JP2007247027A - HIGH HEAT RESISTANT Cr-CONTAINING STEEL FOR BRAKE DISC - Google Patents
HIGH HEAT RESISTANT Cr-CONTAINING STEEL FOR BRAKE DISC Download PDFInfo
- Publication number
- JP2007247027A JP2007247027A JP2006075197A JP2006075197A JP2007247027A JP 2007247027 A JP2007247027 A JP 2007247027A JP 2006075197 A JP2006075197 A JP 2006075197A JP 2006075197 A JP2006075197 A JP 2006075197A JP 2007247027 A JP2007247027 A JP 2007247027A
- Authority
- JP
- Japan
- Prior art keywords
- mass
- less
- high heat
- hot
- steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 38
- 239000010959 steel Substances 0.000 title claims abstract description 38
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 230000007547 defect Effects 0.000 abstract description 12
- 238000005098 hot rolling Methods 0.000 abstract description 9
- 229910052799 carbon Inorganic materials 0.000 abstract description 7
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 7
- 229910052758 niobium Inorganic materials 0.000 abstract description 5
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 4
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 206010039509 Scab Diseases 0.000 abstract 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 13
- 230000000694 effects Effects 0.000 description 11
- 238000010791 quenching Methods 0.000 description 9
- 230000000171 quenching effect Effects 0.000 description 9
- 230000007423 decrease Effects 0.000 description 8
- 230000009467 reduction Effects 0.000 description 8
- 238000005496 tempering Methods 0.000 description 8
- 238000009864 tensile test Methods 0.000 description 7
- 238000011156 evaluation Methods 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 5
- 201000004384 Alopecia Diseases 0.000 description 4
- 230000003676 hair loss Effects 0.000 description 4
- 230000001965 increasing effect Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 229910001105 martensitic stainless steel Inorganic materials 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000009825 accumulation Methods 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 230000020169 heat generation Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 230000001960 triggered effect Effects 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Images
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
本発明は、オートバイや自転車等のブレーキディスクのローター部（ブレーキ摺動部）に用いられる、適正な焼入れ硬さと焼戻し軟化抵抗を有し、耐食性にも優れる低炭素マルテンサイト系の高耐熱Ｃｒ含有鋼に関し、特に、熱間加工性に優れるブレーキディスク用高耐熱Ｃｒ含有鋼に関するものである。 The present invention is used for a rotor part (brake sliding part) of a brake disk of a motorcycle, a bicycle or the like, has a suitable quenching hardness and tempering softening resistance, and has a low carbon martensite-based high heat resistance Cr content. In particular, the present invention relates to a high heat-resistant Cr-containing steel for brake disks that is excellent in hot workability.
オートバイや自転車等のブレーキディスクのローター部には、耐錆性と耐熱性が必要とされる。特に、耐熱性に関しては、ブレーキ制動時のパッドとディスクとの摩擦によって、５００℃を超える温度域まで繰り返し昇温されるため、このようなブレーキ制動時の発熱によっても軟質化せず、変形や磨耗が生じ難い特性が求められる。 Rust resistance and heat resistance are required for the rotor part of a brake disc of a motorcycle or bicycle. In particular, regarding heat resistance, the temperature is repeatedly raised to a temperature range exceeding 500 ° C. due to friction between the pad and the disk at the time of brake braking. A characteristic that does not easily cause wear is required.
このような特性を満たす材料としては、従来、Ｃｒを１２〜１３ｍａｓｓ％含有するＳＵＳ４１０系の低炭素マルテンサイト系ステンレス鋼が多く採用されており、通常、焼入れした状態で使用されている。ローター部は、焼入れた状態において、硬さがＨＲＣ（ロックウェル硬さのＣスケール）で３０〜４５の範囲が適正とされ、また、５００℃で１時間の焼戻しを受けても軟化せず、同レベルの硬さを保持するように成分設計がなされている。 As a material satisfying such characteristics, SUS410-based low carbon martensitic stainless steel containing 12 to 13 mass% of Cr has been conventionally used and is usually used in a quenched state. In the hardened state, the hardness of HRC (Rockwell hardness C scale) in the range of 30 to 45 is appropriate, and the rotor part does not soften even when subjected to tempering at 500 ° C. for 1 hour. Ingredients are designed to maintain the same level of hardness.
さらに、近年では、ブレーキの性能向上やブレーキディスクの軽量化の要望を受けて、より高い耐熱性を有する高耐熱鋼が開発され、使用されるようになってきている。例えば、特許文献１〜４に開示されたような、Ｃ，Ｎ，Ｎｂ，Ｖ，Ｃｕ，Ｔｉ，Ｍｏなどのブレーキ制動時の発熱に対する焼戻し軟化抵抗を高める元素を添加し、または添加量を増加して、焼入れ後や５５０〜６５０℃×１時間の焼戻し後においても、ＨＲＣ硬さで３０〜４５を維持できるような高耐熱鋼が開発されている。
しかしながら、特許文献１〜４に開示されたような、焼戻し軟化抵抗を高める元素を多く含有させた高耐熱鋼は、極めて熱間加工性に乏しいという問題がある。このため、熱間圧延等の製造工程において、鋼板に耳割れやへげ等の欠陥が発生し易く、製造歩留りの低下を招くと共に、その欠陥に起因して、使用時（走行時）にディスクが割れる原因となることもある。中でも、Ｎを０．０３０ｍａｓｓ％以上含有する高Ｎの高耐熱鋼は、５５０℃を超える耐熱性が安定的に得られ、耐錆性にも優れる反面、９００〜１１００℃の温度域における熱間延性が極めて低く、欠陥が発生し易いという問題を抱えている。 However, as disclosed in Patent Documents 1 to 4, there is a problem that the high heat-resistant steel containing a large amount of elements that increase the temper softening resistance is extremely poor in hot workability. For this reason, in a manufacturing process such as hot rolling, defects such as ear cracks and nicks are likely to occur in the steel sheet, resulting in a decrease in manufacturing yield, and due to the defects, the disk is in use (during traveling). May break. Among them, high heat resistant steel with high N containing 0.030 mass% or more of N can stably obtain heat resistance exceeding 550 ° C. and is excellent in rust resistance, but is hot in the temperature range of 900 to 1100 ° C. It has a problem that ductility is extremely low and defects are likely to occur.
