JP2011190503A - Martensitic stainless steel for heat resistant disk brake - Google Patents
Martensitic stainless steel for heat resistant disk brake Download PDFInfo
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- JP2011190503A JP2011190503A JP2010057864A JP2010057864A JP2011190503A JP 2011190503 A JP2011190503 A JP 2011190503A JP 2010057864 A JP2010057864 A JP 2010057864A JP 2010057864 A JP2010057864 A JP 2010057864A JP 2011190503 A JP2011190503 A JP 2011190503A
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- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims abstract description 13
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 17
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 16
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 12
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 11
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 abstract description 9
- 239000000956 alloy Substances 0.000 abstract description 9
- 239000000203 mixture Substances 0.000 abstract description 2
- 229910000831 Steel Inorganic materials 0.000 description 56
- 239000010959 steel Substances 0.000 description 56
- 238000010791 quenching Methods 0.000 description 24
- 230000000171 quenching effect Effects 0.000 description 24
- 230000000694 effects Effects 0.000 description 20
- 239000000463 material Substances 0.000 description 11
- 229910001566 austenite Inorganic materials 0.000 description 9
- 238000012360 testing method Methods 0.000 description 9
- 238000001556 precipitation Methods 0.000 description 8
- 230000007423 decrease Effects 0.000 description 7
- 238000004519 manufacturing process Methods 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 150000004767 nitrides Chemical class 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- 238000005496 tempering Methods 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 4
- 230000007246 mechanism Effects 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- 229910001263 D-2 tool steel Inorganic materials 0.000 description 1
- 238000007550 Rockwell hardness test Methods 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000005422 blasting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000001934 delay Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
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Abstract
Description
本発明は、二輪車のディスクブレーキ用鋼板に関し、比較的低コストであり、特に、ブレーキに加工後、使用時のディスク温度が６００℃で長時間曝された場合にも軟化しにくい耐熱性に優れたマルテンサイト系ステンレス鋼板に関するものである。 The present invention relates to a steel plate for a disc brake of a motorcycle, and is relatively low cost. In particular, after processing into a brake, it has excellent heat resistance that is difficult to soften even when exposed to a disc temperature of 600 ° C. for a long time. The present invention relates to a martensitic stainless steel sheet.
二輪車のディスクブレーキ用鋼板には、耐磨耗性、耐銹性、靭性等の特性が要求される。耐磨耗性は一般に硬さが高いほど大きくなる。一方、硬さが高すぎると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、ブレーキの硬さは、３２〜３８ＨＲＣ（ロックウェル硬さＣスケール）が求められる。これらの要求特性から、二輪車ディスクブレーキ材料にはマルテンサイト系ステンレス鋼板が用いられている。 Steel plates for motorcycle disc brakes are required to have characteristics such as wear resistance, weather resistance, and toughness. Abrasion resistance generally increases with increasing hardness. On the other hand, if the hardness is too high, a so-called brake squeal occurs between the brake and the pad. Therefore, the brake hardness is required to be 32 to 38 HRC (Rockwell hardness C scale). From these required characteristics, martensitic stainless steel plates are used for motorcycle disc brake materials.
従来、ＳＵＳ４２０Ｊ２を焼入れ焼き戻しして所望の硬さに調節し、ブレーキとしていたが、この場合、焼入れと焼き戻しの２つの熱処理工程を要する問題があった。これに対し、特許文献１において、ＳＵＳ４２０Ｊ２鋼の従来鋼より広い焼入れ温度域で、安定して所望の硬さを得ることができ、かつ、焼き入れままで使用できる鋼組成に関する発明が開示された。これは、低Ｃ、Ｎ化し、かつ、それによるオーステナイト温度域の縮小、つまり、焼入れ温度域が狭くなることをオーステナイト形成元素であるＭｎ添加で補ったものである。また、特許文献２において、低Ｍｎ鋼で焼入れままで使用できるオートバイディスクブレーキ用鋼板に関する発明が開示されている。この鋼板は、Ｍｎを低下させる代わりに、オーステナイト形成元素として同様の効果を持つ、ＮｉおよびＣｕを添加したものである。 Conventionally, SUS420J2 was quenched and tempered to adjust to a desired hardness and used as a brake, but in this case, there was a problem that required two heat treatment steps of quenching and tempering. On the other hand, Patent Document 1 discloses an invention relating to a steel composition that can stably obtain desired hardness in a quenching temperature range wider than that of a conventional steel of SUS420J2 steel and that can be used as-quenched. . This compensates for the reduction of C and N and the reduction of the austenite temperature range, that is, the reduction of the quenching temperature range, by the addition of Mn, which is an austenite forming element. Patent Document 2 discloses an invention relating to a steel plate for motorcycle disc brakes that can be used as quenched with low Mn steel. This steel sheet is obtained by adding Ni and Cu having the same effect as an austenite forming element instead of lowering Mn.
最近、二輪車においても車体の軽量化が望まれており、二輪ブレーキディスクの軽量化が検討されている。この場合、課題となるのが制動時の発熱に起因するディスク材軟化によるディスクの変形であり、これを解決するためには、ディスク材の耐熱性を向上させる必要がある。この解決策の１つとして焼き戻し軟化抵抗の向上があり、特許文献３において、Ｎｂ、Ｍｏ添加による耐熱性向上法に関する発明が開示された。しかし、耐熱性向上効果は５３０℃程度であった。さらに、特許文献４において、６００℃を超える温度でも焼き戻し軟化が起こりにくい鋼板に関する発明が開示されている。さらに、特許文献５において、１０００℃を超える温度からの焼入れ処理を行うことにより優れた耐熱性を有するディスク材に関する発明が開示されている。さらには、特許文献６では、比較的少量の合金元素で焼き戻し軟化抵抗を維持できる発明が開示されている。 Recently, it is desired to reduce the weight of a vehicle body in a two-wheeled vehicle, and the weight reduction of a two-wheel brake disc has been studied. In this case, the problem is the deformation of the disk due to the softening of the disk material due to the heat generated during braking. In order to solve this, it is necessary to improve the heat resistance of the disk material. One solution is to improve the temper softening resistance. Patent Document 3 discloses an invention relating to a method for improving heat resistance by adding Nb and Mo. However, the heat resistance improvement effect was about 530 ° C. Furthermore, Patent Document 4 discloses an invention relating to a steel sheet that hardly undergoes temper softening even at temperatures exceeding 600 ° C. Furthermore, Patent Document 5 discloses an invention relating to a disk material having excellent heat resistance by performing a quenching process from a temperature exceeding 1000 ° C. Furthermore, Patent Document 6 discloses an invention that can maintain temper softening resistance with a relatively small amount of alloy elements.
