JP2019178419A - Stainless steel sheet and braking component - Google Patents
Stainless steel sheet and braking component Download PDFInfo
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
本発明は、ステンレス鋼板および制動系部品に関するものであり、特に二輪車や自動車のブレーキ等の制動部品に使用される摩耗性に優れたステンレス鋼板に関する。 The present invention relates to a stainless steel plate and braking system parts, and more particularly to a stainless steel plate having excellent wear properties used for braking parts such as motorcycles and automobile brakes.
二輪車や自動車のブレーキは摩擦現象を利用し、運動エネルギーを熱エネルギーに変換して、減速および停止させる装置であり、高い安全性が要求される。ブレーキは主としてドラムブレーキとディスクブレーキの２種に大別されるが、前者がライニングをドラムに、後者がブレーキパッドをディスクロータに接触させて制動力を付与するものである。車種によってドラムブレーキとディスクブレーキが使い分けられるが、いずれも高い制動能力が要求される。 Motorcycles and automobile brakes are devices that use friction to convert kinetic energy into thermal energy to decelerate and stop, and require high safety. There are two main types of brakes: drum brakes and disk brakes. The former applies the lining to the drum and the latter applies the brake pad to the disk rotor to apply the braking force. Drum brakes and disc brakes are used properly depending on the vehicle type, but both require high braking ability.
上記のブレーキシステムの中でドラムおよびディスクロータには摩耗性が要求されるため鋳鉄が広く使用されている。しかしながら鋳鉄は耐食性が著しく低いため、使用中に発錆が生じる課題があった。特に二輪用ディスクブレーキは人目につきやすい位置に使用されるために、鋳鉄に変わる部材素材としてマルテンサイト系ステンレス鋼板が使用され始めている。一方、鋳鉄は黒鉛が分散生成しているため耐摩耗性に優れている。そのため、強い制動力および耐摩耗性が要求される場合は、現状のマルテンサイト系ステンレス鋼板では課題があった。 Among the above brake systems, cast iron is widely used because the drum and the disk rotor are required to be wearable. However, since cast iron has extremely low corrosion resistance, there is a problem that rusting occurs during use. In particular, since a two-wheel disc brake is used at a position that is easily noticeable, a martensitic stainless steel plate has begun to be used as a member material in place of cast iron. On the other hand, cast iron has excellent wear resistance because graphite is dispersedly produced. Therefore, when a strong braking force and wear resistance are required, the current martensitic stainless steel plate has a problem.
特にディスクブレーキの場合、摩擦の相手材となるパッドについて、近年、用いられる材料の変化が生じつつある。従来はアスベストを基材としたパッドが多用されていたが、人体への影響から使用不可になっている。そのため現状では、セミメタリック、ロースチール、ノンスチールのパッドが使用されている。しかしながら、セミメタリックやロースチールはスチールファイバーを補強材としており、摩擦係数が高いためディスクロータへの攻撃性が強く、ブレーキの効きは良いがディスクロータが摩耗し易く、鳴きが発生し易い。ノンスチールのパッドの場合、アラミド繊維、セラミック繊維、ガラスファイバー等の非金属物質を補強材としており、摩擦係数が低いため、鳴き、ディスクロータの摩耗、ホイール汚れは生じ難いがブレーキの効きは前者二種よりも弱い。二輪車や自動車の要求性能や使用地域によって使用するパッドは異なるものの、最近では効きを重視するとともに摩耗分を削減する観点から相手材となるディスクロータには更なる摩耗性の向上が要求されている。 In particular, in the case of a disc brake, a material used for a pad which is a counterpart material of friction is changing in recent years. Conventionally, pads using asbestos as a base material have been frequently used, but they cannot be used due to the influence on the human body. Therefore, currently, semi-metallic, low steel, and non-steel pads are used. However, semi-metallic and low steel use steel fiber as a reinforcing material, and since the friction coefficient is high, the aggressiveness to the disk rotor is strong and the brake is effective, but the disk rotor is easily worn and squealing is likely to occur. Non-steel pads are made of non-metallic materials such as aramid fiber, ceramic fiber, glass fiber, etc., and the friction coefficient is low. Weaker than two types. Although the pads to be used differ depending on the required performance and usage area of the motorcycle or automobile, recently, the disk rotor as a counterpart material has been required to further improve the wearability from the viewpoint of reducing the amount of wear while emphasizing effectiveness. .
二輪車のディスクロータにはステンレス鋼板が使用される実績があり、例えば特許文献１〜１０の開示がある。これらはいずれも二輪用ディスクロータを対象としており、耐食性と強度を得るためにマルテンサイト系ステンレス鋼板に焼き入れ処理、あるいは焼き入れ−焼き戻し処理を施してディスクロータに適用することを特徴としている。また、特許文献１０には耐摩耗性と加工性に優れたディスクロータ用熱延鋼板およびその製造方法が開示されており、鋳鉄製ディスクと同等の耐摩耗性を発揮させるべく、ステンレス鋼板において、鋼成分や硬さに加えて金属組織をフェライト＋ベイナイト組織にする技術がある。
There is a track record of using a stainless steel plate for a disc rotor of a two-wheeled vehicle. For example, Patent Documents 1 to 10 disclose. These are all intended for two-wheel disc rotors, and are characterized in that they are applied to a disc rotor by subjecting a martensitic stainless steel plate to quenching treatment or quenching-tempering treatment in order to obtain corrosion resistance and strength. .
一方、自動車のブレーキに対するステンレス鋼板の適用事例は少ない。これは、これまでの自動車の構造上、ブレーキは人目につきにくい箇所に配置されるため、錆び（耐食性）に対する要求がさほど高くないことが理由である。そのため、耐食性よりも摩耗性に重点が置かれ、鋳鉄が広く適用されているのが現状である。しかし、特許文献１１に開示されている様に、近年では自動車のブレーキも人目につく様なデザインが多くなり、その場合、適用する鋳鉄では耐食性の観点で不十分となる。また、ハイブリッド車や電気自動車では回生ブレーキと呼ばれる運動エネルギーを電気エネルギーに変換するブレーキシステムが多用されつつある。回生ブレーキの場合これまでのブレーキより、ブレーキ負荷が減るため、鋳鉄よりも熱伝導率が小さいステンレス鋼でも適用可能になった背景がある。 On the other hand, there are few application examples of stainless steel plates for automobile brakes. This is because, because of the structure of conventional automobiles, the brake is disposed at a place where it is difficult to see, so that the demand for rust (corrosion resistance) is not so high. Therefore, the current situation is that cast iron is widely applied with an emphasis on wear rather than corrosion resistance. However, as disclosed in Patent Document 11, in recent years, there are many designs in which automobile brakes are also conspicuous, and in that case, cast iron to be applied is insufficient from the viewpoint of corrosion resistance. Also, in hybrid vehicles and electric vehicles, a brake system called regenerative brake that converts kinetic energy into electric energy is being used frequently. In the case of regenerative braking, the brake load is reduced as compared with conventional brakes, and there is a background that even stainless steel having a lower thermal conductivity than cast iron can be applied.
特許文献１１によると、焼き入れ処理、あるいは焼き入れ−焼き戻し処理を施すと目標の寸法精度や形状を得ることが難しいため、ホットプレス処理を行い、マルテンサイト組織、あるいはマルテンサイト組織とフェライト相からなる混合組織のディスクブレーキロータを製造する方法が開示されている。特許文献１1はホットプレスを前提としているため、冷間プレスでディスクロータを製造する場合には適用出来ない。更に、特許文献１1には、二輪車や自動車のブレーキ等の制動部品重要視される耐摩耗性について技術的な解決方法は記載されていない。 According to Patent Document 11, since it is difficult to obtain a target dimensional accuracy and shape when a quenching process or a quenching-tempering process is performed, a hot press process is performed, and a martensite structure, or a martensite structure and a ferrite phase are obtained. A method of manufacturing a mixed structure disc brake rotor is disclosed. Since Patent Document 11 is premised on a hot press, it cannot be applied when a disk rotor is manufactured by a cold press. Further, Patent Document 11 does not describe a technical solution for wear resistance, which is regarded as important for braking parts such as motorcycles and automobile brakes.
本発明は、上述した課題を解消すべく案出されたものであり、高価な元素に頼らずとも、優れた耐摩耗性を有するステンレス鋼板および制動系部品を提供するものである。 The present invention has been devised to solve the above-described problems, and provides a stainless steel plate and braking system parts having excellent wear resistance without relying on expensive elements.
上記課題を解決するために、本発明者らは低Ｃｒフェライト系ステンレス鋼板の微細組織と耐摩耗特性に関して詳細に調査した。そして、かかる目的を達成すべく種々の検討を重ねた結果、以下の知見を得た。 In order to solve the above problems, the present inventors have investigated in detail the microstructure and wear resistance characteristics of a low Cr ferritic stainless steel sheet. And as a result of repeating various examinations in order to achieve this purpose, the following knowledge was obtained.