そこで、本発明の目的は、熱間圧延工程における耳割れやへげ等の欠陥発生を有効に防止することができるブレーキディスク用の高耐熱Ｃｒ含有鋼を提供することにある。 Then, the objective of this invention is providing the high heat resistant Cr containing steel for brake discs which can prevent effectively generation | occurrence | production of defects, such as an ear crack and a baldness, in a hot rolling process.
本発明が対象とする高耐熱性の低炭素マルテンサイト系Ｃｒ含有鋼は、通常、７００〜１２００℃の温度域で熱間圧延を行って、鋼板とされる。そこで、発明者らは、まず、この温度域における熱間引張試験による断面減少率（ＲＡ）と欠陥発生との関係を調査した。その結果、９００〜１１００℃の温度範囲でＲＡが４０％を下回る材料は、熱間圧延方法の如何に関わらず、耳割れやへげ発生率が極めて高いことが判明した。 The high heat resistant low carbon martensitic Cr-containing steel targeted by the present invention is usually hot rolled in a temperature range of 700 to 1200 ° C. to be a steel plate. In view of this, the inventors first investigated the relationship between the cross-section reduction rate (RA) and the occurrence of defects in a hot tensile test in this temperature range. As a result, it was found that a material having an RA of less than 40% in the temperature range of 900 to 1100 ° C. has a very high rate of occurrence of ear cracks and baldness regardless of the hot rolling method.
そこでさらに、成分組成と熱間延性との関係について検討を進めた結果、含有するＮ量に応じてＢを適正量添加すれば、耐熱性や耐錆性を劣化させることなく、熱間延性をも向上し、ひいては熱間圧延時の欠陥発生を防止できることを見出し、本発明を完成するに至った。 Therefore, as a result of studying the relationship between the component composition and hot ductility, if an appropriate amount of B is added according to the amount of N contained, hot ductility can be improved without deteriorating heat resistance and rust resistance. As a result, it has been found that the occurrence of defects during hot rolling can be prevented, and the present invention has been completed.
すなわち、本発明は、Ｃ：０．０１〜０．１０ｍａｓｓ％、Ｍｎ：０．３〜２．５ｍａｓｓ％、Ｓｉ：０．５ｍａｓｓ％以下、Ｐ：０．０４ｍａｓｓ％以下、Ｓ：０．００８ｍａｓｓ％以下、Ｃｒ：１０．５〜１４．５ｍａｓｓ％、Ａｌ：０．１０ｍａｓｓ％以下、Ｎ：０．０３０〜０．０８０ｍａｓｓ％、Ｎｂ：０．０５〜０．６０ｍａｓｓ％Ｎｉ：０．１〜１．５ｍａｓｓ％、さらに、Ｂ：０．００５０ｍａｓｓ％以下かつＢ／Ｎ≧０．０３０を満たして含有し、さらに、Ｃｕ，Ｖ，Ｍｏ，Ｗ，ＴａおよびＴｉのうちから選ばれる１種または２種以上を合計で０．０５〜２．５ｍａｓｓ％含有し、残部がＦｅおよび不可避的不純物からなるブレーキディスク用の高耐熱Ｃｒ含有鋼である。 That is, the present invention is C: 0.01-0.10 mass%, Mn: 0.3-2.5 mass%, Si: 0.5 mass% or less, P: 0.04 mass% or less, S: 0.008 mass% Hereinafter, Cr: 10.5 to 14.5 mass%, Al: 0.10 mass% or less, N: 0.030 to 0.080 mass%, Nb: 0.05 to 0.60 mass% Ni: 0.1 to 1. 5 mass%, further B: 0.0050 mass% or less and satisfying B / N ≧ 0.030, further containing one or more selected from Cu, V, Mo, W, Ta and Ti Is a high heat-resistant Cr-containing steel for brake discs that contains 0.05 to 2.5 mass% in total, with the balance being Fe and inevitable impurities.
本発明の高耐熱Ｃｒ含有鋼は、上記ＣｕおよびＮｉの組成が、Ｃｕ：０．３０ｍａｓｓ％超〜２．５ｍａｓｓ％、Ｎｉ：０．５×Ｃｕｍａｓｓ％以上であることを特徴とする。 The high heat-resistant Cr-containing steel of the present invention is characterized in that the composition of Cu and Ni is Cu: more than 0.30 mass% to 2.5 mass%, Ni: 0.5 × Cumass% or more.
本発明によれば、オートバイや自転車等のブレーキディスクのローター部に使用される高耐熱Ｃｒ含有鋼の熱間加工性を向上し、欠陥の発生を防止することができる。したがって、本発明によれが、上記鋼を歩留りよく安定して製造できるようになると共に、ローター部の走行中における割れ発生の防止できるので安全性の向上にも寄与することができる。 ADVANTAGE OF THE INVENTION According to this invention, hot workability of the high heat-resistant Cr containing steel used for the rotor part of brake discs, such as a motorcycle and a bicycle, can be improved, and generation | occurrence | production of a defect can be prevented. Therefore, according to the present invention, the steel can be stably manufactured with a high yield, and cracks can be prevented from being generated during the running of the rotor portion, which can contribute to an improvement in safety.
本発明を開発する契機となった実験について説明する。
Ｃ：０．０４ｍａｓｓ％、Ｍｎ：１．５ｍａｓｓ％、Ｎ：０．０５ｍａｓｓ％、Ｎｂ：０．１５ｍａｓｓ％、Ｃｒ：１２ｍａｓｓ％、残部が実質的にＦｅよりなる組成の低炭素マルテンサイト系ステンレス鋼において、Ｂの添加量を変えてＢ／Ｎ比を変化させた鋼を溶製し、この鋼について、熱間圧延温度域である９００〜１１００℃の間で熱間引張試験を行い、Ｂ／Ｎ比と断面減少率（ＲＡ）との関係を調べた。
An experiment that triggered the development of the present invention will be described.