ところが、高い耐熱性を実現するには添加する合金元素量の増加を伴い、合金コストが上昇する。また、それに伴って、焼き入れ性が低下するという課題がある。 However, in order to realize high heat resistance, the alloy cost increases with an increase in the amount of alloy elements to be added. Along with that, there is a problem that hardenability decreases.
本発明の目的は、比較的低コストながら、優れた焼き入れ性および高い耐熱性を保つことを特徴とする耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼を提供することである。 An object of the present invention is to provide a martensitic stainless steel for heat-resistant disc brakes characterized by maintaining excellent hardenability and high heat resistance at a relatively low cost.
本発明の要旨は以下の通りである。
（１）質量％で、Ｃ：０．０２％以上０．０８％以下、Ｓｉ：０．１％以上１％以下、Ｍｎ：０．５％以上２．５％以下、Ｐ：０．０４％以下、Ｓ：０．０１０％以下、Ｎ：０．０２５％以上０．０５％以下、Ｃｒ：１１％以上１４％以下、Ｎｉ：０．１０％以下、Ｖ：０．２％以上０．３％以下、Ｎｂ：０．０５％以上（９３／５１）［％Ｖ］以下、Ｔｉ：０．０５％以下、Ａｌ：０．０１％以下を含有し、Ｃ，Ｎは、Ｃ＋Ｎ：０．０５％以上０．１％以下を満足し、残部Ｆｅおよび不可避的不純物からなり、下記（１）式で表されるγｐが８５以上を満足することを特徴とする耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼板。
γｐ＝４２０［％Ｃ］＋４７０［％Ｎ］＋２３［％Ｎｉ］＋９［％Ｃｕ］＋７［％Ｍｎ］−１１．５［％Ｃｒ］−１１．５［％Ｓｉ］−５２［％Ａｌ］−４９［％Ｔｉ］
−２３［％Ｖ］−１２［％Ｍｏ］−４７［％Ｎｂ］＋１８９ （１）
（２）質量％で、Ｍｏ：０．２％以上１％以下を、さらに含有することを特徴とする、前記（１）に記載の耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼。
（３）質量％で、Ｃｕ：０．２％以上２％以下、をさらに含有することを特徴とする、前記（１）または（２）に記載の耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼。
The gist of the present invention is as follows.
(1) By mass%, C: 0.02% to 0.08%, Si: 0.1% to 1%, Mn: 0.5% to 2.5%, P: 0.04% S: 0.010% or less, N: 0.025% or more and 0.05% or less, Cr: 11% or more and 14% or less, Ni: 0.10% or less, V: 0.2% or more and 0.3 %: Nb: 0.05% or more (93/51) [% V] or less, Ti: 0.05% or less, Al: 0.01% or less, and C and N are C + N: 0.05 % Of martensitic stainless steel plate for heat-resistant disc brakes, characterized by satisfying ≧ 0.1% and satisfying γp expressed by the following formula (1) of 85 or more .
γp = 420 [% C] +470 [% N] +23 [% Ni] +9 [% Cu] +7 [% Mn] −11.5 [% Cr] −11.5 [% Si] −52 [% Al] − 49 [% Ti]
-23 [% V] -12 [% Mo] -47 [% Nb] +189 (1)
(2) The martensitic stainless steel for heat-resistant disc brakes according to (1) above, further containing, by mass%, Mo: 0.2% to 1%.
(3) The martensitic stainless steel for heat-resistant disc brakes according to (1) or (2) above, further containing, by mass%, Cu: 0.2% to 2%.
本発明により、比較的低コストで耐熱二輪車ディスクブレーキ用マルテンサイト系ステンレス鋼板を提供することができ、製造者のみならず本鋼を利用する者にとっても多大な利益を得ることができ、工業的価値は極めて高い。 According to the present invention, it is possible to provide a martensitic stainless steel plate for heat-resistant motorcycle disc brakes at a relatively low cost, and it is possible to obtain great benefits not only for manufacturers but also for those who use this steel. The value is extremely high.
本発明を実施するための形態と限定条件について詳細に説明する。 The mode for carrying out the present invention and the limiting conditions will be described in detail.
発明者らは、焼入れままで使用できる二輪車ディスクブレーキ材料について、詳細な検討を行ってきた。その中で耐熱性に関する検討では、焼き戻し軟化抵抗の向上の検討を中心に進めてきた。焼き戻し軟化抵抗を向上させるには、Ｎｂ、Ｍｏを中心とする合金元素を多く添加することが行われている。そのために焼き入れしても硬度が上昇しにくい、いわゆる、焼き入れ性が低下することや合金コストの上昇が課題になっていた。さらに、二輪車のディスクブレーキ材の耐熱性に関する要求特性は、６００℃を越える温度になった場合、パッド等のディスク周辺部分の耐熱化が非常に困難でコスト上昇が著しく、耐熱温度限界は６００℃程度であることも判明した。また、ブレーキディスク製造工程では通常、高周波焼き入れが行われるため、短時間で焼き入れ処理を完了する必要があるが、耐熱性を向上させるために合金元素を多量に添加した場合、急速に加熱した場合であっても、ピーク温度付近に数分間以内保持する焼き入れ処理では、全体のオーステナイト化が完了しない内に焼き入れが行われる等の原因により、かかる短時間焼き入れ処理での焼き入れ性が顕著に低下する（十分に硬化しない）ことも課題となっていた。 The inventors have conducted a detailed study on a motorcycle disc brake material that can be used as-quenched. Among them, the study on heat resistance has been focused on improving the temper softening resistance. In order to improve the temper softening resistance, a large amount of alloy elements centering on Nb and Mo are added. For this reason, the hardness is hardly increased even after quenching, that is, the so-called hardenability is lowered and the alloy cost is increased. Furthermore, the required heat resistance characteristics of the disc brake material for motorcycles are such that when the temperature exceeds 600 ° C, it is very difficult to heat the peripheral portion of the disc such as a pad and the cost rises significantly. It was also found to be a degree. In addition, in the brake disk manufacturing process, induction hardening is usually performed, so it is necessary to complete the quenching process in a short time. However, when a large amount of alloying elements are added to improve heat resistance, heating is rapidly performed. Even in the case where the quenching process is performed, the quenching process in which the quenching process is performed within a few minutes near the peak temperature causes the quenching to be performed before the entire austenitization is completed. It has also been a problem that the properties are remarkably lowered (not sufficiently cured).