本発明者らは、フェライト相を母相とするステンレス鋼板において分散生成する炭窒化物の量および形態を制御することにより、より耐摩耗性に優れたステンレス鋼板が得られることを見出した。具体的には、母相のフェライト相中に生成する炭窒化物のうち円相当の直径で０．３μｍ以上の炭窒化物を１０〜５０個／１００μｍ2存在させることによって耐摩耗性を向上させるものである。 The inventors of the present invention have found that a stainless steel plate with superior wear resistance can be obtained by controlling the amount and form of carbonitrides dispersed and formed in a stainless steel plate having a ferrite phase as a parent phase. Specifically, wear resistance is improved by making 10-50 pieces / 100 μm 2 of carbonitride having a diameter corresponding to a circle of 0.3 μm or more among the carbonitrides generated in the ferrite phase of the parent phase. Is.
本発明のステンレス鋼板の耐摩耗性は、特に、制動性部品に適用した場合の摩耗特性であり、例えば、ブレーキディスクとパッドの間の摩耗特性である。特に、常温状態から摩擦により高温に発熱しながら摩耗が生じる形態を対象とするものである。この場合、急激な発熱が生じて制動性部品表面は５００℃以上になる。その際に、制動性部品の素材である鋼板表面では摩擦・摩耗が生じ摩耗分が発生するとともに酸化スケールの発生および剥離が生じる。摩耗量が多いと、ブレーキディスクの場合には減肉が生じるとともに、局部的な摩耗が生じた場合に鳴きと呼ばれる制動時に生じる数千〜一万Ｈｚの耳障りな音が発生する。また、これよりも低周波数域ではステアリングの振動も発生する。 The wear resistance of the stainless steel plate of the present invention is a wear characteristic particularly when applied to a braking component, for example, a wear characteristic between a brake disk and a pad. In particular, it is intended for a form in which wear occurs while generating heat to high temperature due to friction from a normal temperature state. In this case, sudden heat generation occurs and the surface of the braking component becomes 500 ° C. or higher. At that time, friction and wear occur on the surface of the steel plate, which is the material of the braking component, and wear is generated and oxide scale is generated and peeled off. When the amount of wear is large, the brake disc is thinned, and when local wear occurs, an harsh sound of several thousand to 10,000 Hz, which is called squealing, is generated. Further, steering vibration also occurs in a lower frequency range.
本発明では、ステンレス鋼板における炭窒化物の析出量と形態を制御することで耐摩耗性の向上が可能である知見を得た。さらに炭窒化物の析出量と形態を制御したステンレス鋼板を素材として制動部品に適用すると、例えば、鳴きなどのブレーキの不具合の原因となるブレーキディスクロータの摩耗を抑制可能な事を見出した。 In the present invention, it has been found that the wear resistance can be improved by controlling the amount and form of carbonitride deposited on the stainless steel plate. Furthermore, it has been found that when a stainless steel plate with controlled carbonitride precipitation amount and form is applied as a material to a braking part, it is possible to suppress wear of the brake disc rotor, which causes a brake failure such as squealing, for example.
本発明は上記知見に基づいて完成したもので、その発明の要旨は、次の通りのものである。 The present invention has been completed based on the above findings, and the gist of the invention is as follows.
［１］質量％で、
Ｃ ：０．００５〜０．１００％、
Ｓｉ：０．０１〜１．００％、
Ｍｎ：０．０１０〜３．００％、
Ｐ ：０．０４０％以下、
Ｓ ：０．０１００％以下、
Ｃｒ：１０．０〜１４．０％、
Ｎ ：０．００５〜０．１００％、
Ｖ ：０．０３〜０．３０％、
Ａｌ：０．００１〜０．０５０％、
Ｂ ：０．０００２〜０．００５０％、
Ｎｉ：０〜２．００％、
Ｃｕ：０〜２．００％、
Ｍｏ：０〜１．００％、
Ｗ ：０〜１．００％、
Ｔｉ：０〜０．４０％、
Ｎｂ：０〜０．４０％、
Ｚｒ：０〜０．４０％、
Ｃｏ：０〜０．４００％、
Ｓｎ：０〜０．４０％、
ＲＥＭ：０〜０．０５０％以下、
Ｍｇ：０〜０．０１００％、
Ｃａ：０〜０．０１００％、
Ｓｂ：０〜０．５０％、
Ｔａ：０〜０．３０００％、
Ｈｆ：０〜０．３０００％、
Ｇａ：０〜０．１０００％を含有し、残部がＦｅ及び不純物からなり、
金属組織がフェライト相からなり、円相当の直径で０．３μｍ以上の炭窒化物が任意断面において１０〜５０個／１００μｍ2存在することを特徴とするステンレス鋼板。
［２］質量％で、Ｎｉ：０．０５〜２．００％、Ｃｕ：０．０５〜２．００％、Ｍｏ：０．０５〜１．００％、Ｗ：０．０５〜１．００％、Ｔｉ：０．００５〜０．４０％、Ｎｂ：０．００５〜０．４０％、Ｚｒ：０．００５〜０．４０％、Ｃｏ：０．００５〜０．４００％、Ｓｎ：０．００５〜０．４０％、ＲＥＭ：０．００１〜０．０５０％以下、Ｍｇ：０．０００２〜０．０１００％、Ｃａ：０．０００２〜０．０１００％、Ｓｂ：０．０５〜０．５０％、Ｔａ：０．００５０〜０．３０００％、Ｈｆ：０．００５０〜０．３０００％、Ｇａ：０．０００２〜０．１０００％の１種または２種以上含有することを特徴とする上記［１］に記載のステンレス鋼板。
［３］制動系部品に適用されること特徴とする上記［１］または［２］に記載のステンス鋼板。
［４］ブレーキディスクロータに適用されること特徴とする上記［１］または［２］に記載のステンレス鋼板。
［５］上記［１］または［２］に記載のステンレス鋼板を用いた制動系部品。
[1] By mass%
C: 0.005 to 0.100%,
Si: 0.01 to 1.00%,
Mn: 0.010 to 3.00%,
P: 0.040% or less,
S: 0.0100% or less,
Cr: 10.0-14.0%,
N: 0.005 to 0.100%,
V: 0.03-0.30%,
Al: 0.001 to 0.050%,
B: 0.0002 to 0.0050%,
Ni: 0 to 2.00%,
Cu: 0 to 2.00%,
Mo: 0 to 1.00%,
W: 0 to 1.00%,
Ti: 0 to 0.40%,
Nb: 0 to 0.40%
Zr: 0 to 0.40%,
Co: 0 to 0.400%,
Sn: 0 to 0.40%,
REM: 0 to 0.050% or less,
Mg: 0 to 0.0100%,
Ca: 0 to 0.0100%,
Sb: 0 to 0.50%,
Ta: 0 to 0.3000%,
Hf: 0 to 0.3000%,
Ga: 0 to 0.1000% is contained, the balance consists of Fe and impurities,
A stainless steel plate, characterized in that the metal structure is composed of a ferrite phase, and there are 10 to 50/100 μm 2 of carbonitride having an equivalent diameter of 0.3 μm or more in an arbitrary cross section.
[2] By mass%, Ni: 0.05-2.00%, Cu: 0.05-2.00%, Mo: 0.05-1.00%, W: 0.05-1.00% , Ti: 0.005 to 0.40%, Nb: 0.005 to 0.40%, Zr: 0.005 to 0.40%, Co: 0.005 to 0.400%, Sn: 0.005 To 0.40%, REM: 0.001 to 0.050% or less, Mg: 0.0002 to 0.0100%, Ca: 0.0002 to 0.0100%, Sb: 0.05 to 0.50% , Ta: 0.0050 to 0.3000%, Hf: 0.0050 to 0.3000%, Ga: 0.0002 to 0.1000%, or one or more of the above [1] ] The stainless steel plate described in the above.
[3] The stainless steel plate according to [1] or [2], which is applied to a brake system component.
[4] The stainless steel plate according to [1] or [2], which is applied to a brake disc rotor.
[5] A braking system component using the stainless steel plate according to [1] or [2].
本発明によれば、高価な元素に頼らずとも、優れた耐摩耗性有するステンレス鋼板および制動系部品を提供することができる。 According to the present invention, it is possible to provide a stainless steel plate and a braking system component having excellent wear resistance without depending on expensive elements.
以下、本発明のステンレス鋼板の一実施形態について詳細に説明する。 Hereinafter, an embodiment of the stainless steel plate of the present invention will be described in detail.
まず、本実施形態のステンレス鋼板の化学成分についての限定理由について説明する。ここで、成分についての「％」は質量％を意味する。 First, the limitation reason about the chemical component of the stainless steel plate of this embodiment is demonstrated. Here, “%” for a component means mass%.
Ｃは、強度向上に寄与するとともに、本実施形態における炭窒化物生成のために重要な元素である。円相当の直径で０．３μｍ以上の炭窒化物を１０〜５０個／１００μｍ2存在させて耐摩耗性を良好にするためにＣを０．００５％以上含有する。一方、０．１００％超含有すると靭性が著しく低下するため、上限を０．１００％以下とする。また、耐食性の観点から０．００５％以上、０．０８０％以下が望ましい。更に、製造コストや製造時の焼鈍効率の観点から０．０１０％以上、０．０５０％以下がより望ましい。 C contributes to strength improvement and is an important element for carbonitride formation in the present embodiment. In order to improve wear resistance by adding 10-50 pieces / 100 μm 2 of carbon nitride having a diameter corresponding to a circle and having a diameter of 0.3 μm or more, 0.005% or more of C is contained. On the other hand, if the content exceeds 0.100%, the toughness is remarkably lowered, so the upper limit is made 0.100% or less. Further, from the viewpoint of corrosion resistance, 0.005% or more and 0.080% or less are desirable. Furthermore, 0.010% or more and 0.050% or less are more desirable from the viewpoint of manufacturing cost and annealing efficiency during manufacturing.