C: 0.04 mass%, Mn: 1.5 mass%, N: 0.05 mass%, Nb: 0.15 mass%, Cr: 12 mass%, low carbon martensitic stainless steel having a composition substantially consisting of Fe. In this example, a steel having a B / N ratio changed by changing the addition amount of B was melted, and a hot tensile test was performed between 900 and 1100 ° C., which is a hot rolling temperature range, for this steel. The relationship between N ratio and cross-sectional area reduction rate (RA) was examined.
図１は、上記試験の結果を示したものである。Ｂ無添加の場合、断面減少率ＲＡは、９００〜１１００℃の間で凹型に低下し、１０００℃近傍では４０％を下回っている。しかし、これにＢを添加してＢ／Ｎを高めていくと、ＲＡは上昇して４０％を上回るようになるが、Ｂを添加し過ぎると、却ってＲＡを減少させる。即ち、ＲＡを改善するには、Ｂ／Ｎを適正範囲に制御する必要があることがわかる。そこで、発明者らは、上記知見にさらに、その他成分の適正組成範囲についても検討を重ねて本発明を完成させた。 FIG. 1 shows the results of the above test. When B is not added, the cross-sectional reduction rate RA decreases to a concave shape between 900 and 1100 ° C., and is below 40% in the vicinity of 1000 ° C. However, when B is added to this to increase B / N, RA increases and exceeds 40%. However, if B is added excessively, RA is decreased. That is, it can be seen that in order to improve RA, it is necessary to control B / N within an appropriate range. Therefore, the inventors completed the present invention by further studying the appropriate composition range of other components in addition to the above knowledge.
次に、本発明のブレーキディスク用の高耐熱Ｃｒ含有鋼について説明する。
本発明が対象とする高耐熱Ｃｒ含有鋼は、ブレーキディスク用材料として十分な耐錆性を有し、ローターに仕上げた状態（通常は焼入れ状態であるが、歪取り焼鈍や若干の焼戻しを行った状態の場合もある）での硬さが、ＨＲＣで３０〜４５であり、また、５５０℃以上の温度で１時間の焼戻し処理後でも、同様の硬さを維持できるように成分設計した、高耐熱性を有する低炭素マルテンサイト系Ｃｒ含有鋼である。
Next, the high heat-resistant Cr-containing steel for the brake disc of the present invention will be described.
The high heat-resistant Cr-containing steel targeted by the present invention has sufficient rust resistance as a material for brake disks, and is finished in a rotor (usually in a quenched state, but is subjected to strain relief annealing and slight tempering) The component was designed so that the same hardness could be maintained even after tempering treatment for 1 hour at a temperature of 550 ° C. or higher. It is a low carbon martensitic Cr-containing steel having high heat resistance.
上記特性を有する本発明の高耐熱Ｃｒ含有鋼は、Ｃ：０．０１〜０．１０ｍａｓｓ％、Ｍｎ：０．３〜２．５ｍａｓｓ％、Ｓｉ：０．５ｍａｓｓ％以下、Ｐ：０．０４ｍａｓｓ％以下、Ｓ：０．００８ｍａｓｓ％以下、Ｃｒ：１０．５〜１４．５ｍａｓｓ％、Ａｌ：０．１０ｍａｓｓ％以下、Ｎ：０．０３０〜０．０８０ｍａｓｓ％、Ｎｂ：０．０５〜０．６０ｍａｓｓ％、Ｎｉ：０．１〜１．５ｍａｓｓ％を含有し、さらに、Ｂを０．００５０ｍａｓｓ％以下かつＢ／Ｎ≧０．０３０を満たして添加した成分系を基本とし、これにさらに、Ｃｕ，Ｖ，Ｍｏ，Ｗ，ＴａおよびＴｉのうちから選ばれる１種または２種以上を合計で０．０５〜２．５ｍａｓｓ％添加したものである。
以下、各成分の組成範囲の限定理由について説明する。
The high heat-resistant Cr-containing steel of the present invention having the above characteristics is C: 0.01-0.10 mass%, Mn: 0.3-2.5 mass%, Si: 0.5 mass% or less, P: 0.04 mass% Hereinafter, S: 0.008 mass% or less, Cr: 10.5 to 14.5 mass%, Al: 0.10 mass% or less, N: 0.030 to 0.080 mass%, Nb: 0.05 to 0.60 mass% , Ni: 0.1 to 1.5 mass%, and B is added in an amount of 0.0050 mass% or less and B / N ≧ 0.030 is added. , Mo, W, Ta and Ti are added in a total amount of 0.05 to 2.5 mass%.
Hereinafter, the reasons for limiting the composition range of each component will be described.
Ｃ：０．０１〜０．１０ｍａｓｓ％
Ｃは、鋼の焼入れ後、焼戻し後の硬さを決定する重要な元素であり、適正な硬さ範囲を確保するためには、０．０１ｍａｓｓ％以上の含有が必要である。しかし、０．１０％を超えて含有すると、粗大な炭化物が多数生成して、発錆の起点となり、耐錆性が低下する。よって、Ｃの範囲は０．０１〜０．１０ｍａｓｓ％とする。なお、より耐錆性を向上する観点からは、Ｃは０．０５０ｍａｓｓ％未満とするのが好ましい。
C: 0.01-0.10 mass%
C is an important element that determines the hardness after quenching and tempering of steel, and in order to ensure an appropriate hardness range, it is necessary to contain 0.01 mass% or more. However, if the content exceeds 0.10%, a large number of coarse carbides are generated, which becomes a starting point of rusting, and rust resistance is lowered. Therefore, the range of C is set to 0.01 to 0.10 mass%. In addition, from the viewpoint of further improving the rust resistance, C is preferably less than 0.050 mass%.