発明者らはこれらの点を考慮し、できるだけ低合金で６００℃以下での焼き戻し軟化抵抗を向上させる方策の検討を詳細に進めた結果、以下の知見を得た。 In consideration of these points, the inventors have studied in detail the measures for improving the temper softening resistance at 600 ° C. or lower with a low alloy as much as possible, and as a result, have obtained the following knowledge.
６００℃以下の焼き戻し軟化抵抗向上に関し、合金元素として、Ｖ，Ｎｂ，Ｎが重要である。特に、ＶとＮを組み合わせることが焼き戻し軟化抵抗を向上させることを見出した。この機構については、まだ詳細を調査中であるが、Ｖの適量添加によりＣｒ2Ｎ型の窒化物の析出が遅れることおよび、かかる窒化物をはじめ析出物の大きさが、Ｖ適量添加することで、平均直径で半分以下に小さくなっていること、さらには、ＶがＶＮを形成するのではなく、Ｃｒ2Ｎ中に固溶していることが分かったことから、ＶがＣｒ2Ｎの析出遅延、および微細化を促進した結果、焼き戻し軟化抵抗が向上したと考えている。これまでＮｂの焼き戻し軟化抵抗向上効果はよく知られているが、Ｖ単独添加でも焼き戻し軟化抵抗が向上することが分かった。さらに、Ｖは、ほぼ同量のＮｂ添加の場合と比較して、前記短時間焼き入れ処理であっても、焼き入れ性を低下させにくいことも判明した。 For improving the temper softening resistance at 600 ° C. or lower, V, Nb, and N are important as alloy elements. In particular, it has been found that combining V and N improves the temper softening resistance. Although the details of this mechanism are still under investigation, the addition of an appropriate amount of V delays the precipitation of Cr 2 N-type nitrides, and the size of such nitrides and other precipitates must be added in an appropriate amount. Thus, it was found that the average diameter was reduced to less than half, and that V did not form VN but was dissolved in Cr 2 N, so that V was Cr 2 N. It is believed that temper softening resistance has improved as a result of promoting precipitation delay and refinement. So far, the effect of improving the temper softening resistance of Nb is well known, but it has been found that the temper softening resistance can be improved even by adding V alone. Furthermore, it has also been found that V is less likely to reduce the hardenability even in the case of the short-time quenching treatment as compared with the case of adding approximately the same amount of Nb.
このＶの焼き戻し軟化抵抗向上効果を十分に活用するためには、Ｎが必要である。Ｎが少ない場合は、窒化物の量が少なく、Ｖ添加による析出遅延および微細化による焼き戻し軟化抵抗向上効果はあまり期待できない。また、過剰にＮを添加した場合も焼き戻し軟化抵抗はあまり向上しない上に、短時間での焼き入れ性が低下する。このことについては、Ｃｒ2Ｎ以外にＶＮが析出するためにではないかと推定している。 In order to fully utilize the effect of improving the temper softening resistance of V, N is necessary. When N is small, the amount of nitride is small, and the effect of improving the temper softening resistance due to the delay in precipitation due to V addition and refinement cannot be expected. Further, when N is added excessively, the temper softening resistance is not improved so much and the hardenability in a short time is lowered. It is estimated that this is because VN precipitates in addition to Cr 2 N.
前述したように、十分にオーステナイト化後に焼き入れ処理した場合の単位合金添加量あたりの硬化量は、ＮｂもＶとほぼ同じ効果が期待できるが、同程度をそれぞれ単独に添加した場合、Ｎｂの焼き戻し軟化抵抗はＶより向上代が小さく、特に短時間での焼き入れ性では、低下代が大きいことが判明した。したがって、本発明ではＶ添加を中心とすることにした。 As described above, the hardening amount per unit alloy addition amount when quenching is sufficiently performed after austenite formation can be expected to have almost the same effect as Nb, but when the same degree is added individually, It has been found that the temper softening resistance has a smaller allowance for improvement than V, and particularly for the hardenability in a short time, the decrease allowance is large. Therefore, in the present invention, the addition of V is centered.
しかしながら、Ｖ添加に加えて、Ｎｂを複合添加することにより、さらに、焼き戻し軟化抵抗を向上できることも判明した。これは、Ｖ量を増大させると、Ｖ添加による効果が飽和傾向になる一方、Ｎｂを適量添加すると、新たな効果代が付加される現象が見られるからである。しかし、Ｎｂを過剰に添加するとその効果が減少することを見出した。これは、Ｖ量とＮｂ量の相関があり、ｍｏｌ％（ａｔ．％）で、Ｎｂ≦Ｖ、質量％で、Ｎｂ≦（９３／５１）［％Ｖ］となるように制御する必要がある。これを超えてＮｂを添加すると、前記短時間焼き入れ性は劣化し、焼き戻し軟化抵抗はかえって低下する。この理由は必ずしも明確でないが、やはり、Ｃｒ2Ｎ以外の窒化物、ＮｂＮやＶＮなどが形成するために、Ｃｒ2Ｎの析出遅延、微細化が起こりにくくなっているためではないかと推定している。 However, it has also been found that temper softening resistance can be further improved by adding Nb in addition to V. This is because if the amount of V is increased, the effect of V addition tends to saturate, while if an appropriate amount of Nb is added, a new effect margin is added. However, it has been found that the effect decreases when Nb is added excessively. This has a correlation between the amount of V and the amount of Nb, and it is necessary to control so that Nb ≦ V, mass% and Nb ≦ (93/51) [% V] in mol% (at.%). . When Nb is added beyond this, the short-time hardenability deteriorates, and the temper softening resistance is lowered. The reason for this is not necessarily clear, but it is presumed that the reason is that precipitation of Cr 2 N and miniaturization are less likely to occur due to the formation of nitrides other than Cr 2 N, NbN, VN, and the like. Yes.