Ｓｉは、脱酸剤としても有用な元素であり、固溶強化による高強度化によって耐摩耗性を向上させるため０．０１％以上添加する。しかしながら、１．００％超含有すると靭性が著しく劣化するため上限を１．００％以下とする。また、精錬コスト、耐酸化性、耐食性を考慮すると、０．２０％以上、０．８０％以下が望ましい。 Si is an element useful as a deoxidizer, and is added in an amount of 0.01% or more in order to improve wear resistance by increasing the strength by solid solution strengthening. However, if the content exceeds 1.00%, the toughness deteriorates remarkably, so the upper limit is made 1.00% or less. Further, considering refining cost, oxidation resistance, and corrosion resistance, 0.20% or more and 0.80% or less are desirable.
Ｍｎは、脱酸剤として含有される元素であるため０．０１０％以上含有する。過度に含有すると高温摩耗時にスケール剥離が生じ易くなり、鳴きの原因となるため３．００％以下を上限とする。更に、耐酸化性や製造時の酸洗性を考慮すると、０．１０％以上、２．００％以下が望ましい。 Since Mn is an element contained as a deoxidizer, it is contained in an amount of 0.010% or more. If it is contained excessively, scale peeling is likely to occur during high-temperature wear, and it causes squealing, so 3.00% or less is made the upper limit. Furthermore, considering oxidation resistance and pickling properties during production, 0.10% or more and 2.00% or less are desirable.
Ｐは、不純物として含有され製造時の熱間加工性を劣化させるため、その含有量は少ないほどよく上限を０．０４０％以下と制限する。但し、過度の低減は精錬コストの増加につながる他、耐食性を考慮すると、０．０２０％以上、０．０３０％以下が望ましい。 P is contained as an impurity and deteriorates the hot workability during production. Therefore, the lower the content, the better the upper limit is limited to 0.040% or less. However, excessive reduction leads to an increase in refining costs, and considering corrosion resistance, 0.020% or more and 0.030% or less are desirable.
Ｓは、鋼中に不可避に含まれる不純物元素であり、その含有量は少ないほどよい。また、介在物等の形成によって高温強度を低下させる作用を持つ。これらのことからＳ量の上限は０．０１００％以下とする。但し、Ｓの過度の低減は原料や精錬コストの上昇に繋がるため、下限は０．００１％％とすることが好ましい。Ｓのさらに好ましい範囲は０．００２〜０．００８％である。 S is an impurity element inevitably contained in the steel, and the smaller the content, the better. Moreover, it has the effect | action which reduces high temperature intensity | strength by formation of an inclusion etc. For these reasons, the upper limit of the amount of S is set to 0.0100% or less. However, since excessive reduction of S leads to an increase in raw materials and refining costs, the lower limit is preferably 0.001%. A more preferable range of S is 0.002 to 0.008%.
Ｃｒは耐食性を確保する上で基本となる元素である。また耐食性向上によって、ディスクロータなど制動性部品の外観を良くする。また、鋼板中に炭窒化物を生成させて耐摩耗性を確保するために１０．０％以上含有する。一方、多量の含有は合金コストの増加や靭性の低下につながるため上限を１４．０％以下とする。更に、加工性や製造性を考慮すると１３．０％以下が望ましく、１２．０％以下がより望ましい。 Cr is an element that is fundamental in securing corrosion resistance. In addition, the appearance of braking parts such as disk rotors is improved by improving corrosion resistance. Moreover, in order to produce | generate a carbonitride in a steel plate and to ensure abrasion resistance, it contains 10.0% or more. On the other hand, a large amount leads to an increase in alloy costs and a decrease in toughness, so the upper limit is made 14.0% or less. Furthermore, considering workability and manufacturability, 13.0% or less is desirable, and 12.0% or less is more desirable.
ＮはＣと同様に強度向上に寄与するとともに、本実施形態における炭窒化物生成のために重要な元素である。円相当の直径で０．３μｍ以上の炭窒化物を１０〜５０個／１００μｍ2生成させて耐摩耗性を良好にするためにＮを０．００５％以上含有する。一方、０．１００％超含有すると靭性が著しく低下するため、上限を０．１００％以下とする。また、耐食性の観点から０．００５％以上、０．０８０％以下が望ましい。更に、製造コストや製造時の焼鈍効率の観点から０．０１０％以上、０．０５０％以下がより望ましい。 N, like C, contributes to strength improvement and is an important element for carbonitride generation in the present embodiment. In order to generate 10-50 pieces / 100 μm 2 of carbonitride having a diameter corresponding to a circle and having a diameter of 0.3 μm or more to improve wear resistance, N is contained in an amount of 0.005% or more. On the other hand, if the content exceeds 0.100%, the toughness is remarkably lowered, so the upper limit is made 0.100% or less. Further, from the viewpoint of corrosion resistance, 0.005% or more and 0.080% or less are desirable. Furthermore, 0.010% or more and 0.050% or less are more desirable from the viewpoint of manufacturing cost and annealing efficiency during manufacturing.
ＶはＣやＮと結合してＶ（Ｃ，Ｎ）を形成し、耐摩耗性を向上させる元素である。この効果は０．０３以上から発現するため下限を０．０３％以上とする。一方、過度に含油させるとコスト増に繋がるため上限を０．３０％以下とする。更に、精錬コストや耐食性を考慮すると、０．０５％以上、０．２０％以下が望ましい。 V is an element that combines with C or N to form V (C, N) and improves wear resistance. Since this effect is manifested from 0.03 or more, the lower limit is made 0.03% or more. On the other hand, excessive oil impregnation leads to an increase in cost, so the upper limit is made 0.30% or less. Furthermore, considering refining cost and corrosion resistance, 0.05% or more and 0.20% or less are desirable.
Ａｌは、脱酸剤として活用出来る他、耐酸化性や耐食性を向上させる元素である。さらに、Ａｌは介在物の清浄度を上げて耐摩耗性を向上させる効果も有する。これらの効果を発揮させるため、０．００１％以上含有する。一方、０．０５０％超含有させると、耐酸化性や耐食性の向上が飽和するとともに、ＡｌＮやＡｌ系酸化物が凝集粗大化して摩耗時の鳴きの原因となるため、０．０５０％以下とする。精錬コストや耐食性を考慮すると０．００５％以上、０．０３０％以下が望ましい。 Al is an element that can be used as a deoxidizer and also improves oxidation resistance and corrosion resistance. Furthermore, Al has the effect of increasing the cleanliness of inclusions and improving the wear resistance. In order to exhibit these effects, 0.001% or more is contained. On the other hand, if the content exceeds 0.050%, the improvement in oxidation resistance and corrosion resistance is saturated, and AlN and Al-based oxides become agglomerated and coarsened and cause noise during wear. To do. Considering the refining cost and corrosion resistance, 0.005% or more and 0.030% or less are desirable.
Ｂは、ＢＮを形成して耐摩耗性を向上させる元素であるため、０．０００２％以上含有する。一方、０．００５０％超含有すると焼き入れ性が過度に向上して靭性が劣化するため上限を０．００５０％以下とする。耐食性を考慮すると０．００１５％以下が望ましい。 Since B is an element that forms BN and improves the wear resistance, it is contained in an amount of 0.0002% or more. On the other hand, if the content exceeds 0.0050%, the hardenability is excessively improved and the toughness deteriorates, so the upper limit is made 0.0050% or less. In consideration of corrosion resistance, 0.0015% or less is desirable.
本実施形態に係るステンレス鋼板は、上述してきた元素以外（残部）は、Ｆｅ及び不純物からなるが、後述する任意元素についても含有させることができる。よって、Ｎｉ、Ｃｕ、Ｍｏ、Ｗ、Ｔｉ、Ｎｂ、Ｚｒ、Ｃｏ、Ｓｎ、ＲＥＭ、Ｍｇ、Ｃａ、Ｓｂ、Ｔａ、Ｈｆ、Ｇａの含有量の下限は０％以上である。
なお、本実施形態における「不純物」とは、鋼を工業的に製造する際に鉱石やスクラップ等のような原料をはじめとして製造工程の種々の要因によって混入する成分であり、不可避的に混入する成分も含む。
The stainless steel plate according to the present embodiment is composed of Fe and impurities other than the above-described elements (remainder), but can also contain arbitrary elements described later. Therefore, the lower limit of the content of Ni, Cu, Mo, W, Ti, Nb, Zr, Co, Sn, REM, Mg, Ca, Sb, Ta, Hf, and Ga is 0% or more.
The “impurities” in the present embodiment are components that are mixed due to various factors in the manufacturing process including raw materials such as ores and scraps when industrially manufacturing steel, and are inevitably mixed. Including ingredients.