Ｓｉ：０．５ｍａｓｓ％以下
Ｓｉは、脱酸剤として添加される元素であり、０．０５ｍａｓｓ％以上含有することが望ましい。しかし、０．５ｍａｓｓ％を超えて添加すると、焼入れ後に十分なマルテンサイト相が生成せず、焼入れ後の硬さの低下や靭性の低下を招くため、０．５ｍａｓｓ％以下とする。
Si: 0.5 mass% or less Si is an element added as a deoxidizing agent, and it is desirable to contain 0.05 mass% or more. However, if added in excess of 0.5 mass%, a sufficient martensite phase is not formed after quenching, leading to a decrease in hardness and a decrease in toughness after quenching.
Ｍｎ：０．３〜２．５ｍａｓｓ％
Ｍｎは、高温でのフェライト相の生成を抑制して焼入れ性を向上し、焼入れ後の硬さを安定して所定の範囲に制御するのに有用な元素であり、この効果を得るためには、０．３ｍａｓｓ％以上の添加が必要である。しかし、２．５ｍａｓｓ％を超えて添加すると、加工性や耐錆性が低下するため、０．３〜２．５ｍａｓｓ％とする。なお、焼入れ性を向上する観点からは０．５ｍａｓｓ％以上、一方、加工性や耐錆性を向上する観点からは２．０ｍａｓｓ％以下とするのが好ましい。
Mn: 0.3 to 2.5 mass%
Mn is an element useful for improving the hardenability by suppressing the formation of a ferrite phase at a high temperature and stably controlling the hardness after quenching within a predetermined range. , Addition of 0.3 mass% or more is necessary. However, if added over 2.5 mass%, the workability and rust resistance are lowered, so 0.3 to 2.5 mass%. In addition, from the viewpoint of improving hardenability, 0.5 mass% or more is preferable, and from the viewpoint of improving workability and rust resistance, 2.0 mass% or less is preferable.
Ｐ：０．０４ｍａｓｓ％以下
Ｐは、鋼の熱間加工性や靭性を低下させるため、できる限り低減することが望ましい。しかし、Ｐの極度の低減は、製鋼コストの上昇を招くため、本発明では、０．０４ｍａｓｓ％以下とする。好ましくは、０．０３ｍａｓｓ％以下である。
P: 0.04 mass% or less P is desirably reduced as much as possible in order to reduce the hot workability and toughness of steel. However, the extreme reduction of P leads to an increase in steelmaking costs, so in the present invention, it is made 0.04 mass% or less. Preferably, it is 0.03 mass% or less.
Ｓ：０．００８ｍａｓｓ％以下
Ｓは、鋼の熱間加工性や耐錆性を低下させるため、できる限り低減することが望ましい。しかし、Ｓの極度の低減は、製鋼コストの上昇を招くため、０．００８ｍａｓｓ％以下とする。好ましくは、０．００３ｍａｓｓ％以下、さらに好ましくは０．００１ｍａｓｓ％以下である。
S: 0.008 mass% or less S is desirably reduced as much as possible in order to reduce the hot workability and rust resistance of steel. However, the extreme reduction of S leads to an increase in steelmaking cost, so it is set to 0.008 mass% or less. Preferably, it is 0.003 mass% or less, More preferably, it is 0.001 mass% or less.
Ｃｒ：１０．５〜１４．５ｍａｓｓ％
Ｃｒは、鋼の耐錆性を向上する主たる元素であり、ディスクブレーキ材としての十分な耐錆性を確保するためには、１０．５ｍａｓｓ％以上の添加が必要である。一方、１４．５ｍａｓｓ％を超えて含有すると、十分な量のマルテンサイト相が生成せず、焼入れ後に適正な硬さを確保できなくなる他、加工性や靭性の低下も起こるようになる。よって、本発明では、Ｃｒは１０．５〜１４．５ｍａｓｓ％の範囲とする。なお、耐錆性をより高めるためには１１．５ｍａｓｓ％以上、一方、加工性や靭性をより向上するためには１３．５ｍａｓｓ％未満が好ましい。
Cr: 10.5 to 14.5 mass%
Cr is a main element for improving the rust resistance of steel, and in order to ensure sufficient rust resistance as a disc brake material, addition of 10.5 mass% or more is necessary. On the other hand, if the content exceeds 14.5 mass%, a sufficient amount of martensite phase is not generated, and appropriate hardness cannot be secured after quenching, and workability and toughness are reduced. Therefore, in this invention, Cr is taken as the range of 10.5-14.5 mass%. In addition, in order to improve rust resistance more, 11.5 mass% or more is preferable, and in order to improve workability and toughness more, less than 13.5 mass% is preferable.
Ａｌ：０．１０ｍａｓｓ％以下
Ａｌは、Ｓｉと同様に、通常、脱酸剤として添加されるが、過剰に含有すると、硬質の介在物や析出物が増加して、表面痕などの欠陥の発生原因となるので、本発明では０．１０ｍａｓｓ％以下とする。なお、脱酸剤としてＳｉも添加する場合には、介在物や析出物の増加を抑えるため、Ａｌの添加量は少なくした方が好ましく、Ｓｉが０．０５ｍａｓｓ％以上０．１０ｍａｓｓ％未満であれば、Ａｌは０．０３ｍａｓｓ％以下、Ｓｉが０．１０ｍａｓｓ％以上であれば、Ａｌは０．０１ｍａｓｓ％以下が好ましい。
Al: 0.10 mass% or less Al, like Si, is usually added as a deoxidizer, but if it is contained excessively, hard inclusions and precipitates increase, and defects such as surface marks are generated. In order to cause this, in the present invention, it is set to 0.10 mass% or less. When Si is also added as a deoxidizer, it is preferable to reduce the amount of Al added in order to suppress the increase of inclusions and precipitates, and Si should be 0.05 mass% or more and less than 0.10 mass%. For example, if Al is 0.03 mass% or less and Si is 0.10 mass% or more, Al is preferably 0.01 mass% or less.