発明者らは、以上の知見を基に詳細な検討を進め、発明を完成した。
初めに各成分に関する限定条件を述べる。
The inventors proceeded with a detailed study based on the above knowledge and completed the invention.
First, limiting conditions for each component will be described.
Ｃは、焼入れ後所定の硬さを得るためには必須の元素であり、所定の硬度レベルになるようにＮと組み合わせて添加する。Ｎの効果を最大限利用するために、本発明では０．０８％を上限とする。これを超える添加すると硬度が硬すぎて、ブレーキの鳴き、靭性劣化等の不具合を生じるからである。硬度制御の安定性から、上限は望ましくは０．０４％である。また一方、０．０２％未満では、硬さを得るためにＮを過大に添加しなければならないことから０．０２％を下限とする。 C is an essential element for obtaining a predetermined hardness after quenching, and is added in combination with N so as to obtain a predetermined hardness level. In order to make maximum use of the effect of N, the upper limit is set to 0.08% in the present invention. This is because if the amount exceeds this, the hardness is too hard, causing problems such as brake squeal and toughness deterioration. From the viewpoint of stability of hardness control, the upper limit is desirably 0.04%. On the other hand, if less than 0.02%, N must be added excessively to obtain hardness, so 0.02% is made the lower limit.
Ｎは、本発明において非常に重要な元素の１つである。Ｃと同様に焼入れ後に所定の硬度を得るためには必須の元素であり、所定の硬度レベルになるようにＣと組み合わせて添加する。焼き戻し軟化抵抗を向上させるためには、０．０２５％以上が必要である。しかし、０．０５％を超えてＮを添加すると焼き戻し軟化抵抗向上効果はかえって低下する。また、０．０５％を超えてＮを添加するためには特別な添加方法で添加する必要があり、コスト上昇となるため好ましくない。したがって、Ｎの上限を０．０５％とする。安定的な製造のためには、上限は望ましくは、０．０４５％である。 N is one of the very important elements in the present invention. Like C, it is an essential element for obtaining a predetermined hardness after quenching, and is added in combination with C so as to obtain a predetermined hardness level. In order to improve the temper softening resistance, 0.025% or more is necessary. However, when N is added in excess of 0.05%, the temper softening resistance improving effect is reduced. Moreover, in order to add N exceeding 0.05%, it is necessary to add by the special addition method, and since it becomes a cost rise, it is unpreferable. Therefore, the upper limit of N is set to 0.05%. For stable production, the upper limit is desirably 0.045%.
Ｃ＋Ｎは、焼入れ後の硬さに直接関係する量であり、添加量が増加するほど硬くなる傾向にあり、ＨＲＣ３２−３８の所定の硬さレベルに調整するためには０．０５％以上０．１％以下とする必要がある。焼き入れ性により多少の違いはあるが、０．０５％未満であるとＨＲＣ３２を下回ることが多くなり、０．１％超では、ＨＲＣ３８を超えることが多くなるので好ましくない。なお、硬度制御の安定性、安定的な製造の観点から、Ｃ＋Ｎは、０．０５％以上０．０８％以下が望ましい。 C + N is an amount directly related to the hardness after quenching, and tends to become harder as the addition amount increases. In order to adjust to a predetermined hardness level of HRC32-38, 0.05% or more and 0.0. It is necessary to make it 1% or less. Although there are some differences depending on the hardenability, if it is less than 0.05%, it often falls below HRC32, and if it exceeds 0.1%, it often exceeds HRC38, which is not preferable. C + N is preferably 0.05% or more and 0.08% or less from the viewpoints of hardness control stability and stable production.
Ｓｉはフェライト形成元素として非常に強力であり、この点では抑制する必要がある。よって、その好適範囲は、１％以下とする。また、Ｓｉは耐酸化性を向上させる元素でもあるので、０．１％以上添加する。したがって、その好適範囲は、０．１％以上１％以下とする。 Si is very strong as a ferrite forming element, and it is necessary to suppress it in this respect. Therefore, the preferable range is 1% or less. Si is also an element that improves oxidation resistance, so 0.1% or more is added. Therefore, the preferable range is 0.1% or more and 1% or less.
Ｍｎは、鋼中に不可避的に含まれる成分であるが、重要なオーステナイト形成元素である。本発明では、Ｎｉ、Ｃｕとともに高温でのオーステナイト相を確保して焼入れ性を確保するため、０．５％以上の添加を必要とする。２．５％を超えると、耐銹性の劣化が見られるため、２．５％を上限とする。 Mn is a component inevitably contained in the steel, but is an important austenite forming element. In the present invention, it is necessary to add 0.5% or more in order to secure a hardenability by securing an austenite phase at a high temperature together with Ni and Cu. If it exceeds 2.5%, deterioration of weather resistance is observed, so 2.5% is made the upper limit.
Ｐは、鋼中に不可避的に含まれる成分であるが、０．０４％を越えて含有すると靭性が低下するために０．０４％を上限とした。 P is a component inevitably contained in the steel, but if it exceeds 0.04%, the toughness decreases, so 0.04% was made the upper limit.
Ｃｒは、二輪ディスクブレーキ材料として必要な耐銹性を確保するための必要な基本元素であり、その含有量が１１％未満では十分な耐銹性を得ることができない。また、Ｃｒはフェライト形成元素であるため、１４％を超えて添加すると、オーステナイト相生成温度域が縮小し、焼入れ温度域でのマルテンサイト相の変態しないフェライト相が生成し、焼入れ後の硬さを満足することができなくなる。よって、Ｃｒ添加量は、１０％以上１４％以下とする。 Cr is a necessary basic element for ensuring the weather resistance required as a two-wheel disc brake material. If the content is less than 11%, sufficient weather resistance cannot be obtained. Also, since Cr is a ferrite-forming element, if added over 14%, the austenite phase generation temperature range is reduced, and a ferrite phase that does not transform the martensite phase in the quenching temperature range is generated, and the hardness after quenching Can not be satisfied. Therefore, the Cr addition amount is 10% or more and 14% or less.