本実施形態のステンレス鋼板は、必要に応じて、Ｎｉ：０．０５〜２．００％、Ｃｕ：０．０５〜２．００％、Ｍｏ：０．０５〜１．００％、Ｗ：０．０５〜１．００％、Ｔｉ：０．００５〜０．４０％、Ｎｂ：０．００５〜０．４０％、Ｚｒ：０．００５〜０．４０％、Ｃｏ：０．００５〜０．４００％、Ｓｎ：０．００５〜０．４０％、ＲＥＭ：０．００１〜０．０５０％以下、Ｍｇ：０．０００２〜０．０１００％、Ｃａ：０．０００２〜０．０１００％、Ｓｂ：０．０５〜０．５０％、Ｔａ：０．００５０〜０．３０００％、Ｈｆ：０．００５０〜０．３０００％、Ｇａ：０．０００２〜０．１０００％の１種または２種以上を含有しているものであってもよい。 The stainless steel plate according to the present embodiment has Ni: 0.05 to 2.00%, Cu: 0.05 to 2.00%, Mo: 0.05 to 1.00%, and W: 0.0. 05-1.00%, Ti: 0.005-0.40%, Nb: 0.005-0.40%, Zr: 0.005-0.40%, Co: 0.005-0.400% Sn: 0.005-0.40%, REM: 0.001-0.050% or less, Mg: 0.0002-0.0100%, Ca: 0.0002-0.0100%, Sb: 0.0. Contains one or more of 05 to 0.50%, Ta: 0.0050 to 0.3000%, Hf: 0.0050 to 0.3000%, Ga: 0.0002 to 0.1000% It may be.
Ｎｉは、強度向上に寄与する元素であり、必要に応じて０．０５％以上含有する。一方、２．００％超含有させるとコスト高になる他、焼き入れ時に残留オーステナイト相が生成して靭性が劣化するため上限を２．００％とする。耐食性や製造コストの観点から０．１０％以上、０．５０％以下が望ましい。 Ni is an element that contributes to strength improvement, and is contained in an amount of 0.05% or more as necessary. On the other hand, if the content exceeds 2.00%, the cost is increased, and a retained austenite phase is generated at the time of quenching to deteriorate toughness, so the upper limit is made 2.00%. 0.10% or more and 0.50% or less are desirable from the viewpoint of corrosion resistance and manufacturing cost.
Ｃｕは、強度向上に寄与する元素であり、さらに耐食性に寄与する元素でもある。また、摩耗熱によってε−Ｃｕが析出することで耐摩耗性を向上させるため必要に応じて０．０５％以上含有する。一方、２．００％超含有すると靭性が著しく劣化するほか、摩耗性も劣化するため上限を２．００％以下とする。更に、精錬コストや熱間加工性、酸洗性を考慮すると、０．４０％以上、１．２０％以下が望ましい。 Cu is an element that contributes to strength improvement, and further contributes to corrosion resistance. Moreover, in order to improve abrasion resistance because ε-Cu is precipitated by wear heat, it is contained in an amount of 0.05% or more as necessary. On the other hand, if the content exceeds 2.00%, the toughness is remarkably deteriorated and the wearability is also deteriorated, so the upper limit is made 2.00% or less. Furthermore, considering refining costs, hot workability, and pickling properties, 0.40% or more and 1.20% or less are desirable.
Ｍｏは、耐食性を向上させるため必要に応じて０．０５％以上含有する。一方、１．００％超含有すると、本実施形態の鋼板を用いたその後の熱処理（焼き入れ）時に所定のマルテンサイト組織が得られない場合が生じるため上限を１．００％とする。一方、過度に含有させるとコスト高になるため上限を１．００％以下とする。更に、合金コストや製造性を考慮すると、０．１０％以上、０．５０％以下が望ましい。 Mo is contained in an amount of 0.05% or more as necessary in order to improve the corrosion resistance. On the other hand, if the content exceeds 1.00%, a predetermined martensite structure may not be obtained during subsequent heat treatment (quenching) using the steel sheet of the present embodiment, so the upper limit is made 1.00%. On the other hand, if it is excessively contained, the cost increases, so the upper limit is made 1.00% or less. Furthermore, if alloy costs and manufacturability are taken into consideration, 0.10% or more and 0.50% or less are desirable.
ＷはＭｏと同様に耐食性を向上させるため必要に応じて０．０５％以上含有する。一方、１．００％超含有すると、本実施形態の鋼板を用いたその後の熱処理（焼き入れ）時に所定のマルテンサイト組織が得られない場合が生じるため上限を１．００％以下とする。一方、過度に含有させるとコスト高になるため上限を１．００％以下とする。更に、合金コストや製造性を考慮すると、０．１０％以上、０．５０％以下が望ましい。 W is contained in an amount of 0.05% or more as necessary in order to improve the corrosion resistance like Mo. On the other hand, if the content exceeds 1.00%, a predetermined martensite structure may not be obtained during subsequent heat treatment (quenching) using the steel plate of the present embodiment, so the upper limit is made 1.00% or less. On the other hand, if it is excessively contained, the cost increases, so the upper limit is made 1.00% or less. Furthermore, if alloy costs and manufacturability are taken into consideration, 0.10% or more and 0.50% or less are desirable.
Ｔｉ、Ｎｂ、Ｚｒは、ＣやＮと結合して炭窒化物を形成して耐摩耗性を向上させるため、必要に応じて０．００５％以上含有する。一方、０．４０％超含有すると炭窒化物が過度に粗大化して摩耗時に炭窒化物の脱落が生じて鳴きの原因になることから上限を０．４０％以下とする。また、耐食性、鋼板製造性、表面疵の観点から０．０５％以上、０．２０％以下が望ましい。 Ti, Nb, and Zr are combined with C and N to form a carbonitride to improve wear resistance, so 0.005% or more is contained as necessary. On the other hand, if the content exceeds 0.40%, the carbonitrides become excessively coarse and the carbonitrides fall off during wear, causing squealing, so the upper limit is made 0.40% or less. Moreover, 0.05% or more and 0.20% or less are desirable from a viewpoint of corrosion resistance, steel plate manufacturability, and surface flaws.
Ｃｏは、靭性を向上させる元素であるため必要に応じて０．００５％以上含有する。一方、過度な含有はコスト高になるため上限を０．４００％以下とする。また、精錬コストや製造性を考慮すると、０．０１０％以上、０．１００％以下が望ましい。 Co is an element that improves toughness, so 0.005% or more is contained as necessary. On the other hand, the excessive content increases the cost, so the upper limit is made 0.400% or less. In consideration of refining costs and manufacturability, it is preferably 0.010% or more and 0.100% or less.
ＳｎやＳｂは、耐食性を向上させる元素であり、必要に応じて０．００５％以上含有する。Ｓｎ、Ｓｂともに各含有量が０．００５％未満では、耐食性の向上効果が無い。一方、Ｓｎ、Ｓｂを過度に含有すると、その効果は飽和するため、Ｓｎは０．４０％以下、Ｓｂは０．５０％以下とする。但し、熱間加工性や溶接性を考慮すると、ともに、０．０１％以上、０．２０％以下が望ましい。 Sn and Sb are elements that improve the corrosion resistance, and are contained in an amount of 0.005% or more as necessary. If the contents of both Sn and Sb are less than 0.005%, there is no effect of improving the corrosion resistance. On the other hand, when Sn and Sb are contained excessively, the effect is saturated, so Sn is 0.40% or less and Sb is 0.50% or less. However, in consideration of hot workability and weldability, both 0.01% or more and 0.20% or less are desirable.
ＲＥＭは、種々の析出物の微細化による靭性向上や耐酸化性の向上の観点から必要に応じて含有される場合があり、この効果は０．００１％以上で発現することから下限を０．００１％以上とする。しかしながら、０．０５０％超含有すると鋳造性が著しく悪くなることから上限を０．０５０％以下とする。更に、精錬コストや製造性を考慮すると、０．０１０％以下が望ましい。ＲＥＭ（希土類元素）は、一般的な定義に従い、スカンジウム （Ｓｃ）、イットリウム （Ｙ）の２元素と、ランタン（Ｌａ）からルテチウム（Ｌｕ） までの１５元素（ランタノイド）の総称を指す。単独で添加してもよいし、混合物であってもよい。 REM may be contained as required from the viewpoint of improving toughness and oxidation resistance by refining various precipitates, and this effect is manifested at 0.001% or more, so the lower limit is set to 0.00. 001% or more. However, if the content exceeds 0.050%, the castability deteriorates remarkably, so the upper limit is made 0.050% or less. Furthermore, considering refining cost and manufacturability, 0.010% or less is desirable. REM (rare earth element) refers to a generic name of two elements of scandium (Sc) and yttrium (Y) and 15 elements (lanthanoid) from lanthanum (La) to lutetium (Lu) according to a general definition. It may be added alone or as a mixture.
Ｍｇは、脱酸剤として活用する他、溶接部および鋳造組織の組織微細化に有効な元素であるため、必要に応じて０．０００２％以上含有する。０．０００２％未満では、溶接部および鋳造組織の組織微細化に対し効果がない。一方、０．０１００％超では、その効果は飽和するとともに、介在物の粗大化に起因して耐摩耗性が劣化する原因になるため、上限を０．０１００％以下とする。但し、製造性を考慮すると、０．００２０％以下が望ましい。 Mg is used as a deoxidizing agent and is an element effective for refining the welded portion and the cast structure, and therefore is contained in an amount of 0.0002% or more as necessary. If it is less than 0.0002%, there is no effect on the refinement of the welded portion and the cast structure. On the other hand, if it exceeds 0.0100%, the effect is saturated and wear resistance deteriorates due to the coarsening of inclusions, so the upper limit is made 0.0100% or less. However, considering productivity, 0.0020% or less is desirable.