Ｎ：０．０３０〜０．０８０ｍａｓｓ％
Ｎは、Ｃと同様、焼入れ後、焼戻し後の硬さを決定する重要な元素であり、特に、微細な窒化物を形成し、５５０〜７００℃の温度範囲での焼戻し軟化抵抗を向上する効果が大きい。適正な硬さ範囲を保持するために、０．０３０ｍａｓｓ％以上の添加が必要である。一方、過度の添加は、熱間加工性の低下をもたらすため、上限は０．０８０ｍａｓｓ％とする。
N: 0.030-0.080 mass%
N, like C, is an important element that determines the hardness after quenching and after tempering, and in particular, the effect of forming fine nitrides and improving the temper softening resistance in the temperature range of 550 to 700 ° C. Is big. In order to maintain an appropriate hardness range, addition of 0.030 mass% or more is necessary. On the other hand, excessive addition causes a decrease in hot workability, so the upper limit is made 0.080 mass%.
Ｎｂ：０．０５〜０．６０ｍａｓｓ％
Ｎｂは、Ｎと析出物を形成し、５５０〜７００℃での焼戻し軟化抵抗を向上する効果が大きいため、本発明の高耐熱鋼では、必須元素の一つである。この効果を得るためには、０．０５ｍａｓｓ％以上の添加が必要である。しかし、過度に添加すると、靭性が低下するため、上限は０．６０％とする。
Nb: 0.05-0.60 mass%
Nb forms a precipitate with N and has a great effect of improving the temper softening resistance at 550 to 700 ° C., and thus is one of the essential elements in the high heat resistant steel of the present invention. In order to obtain this effect, addition of 0.05 mass% or more is necessary. However, if added excessively, the toughness decreases, so the upper limit is made 0.60%.
Ｎｉ：０．１〜１．５ｍａｓｓ％
Ｎｉは、鋼の耐食性を向上する元素であり、この効果を得るためには、０．１ｍａｓｓ％以上添加することが必要である。しかし、過剰に添加すると、熱間圧延後の軟化焼鈍に長時間が必要となり、生産性が低下するので、上限は１．５ｍａｓｓ％とする。
Ni: 0.1 to 1.5 mass%
Ni is an element that improves the corrosion resistance of steel. In order to obtain this effect, it is necessary to add 0.1 mass% or more. However, if added excessively, a long time is required for soft annealing after hot rolling, and the productivity is lowered, so the upper limit is made 1.5 mass%.
Ｂ：０．０３０×Ｎ〜０．００５０ｍａｓｓ％
本発明の高耐熱Ｃｒ含有鋼は、上記成分組成に加えて、Ｂを適正量添加することよって、熱間加工性を向上させるところに特徴がある。Ｂは、粒界や相境界に集積して、それらの強度を高める一方、有害なＳやＰの集積を抑制し、さらには、析出物の粗大化をも抑制することによって、熱間延性を高める効果がある。特に、Ｂは、Ｎとの関係において、Ｂ／Ｎが０．０３０以上になると、熱間延性が向上する効果が得られ０．０３５以上になるとその効果が顕著となり、熱間圧延での耳割れやへげの発生を軽減することができる。Ｂ／Ｎが０．０５０を超えると、その効果がより大きくなり、熱間圧延での耳割れやへげの発生が殆どなくなる。しかし、Ｂ／Ｎが０．１００以上になるか、Ｂの添加量が０．００４５ｍａｓｓ％を超えると、その効果がやや低下し、さらに、Ｂの添加量が０．００５０ｍａｓｓ％を超えると、熱間延性が逆に低下する。この原因は、ＢＮの析出量が過剰となり、粒界強度を低下させるためと考えられる。よって、本発明では、Ｂは、Ｂ：０．００５０ｍａｓｓ％以下かつＢ／Ｎ≧０．０３０の範囲で添加する必要がある。Ｂ／Ｎは、好ましくは０．０３５以上０．１００未満、さらに好ましくは０．０５０超０．１００未満である。
B: 0.030 × N to 0.0050 mass%
The high heat-resistant Cr-containing steel of the present invention is characterized in that hot workability is improved by adding an appropriate amount of B in addition to the above component composition. B accumulates at grain boundaries and phase boundaries to increase their strength, while suppressing the accumulation of harmful S and P, and further suppressing the coarsening of precipitates, thereby increasing hot ductility. There is an effect to increase. In particular, when B / N is 0.030 or more in relation to N, the effect of improving hot ductility is obtained, and when B / N is 0.035 or more, the effect becomes remarkable. It is possible to reduce the occurrence of cracks and baldness. When B / N exceeds 0.050, the effect is further increased, and the occurrence of ear cracks and baldness in hot rolling is almost eliminated. However, when B / N is 0.100 or more, or the amount of B exceeds 0.0045 mass%, the effect is slightly reduced. Further, when the amount of B exceeds 0.0050 mass%, On the contrary, the ductility decreases. This is thought to be because the amount of BN deposited becomes excessive and the grain boundary strength is lowered. Therefore, in the present invention, B needs to be added in the range of B: 0.0050 mass% or less and B / N ≧ 0.030. B / N is preferably 0.035 or more and less than 0.100, more preferably more than 0.050 and less than 0.100.
Ｃｕ，Ｖ，Ｍｏ，Ｗ，ＴａおよびＴｉのうちから選ばれる１種または２種以上を合計で０．０５〜２．５ｍａｓｓ％
Ｃｕ，Ｖ，Ｍｏ，Ｗ，ＴａおよびＴｉは、何れも焼入れ性を高め、焼入れや焼戻し後の硬さを安定的に確保するの有用な元素であり、１種以上を合計で０．０５以上添加する必要がある。しかし、過剰に添加すると、必要以上の硬さ増加あるいは低下を招き、硬さの適正範囲から外れる原因となるため、合計で２．５ｍａｓｓ％以下とする。
0.05 to 2.5 mass% in total of one or more selected from Cu, V, Mo, W, Ta and Ti
Cu, V, Mo, W, Ta and Ti are all useful elements for enhancing the hardenability and ensuring the hardness after quenching and tempering stably, and one or more of them are 0.05 or more in total. It is necessary to add. However, if added excessively, the hardness is increased or decreased more than necessary, which causes the hardness to deviate from the appropriate range. Therefore, the total amount is 2.5 mass% or less.