ＮｉはＭｎと同じくオーステナイト形成元素であり、高温でオーステナイト相を確保して焼入れ性を確保するために有効な元素である。しかしながら、非常に高価であるため、本発明では、出来るだけ低減し、０．１０％以下とする。 Ni is an austenite-forming element like Mn, and is an effective element for securing the austenite phase at a high temperature to ensure hardenability. However, since it is very expensive, in the present invention, it is reduced as much as possible to 0.10% or less.
Ｓは、鋼中に不可避的に含まれる成分であるが、本発明では０．０１％を越えて含有するとＣａＳが生成しやすいため、０．０１％を上限とする。また、Ｓを０．００１％未満とすることは製鋼コストの非常な増大を招くため、０．００１％を下限とすることが好ましい。 S is a component inevitably contained in the steel, but in the present invention, if it exceeds 0.01%, CaS is likely to be generated, so 0.01% is made the upper limit. Moreover, since making S less than 0.001% causes a great increase in steelmaking costs, it is preferable to make 0.001% the lower limit.
Ｖは本発明で非常に重要な元素である。Ｖを適量添加することにより焼き戻し軟化抵抗が顕著に向上する。特にＮが多い場合にこの効果は大きい。この機構はいまだ明らかではないが、前述したように、ＶはＮと相関が大きく、Ｃｒ窒化物（Ｃｒ2Ｎ）の析出および粗大化を抑制し、転位運動を抑制し焼き戻し軟化抵抗を向上させているものと考えている。焼き戻し軟化抵抗を向上させるためには、０．２％以上の添加が必要であり、０．３％を超える添加は前記短時間焼き入れ性が劣化するため上限を０．３％とする。前記短時間焼き入れ性の安定性の観点から、好ましくは、０．２％以上０．２５％以下が良い。 V is a very important element in the present invention. The temper softening resistance is remarkably improved by adding an appropriate amount of V. This effect is particularly large when N is large. Although this mechanism is not yet clear, as described above, V has a large correlation with N, suppresses precipitation and coarsening of Cr nitride (Cr 2 N), suppresses dislocation motion, and improves temper softening resistance. I believe that In order to improve the temper softening resistance, addition of 0.2% or more is necessary, and addition exceeding 0.3% degrades the short-time hardenability, so the upper limit is made 0.3%. From the viewpoint of the stability of the short-time hardenability, 0.2% to 0.25% is preferable.
Ｎｂは、本発明で非常に重要な元素である。Ｖに加えて、Ｎｂを適量添加することにより焼き戻し軟化抵抗は顕著に向上する。特にＮとＶが多い場合にこの効果は大きい。この機構はいまだ明らかではないが、ＮｂはＶと同様にＮと相関が大きいので、Ｖと共に、Ｃｒ窒化物の析出および粗大化を抑制し、転位運動を抑制し焼き戻し軟化抵抗を向上させているものと考えている。そのため、焼き戻し軟化抵抗を向上させるためには、０．０５％以上の添加が必要である。しかし、ＮｂＮの形で析出しやすく、この形で析出すると強化機能がなく、さらにＮの固溶強化効果を減少させ、さらに、焼き入れ性を減少させる原因となり、過剰の添加は避ける必要がある。そこで、焼き戻し軟化抵抗向上効果の低下および、焼き入れ性の悪影響を避けるためには、過剰添加を避ける必要があり、その上限はＶと相関があり、Ｎｂは、（９３／５１）［％Ｖ］以下とする。これは、ｍｏｌ％（ａｔ．％）でＶ量を超えないためであることを意味する。これを超えると、前記短時間焼き入れ性、焼き戻し軟化抵抗は低下する傾向にある。 Nb is a very important element in the present invention. In addition to V, the temper softening resistance is remarkably improved by adding an appropriate amount of Nb. This effect is particularly great when N and V are large. Although this mechanism is not yet clear, Nb has a large correlation with N as with V. Therefore, together with V, it suppresses precipitation and coarsening of Cr nitride, suppresses dislocation motion, and improves temper softening resistance. I believe that. Therefore, in order to improve the temper softening resistance, addition of 0.05% or more is necessary. However, it is easy to precipitate in the form of NbN, and if precipitated in this form, there is no strengthening function, further reducing the solid solution strengthening effect of N and further reducing the hardenability, and it is necessary to avoid excessive addition. . Therefore, in order to avoid a decrease in the effect of improving the temper softening resistance and the adverse effect of the hardenability, it is necessary to avoid excessive addition, the upper limit being correlated with V, and Nb is (93/51) [% V] or less. This means that the amount of V does not exceed the mol% (at.%). Beyond this, the short-time hardenability and temper softening resistance tend to decrease.
Ｔｉは本発明では制限すべき元素である。Ｎが多い場合、Ｖ，Ｎｂと比較して窒化物を形成しやすいため、前記短時間焼き入れ性を低下させる傾向にある。そのため、出来るだけ低減するほうが良く、０．０５％以下が好ましい。 Ti is an element to be limited in the present invention. When N is large, nitrides are easily formed as compared with V and Nb, and thus the short-time hardenability tends to be reduced. Therefore, it is better to reduce as much as possible, and 0.05% or less is preferable.
Ａｌは、０．０１％を超えると耐銹性の低下が見られるため０．０１％を上限とする。 If Al exceeds 0.01%, a decrease in weather resistance is observed, so 0.01% is made the upper limit.
以上の成分に加えて、さらに特性向上のために以下の元素を添加できる。 In addition to the above components, the following elements can be added to further improve the characteristics.
Ｍｏを適量添加することにより焼き戻し軟化抵抗は顕著に向上する。この機構はいまだ明らかではないが、Ｃｒ炭化物の析出および粗大化を抑制し、高温でも転位運動を抑制可能で焼き戻し軟化抵抗を向上させているものと考えている。また、耐食性も向上させる元素である。これらの効果を発現させるためには０．２％以上必要である。しかし、１％を超える添加は靭性が劣化するため上限は１％とする。 The temper softening resistance is remarkably improved by adding an appropriate amount of Mo. Although this mechanism is not yet clear, it is considered that the precipitation and coarsening of Cr carbides are suppressed, the dislocation motion can be suppressed even at high temperatures, and the temper softening resistance is improved. It is also an element that improves corrosion resistance. In order to develop these effects, 0.2% or more is necessary. However, since addition exceeding 1% deteriorates toughness, the upper limit is made 1%.
Ｃｕは、Ｍｎ、Ｎｉと同じく、オーステナイト相を確保して焼入れ性を確保するために有効な元素である。また、耐銹性を向上させる効果もある。さらには、焼き戻し時にＣｕ粒子として析出する２次硬化作用を有する場合もある。これはＣｕが多い場合、顕著である。これらの効果は０．２％以上の添加で発現する。また、２％を超えると靭性が劣化するため好ましくない。 Cu, like Mn and Ni, is an element effective for securing the austenite phase and ensuring hardenability. It also has the effect of improving weather resistance. Furthermore, it may have a secondary curing action that precipitates as Cu particles during tempering. This is remarkable when there is much Cu. These effects are manifested when 0.2% or more is added. On the other hand, if it exceeds 2%, the toughness deteriorates, which is not preferable.
さらに、これら述べてきた各元素はその成分範囲の中で、９００〜１１００℃の温度範囲で安定して焼入れを行えるために、次式（１）で表されるγｐが、８５以上を満足するよう相互に調整される必要がある。γｐが８５未満であると、９００〜１１００℃の温度範囲で１分程度の短時間保持後焼入れした場合、オーステナイト化が十分に進まず、フェライト相が残る場合があり、所定の硬度レベルに達しない場合があるからである。
γｐ＝４２０［％Ｃ］＋４７０［％Ｎ］＋２３［％Ｎｉ］＋９［％Ｃｕ］＋７［％Ｍｎ］−１１．５［％Ｃｒ］−１１．５［％Ｓｉ］−５２［％Ａｌ］−４９［％Ｔｉ］
−２３［％Ｖ］−１２［％Ｍｏ］−４７［％Ｎｂ］＋１８９ （１）
Furthermore, since each of the elements described above can be stably quenched in the temperature range of 900 to 1100 ° C. within the component range, γp represented by the following formula (1) satisfies 85 or more. Need to be coordinated with each other. When γp is less than 85, when quenched for a short period of time of about 1 minute in the temperature range of 900 to 1100 ° C., austenitization may not proceed sufficiently and the ferrite phase may remain, reaching a predetermined hardness level. It is because there is a case not to do.
γp = 420 [% C] +470 [% N] +23 [% Ni] +9 [% Cu] +7 [% Mn] −11.5 [% Cr] −11.5 [% Si] −52 [% Al] − 49 [% Ti]
-23 [% V] -12 [% Mo] -47 [% Nb] +189 (1)
焼き入れ温度に関しては、通常のブレーキディスクの製造では高周波加熱が使用される場合がほとんどである。この場合、加熱保持時間は短く、１分程度である。したがって、焼き入れ性を評価する場合、加熱保持時間を短くして評価する必要がある。本発明鋼は加熱保持時間を１分とした場合でも、９００℃以上１１００℃以下であれば、十分焼きが入るが、あまり高温すぎる場合は、製造時間の増大、コストの増加を招くため、９００℃以上１０００℃以下で行うことが好ましく、その温度範囲からの焼き入れでも本発明鋼は、所定の硬さ範囲を満足する。本発明鋼は焼入れままで使用することができる。 Regarding the quenching temperature, high-frequency heating is mostly used in the production of ordinary brake discs. In this case, the heating and holding time is short and is about 1 minute. Therefore, when evaluating hardenability, it is necessary to shorten the heat holding time for evaluation. Even if the steel of the present invention has a heating and holding time of 1 minute, if it is 900 ° C. or higher and 1100 ° C. or lower, it will be sufficiently baked, but if it is too high, it will cause an increase in manufacturing time and cost. It is preferable to carry out at a temperature not lower than 1000 ° C. and not higher than 1000 ° C. The steel of the present invention satisfies a predetermined hardness range even when quenched from the temperature range. The steel of the present invention can be used as it is.
次に製造方法について詳細に説明する。 Next, the manufacturing method will be described in detail.
以上、述べてきた成分と残部Ｆｅおよび不可避的不純物を含むスラブ、インゴット等の鋼片（以下、単にスラブともいう。）を溶製し、熱間圧延によって、２ｍｍ〜８ｍｍ程度の熱延板とした後、焼鈍を行って、軟化させた後、酸洗して製品とする。酸洗せずにショットブラストによる仕上げでもよい。 As described above, steel pieces (hereinafter also simply referred to as slabs) such as slabs, ingots, etc. containing the above-described components and the remaining Fe and inevitable impurities are melted, and hot rolled sheets of about 2 mm to 8 mm are obtained by hot rolling. After annealing, the product is softened and then pickled to obtain a product. Finishing by shot blasting may be performed without pickling.
これらは、ディスク製造工程において、ディスク形状に加工された後、９００−１０００℃に加熱されてから焼き入れられ、両面を研磨されて、ブレーキディスクとなる。 In the disk manufacturing process, these are processed into a disk shape, then heated to 900-1000 ° C., quenched, and polished on both sides to form a brake disk.
以下、実施例に従って、さらに詳細に本発明を説明する。 Hereinafter, the present invention will be described in more detail with reference to examples.
表１に示す化学成分を有する厚み２００ｍｍの鋼片を溶製した後、熱間圧延によって、厚さ６ｍｍの熱延板を得た。さらに、８５０℃まで加熱して徐冷する軟化焼鈍を施した。これらの鋼板から、焼き入れ性評価試験を採取し、残りは９５０℃または１０００℃で１０分間保持後、水冷する焼入れ処理を行った。 After melting a steel piece having a thickness of 200 mm having the chemical components shown in Table 1, a hot-rolled sheet having a thickness of 6 mm was obtained by hot rolling. Furthermore, the softening annealing which heats to 850 degreeC and anneals was given. From these steel plates, a hardenability evaluation test was collected, and the rest was held at 950 ° C. or 1000 ° C. for 10 minutes and then subjected to a quenching treatment with water cooling.
