜１．２％
Ｓｉは、鋼の表面に安定な酸化物を形成する作用がある。しかし、その含有量が０．０１％未満では、添加効果に乏しく、１．２％を超えると靱性及び高温強度が低下する。したがって、（１）の発明においては、Ｓｉの含有量を０．０１〜１．２％とした。なお、厳しい靱性が要求される場合のＳｉの含有量は、０．０１〜１．０％とすることが好ましいので、（２）の発明においては、Ｓｉの含有量を０．０１〜１．０％とした。なお、靱性向上のためのＳｉ含有量は０．０５〜０．５％とすれば一層好ましく、０．０７〜０．３％とすれば極めて好ましい。一方、Ａｃ３変態点以上に上昇したブレーキディスク表面が急冷されることで、ブレーキディスクに割れを生じることがあるが、こうした割れの発生を低減させるためには、Ｓｉの含有量を高めにしてＡｃ３変態点を上昇させることも有効である。この場合のＳｉ含有量は、０．９〜１．２％とすることが望ましい。
Si: 0.01-1.2%
Si has an action of forming a stable oxide on the surface of steel. However, if the content is less than 0.01%, the effect of addition is poor, and if it exceeds 1.2%, toughness and high-temperature strength are lowered. Therefore, in the invention of (1), the Si content is set to 0.01 to 1.2%. In addition, since content of Si when severe toughness is required is preferably 0.01 to 1.0%, in the invention of (2), the content of Si is 0.01 to 1.%. 0%. The Si content for improving toughness is more preferably 0.05 to 0.5%, and extremely preferably 0.07 to 0.3%. On the other hand, the brake disk surface that has risen above the Ac3 transformation point is rapidly cooled, which may cause cracks in the brake disk. In order to reduce the occurrence of such cracks, the content of Si is increased by increasing the content of Si. It is also effective to raise the transformation point. In this case, the Si content is desirably 0.9 to 1.2%.
Ｍｎ：０．２〜２．０％
Ｍｎは、鋼の焼入れ性を向上させて靱性を高めるのに有効な元素である。しかし、その含有量が０．２％未満では添加効果が得られず、２．０％を超えると偏析を生じて靱性と強度の低下を招く。したがって、Ｍｎの含有量を０．２〜２．０％とした。なお、Ｍｎの含有量は、０．３〜０．８％とすることが好ましく、０．５〜０．６５％とすれば一層好ましい。
Mn: 0.2 to 2.0%
Mn is an element effective in improving the hardenability of steel and increasing toughness. However, if the content is less than 0.2%, the effect of addition cannot be obtained. If the content exceeds 2.0%, segregation occurs and the toughness and strength decrease. Therefore, the Mn content is set to 0.2 to 2.0%. Note that the Mn content is preferably 0.3 to 0.8%, and more preferably 0.5 to 0.65%.
Ｎｉ：０．８〜３．０％
Ｎｉは、靱性を向上させるのに有効な元素であり、ブレーキディスクの耐摩耗性を高めるためにＣｒ炭化物、Ｍｏ炭化物及びＶ炭化物の量を増加させた場合でも靱性を改善する作用を有する。しかし、その含有量が０．８％未満では添加効果に乏しく、３．０％を超えると変態点が下がるため高温強度の低下を招く。したがって、（１）の発明においては、Ｎｉの含有量を０．８〜３．０％とした。なお、変態点をあまり下げることなく良好な靱性を具備させるためには、１．５〜３．０％のＮｉを含有させることが好ましいので、（２）の発明においては、Ｎｉの含有量を１．５〜３．０％とした。なお、変態点をあまり下げることなく良好な靱性を具備させるためのＮｉ含有量は、１．６〜２．５％とすれば一層好ましく、１．７〜１．９％とすれば極めて好ましい。一方、ブレーキディスクの変形が問題となる場合には、７００℃での高温強度を高めるために、Ｎｉの含有量は低めにすることが有効で、０．８〜１．２％とすることが好ましい。
Ni: 0.8-3.0%
Ni is an element effective for improving toughness, and has an effect of improving toughness even when the amount of Cr carbide, Mo carbide and V carbide is increased in order to increase the wear resistance of the brake disk. However, if the content is less than 0.8%, the effect of addition is poor, and if it exceeds 3.0%, the transformation point is lowered, leading to a decrease in high temperature strength. Therefore, in the invention of (1), the Ni content is set to 0.8 to 3.0%. In order to provide good toughness without significantly lowering the transformation point, it is preferable to contain 1.5 to 3.0% of Ni. Therefore, in the invention of (2), the content of Ni is 1.5 to 3.0%. The Ni content for providing good toughness without significantly lowering the transformation point is more preferably 1.6 to 2.5%, and extremely preferably 1.7 to 1.9%. On the other hand, when the deformation of the brake disk becomes a problem, it is effective to lower the Ni content in order to increase the high temperature strength at 700 ° C., and it should be 0.8 to 1.2%. preferable.