Ｃｕ：０．３０ｍａｓｓ％超〜２．５ｍａｓｓ％、Ｎｉ：０．５×Ｃｕｍａｓｓ％以上
なお、上記元素のうち、Ｃｕを添加する場合には、その添加量に応じて、Ｎｉを複合添加することが望ましい。というのは、Ｃｕは、鋳造後の鋼片中に、低融点の富Ｃｕ相を形成し、熱間加工性を著しく低下させる場合があるが、Ｎｉは、これら富Ｃｕ相の融点を高め、熱間加工性の低下を抑制する効果があるからである。特に、Ｃｕの添加量が０．３０ｍａｓｓ％を超えると、粗大な富Ｃｕ相の量が増加し、熱間加工性の低下が著しくなるため、ＮｉをＣｕ添加量の１／２以上添加することが望ましい。
Cu: more than 0.30 mass% to 2.5 mass%, Ni: 0.5 × Cumass% or more In addition, when adding Cu among the above elements, Ni should be added in combination according to the addition amount. Is desirable. This is because Cu forms a low melting point rich Cu phase in the steel slab after casting, which may significantly reduce hot workability, but Ni increases the melting point of these Cu rich phases, This is because there is an effect of suppressing a decrease in hot workability. In particular, if the amount of Cu exceeds 0.30 mass%, the amount of coarse Cu-rich phase increases and the hot workability deteriorates significantly. Is desirable.
本発明の高耐熱Ｃｒ含有鋼は、上記成分以外の残部は、Ｆｅおよび不可避的不純物からなるものである。ただし、本発明の効果を害しない範囲であれば、耐熱性、耐錆性の向上および製造性を改善する観点から、Ｃｏ，Ｃａ，Ｍｇ，Ｈｆ，Ｙ，Ｚｒ等を合計で０．５ｍａｓｓ％以下の範囲で添加してもよい。 In the high heat-resistant Cr-containing steel of the present invention, the balance other than the above components is composed of Fe and inevitable impurities. However, within a range that does not impair the effects of the present invention, from the viewpoint of improving heat resistance, rust resistance and manufacturability, a total of 0.5 mass% of Co, Ca, Mg, Hf, Y, Zr, etc. You may add in the following ranges.
表１に示した各種成分組成を有するＮｏ．１〜１９の鋼を高周波溶解炉で溶解し、厚さ１７０ｍｍの鋳塊を作製し、この鋳塊を、１２００℃×１時間加熱し、熱間圧延して板厚が３〜６ｍｍの熱延板とした。この熱延板について、鋼板端部に発生した割れの長さを測定し、この結果から、１０ｍｍ超を、熱間加工性をＤ、５〜１０ｍｍをＣ、５ｍｍ未満をＢ、さらに３ｍｍ未満をＡと評価した。 No. having various component compositions shown in Table 1. 1 to 19 steel was melted in a high-frequency melting furnace to produce an ingot having a thickness of 170 mm. The ingot was heated at 1200 ° C. for 1 hour and hot-rolled to obtain a hot rolled sheet having a thickness of 3 to 6 mm. A board was used. About this hot-rolled sheet, the length of a crack generated at the end of the steel sheet was measured, and from this result, the hot workability was D, the 5 to 10 mm was C, the less than 5 mm was B, and further less than 3 mm. Rated A.
また、上記鋳塊からは、別途、熱間引張試験用として、平行部の直径が１０ｍｍφの試験片を採取し、グリーブル試験機を用いて、熱間引張試験を行い、熱間延性を評価した。なお、熱間引張試験は、上記試験片を、１２００℃×３０分の加熱後、５０℃／分で所定の温度まで冷却し、１０秒間保持し、その後、引張速度１００ｍｍ／秒（歪み速度１０／秒）で変形を加える条件で行った。試験温度は、９００℃から５０℃間隔で１１００℃まで行い、各温度で５本ずつ断面減少率を測定し、最大値と最小値を除いた３本の平均値を求めた。その結果、断面減少率ＲＡの最小値（各温度での３本の平均値の最小値）が４０％未満であれば熱間延性がＤ、４５％未満であれば熱間延性がＣ、４５〜５０％であれば熱間延性がＢ、５０％超えであれば熱間延性がＡと評価した。 In addition, from the above ingot, a test piece having a parallel part diameter of 10 mmφ was sampled separately for the hot tensile test, and a hot tensile test was performed using a Gleeble tester to evaluate the hot ductility. . In the hot tensile test, the test piece was heated to 1200 ° C. for 30 minutes, cooled to a predetermined temperature at 50 ° C./minute, held for 10 seconds, and then pulled at a speed of 100 mm / second (strain rate of 10 / Sec) under the condition of applying deformation. The test temperature was 900 ° C. to 1100 ° C. at intervals of 50 ° C., and the cross-section reduction rate was measured at each temperature, and the average value of three samples excluding the maximum value and the minimum value was obtained. As a result, the hot ductility is D if the minimum value of the cross-section reduction rate RA (minimum value of three average values at each temperature) is less than 40%, and the hot ductility is C, 45 if it is less than 45%. When it was ˜50%, the hot ductility was evaluated as B, and when it exceeded 50%, the hot ductility was evaluated as A.
上記熱間加工性（欠陥評価）および熱間引張試験（熱間延性）の評価結果について、表１に併記して示した。表１から、本発明の成分組成に適合するＮｏ．１〜１２の鋼は、いずれも欠陥評価および熱間延性の評価がＡまたはＢが得られており、熱間加工性に優れていることがわかる。これに対して、本発明の成分組成を満たさないＮｏ．１３〜１９の鋼は、いずれも欠陥評価および延性評価がＣまたはＤであり、熱間加工性に劣ることがわかる。 The evaluation results of the hot workability (defect evaluation) and the hot tensile test (hot ductility) are shown together in Table 1. From Table 1, No. which is suitable for the component composition of the present invention. It can be seen that the steels Nos. 1 to 12 are excellent in hot workability because the defect evaluation and the hot ductility evaluation are A or B. On the other hand, No. which does not satisfy the component composition of the present invention. It can be seen that the steels Nos. 13 to 19 have a defect evaluation and a ductility evaluation of C or D, and are inferior in hot workability.