焼き入れ性評価試験は、９００℃〜１０００℃の温度に１分間保持した後に、水冷した焼入れ材を、ＪＩＳ Ｚ ２２４５に準拠した、ロックウェル硬さ試験（ＨＲＣ）で行った。ＨＲＣで３２から３８が合格である。 The hardenability evaluation test was performed by a Rockwell hardness test (HRC) based on JIS Z 2245 for a quenching material cooled to water after being held at a temperature of 900 ° C. to 1000 ° C. for 1 minute. HRC 32 to 38 pass.
１０００℃で１分間保持してから水冷して焼き入れ処理した鋼板から、各種試験片を採取し、評価試験を行った。焼き戻し軟化特性に関しては、５００℃から６００℃で２時間の焼き戻しを行った後、焼入れ材の硬さ試験と同様にロックウェル試験で評価した。焼き戻し後の硬さがＨＲＣ３０を下回らないことが合格基準である。また、耐銹性試験は、試験片両面を＃２４０研磨し、２４０時間の塩水噴霧試験（ＪＩＳ Ｚ ２３７１準拠）を行い、発銹程度を調査した。発銹しないものを合格、発銹したものを不合格とした。 Various test pieces were sampled from the steel sheet which was kept at 1000 ° C. for 1 minute and then cooled with water and quenched and subjected to an evaluation test. Regarding the temper softening property, after tempering at 500 to 600 ° C. for 2 hours, it was evaluated by the Rockwell test in the same manner as the hardness test of the quenched material. The acceptance criterion is that the hardness after tempering does not fall below HRC30. Further, in the weather resistance test, both sides of the test piece were polished by # 240, and a salt spray test (conforming to JIS Z 2371) for 240 hours was performed to examine the degree of rusting. Those that did not occur were accepted and those that did not were rejected.
これらの結果を表２に示す。 These results are shown in Table 2.
Ａ１鋼からＡ５鋼は、１２Ｃｒ−１．８Ｍｎ−０．０５Ｎｂ系にＶ添加量を変化させた鋼である。Ｖの少ないＡ１鋼は焼き戻し軟化特性が良くない。また、Ｖ量が過度に添加されているＡ５鋼は焼き入れ性が不十分である。本発明鋼であるＡ２鋼からＡ４鋼は優れた焼き戻し軟化抵抗を示すとともに焼き入れ性、耐銹性の問題もなく、ブレーキ用材料として好適である。 A1 steel to A5 steel are steels in which the V addition amount is changed to 12Cr-1.8Mn-0.05Nb. A1 steel with less V has poor temper softening properties. Moreover, A5 steel to which V amount is excessively added has insufficient quenchability. Steels A2 to A4, which are the steels of the present invention, are excellent as temper softening resistance and have no problems of hardenability and weather resistance, and are suitable as brake materials.
Ｂ１鋼からＢ５鋼は１２Ｃｒ−１．８Ｍｎ−０．２Ｖ系にＮｂ添加量を変化させた鋼である。Ｎｂ量の少ないＢ１鋼は焼き戻し軟化特性がやや低い。本発明鋼である、Ｎｂを好適範囲で添加したＢ２鋼からＢ４鋼は、Ｎｂ添加により焼き戻し軟化抵抗が向上している。Ｎｂを過剰に添加しているＢ５鋼は焼き入れ性が低下している。 B1 steel to B5 steel are steels in which the Nb addition amount is changed to 12Cr-1.8Mn-0.2V system. B1 steel with a small amount of Nb has a slightly low temper softening property. B2 steel to B4 steel to which Nb is added in a suitable range, which is the steel of the present invention, have improved temper softening resistance by adding Nb. B5 steel to which Nb is excessively added has a reduced hardenability.
Ｃ１鋼からＣ４鋼はＣｕを添加した鋼である。本発明鋼であるＣ１鋼からＣ３鋼はＣｕ添加で焼き戻し軟化抵抗が向上しており、優れた鋼であることがわかる。これに対し、Ｃｕを過度に添加したＣ４鋼はＣｕ析出による２次硬化が大きくなり、焼き戻しで硬度が硬くなることため、好ましくない。 C1 steel to C4 steel are steels to which Cu is added. It can be seen that C1 steel to C3 steel, which are the steels of the present invention, have improved temper softening resistance when Cu is added, and are excellent steels. On the other hand, C4 steel to which Cu is excessively added is not preferable because secondary hardening due to Cu precipitation is increased and hardness is increased by tempering.
Ｄ１鋼からＤ２鋼はＭｏ添加鋼である。Ｍｏ添加による焼き戻し軟化抵抗は向上している。 D1 steel to D2 steel are Mo-added steels. The temper softening resistance by adding Mo is improved.
Ｅ１鋼からＥ８鋼は比較例である。Ｎ及びＣ＋Ｎの低いＥ１鋼は焼き入れ性が乏しく、硬くならない。Ｎが低いＥ２鋼はＶ、Ｎｂ添加による焼き戻し軟化抵抗向上効果が小さく、好ましくない。Ｍｎの低いＥ３鋼はγｐが小さくなり焼き入れ安定性に欠ける。高ＭｎであるＥ４鋼は耐銹性が不十分である。Ｎ及びＣ＋Ｎが高過ぎるＥ５鋼は焼き入れ硬度が適正範囲を超え、好ましくない。Ｃｒが低いＥ６鋼は耐銹性が不十分である。Ｃｒが高いＥ７鋼はγｐが小さくなり、焼き入れ後の硬度は低すぎるため、好ましくない。Ｔｉが多いＥ８鋼は焼き入れ性が不十分で焼き入れ後の硬度は低い。 E1 steel to E8 steel are comparative examples. E1 steel with low N and C + N has poor hardenability and does not become hard. E2 steel with low N is not preferable because the effect of improving temper softening resistance by adding V and Nb is small. E3 steel with low Mn has low γp and lacks quenching stability. E4 steel, which has a high Mn, has insufficient weather resistance. E5 steel with N and C + N being too high is not preferable because the quenching hardness exceeds the appropriate range. E6 steel with low Cr has insufficient weather resistance. E7 steel with high Cr is not preferable because γp is small and the hardness after quenching is too low. E8 steel with much Ti has insufficient hardenability and has low hardness after quenching.