Ｃａは、Ｓと結合して熱間加工性を向上させるため必要に応じて０．０００２％以上含有する。０．０００２％未満では、熱間加工性に対し効果がない。一方、０．０１００％超で、その効果は飽和するするとともに、介在物の粗大化に起因して耐摩耗性が劣化する原因になるため、上限を０．０１００％以下とする。但し、耐食性を考慮すると、０．００１０％以下が望ましい。 Ca is contained in an amount of 0.0002% or more as necessary in order to combine with S to improve hot workability. If it is less than 0.0002%, there is no effect on hot workability. On the other hand, if it exceeds 0.0100%, the effect is saturated and wear resistance is deteriorated due to the coarsening of inclusions, so the upper limit is made 0.0100% or less. However, considering corrosion resistance, 0.0010% or less is desirable.
ＴａおよびＨｆは、ＴｉやＮｂと類似の作用があるとともに耐酸化性を向上させる元素であり、必要に応じて０．００５％以上含有する。０．００５％未満では、溶接部および鋳造組織の組織微細化に対し効果が無く、耐酸化性の効果を発現しない。一方、０．３０００％超で、その効果は飽和するとともに、各窒化物や炭化物が粗大に生成し、耐摩耗性が劣化する原因になるため、Ｔａ、Ｈｆともに上限を０．３０００％以下とする。但し、合金コストや靭性を考慮すると、０．１５００％以下が望ましい。 Ta and Hf are elements that have similar effects to Ti and Nb and improve oxidation resistance, and are contained in an amount of 0.005% or more as necessary. If it is less than 0.005%, there is no effect on the refinement of the welded part and the cast structure, and no effect of oxidation resistance is exhibited. On the other hand, if it exceeds 0.3000%, the effect is saturated and each nitride or carbide is coarsely formed, causing wear resistance to deteriorate. Therefore, the upper limit for both Ta and Hf is 0.3000% or less. To do. However, considering the alloy cost and toughness, 0.1500% or less is desirable.
Ｇａは、耐食性向上や水素脆化抑制のため、０．１０００％以下の範囲で含有してもよい。硫化物や水素化物形成の観点から下限は０．０００２％以上とする。さらに、製造性やコストの観点ならびに、延性や靭性の観点から０．００２０％以下が好ましい。 Ga may be contained within a range of 0.1000% or less in order to improve corrosion resistance and suppress hydrogen embrittlement. From the viewpoint of sulfide or hydride formation, the lower limit is made 0.0002% or more. Furthermore, 0.0020% or less is preferable from the viewpoints of manufacturability and cost and from the viewpoints of ductility and toughness.
その他の成分について本発明では特に規定するものではないが、本発明においては、Ｂｉ等を必要に応じて、０．００１〜０．１％添加してもよい。なお、Ａｓ、Ｐｂ等の一般的な有害な元素や不純物元素はできるだけ低減することが好ましい。 Although it does not prescribe | regulate especially in this invention about another component, in this invention, you may add 0.001 to 0.1% of Bi etc. as needed. Note that it is preferable to reduce general harmful elements and impurity elements such as As and Pb as much as possible.
本実施形態に係るステンレス鋼板は、上述してきた元素以外は、Ｆｅ及び不純物（不可避的不純物を含む）からなるが、以上説明した各元素の他にも、本発明の効果を損なわない範囲で含有させることができる。一般的な不純物元素である前述のＰ、Ｓを始め、Ｂｉ、Ｓｅ等は可能な限り低減することが好ましい。一方、これらの元素は、本発明の課題を解決する限度において、その含有割合が制御され、必要に応じて、Ｂｉ≦１００ｐｐｍ、Ｓｅ≦１００ｐｐｍの１種以上を含有してもよい。 The stainless steel plate according to the present embodiment is composed of Fe and impurities (including unavoidable impurities) except for the elements described above, but contains the elements other than the elements described above within a range not impairing the effects of the present invention. Can be made. It is preferable to reduce as much as possible Bi, Se, etc. as well as the aforementioned P and S, which are general impurity elements. On the other hand, the content ratio of these elements is controlled to the extent that the problem of the present invention is solved, and may include one or more of Bi ≦ 100 ppm and Se ≦ 100 ppm as necessary.
本実施形態のステンレス鋼板の金属組織はフェライト単相組織よりなる。これはオーステナイト相やマルテンサイト組織を含まないことを意味している。オーステナイト相やマルテンサイト組織を含む場合は、原料コストが高くなることに加えて、製造時に耳割れ等の歩留まり低下が起こりやすくなるため、金属組織はフェライト単相組織とする。 The metal structure of the stainless steel plate of the present embodiment is a ferrite single phase structure. This means that an austenite phase and a martensite structure are not included. When an austenite phase or a martensite structure is included, in addition to an increase in raw material cost, a yield reduction such as an ear crack is likely to occur at the time of manufacture, so the metal structure is a ferrite single phase structure.
次に、本実施形態における炭窒化物の生成量および形態について説明する。 Next, the production amount and form of carbonitrides in this embodiment will be described.
本実施形態のステンレス鋼板では、母相であるフェライト相中に炭窒化物が生成する。本実施形態での炭窒化物とは主にＣｒと炭素、窒素の化合物であるが、ＶやＡｌ等の他元素で構成される場合もある。この炭窒化物は母相のフェライト相よりも硬質であることから、本実施形態ではこれを活用して耐摩耗性を向上させる。 In the stainless steel plate of this embodiment, carbonitrides are generated in the ferrite phase that is the parent phase. The carbonitride in the present embodiment is mainly a compound of Cr, carbon, and nitrogen, but may be composed of other elements such as V and Al. Since this carbonitride is harder than the ferrite phase of the parent phase, this embodiment is utilized to improve wear resistance.
図１に、炭窒化物の数密度と耐摩耗性（摩耗率）の関係を示す。ここで耐摩耗性の評価には、ピンオンディスク型摩耗試験機を用い、ステンレス鋼板をディスクとし、ピンをロースチールパッドとして無潤滑大気中で行った。ピン試験片は回転面に垂直に荷重５０Ｎ一定で押し付け、すべり速度０．１〜３ｍ／ｓで変化させてすべり距離が２０００ｍに達するまで試験を行った。摩耗重量を体積に換算し、摩耗率（単位距離当たりの摩耗体積；ｍ３／ｍ）を得た。図１に示す試験結果において、用いたステンレス鋼板の鋼成分は０．０３５％Ｃ−０．３０％Ｓｉ−１．１０％Ｍｎ−０．０２３％Ｐ−０．００３％Ｓ−１１．５％Ｃｒ−０．０２％Ｃｕ−０．００５％Ａｌ−０．０４４％Ｎ−０．００１％Ｂであり、熱間圧延後に種々の熱処理条件で焼鈍することによって炭窒化物の生成状態を変化させている。得られたこれらの焼鈍板から抽出レプリカ法によって炭窒化物を抽出し、透過型電子顕微鏡で炭窒化物を観察した。なお、炭窒化物の組成についてはＥＤＳ分析で同定できる。
その後、画像解析処理によって炭窒化物のサイズを円相当換算した。対象とする炭窒化物のサイズは円相当径で０．３μｍ以上とする。これは、微細な炭窒化物は耐摩耗性に及ぼす影響が小さいためである。炭窒化物の個数については、１４μｍ×２０μｍの視野を１０箇所測定し、１００μｍ2当たりの炭窒化物の個数に換算して摩耗率との関係を調べた。
FIG. 1 shows the relationship between the number density of carbonitrides and the wear resistance (wear rate). Here, the wear resistance was evaluated using a pin-on-disk type abrasion tester in a non-lubricated atmosphere using a stainless steel plate as a disk and a pin as a low steel pad. The pin test piece was pressed perpendicularly to the rotating surface at a constant load of 50 N and changed at a sliding speed of 0.1 to 3 m / s until the sliding distance reached 2000 m. Converts the wear weight volume wear rate; was obtained (abrasion volume per unit length m 3 / m). In the test results shown in FIG. 1, the steel components of the stainless steel plate used were 0.035% C-0.30% Si-1.10% Mn-0.023% P-0.003% S-11.5%. Cr-0.02% Cu-0.005% Al-0.044% N-0.001% B, which changes the production state of carbonitride by annealing under various heat treatment conditions after hot rolling. ing. Carbonitrides were extracted from these obtained annealed plates by the extraction replica method, and the carbonitrides were observed with a transmission electron microscope. The carbonitride composition can be identified by EDS analysis.
Thereafter, the size of carbonitride was converted into a circle equivalent by image analysis processing. The target carbonitride size is 0.3 μm or more in terms of equivalent circle diameter. This is because fine carbonitride has a small effect on wear resistance. Regarding the number of carbonitrides, 10 fields of view of 14 μm × 20 μm were measured and converted into the number of carbonitrides per 100 μm 2 to examine the relationship with the wear rate.
図１の調査結果からも明らかなように、円相当の直径で０．３μｍ以上の炭窒化物が１０個／１００μｍ2以上の場合に耐摩耗性が向上することがわかる。ここで一般的な鋳鉄材の摩耗率が１×１０-11ｍ３／ｍであることからこの値以下を目標値とした。一方、炭窒化物の数密度が５０個／１００μｍ2になると摩耗性の効果が飽和するとともに、摩耗時の炭窒化物の脱落による鳴きが課題になるため上限を５０個／１００μｍ2以下とする。更に、鋼靭性を考慮すると炭窒化物の数密度は３０個／１００μｍ2以下が望ましい。
As is clear from the investigation results in FIG. 1, it can be seen that the wear resistance is improved when the number of carbonitrides having a diameter corresponding to a circle of 0.3 μm or more is 10/100 μm 2 or more. Here, since the wear rate of a general cast iron material is 1 × 10 −11 m 3 / m, this value or less was set as a target value. On the other hand, carbonitride the number density with fifty / 100 [mu] m between the wear resistance becomes 2 effect saturates, squeal by dropping of carbonitride during wear the
次に、本実施形態のステンレス鋼板の製造方法は特に規定するものではなく、ステンレス鋼板の汎用的な製造工程で製造すればよい。具体的には、製鋼−熱間圧延−焼鈍−酸洗の各工程よりなる。必要に応じて、適宜、研磨や酸浸漬によるデスケーリングを行ってよい。なお、炭窒化物の析出量を制御し、数密度を上記範囲内とするためには、熱延板焼鈍条件を下記のように制御するとよい。 Next, the manufacturing method of the stainless steel plate of the present embodiment is not particularly specified, and may be manufactured by a general manufacturing process of the stainless steel plate. Specifically, it consists of each process of steelmaking-hot rolling-annealing-pickling. As needed, you may perform descaling by grinding | polishing or acid immersion suitably. In addition, in order to control the precipitation amount of carbonitride and make a number density into the said range, it is good to control hot-rolled sheet annealing conditions as follows.
まず、製鋼においては、上記の成分を含有する鋼を、転炉あるいは電炉溶製し、続いて２次精錬を行う方法が好適である。溶製した溶鋼は、公知の鋳造方法（連続鋳造）に従ってスラブとする。スラブは、所定の温度に加熱され、所定の板厚に連続圧延で熱間圧延される。熱間圧延は複数スタンドから成る熱間圧延機で圧延された後に巻き取られる。 First, in steelmaking, a method in which steel containing the above-described components is made into a converter or an electric furnace and subsequently subjected to secondary refining is preferable. The molten steel is made into a slab according to a known casting method (continuous casting). The slab is heated to a predetermined temperature and hot-rolled to a predetermined plate thickness by continuous rolling. Hot rolling is rolled up after being rolled by a hot rolling mill comprising a plurality of stands.
熱間圧延後は、熱延板焼鈍を施すが、連続焼鈍でもバッチ式焼鈍でも構わない。炭窒化物を所定量均一析出させ、上記範囲内の数密度とするためには、バッチ式焼鈍の方がよい。更に、靭性の観点から熱延板焼鈍の条件としては８００℃以上で１時間超の加熱とし、その後の冷却工程では、４００℃までの平均冷却速度を１℃／ｓｅｃ以下とすることが望ましく、０．１℃／ｓｅｃ以下がより望ましい。なお、平均冷却速度とは、冷却開始時から４００℃までの鋼板の温度降下幅を、冷却開始時から４００℃までの所要時間で除した値とする。 After hot rolling, hot-rolled sheet annealing is performed, but continuous annealing or batch annealing may be performed. In order to uniformly precipitate a predetermined amount of carbonitride and obtain a number density within the above range, batch annealing is better. Furthermore, from the viewpoint of toughness, as a condition for hot-rolled sheet annealing, it is preferable to heat at 800 ° C. or more for more than 1 hour, and in the subsequent cooling step, the average cooling rate to 400 ° C. is desirably 1 ° C./sec or less, More preferably, it is 0.1 ° C./sec or less. The average cooling rate is a value obtained by dividing the temperature drop width of the steel sheet from the start of cooling to 400 ° C. by the required time from the start of cooling to 400 ° C.
熱延焼鈍後の酸洗工程ではショットブラストやベンディング等のメカニカルデスケールの後、硫酸、硝弗酸等に漬浸して酸化スケールを除去する。なお、部品製造工程で表面を研削する場合は、当該酸洗工程を省略しても構わない。また、メカニカルデスケールのみの処理としても構わない。 In the pickling process after hot rolling annealing, after mechanical descale such as shot blasting or bending, the oxide scale is removed by dipping in sulfuric acid, nitric hydrofluoric acid or the like. In addition, when the surface is ground in the component manufacturing process, the pickling process may be omitted. Moreover, it does not matter as a process only of mechanical descale.
更に、酸洗処理後に、板厚やその精度を考慮して冷間圧延を付与し焼鈍・酸洗処理することも可能である。この他、形状調整のために調質圧延やテンションレベラーを付与しても構わない。なお、最終鋼板（製品）の板厚については、要求される部材厚に応じて選択すればよいが、例えば、１．０〜１０．０ｍｍとすることができる。 Further, after the pickling treatment, it is possible to perform cold rolling and annealing / pickling treatment in consideration of the plate thickness and its accuracy. In addition, temper rolling or tension leveler may be applied for shape adjustment. In addition, about the plate | board thickness of a final steel plate (product), what is necessary is just to select according to the member thickness requested | required, For example, it can be set as 1.0-10.0 mm.
以上説明した製造方法により、本実施形態に係るステンレス鋼板を得ることができる。なお、ディスクブレーキ等の制動系部品の製造段階において、８００℃程度に加熱して焼き入れする熱処理が行われる場合があるが、その場合でも、本実施形態と同様の炭窒化物の数密度および摩耗性は満足できる。すなわち、制動系部品の製造段階でホットプレスによる成形（温間成形等）、あるいは冷間プレス後の焼き入れ処理を施しても本発明の効果を享受でき、さらに言えば、上記の焼鈍条件を、当該ホットプレスによる成形（温間成形等）や冷間プレス後の焼き入れ処理に適用するとなお望ましい。 The stainless steel plate according to the present embodiment can be obtained by the manufacturing method described above. In addition, in the manufacturing stage of a brake system component such as a disc brake, there is a case where a heat treatment is performed by heating to about 800 ° C. and quenching, but even in this case, the number density and wearability of the carbonitride similar to this embodiment Can be satisfied. In other words, the effects of the present invention can be enjoyed even when hot press molding (warm molding or the like) or quenching after cold pressing is performed at the manufacturing stage of the brake system parts. Further, it is more preferable to apply to molding by hot press (warm molding or the like) or quenching after cold pressing.
本実施形態によれば、二輪車や自動車の制動系部品にステンレス鋼板を適用するに際して課題であった摩耗性を大幅に改善できるため、制動性部品に本実施形態のステンレス鋼板を適用することにより、鋳鉄に比べて耐食性に優れかつ耐摩耗性の向上が可能となる。特に、自動車に対しては、鋳鉄の代替として本実施形態のステンレス鋼板を適用することによって薄肉軽量化の効果も得られる他、二輪車、航空、鉄道車両等の制動系も対象となる。 According to this embodiment, since it is possible to greatly improve the wear that was a problem when applying a stainless steel plate to the braking system parts of motorcycles and automobiles, by applying the stainless steel plate of this embodiment to the braking parts, Compared to cast iron, it has excellent corrosion resistance and can improve wear resistance. In particular, for automobiles, the effect of reducing the thickness and weight can be obtained by applying the stainless steel plate of the present embodiment as an alternative to cast iron, and braking systems such as motorcycles, aviation, and railway vehicles are also targeted.
次に本発明の実施例を示すが、実施例での条件は、本発明の実施可能性及び効果を確認するために採用した一条件例であり、本発明は、以下の実施例で用いた条件に限定されるものではない。本発明は、本発明の要旨を逸脱せず、本発明の目的を達成する限りにおいて、種々の条件を採用し得るものである。
なお、下記にて示す表中の下線は、本発明の範囲から外れているものを示す。
Next, examples of the present invention will be described. The conditions in the examples are one example of conditions used to confirm the feasibility and effects of the present invention, and the present invention was used in the following examples. It is not limited to the conditions. The present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.
In addition, the underline in the table | surface shown below shows what has remove | deviated from the scope of the present invention.
（実施例１）
表１に示す成分組成のフェライト系ステンレス鋼を溶製し、熱間圧延して４ｍｍ厚の熱延板とした後、熱延板焼鈍および酸洗を行った。この際の熱延板焼鈍はバッチ式焼鈍とし、加熱温度は８００℃、保持温度は４時間、４００℃までの平均冷却速度は０．１℃／ｓｅｃとした。
Example 1
A ferritic stainless steel having the component composition shown in Table 1 was melted and hot-rolled to form a hot-rolled sheet having a thickness of 4 mm, followed by hot-rolled sheet annealing and pickling. The hot-rolled sheet annealing at this time was batch annealing, the heating temperature was 800 ° C., the holding temperature was 4 hours, and the average cooling rate to 400 ° C. was 0.1 ° C./sec.
このようにして得られた熱延焼鈍板（試験Ｎｏ，１〜２７）から、上述した方法で摩耗試験および炭窒化物の観察・測定を行った。 From the thus obtained hot-rolled annealed plates (test Nos. 1 to 27), the wear test and the observation and measurement of carbonitrides were performed by the above-described methods.
＜摩耗試験＞
摩耗試験については上記記載の方法で摩耗試験を行った。
ピンオンディスク型摩耗試験機を用い、ステンレス鋼板をディスクとし、ピンをロースチールパッドとして無潤滑大気中で行った。ピン試験片は回転面に垂直に荷重５０Ｎ一定で押し付け、すべり速度０．１〜３ｍ／ｓで変化させてすべり距離が２０００ｍに達するまで試験を行った。摩耗重量を体積に換算し、摩耗率（単位距離当たりの摩耗体積；ｍ３／ｍ）を得た。摩耗率が１×１０-11ｍ３／ｍ以下の場合を合格（○）、摩耗率が１×１０-11ｍ３／ｍを超える場合を不合格（×）とした。
<Abrasion test>
As for the abrasion test, the abrasion test was performed by the method described above.
Using a pin-on-disk wear tester, the test was performed in a non-lubricated atmosphere using a stainless steel plate as a disk and a pin as a low steel pad. The pin test piece was pressed perpendicularly to the rotating surface at a constant load of 50 N and changed at a sliding speed of 0.1 to 3 m / s until the sliding distance reached 2000 m. The wear weight was converted into a volume to obtain a wear rate (wear volume per unit distance; m 3 / m). The case where the wear rate was 1 × 10 −11 m 3 / m or less was determined to be acceptable (◯), and the case where the wear rate exceeded 1 × 10 −11 m 3 / m was determined to be unacceptable (×).
＜炭窒化物の数密度＞
得られた熱延焼鈍板（試験Ｎｏ，１〜２７）から抽出レプリカ法によって炭窒化物を抽出し、透過型電子顕微鏡で炭窒化物を観察した。その後、画像解析処理によって炭窒化物のサイズを円相当換算した。炭窒化物の個数については、１４μｍ×２０μｍの視野を１０箇所測定し、１００μｍ2当たりの炭窒化物（円相当径で０．３μｍ以上）の個数に換算した。
<Number density of carbonitride>
Carbonitrides were extracted from the obtained hot-rolled annealed plates (Test Nos. 1-27) by the extraction replica method, and the carbonitrides were observed with a transmission electron microscope. Thereafter, the size of carbonitride was converted into a circle equivalent by image analysis processing. Regarding the number of carbonitrides, 10 fields of view of 14 μm × 20 μm were measured and converted to the number of carbonitrides (equivalent circle diameter of 0.3 μm or more) per 100 μm 2 .
＜鳴き＞
加えて、試験中に鳴きの発生有無についても調べた。具体的には、上記のピンオンディスク型摩耗試験機を用いて摩耗試験を行った際に、ノイズを測定し、１ｋＨｚのノイズが発生した場合を鳴き発生とした。
<Sound>
In addition, the occurrence of squeaking during the test was also examined. Specifically, when a wear test was performed using the above-described pin-on-disk type wear tester, noise was measured, and a case where noise of 1 kHz was generated was regarded as occurrence of squeal.
＜靭性＞
加えて、ディスクブレーキ素材には靭性も要求されることからシャルピー衝撃試験によって靭性を評価した。具体的には、熱延鋼板から、試験片の長手方向が圧延方向と平行かつ直角になるようにＶノッチ試験片を採取し、この試験片に対して室温にてシャルピー衝撃試験（（ＪＩＳ Ｚ ２２４２）を行い、脆性破壊の有無を調べた。脆性破壊（脆性破面率が５０％以上）したものを不合格（×）、延性破壊（脆性破面率が５０％未満）したものを合格（○）とした。
<Toughness>
In addition, the toughness was evaluated by the Charpy impact test because the disc brake material also requires toughness. Specifically, a V-notch test piece was sampled from a hot-rolled steel sheet so that the longitudinal direction of the test piece was parallel to and perpendicular to the rolling direction, and Charpy impact test ((JIS Z 2242), and examined the presence or absence of brittle fracture: rejected brittle fracture (brittle
＜耐食性＞
更に、上記摩耗試験後の耐食性の評価を行い、発錆が生じない場合を合格（○）、発錆が生じた場合を不合格（×）とした。ここで耐食性の試験としては、ＪＩＳ Ｚ ２３７１に準拠したＳＳＴ試験を２４時間行い、目視で発錆の有無を確認した。
<Corrosion resistance>
Further, the corrosion resistance after the wear test was evaluated, and the case where rusting did not occur was judged as acceptable (◯), and the case where rusting occurred was considered as unacceptable (x). Here, as a corrosion resistance test, an SST test based on JIS Z 2371 was performed for 24 hours, and the presence or absence of rusting was visually confirmed.
以上の試験結果、炭窒化物の数密度の調査の結果を表２に示す。本発明例の鋼板（試験Ｎｏ．１〜１１）は摩耗特性に優れており、鳴きの発生についても満足する。本発明例の鋼板（試験Ｎｏ．１〜１１）はいずれも、靭性、耐食性に優れていることがわかる。また、表には記載していないが、本発明例の鋼板を用いたディスクブレーキの製造段階において、８００℃に加熱して焼き入れた場合においても同様の炭窒化物の数密度および各特性を満足することがわかった。このことから、ディスクブレーキ等の制動系部品の製造段階でホットプレスによる成形（温間成形等）、あるいは冷間プレス後の焼き入れ処理を施してもよいことが分かる。 Table 2 shows the above test results and the results of the investigation of the number density of carbonitrides. The steel plates of the present invention (Test Nos. 1 to 11) are excellent in wear characteristics and satisfy the occurrence of squeal. It turns out that all the steel plates (test Nos. 1 to 11) of the examples of the present invention are excellent in toughness and corrosion resistance. Further, although not shown in the table, the same number density and various characteristics of carbonitride are satisfied even when heated to 800 ° C. and hardened in the manufacturing stage of the disc brake using the steel plate of the present invention. I understood it. From this, it is understood that hot press molding (warm molding or the like) or quenching after cold pressing may be performed in the manufacturing stage of braking system parts such as disc brakes.
（実施例２）
次に、表３に表１に示した本発明鋼の鋼Ｎｏ．１とＮｏ．２を用いて熱延焼鈍条件を変更した際の結果を示す。なお、表３に示す試験Ｎｏ．２８〜３５はいずれも、熱延焼鈍以外の製造条件は実施例１と同様とした。表３に示すとおり、熱延焼鈍条件が望ましい範囲から外れる場合には炭窒化物の生成量（数密度）が減少し、耐摩耗性、靭性および鳴き特性が劣化することがわかる。
(Example 2)
Next, Table 3 shows the steel No. of the steel of the present invention shown in Table 1. 1 and No. The result at the time of changing hot-rolling annealing conditions using 2 is shown. In addition, test No. shown in Table 3 28 to 35 were the same as in Example 1 except for hot rolling annealing. As shown in Table 3, it can be seen that when the hot rolling annealing condition deviates from the desired range, the amount of carbonitride produced (number density) decreases, and the wear resistance, toughness and squeal characteristics deteriorate.
本発明によれば、耐摩耗性とともにディスクブレーキに適用した場合の鳴き発生を抑制し、耐食性にも優れたステンレス鋼板を提供することが可能である。特に、自動車、二輪、鉄道車両などの制動系部品として使用することによって、薄肉軽量化や複雑構造の成形品に展開することが可能であることから産業上極めて有益である。 ADVANTAGE OF THE INVENTION According to this invention, it is possible to provide the stainless steel plate which suppressed generation | occurrence | production of the squeal when it applies to a disc brake with wear resistance, and was excellent also in corrosion resistance. In particular, it can be used as a braking system component for automobiles, motorcycles, railway vehicles, and the like, and thus can be developed into a molded product having a thin wall and light weight and a complicated structure.
［１］質量％で、
Ｃ ：０．００５〜０．１００％、
Ｓｉ：０．０１〜１．００％、
Ｍｎ：０．０１０〜３．００％、
Ｐ ：０．０４０％以下、
Ｓ ：０．０１００％以下、
Ｃｒ：１０．０〜１４．０％、
Ｎ ：０．００５〜０．１００％、
Ｖ ：０．０３〜０．３０％、
Ａｌ：０．００１〜０．０５０％、
Ｂ ：０．０００２〜０．００５０％、
Ｎｉ：０〜２．００％、
Ｃｕ：０〜２．００％、
Ｍｏ：０〜１．００％、
Ｗ ：０〜１．００％、
Ｔｉ：０〜０．４０％、
Ｎｂ：０〜０．４０％、
Ｚｒ：０〜０．４０％、
Ｃｏ：０〜０．４００％、
Ｓｎ：０〜０．４０％、
ＲＥＭ：０〜０．０５０％以下、
Ｍｇ：０〜０．０１００％、
Ｃａ：０〜０．０１００％、
Ｓｂ：０〜０．５０％、
Ｔａ：０〜０．３０００％、
Ｈｆ：０〜０．３０００％、
Ｇａ：０〜０．１０００％を含有し、残部がＦｅ及び不純物からなり、
金属組織がフェライト相からなり、円相当の直径で０．３μｍ以上の炭窒化物が任意断面において１０〜５０個／１００μｍ2存在し、
制動系部品に適用されることを特徴とするステンレス鋼板。
［２］ 質量％で、
Ｃ ：０．００５〜０．１００％、
Ｓｉ：０．０１〜１．００％、
Ｍｎ：０．０１０〜３．００％、
Ｐ ：０．０４０％以下、
Ｓ ：０．０１００％以下、
Ｃｒ：１０．０〜１４．０％、
Ｎ ：０．００５〜０．１００％、
Ｖ ：０．０３〜０．３０％、
Ａｌ：０．００１〜０．０５０％、
Ｂ ：０．０００２〜０．００５０％、
Ｎｉ：０〜２．００％、
Ｃｕ：０〜２．００％、
Ｍｏ：０〜１．００％、
Ｗ ：０〜１．００％、
Ｔｉ：０〜０．４０％、
Ｎｂ：０〜０．４０％、
Ｚｒ：０〜０．４０％、
Ｃｏ：０〜０．４００％、
Ｓｎ：０〜０．４０％、
ＲＥＭ：０〜０．０５０％以下、
Ｍｇ：０〜０．０１００％、
Ｃａ：０〜０．０１００％、
Ｓｂ：０〜０．５０％、
Ｔａ：０〜０．３０００％、
Ｈｆ：０〜０．３０００％、
Ｇａ：０〜０．１０００％を含有し、残部がＦｅ及び不純物からなり、
金属組織がフェライト相からなり、円相当の直径で０．３μｍ以上の炭窒化物が任意断面において１０〜５０個／１００μｍ 2 存在し、
ブレーキディスクロータに適用されることを特徴とするステンレス鋼板。
［３］質量％で、Ｎｉ：０．０５〜２．００％、Ｃｕ：０．０５〜２．００％、Ｍｏ：０．０５〜１．００％、Ｗ：０．０５〜１．００％、Ｔｉ：０．００５〜０．４０％、Ｎｂ：０．００５〜０．４０％、Ｚｒ：０．００５〜０．４０％、Ｃｏ：０．００５〜０．４００％、Ｓｎ：０．００５〜０．４０％、ＲＥＭ：０．００１〜０．０５０％以下、Ｍｇ：０．０００２〜０．０１００％、Ｃａ：０．０００２〜０．０１００％、Ｓｂ：０．０５〜０．５０％、Ｔａ：０．００５０〜０．３０００％、Ｈｆ：０．００５０〜０．３０００％、Ｇａ：０．０００２〜０．１０００％の１種または２種以上含有することを特徴とする上記［１］または上記［２］に記載のステンレス鋼板。
［４］上記［１］乃至上記［３］の何れか一項に記載のステンレス鋼板を用いた制動系部品。
[1] By mass%
C: 0.005 to 0.100%,
Si: 0.01 to 1.00%,
Mn: 0.010 to 3.00%,
P: 0.040% or less,
S: 0.0100% or less,
Cr: 10.0-14.0%,
N: 0.005 to 0.100%,
V: 0.03-0.30%,
Al: 0.001 to 0.050%,
B: 0.0002 to 0.0050%,
Ni: 0 to 2.00%,
Cu: 0 to 2.00%,
Mo: 0 to 1.00%,
W: 0 to 1.00%,
Ti: 0 to 0.40%,
Nb: 0 to 0.40%
Zr: 0 to 0.40%,
Co: 0 to 0.400%,
Sn: 0 to 0.40%,
REM: 0 to 0.050% or less,
Mg: 0 to 0.0100%,
Ca: 0 to 0.0100%,
Sb: 0 to 0.50%,
Ta: 0 to 0.3000%,
Hf: 0 to 0.3000%,
Ga: 0 to 0.1000% is contained, the balance consists of Fe and impurities,
The metal structure is composed of a ferrite phase, and there are 10-50 pieces / 100 μm 2 of carbonitride having a diameter equivalent to a circle of 0.3 μm or more in an arbitrary cross section ,
Stainless steel sheet characterized by being applied to braking system parts .
[2] By mass%
C : 0.005 to 0.100%,
Si: 0.01 to 1.00%,
Mn: 0.010 to 3.00%,
P: 0.040% or less,
S : 0.0100% or less,
Cr: 10.0-14.0%,
N : 0.005 to 0.100%,
V : 0.03-0.30%,
Al: 0.001 to 0.050%,
B : 0.0002 to 0.0050%,
Ni: 0 to 2.00%,
Cu: 0 to 2.00%,
Mo: 0 to 1.00%,
W : 0 to 1.00%,
Ti: 0 to 0.40%,
Nb: 0 to 0.40%
Zr: 0 to 0.40%,
Co: 0 to 0.400%,
Sn: 0 to 0.40%,
REM: 0 to 0.050% or less,
Mg: 0 to 0.0100%,
Ca: 0 to 0.0100%,
Sb: 0 to 0.50%,
Ta: 0 to 0.3000%,
Hf: 0 to 0.3000%,
Ga: 0 to 0.1000% is contained, the balance consists of Fe and impurities,
The metal structure is composed of a ferrite phase, and there are 10-50 pieces / 100 μm 2 of carbonitride having a diameter equivalent to a circle of 0.3 μm or more in an arbitrary cross section ,
A stainless steel plate characterized by being applied to a brake disc rotor.
[ 3 ] By mass%, Ni: 0.05-2.00%, Cu: 0.05-2.00%, Mo: 0.05-1.00%, W: 0.05-1.00% , Ti: 0.005 to 0.40%, Nb: 0.005 to 0.40%, Zr: 0.005 to 0.40%, Co: 0.005 to 0.400%, Sn: 0.005 To 0.40%, REM: 0.001 to 0.050% or less, Mg: 0.0002 to 0.0100%, Ca: 0.0002 to 0.0100%, Sb: 0.05 to 0.50% , Ta: 0.0050 to 0.3000%, Hf: 0.0050 to 0.3000%, Ga: 0.0002 to 0.1000%, or one or more of the above [1] ] Or the stainless steel plate according to [2] above .
[ 4 ] A braking system component using the stainless steel plate according to any one of [1] to [3] .
Claims (5)
Ｃ ：０．００５〜０．１００％、
Ｓｉ：０．０１〜１．００％、
Ｍｎ：０．０１０〜３．００％、
Ｐ ：０．０４０％以下、
Ｓ ：０．０１００％以下、
Ｃｒ：１０．０〜１４．０％、
Ｎ ：０．００５〜０．１００％、
Ｖ ：０．０３〜０．３０％、
Ａｌ：０．００１〜０．０５０％、
Ｂ ：０．０００２〜０．００５０％、
Ｎｉ：０〜２．００％、
Ｃｕ：０〜２．００％、
Ｍｏ：０〜１．００％、
Ｗ ：０〜１．００％、
Ｔｉ：０〜０．４０％、
Ｎｂ：０〜０．４０％、
Ｚｒ：０〜０．４０％、
Ｃｏ：０〜０．４００％、
Ｓｎ：０〜０．４０％、
ＲＥＭ：０〜０．０５０％以下、
Ｍｇ：０〜０．０１００％、
Ｃａ：０〜０．０１００％、
Ｓｂ：０〜０．５０％、
Ｔａ：０〜０．３０００％、
Ｈｆ：０〜０．３０００％、
Ｇａ：０〜０．１０００％を含有し、残部がＦｅ及び不純物からなり、
金属組織がフェライト相からなり、円相当の直径で０．３μｍ以上の炭窒化物が任意断面において１０〜５０個／１００μｍ2存在することを特徴とするステンレス鋼板。 % By mass
C: 0.005 to 0.100%,
Si: 0.01 to 1.00%,
Mn: 0.010 to 3.00%,
P: 0.040% or less,
S: 0.0100% or less,
Cr: 10.0-14.0%,
N: 0.005 to 0.100%,
V: 0.03-0.30%,
Al: 0.001 to 0.050%,
B: 0.0002 to 0.0050%,
Ni: 0 to 2.00%,
Cu: 0 to 2.00%,
Mo: 0 to 1.00%,
W: 0 to 1.00%,
Ti: 0 to 0.40%,
Nb: 0 to 0.40%
Zr: 0 to 0.40%,
Co: 0 to 0.400%,
Sn: 0 to 0.40%,
REM: 0 to 0.050% or less,
Mg: 0 to 0.0100%,
Ca: 0 to 0.0100%,
Sb: 0 to 0.50%,
Ta: 0 to 0.3000%,
Hf: 0 to 0.3000%,
Ga: 0 to 0.1000% is contained, the balance consists of Fe and impurities,
A stainless steel plate, characterized in that the metal structure is composed of a ferrite phase, and there are 10 to 50/100 μm 2 of carbonitride having an equivalent diameter of 0.3 μm or more in an arbitrary cross section.
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| WO2020195915A1 (en) * | 2019-03-28 | 2020-10-01 | 日鉄ステンレス株式会社 | Ferritic stainless steel sheet for automobile brake disk rotors, automobile brake disk rotor, and hot-stamped article for automobile brake disk rotors |
| WO2021256336A1 (en) | 2020-06-16 | 2021-12-23 | 日清紡ブレーキ株式会社 | Friction pair |
| WO2021256338A1 (en) | 2020-06-16 | 2021-12-23 | 日清紡ブレーキ株式会社 | Friction pair |
| WO2021256337A1 (en) | 2020-06-16 | 2021-12-23 | 日清紡ブレーキ株式会社 | Friction pair |
| WO2022176707A1 (en) * | 2021-02-18 | 2022-08-25 | 日鉄ステンレス株式会社 | Martensitic stainless steel plate for brake disk rotor, brake disk rotor, and method for manufacturing martensitic stainless steel plate for brake disk rotor |
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