なお、上記の熱間圧延して得た熱延板は、その後、７００〜８５０℃の温度で４〜２０時間の焼鈍を施し、軟質化してから、９５０〜１２５０℃×１〜１０分加熱後、空冷する焼入処理を施し、硬さを測定した。その結果、いずれの鋼板も、ＨＲＣで３０〜４５の適正な範囲となることを確認した。 The hot-rolled sheet obtained by hot rolling is annealed for 4 to 20 hours at a temperature of 700 to 850 ° C., softened, and then heated at 950 to 1250 ° C. for 1 to 10 minutes. Then, it was quenched by air cooling, and the hardness was measured. As a result, it was confirmed that all the steel sheets were within an appropriate range of 30 to 45 by HRC.
Claims (2)
Ｓｉ：０．５ｍａｓｓ％以下、
Ｍｎ：０．３〜２．５ｍａｓｓ％、
Ｐ：０．０４ｍａｓｓ％以下、
Ｓ：０．００８ｍａｓｓ％以下、
Ｃｒ：１０．５〜１４．５ｍａｓｓ％、
Ａｌ：０．１０ｍａｓｓ％以下、
Ｎ：０．０３０〜０．０８０ｍａｓｓ％、
Ｎｂ：０．０５〜０．６０ｍａｓｓ％、
Ｎｉ：０．１〜１．５ｍａｓｓ％、さらに、
Ｂ：０．００５０ｍａｓｓ％以下かつＢ／Ｎ≧０．０３０を満たして含有し、
さらに、Ｃｕ，Ｖ，Ｍｏ，Ｗ，ＴａおよびＴｉのうちから選ばれる１種または２種以上を合計で０．０５〜２．５ｍａｓｓ％含有し、残部がＦｅおよび不可避的不純物からなるブレーキディスク用高耐熱Ｃｒ含有鋼。 C: 0.01-0.10 mass%,
Si: 0.5 mass% or less,
Mn: 0.3 to 2.5 mass%,
P: 0.04 mass% or less,
S: 0.008 mass% or less,
Cr: 10.5 to 14.5 mass%,
Al: 0.10 mass% or less,
N: 0.030-0.080 mass%,
Nb: 0.05-0.60 mass%,
Ni: 0.1 to 1.5 mass%,
B: 0.0050 mass% or less and satisfying B / N ≧ 0.030,
Further, for brake discs containing 0.05 to 2.5 mass% in total of one or more selected from Cu, V, Mo, W, Ta and Ti, with the balance being Fe and unavoidable impurities High heat resistant Cr-containing steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2006075197A JP4788421B2 (en) | 2006-03-17 | 2006-03-17 | High heat-resistant Cr-containing steel for brake discs |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2006075197A JP4788421B2 (en) | 2006-03-17 | 2006-03-17 | High heat-resistant Cr-containing steel for brake discs |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2007247027A true JP2007247027A (en) | 2007-09-27 |
| JP4788421B2 JP4788421B2 (en) | 2011-10-05 |
Family
ID=38591644
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2006075197A Active JP4788421B2 (en) | 2006-03-17 | 2006-03-17 | High heat-resistant Cr-containing steel for brake discs |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4788421B2 (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2009041472A1 (en) | 2007-09-25 | 2009-04-02 | Hitachi Chemical Company, Ltd. | Thermosetting resin composition for light reflection, substrate made therefrom for photosemiconductor element mounting, process for producing the same, and photosemiconductor device |
| WO2010140696A1 (en) * | 2009-06-01 | 2010-12-09 | Ｊｆｅスチール株式会社 | Steel sheet for brake disc, and brake disc |
| EP2287350A1 (en) * | 2008-04-25 | 2011-02-23 | JFE Steel Corporation | Low-carbon martensitic cr-containing steel |
| WO2012157680A1 (en) * | 2011-05-16 | 2012-11-22 | 新日鐵住金ステンレス株式会社 | Martensitic stainless steel plate for bicycle disc brake rotor and manufacturing method therefor |
| WO2014123229A1 (en) * | 2013-02-08 | 2014-08-14 | 新日鐵住金ステンレス株式会社 | Stainless steel brake disc and method for manufacturing same |
| WO2014148015A1 (en) * | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | Stainless steel sheet |
| 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 |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002146489A (en) * | 2000-08-31 | 2002-05-22 | Kawasaki Steel Corp | Low carbon martensitic stainless steel sheet having excellent heat resistance |
| JP2005126735A (en) * | 2003-10-21 | 2005-05-19 | Jfe Steel Kk | Brake disk with excellent temper softening resistance, and its manufacturing method |
| JP2005133204A (en) * | 2003-10-08 | 2005-05-26 | Jfe Steel Kk | Brake disk having excellent temper softening resistance, and its production method |
-
2006
- 2006-03-17 JP JP2006075197A patent/JP4788421B2/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002146489A (en) * | 2000-08-31 | 2002-05-22 | Kawasaki Steel Corp | Low carbon martensitic stainless steel sheet having excellent heat resistance |
| JP2005133204A (en) * | 2003-10-08 | 2005-05-26 | Jfe Steel Kk | Brake disk having excellent temper softening resistance, and its production method |
| JP2005126735A (en) * | 2003-10-21 | 2005-05-19 | Jfe Steel Kk | Brake disk with excellent temper softening resistance, and its manufacturing method |
Cited By (25)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2009041472A1 (en) | 2007-09-25 | 2009-04-02 | Hitachi Chemical Company, Ltd. | Thermosetting resin composition for light reflection, substrate made therefrom for photosemiconductor element mounting, process for producing the same, and photosemiconductor device |
| EP2540776A2 (en) | 2007-09-25 | 2013-01-02 | Hitachi Chemical Co., Ltd. | Thermosetting light-reflecting resin composition, optical semiconductor element mounting board produced therewith, method for manufacture thereof, and optical semiconductor device |
| EP2540775A2 (en) | 2007-09-25 | 2013-01-02 | Hitachi Chemical Co., Ltd. | Thermosetting light-reflecting resin composition, optical semiconductor element mounting board produced therewith, method for manufacture thereof, and optical semiconductor device |
| EP2287350A1 (en) * | 2008-04-25 | 2011-02-23 | JFE Steel Corporation | Low-carbon martensitic cr-containing steel |
| EP2287350A4 (en) * | 2008-04-25 | 2014-01-15 | Jfe Steel Corp | Low-carbon martensitic cr-containing steel |
| EP2439304A1 (en) * | 2009-06-01 | 2012-04-11 | JFE Steel Corporation | Steel sheet for brake disc, and brake disc |
| CN102449181A (en) * | 2009-06-01 | 2012-05-09 | 杰富意钢铁株式会社 | Steel sheet for brake disc, and brake disc |