以上から、本発明鋼が、合金量が比較的少なく、低コストでありながら、焼き入れ性および耐熱性に優れており、ディスクブレーキ用材料として好適であることは明らかである。 From the above, it is clear that the steel of the present invention is suitable as a material for a disc brake because it has a relatively small amount of alloy and is low in cost and excellent in hardenability and heat resistance.
Claims (3)
Ｃ ：０．０２％以上０．０８％以下、
Ｓｉ：０．１％以上１％以下
Ｍｎ：０．５％以上２．５％以下
Ｐ ：０．０４％以下、
Ｓ ：０．０１０％以下、
Ｎ ：０．０２５％以上０．０５％以下、
Ｃｒ：１１％以上１４％以下、
Ｎｉ：０．１０％以下
Ｖ ：０．２％以上０．３％以下
Ｎｂ：０．０５％以上（９３／５１）［％Ｖ］以下
Ｔｉ：０．０５％以下
Ａｌ：０．０１％以下
を含有し、
Ｃ，Ｎは、
Ｃ＋Ｎ：０．０５％以上０．１％以下
を満足し、残部Ｆｅおよび不可避的不純物からなり、下記（１）式で表されるγｐが８５以上を満足することを特徴とする耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼板。
γｐ＝４２０［％Ｃ］＋４７０［％Ｎ］＋２３［％Ｎｉ］＋９［％Ｃｕ］＋７［％Ｍｎ］−１１．５［％Ｃｒ］−１１．５［％Ｓｉ］−５２［％Ａｌ］−４９［％Ｔｉ］
−２３［％Ｖ］−１２［％Ｍｏ］−４７［％Ｎｂ］＋１８９ （１） % By mass
C: 0.02% to 0.08%,
Si: 0.1% to 1% Mn: 0.5% to 2.5% P: 0.04% or less
S: 0.010% or less,
N: 0.025% or more and 0.05% or less,
Cr: 11% or more and 14% or less,
Ni: 0.10% or less V: 0.2% or more and 0.3% or less Nb: 0.05% or more (93/51) [% V] or less Ti: 0.05% or less Al: 0.01% or less Containing
C and N are
C + N: 0.05% to 0.1%
The martensitic stainless steel plate for heat-resistant disc brakes, characterized by satisfying the above, comprising the balance Fe and inevitable impurities, and satisfying γp represented by the following formula (1) of 85 or more.
γp = 420 [% C] +470 [% N] +23 [% Ni] +9 [% Cu] +7 [% Mn] −11.5 [% Cr] −11.5 [% Si] −52 [% Al] − 49 [% Ti]
-23 [% V] -12 [% Mo] -47 [% Nb] +189 (1)
Ｍｏ：０．２％以上１％以下
をさらに含有することを特徴とする、請求項１に記載の耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼。 The martensitic stainless steel for heat-resistant disc brakes according to claim 1, further comprising Mo: 0.2% to 1% by mass.
Ｃｕ：０．２％以上２％以下
をさらに含有することを特徴とする、請求項１または２に記載の耐熱ディスクブレーキ用マルテンサイト系ステンレス鋼。 The martensitic stainless steel for heat-resistant disk brakes according to claim 1 or 2, further comprising Cu: 0.2% or more and 2% or less by mass%.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012056866A1 (en) | 2010-10-25 | 2012-05-03 | 日産自動車株式会社 | Fuel cell system |
| JP2017197820A (en) * | 2016-04-27 | 2017-11-02 | 新日鐵住金ステンレス株式会社 | Martensitic stainless cold rolled steel sheet for bicycle disc brake rotor excellent in hardenability and manufacturing method therefor |
| JP2020164901A (en) * | 2019-03-28 | 2020-10-08 | 日鉄ステンレス株式会社 | Ferritic stainless steel for disc rotors and disc rotors for brakes |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001220654A (en) * | 1999-11-30 | 2001-08-14 | Nippon Steel Corp | Stainless steel for disk brake, increased in resistance to temper softening |
| JP2005146298A (en) * | 2003-11-11 | 2005-06-09 | Jfe Steel Kk | Stainless steel sheet for disc brake having excellent temper softening resistance |
| JP2005307346A (en) * | 2004-03-22 | 2005-11-04 | Jfe Steel Kk | Stainless steel for disc brake having excellent heat resistance and corrosion resistance |
| JP2009280912A (en) * | 2008-04-25 | 2009-12-03 | Jfe Steel Corp | LOW-CARBON MARTENSITIC Cr-CONTAINING STEEL |
-
2010
- 2010-03-15 JP JP2010057864A patent/JP5553651B2/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001220654A (en) * | 1999-11-30 | 2001-08-14 | Nippon Steel Corp | Stainless steel for disk brake, increased in resistance to temper softening |
| JP2005146298A (en) * | 2003-11-11 | 2005-06-09 | Jfe Steel Kk | Stainless steel sheet for disc brake having excellent temper softening resistance |
| JP2005307346A (en) * | 2004-03-22 | 2005-11-04 | Jfe Steel Kk | Stainless steel for disc brake having excellent heat resistance and corrosion resistance |
| JP2009280912A (en) * | 2008-04-25 | 2009-12-03 | Jfe Steel Corp | LOW-CARBON MARTENSITIC Cr-CONTAINING STEEL |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012056866A1 (en) | 2010-10-25 | 2012-05-03 | 日産自動車株式会社 | Fuel cell system |
| JP2017197820A (en) * | 2016-04-27 | 2017-11-02 | 新日鐵住金ステンレス株式会社 | Martensitic stainless cold rolled steel sheet for bicycle disc brake rotor excellent in hardenability and manufacturing method therefor |
| JP2020164901A (en) * | 2019-03-28 | 2020-10-08 | 日鉄ステンレス株式会社 | Ferritic stainless steel for disc rotors and disc rotors for brakes |
| JP7325206B2 (en) | 2019-03-28 | 2023-08-14 | 日鉄ステンレス株式会社 | Ferritic stainless steel for disc rotors and disc rotors for brakes |
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