Ｃｒ：１．３〜５．０％
Ｃｒは、靱性及び耐摩耗性の向上に有効な元素である。また、ＣｒがＣと結合したＣｒ炭化物は、銅系焼結材料からなる摩擦材が圧着された場合のブレーキディスクの摩耗を防ぐのに大きい効果を有する。しかし、Ｃｒの含有量が少なく１．３％未満の場合には十分な効果が得られず、逆に含有量が多すぎて５．０％を超えると却って靱性の低下を招く。したがって、（１）の発明においては、Ｃｒの含有量を１．３〜５．０％とした。なお、厳しい耐摩耗性の確保のためには、Ｃｒの含有量は、１．５％を超えて５．０％までとすることが好ましいので、（２）の発明においては、Ｃｒの含有量を１．５％を超えて５．０％までとした。なお、耐摩耗性と靱性とを両立させるためには、Ｃｒ含有量は、２．０〜４．０％とすることが一層好ましく、２．５〜３．０％とすれば極めて好ましい。一方、ブレーキディスクの変形が問題となる場合には、７００℃での高温強度を高めるために、Ｃｒの含有量は低めにすることが有効で、１．３〜１．８％とすることが好ましい。
Cr: 1.3-5.0%
Cr is an element effective for improving toughness and wear resistance. Further, Cr carbide in which Cr is combined with C has a great effect in preventing wear of the brake disc when a friction material made of a copper-based sintered material is pressed. However, when the content of Cr is small and less than 1.3%, a sufficient effect cannot be obtained. Conversely, when the content is too large and exceeds 5.0%, the toughness is deteriorated. Therefore, in the invention of (1), the Cr content is set to 1.3 to 5.0%. In order to ensure strict wear resistance, the Cr content is preferably more than 1.5% and up to 5.0%. Therefore, in the invention of (2), the Cr content Was over 1.5% and up to 5.0%. In order to achieve both wear resistance and toughness, the Cr content is more preferably 2.0 to 4.0%, and extremely preferably 2.5 to 3.0%. On the other hand, when the deformation of the brake disc becomes a problem, it is effective to lower the Cr content in order to increase the high temperature strength at 700 ° C., and it should be 1.3 to 1.8%. preferable.
Ｍｏ：０．１〜３．０％
Ｍｏは、鋼の焼入れ性を高めるとともに焼戻し軟化抵抗を増大させて、靱性及び高温強度を高める作用を有する。更に、Ｍｏの炭化物は、銅系焼結材料からなる摩擦材が圧着された場合のブレーキディスクの摩耗を防ぐのに大きい効果を有する。しかし、Ｍｏの含有量が０．１％未満では前記の効果が得られず、３．０％を超えると却って靱性の低下を招く。したがって、Ｍｏの含有量を０．１〜３．０％とした。なお、靱性を考慮する必要が高い場合には、Ｍｏの含有量は、０．１〜０．８％未満とすることが好ましく、靱性と耐摩耗性の双方を考慮する必要がある場合には、０．２〜０．５％とすれば一層好ましい。
Mo: 0.1-3.0%
Mo has the effect of increasing the toughness and high-temperature strength by increasing the hardenability of the steel and increasing the temper softening resistance. Furthermore, the carbide of Mo has a great effect in preventing wear of the brake disc when a friction material made of a copper-based sintered material is pressure-bonded. However, if the Mo content is less than 0.1%, the above effect cannot be obtained, and if it exceeds 3.0%, the toughness is reduced. Therefore, the Mo content is set to 0.1 to 3.0%. In addition, when it is necessary to consider toughness, the Mo content is preferably 0.1 to less than 0.8%, and when it is necessary to consider both toughness and wear resistance. 0.2 to 0.5% is more preferable.
Ｖ：０．００５〜０．５％
Ｖは、高温強度と耐摩耗性の向上に有効な元素であり、Ｖの炭化物は、銅系焼結材料からなる摩擦材が圧着された場合のブレーキディスクの摩耗を防ぐのに大きい効果を有する。しかし、Ｖの含有量が０．００５％未満では前記効果が得られず、０．５％を超えると靱性の低下が著しくなる。したがって、Ｖの含有量を０．００５〜０．５％とした。なお、Ｖの含有量は、０．０１〜０．４％とすることが好ましく、０．０１〜０．３％とすれば一層好ましい。
V: 0.005-0.5%
V is an element effective for improving high-temperature strength and wear resistance, and the carbide of V has a great effect in preventing wear of the brake disc when a friction material made of a copper-based sintered material is pressure-bonded. . However, if the V content is less than 0.005%, the above effect cannot be obtained, and if it exceeds 0.5%, the toughness is significantly reduced. Therefore, the content of V is set to 0.005 to 0.5%. Note that the V content is preferably 0.01 to 0.4%, and more preferably 0.01 to 0.3%.
Ａｌ：０．０６％未満
Ａｌは添加しなくてもよい。添加すれば、鋼の脱酸作用を有する。この効果を確実に得るにはＡｌは０．０１％以上の含有量とすることが好ましい。しかし、Ａｌを多量に含有すると靱性の低下を招き、また、鋼の地きずの原因となる。特に、その量が０．０６％以上になると靱性の低下が著しくなるし、鋼の地きずも多くなる。したがって、Ａｌの含有量を０．０６％未満とした。なお、Ａｌの含有量の上限は０．０５５％とするのが好ましく、０．０５％とすれば一層好ましい。
Al: less than 0.06% Al may not be added. If added, it has a deoxidizing action of steel. In order to reliably obtain this effect, the Al content is preferably 0.01% or more. However, when a large amount of Al is contained, the toughness is lowered and it becomes a cause of steel flaws. In particular, when the amount is 0.06% or more, the toughness is remarkably lowered, and the number of steel flaws increases. Therefore, the Al content is less than 0.06%. Note that the upper limit of the Al content is preferably 0.055%, and more preferably 0.05%.
ｆｎ１：０以上
前記(1)式で表されるｆｎ１の値が０以上の場合にＣｒ炭化物、Ｍｏ炭化物及びＶ炭化物の存在割合が適正化されて高温での良好な耐摩耗性が確保される。したがって、ｆｎ１の値を０以上と規定した。なお、ｆｎ１の値は５以上であることが好ましい。なお、ｆｎ１の値の最大値は、Ｃ、Ｃｒ、Ｍｏ及びＶの含有量がそれぞれ前記した上限値である０．６％、５．０％、３．０％及び０．５％の場合の１４２であってもよいが、良好な靱性を確保するためには、ｆｎ１の値は７０以下とすることが好ましく、２０以下とすれば更に好ましい。
fn1: 0 or more When the value of fn1 represented by the above formula (1) is 0 or more, the existence ratio of Cr carbide, Mo carbide and V carbide is optimized, and good wear resistance at high temperature is secured. . Therefore, the value of fn1 is defined as 0 or more. Note that the value of fn1 is preferably 5 or more. In addition, the maximum value of the value of fn1 is the case where the contents of C, Cr, Mo, and V are the above-described upper limit values of 0.6%, 5.0%, 3.0%, and 0.5%, respectively. 142 may be used, but in order to ensure good toughness, the value of fn1 is preferably 70 or less, and more preferably 20 or less.
（１）の発明及び（２）の発明に係るブレーキディスク用鋼は前記した量のＣからＡｌまでの元素を含み、残部がＦｅと不純物からなる鋼である。ここで、不純物中のＰ、Ｓ、Ｃｕ及びＴｉの含有量はそれぞれ次のようにすることが好ましい。 The brake disk steel according to the invention of (1) and the invention of (2) is a steel containing the above-mentioned amounts of elements from C to Al, with the balance being Fe and impurities. Here, the contents of P, S, Cu and Ti in the impurities are preferably as follows.
Ｐ：０．０３％以下
不純物としてのＰは含有量が多いと偏析が大きくなって、靱性の低下や熱亀裂の発生を助長し、特に、その含有量が０．０３％を超えると靱性の低下や熱亀裂の発生が著しくなる。したがって、Ｐの含有量は０．０３％以下とするのがよく、低ければ低いほどよい。
P: 0.03% or less P as an impurity increases segregation when the content is large, and promotes the deterioration of toughness and the occurrence of thermal cracks. In particular, when the content exceeds 0.03%, Deterioration and generation of thermal cracks become significant. Therefore, the P content is preferably 0.03% or less, and the lower the better.
Ｓ：０．０３％以下
不純物としてのＳは靱性を低下させ、特に、その含有量が０．０３％を超えると靱性の低下が著しくなる。したがって、Ｓの含有量は０．０３％以下とするのがよく、低ければ低いほどよい。
S: 0.03% or less S as an impurity reduces toughness, and particularly when its content exceeds 0.03%, the toughness is significantly reduced. Therefore, the S content is preferably 0.03% or less, and the lower the better.
Ｃｕ：０．１％未満
不純物としてのＣｕは靱性を低下させ、特に、その含有量が０．１％以上になると靱性の低下が著しくなる。したがって、Ｃｕの含有量は０．１％未満とするのがよく、低ければ低いほどよい。
Cu: Less than 0.1% Cu as an impurity decreases toughness, and particularly when its content is 0.1% or more, the toughness is significantly decreased. Therefore, the Cu content should be less than 0.1%, and the lower the better.
Ｔｉ：０．０１％未満
不純物としてのＴｉは偏析しやすく、靱性の低下を招き、特に、その含有量が０．０１％以上になると靱性の低下が著しくなる。したがって、Ｔｉの含有量は０．０１％未満とするのがよく、低ければ低いほどよい。
Ti: Less than 0.01% Ti as an impurity is easily segregated and causes a decrease in toughness. In particular, when the content is 0.01% or more, the toughness is significantly decreased. Therefore, the Ti content is preferably less than 0.01%, and the lower the better.
（Ｂ）ディスクブレーキ装置の構成
（３）の発明に係るディスクブレーキ装置は、摩擦材が銅系焼結材料からなり、ブレーキディスクが上記（Ａ）項で述べた化学組成を有する（１）の発明又は（２）の発明に係るブレーキディスク用鋼からなるものとする。
(B) Configuration of Disc Brake Device In the disc brake device according to the invention of (3), the friction material is made of a copper-based sintered material, and the brake disc has the chemical composition described in (A) above. It shall consist of steel for brake discs which concerns on invention or invention of (2).
これは、ブレーキディスク用鋼として前記（１）の発明又は（２）の発明に係る鋼を用いるとともに摩擦材として銅系焼結材料を用いることで、高速走行時の車輪の回転制動性、特に２００ｋｍ／時以上で高速走行するような場合の車輪の回転制動性を高めるとともに耐摩耗性をも高めることができるからである。 This is because the steel according to the invention of the above (1) or the invention of (2) is used as the steel for the brake disc and the copper-based sintered material is used as the friction material. This is because the rotational braking performance of the wheel when traveling at a high speed of 200 km / hour or more can be enhanced and the wear resistance can be enhanced.
以下、実施例により本発明を更に詳しく説明する。 Hereinafter, the present invention will be described in more detail with reference to examples.
（実施例１）
表１に示す化学組成を有する材料を１５０ｋｇの真空溶解炉を用いて溶製した。表１において、材料６〜１０は化学組成及びｆｎ１の値が本発明で規定する範囲内の本発明例の鋼、材料１、材料３〜５は成分のいずれかの含有量又はｆｎ１の値が本発明の規定から外れた比較例の鋼である。また、材料２はブレーキディスクに用いられている鋳鉄である。なお、以下の説明においては、材料２の鋳鉄を含めて「鋼」ともいう。
(Example 1)
A material having the chemical composition shown in Table 1 was melted using a 150 kg vacuum melting furnace. In Table 1, the materials 6 to 10 are steels of the present invention examples in which the chemical composition and the value of fn1 are within the range defined by the present invention, and the materials 1 and 3 to 5 have the content of any of the components or the value of fn1. It is steel of the comparative example which is outside the definition of the present invention. Material 2 is cast iron used for brake discs. In the following description, the cast iron of material 2 is also referred to as “steel”.
次いで、上記各鋼の鋼塊を通常の方法によって熱間鍛造と圧延を行い、８０ｍｍ×２５０ｍｍ×２５ｍｍの鋼片にした。このようにして得た鋼片を、その化学組成に応じて、通常の方法で８５０〜１０００℃に加熱した後、油焼入れ又は大気中放冷して焼入れ処理を行った。次いで、５５０〜６５０℃に加熱・保持した後、大気中放冷して焼戻し処理を施し、硬さをブリネル硬さ（ＨＢ硬さ）で２８０〜３１０に調整した。 Subsequently, the steel ingot of each said steel was hot forged and rolled by the normal method, and was made into the steel piece of 80 mm x 250 mm x 25 mm. The steel piece thus obtained was heated to 850 to 1000 ° C. by a normal method according to its chemical composition, and then quenched by oil quenching or standing in the air. Subsequently, after heating and holding at 550-650 degreeC, it stood to cool in air | atmosphere and gave the tempering process, and the hardness was adjusted to 280-310 by Brinell hardness (HB hardness).
上記のようにして得た焼入れ−焼戻し後の各鋼片から通常の方法で、いわゆる「ピンオンディスク摩耗試験」のためのディスク試験片を切り出した。また、鋳鉄である材料２を除いた各鋼片から、破壊靱性試験のためのいわゆる「ＣＴ試験片（コンパクト試験片）」を切り出した。材料２についてＣＴ試験片を採取しなかったのは、一般に鋳鉄の破壊靱性値は低く２０ＭＰａ・ｍ0.5以下の低レベルとなるためである。 A disk test piece for so-called “pin-on-disk wear test” was cut out from each steel piece after quenching and tempering obtained as described above by a conventional method. Further, a so-called “CT test piece (compact test piece)” for fracture toughness test was cut out from each steel piece excluding the material 2 which was cast iron. The reason why the CT test piece was not collected for material 2 is that the fracture toughness value of cast iron is generally low and a low level of 20 MPa · m 0.5 or less.
ピンオンディスク摩耗試験は、銅系焼結材料の直径が１０ｍｍで長さが２５ｍｍのピン試験片を、鋼１〜１０を素材とする直径が１７５ｍｍで厚さが１５ｍｍのディスク試験片に押し付けて次に示す条件で実施し、試験前後のディスクの質量変化から摩耗量を求めた。 In the pin-on-disk wear test, a copper-based sintered material having a diameter of 10 mm and a length of 25 mm is pressed against a disk test piece having a diameter of 175 mm and a thickness of 15 mm made of steel 1-10. The test was carried out under the following conditions, and the amount of wear was determined from the mass change of the disk before and after the test.
・押し付け圧：０．９ＭＰａ、
・ディスク回転速度：５００ｒｐｍ、
・摺動距離：１０5ｍ、
・潤滑：無し。
・ Pressing pressure: 0.9 MPa,
-Disk rotation speed: 500 rpm,
・ Sliding distance: 10 5 m
・ Lubrication: None.
破壊靱性試験は、厚さ２．５ｃｍのＴ−ＳＴ方向の「ＣＴ試験片」を用いて、ASTM E399-83に記載の方法で、常温（室温）で行った。 The fracture toughness test was performed at room temperature (room temperature) by the method described in ASTM E399-83 using a “CT specimen” in the T-ST direction having a thickness of 2.5 cm.
表２に、ピンオンディスク摩耗試験と破壊靱性試験の結果をまとめて示す。 Table 2 summarizes the results of the pin-on-disk wear test and fracture toughness test.
表２から、ピン試験片に銅系焼結材料を用いた場合の本発明例の鋼６〜１０を素材とするディスクの摩耗量はいずれも２５０ｍｍ3を下回っており、耐摩耗性に優れていることが明らかである。更に、鋼６〜１０の常温での破壊靱性値は９３ＭＰａ・ｍ0.5以上であり、靱性にも優れている。 From Table 2, when the copper-based sintered material is used for the pin test piece, the wear amount of the disk made of steel 6 to 10 of the present invention is less than 250 mm 3 , and the wear resistance is excellent. It is clear that Furthermore, the fracture toughness value at normal temperature of steels 6 to 10 is 93 MPa · m 0.5 or more, and the toughness is also excellent.
これに対して、ピン試験片に銅系焼結材料を用いた場合、比較例の鋼１、鋼２、鋼４及び鋼５を素材とするディスクの摩耗量はいずれも２５０ｍｍ3を超えており、耐摩耗性に劣ることが明らかである。また、鋼３の場合は常温での破壊靱性値が低く、靱性面で劣っている。なお、ブレーキディスクに用いられている鋳鉄の場合、前記のとおり、その破壊靱性値は２０ＭＰａ・ｍ0.5以下の低レベルであるため、鋼２は摩耗量も必ずしも優れていらず、靱性もまた劣るものである。 On the other hand, when a copper-based sintered material is used for the pin specimen, the wear amount of the disk made of steel 1, steel 2, steel 4 and steel 5 of the comparative example is over 250 mm 3. It is clear that the wear resistance is inferior. In the case of steel 3, the fracture toughness value at room temperature is low and the toughness is inferior. In addition, in the case of cast iron used for a brake disk, as described above, the fracture toughness value is a low level of 20 MPa · m 0.5 or less, so that the amount of wear of steel 2 is not necessarily excellent, and the toughness is also inferior. Is.
（実施例２）
表３に示す化学組成を有する鋼を１５０ｋｇの真空溶解炉を用いて溶製した。表３において、鋼１２は化学組成及びｆｎ１の値が本発明で規定する範囲内の本発明例の鋼、鋼１１はＣｒの含有量及びｆｎ１の値が本発明の規定から外れた比較例の鋼である。
(Example 2)
Steel having the chemical composition shown in Table 3 was melted using a 150 kg vacuum melting furnace. In Table 3, steel 12 is a steel of the present invention within the range defined by the present invention in terms of chemical composition and fn1 value, and steel 11 is a comparative example in which the Cr content and fn1 value deviate from the present invention. It is steel.
次いで、上記各鋼の鋼塊を通常の方法によって熱間鍛造と圧延を行い、１５０ｍｍ×１５０ｍｍ×８０ｍｍの鋼片にした。このようにして得た鋼片を、通常の方法で９００℃に加熱した後、油焼入れした。次いで、６００〜６２０℃に加熱・保持し、その後大気中放冷して焼戻し処理を施し、硬さをブリネル硬さ（ＨＢ硬さ）で２９０〜３１０に調整した。 Next, the steel ingots of the above steels were hot forged and rolled by ordinary methods to form steel pieces of 150 mm × 150 mm × 80 mm. The steel piece thus obtained was heated to 900 ° C. by a normal method and then quenched with oil. Subsequently, it heated and hold | maintained at 600-620 degreeC, after that, it stood to cool in air | atmosphere, the tempering process was performed, and hardness was adjusted to 290-310 by Brinell hardness (HB hardness).
このようにして得た鋼片からディスク試験片を切り出し、銅系焼結材料を摩擦材としたブレーキ試験を行った。 A disk test piece was cut out from the steel piece thus obtained, and a brake test was conducted using a copper-based sintered material as a friction material.
なお、上記ブレーキ試験は摩擦材である銅系焼結材料の押し付け力を２．２４ｋＮとし、回転数を５３８〜３２２５ｒｐｍとしてブレーキ回数が１００の条件で行った。ここで、前記の５３８〜３２２５ｒｐｍという回転数は、ほぼ５０〜３００ｋｍ／時の車両走行速度に相当する。 The brake test was performed under the condition that the pressing force of the copper-based sintered material as the friction material was 2.24 kN, the rotation speed was 538 to 3225 rpm, and the number of brakes was 100. Here, the rotational speed of 538 to 3225 rpm corresponds to a vehicle traveling speed of approximately 50 to 300 km / hour.
表４に、上記ブレーキ試験でのディスク摩耗量（摩耗体積）を示す。 Table 4 shows the disk wear amount (wear volume) in the brake test.
表４から明らかなように、比較例の鋼１１を素材とするディスクの摩耗量は回転数２１５０ｒｐｍ（車両走行速度で２００ｋｍ／時に相当）の場合でも１４３５ｍｍ3と大きい。これに対して、本発明例の鋼１２を素材とするディスクの摩耗量は回転数２６８８ｒｐｍ（車両走行速度で２５０ｋｍ／時に相当）の場合でも３８３ｍｍ3と小さく、耐摩耗性に優れていることが明らかである。 As is apparent from Table 4, the wear amount of the disk made of the steel 11 of the comparative example is as large as 1435 mm 3 even when the rotational speed is 2150 rpm (corresponding to 200 km / hour in vehicle traveling speed). On the other hand, the wear amount of the disk made of the steel 12 of the present invention is as small as 383 mm 3 even when the rotational speed is 2688 rpm (corresponding to 250 km / hour in the vehicle running speed), and the wear resistance is excellent. it is obvious.
本発明のブレーキディスク用鋼は耐摩耗性と靱性とに優れるため、車両速度が大きくなって２００ｋｍ／時以上で高速走行するような場合のブレーキディスクの素材として用いることができる。また、本発明のディスクブレーキ装置は１６０ｋｍ／時以上の高速走行の場合にも速度制御性に優れるので、高速走行用車両のディスクブレーキ装置として好適である。
Since the brake disc steel of the present invention is excellent in wear resistance and toughness, it can be used as a material for a brake disc when the vehicle speed increases and the vehicle travels at a high speed of 200 km / hour or more. Further, the disc brake device of the present invention is excellent in speed controllability even at a high speed of 160 km / hour or more, and is therefore suitable as a disc brake device for a high speed vehicle.
Claims (3)
ｆｎ１＝１５Ｃ＋１０Ｃｒ＋６Ｍｏ＋２００Ｖ−３５・・・・・(1)
但し、(1)式中の元素記号は、その元素の質量％での鋼中含有量を表す。 In mass%, C: 0.1-0.6%, Si: 0.01-1.2%, Mn: 0.2-2.0%, Ni: 0.8-3.0%, Cr: 1.3 to 5.0%, Mo: 0.1 to 3.0%, V: 0.005 to 0.5%, Al: less than 0.06%, the balance consisting of Fe and impurities, Steel for brake discs having a value of fn1 represented by the following formula (1) of 0 or more.
fn1 = 15C + 10Cr + 6Mo + 200V−35 (1)
However, the element symbol in the formula (1) represents the content in steel in mass% of the element.
ｆｎ１＝１５Ｃ＋１０Ｃｒ＋６Ｍｏ＋２００Ｖ−３５・・・・・(1)
但し、(1)式中の元素記号は、その元素の質量％での鋼中含有量を表す。 In mass%, C: 0.1-0.6%, Si: 0.01-1.0%, Mn: 0.2-2.0%, Ni: 1.5-3.0%, Cr: More than 1.5% to 5.0%, Mo: 0.1 to 3.0%, V: 0.005 to 0.5%, Al: less than 0.06%, the balance being Fe and Steel for brake discs which is made of impurities and has a value of fn1 represented by the following formula (1) of 0 or more.
fn1 = 15C + 10Cr + 6Mo + 200V−35 (1)
However, the element symbol in the formula (1) represents the content in steel in mass% of the element.
3. A disc brake device that presses a friction material against a brake disc to perform rotational braking of a wheel, wherein the friction material is made of a copper-based sintered material, and the brake disc is a brake disc steel according to claim 1 or 2. Disc brake device consisting of
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| JP2004143389A JP4207841B2 (en) | 2003-06-30 | 2004-05-13 | Steel for brake disc and disc brake device |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2009149922A (en) * | 2007-12-19 | 2009-07-09 | Sumitomo Metal Ind Ltd | Steel material for brake disc, and brake disc |
| CN104878308A (en) * | 2014-02-27 | 2015-09-02 | 天津威尔朗科技有限公司 | Novel high-strength and high-hardness wear resistant cutter tooth and making technology thereof |
| CN106282817A (en) * | 2016-10-13 | 2017-01-04 | 南京创贝高速传动机械有限公司 | A kind of high-speed gear box wear-resistant gear |
| CN106566999A (en) * | 2016-11-04 | 2017-04-19 | 南京工程学院 | Wear-resisting material used for brake disc of high-speed train and preparation method for wear-resisting material |
| JP2017514992A (en) * | 2014-03-11 | 2017-06-08 | ダイムラー・アクチェンゲゼルシャフトＤａｉｍｌｅｒ ＡＧ | Brake disc coating comprising iron alloy composition and method for producing the same |
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| CN103510024B (en) * | 2012-06-28 | 2016-05-25 | 中车戚墅堰机车车辆工艺研究所有限公司 | For the alloy cast steel of brake disc of high-speed train and heat treatment method thereof and the brake disc of high-speed train manufactured by this alloy cast steel |
| CN105779893B (en) * | 2012-06-28 | 2018-08-10 | 中车戚墅堰机车车辆工艺研究所有限公司 | Alloy cast steel for brake disc of high-speed train and the brake disc of high-speed train that is manufactured by the alloy cast steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009149922A (en) * | 2007-12-19 | 2009-07-09 | Sumitomo Metal Ind Ltd | Steel material for brake disc, and brake disc |
| CN104878308A (en) * | 2014-02-27 | 2015-09-02 | 天津威尔朗科技有限公司 | Novel high-strength and high-hardness wear resistant cutter tooth and making technology thereof |
| JP2017514992A (en) * | 2014-03-11 | 2017-06-08 | ダイムラー・アクチェンゲゼルシャフトＤａｉｍｌｅｒ ＡＧ | Brake disc coating comprising iron alloy composition and method for producing the same |
| US10288136B2 (en) | 2014-03-11 | 2019-05-14 | Daimler Ag | Brake disc coating made from an iron alloy composition and method for the production thereof |
| CN106282817A (en) * | 2016-10-13 | 2017-01-04 | 南京创贝高速传动机械有限公司 | A kind of high-speed gear box wear-resistant gear |
| CN106566999A (en) * | 2016-11-04 | 2017-04-19 | 南京工程学院 | Wear-resisting material used for brake disc of high-speed train and preparation method for wear-resisting material |
| CN115505853A (en) * | 2022-10-26 | 2022-12-23 | 本钢板材股份有限公司 | Square steel for high-speed rail brake and preparation method thereof |
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