| JP2011012343A (en) * | 2009-06-01 | 2011-01-20 | Jfe Steel Corp | Steel sheet for brake disc, and brake disc |
| WO2010140696A1 (en) * | 2009-06-01 | 2010-12-09 | Ｊｆｅスチール株式会社 | Steel sheet for brake disc, and brake disc |
| KR101248317B1 (en) * | 2009-06-01 | 2013-03-27 | 제이에프이 스틸 가부시키가이샤 | Steel sheet for brake disc, and brake disc |
| EP2439304A4 (en) * | 2009-06-01 | 2013-07-10 | Jfe Steel Corp | Steel sheet for brake disc, and brake disc |
| US8607941B2 (en) | 2009-06-01 | 2013-12-17 | Jfe Steel Corporation | Steel sheet for brake disc, and brake disc |
| CN102449181B (en) * | 2009-06-01 | 2014-01-08 | 杰富意钢铁株式会社 | Steel sheet for brake disc, and brake disc |
| WO2012157680A1 (en) * | 2011-05-16 | 2012-11-22 | 新日鐵住金ステンレス株式会社 | Martensitic stainless steel plate for bicycle disc brake rotor and manufacturing method therefor |
| CN103534377A (en) * | 2011-05-16 | 2014-01-22 | 新日铁住金不锈钢株式会社 | Martensitic stainless steel plate for bicycle disc brake rotor and manufacturing method therefor |
| JP5863785B2 (en) * | 2011-05-16 | 2016-02-17 | 新日鐵住金ステンレス株式会社 | Martensitic stainless steel sheet for bicycle disc brake rotor and method for manufacturing the same |
| WO2014123229A1 (en) * | 2013-02-08 | 2014-08-14 | 新日鐵住金ステンレス株式会社 | Stainless steel brake disc and method for manufacturing same |
| CN104321456A (en) * | 2013-02-08 | 2015-01-28 | 新日铁住金不锈钢株式会社 | Stainless steel brake disc and method for manufacturing same |
| KR20150013885A (en) * | 2013-02-08 | 2015-02-05 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | Stainless steel brake disc and method for manufacturing same |
| KR101656980B1 (en) | 2013-02-08 | 2016-09-12 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | Stainless steel brake disc and method for manufacturing same |
| US9523402B2 (en) | 2013-02-08 | 2016-12-20 | Nippon Steel & Sumikin Stainless Steel Corporation | Stainless steel brake disc and method for production thereof |
| WO2014148015A1 (en) * | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | Stainless steel sheet |
| EP2947170A4 (en) * | 2013-03-19 | 2016-02-10 | Jfe Steel Corp | Stainless steel sheet |
| 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 |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4788421B2 (en) | 2011-10-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR101248317B1 (en) | Steel sheet for brake disc, and brake disc | |
| JP5714185B2 (en) | Stainless steel brake disc and its manufacturing method | |
| TWI390051B (en) | Cr-containing low-carbon terrestrial steel | |
| JP5863785B2 (en) | Martensitic stainless steel sheet for bicycle disc brake rotor and method for manufacturing the same | |
| JP6417252B2 (en) | Martensitic stainless steel for brake disc and its manufacturing method | |
| JP5700172B2 (en) | Stainless steel sheet | |
| JP4788421B2 (en) | High heat-resistant Cr-containing steel for brake discs | |
| JP6065121B2 (en) | High carbon hot rolled steel sheet and manufacturing method thereof | |
| JP2017172038A (en) | Martensitic stainless steel for brake disc, and blake disc | |
| JP2017197820A (en) | Martensitic stainless cold rolled steel sheet for bicycle disc brake rotor excellent in hardenability and manufacturing method therefor | |
| JP2017179596A (en) | High carbon steel sheet and manufacturing method therefor | |
| JP4496908B2 (en) | Brake disc excellent in tempering softening resistance and manufacturing method thereof | |
| JP6537659B1 (en) | Martensitic stainless hot rolled steel sheet, method of manufacturing disc brake rotor using the same | |
| JP2020152959A (en) | Martensitic stainless steel sheet for brake disc, production method therefor, brake disc and martensitic stainless steel slab | |
| JP4830239B2 (en) | Manufacturing method of low carbon martensitic stainless hot rolled steel sheet with excellent punchability | |
| JP4182865B2 (en) | Stainless steel plate for disc brakes with excellent temper softening resistance | |
| JP5278889B2 (en) | Martensitic stainless steel for disc brakes | |
| JP4308622B2 (en) | Brake disc excellent in tempering softening resistance and manufacturing method thereof | |
| JP2022069229A (en) | Austenite stainless steel and method for manufacturing the same | |
| JP5301949B2 (en) | Martensitic stainless steel for disc brakes | |
| JP3900169B2 (en) | Martensitic stainless steel for disc brakes | |
| JP2008202090A (en) | Manufacturing method of highly heat-resistant brake disk with excellent braking stability | |
| JP2011225948A (en) | Cr-containing hot rolled steel sheet for brake disk, and the brake disk | |
| WO2016043050A1 (en) | Martensitic stainless steel for brake disk and method for producing said steel | |
| JP2006169582A (en) | Stainless steel plate for disc brake with excellent thermal stress cracking resistance |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20090213 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20110228 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20110322 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20110510 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20110621 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20110704 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140729 Year of fee payment: 3 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4788421 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |