JPH04371518A - Production of ferritic stainless steel for electric material having excellent ductility, wear resistance and rust resistance - Google Patents

Production of ferritic stainless steel for electric material having excellent ductility, wear resistance and rust resistance

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Publication number
JPH04371518A
JPH04371518A JP17471091A JP17471091A JPH04371518A JP H04371518 A JPH04371518 A JP H04371518A JP 17471091 A JP17471091 A JP 17471091A JP 17471091 A JP17471091 A JP 17471091A JP H04371518 A JPH04371518 A JP H04371518A
Authority
JP
Japan
Prior art keywords
less
steel
resistance
nitric acid
wear resistance
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
JP17471091A
Other languages
Japanese (ja)
Other versions
JP2583694B2 (en
Inventor
Yoshihiro Yazawa
好弘 矢沢
Motohiko Takeda
竹田 元彦
Tetsuo Kanetani
金谷 哲郎
Sadao Hasuno
貞夫 蓮野
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
Kawasaki Steel Corp
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Filing date
Publication date
Application filed by Kawasaki Steel Corp filed Critical Kawasaki Steel Corp
Priority to JP3174710A priority Critical patent/JP2583694B2/en
Publication of JPH04371518A publication Critical patent/JPH04371518A/en
Application granted granted Critical
Publication of JP2583694B2 publication Critical patent/JP2583694B2/en
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

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Abstract

PURPOSE:To obtain the steel blank material which has corrosion resistance and excellent ductility and wear resistance by subjecting a steel specified in component compsn. to hard ' rolling, then to reheating under specific conditions, followed by nitric acid electrolysis. CONSTITUTION:The compsn. of the steel is specified, by weight %, to 0.12% C, <=1.0% Si, <=1.0% Mn, 15 to 20% Cr, <=1.0% Ni, <=0.3% Al, <=0.003% O, <=0.04% P, <=0.03% S, <=0.1% N, and the balance Fe and unavoidable impurities. This steel is subjected to finish annealing, then to cold rolling at >=10%. The steel is thereafter subjected to reheating for 10 seconds to 10 minutes in a 500 to 750 deg.C range. Further, the scale on the surfaces is removed by executing nitric acid electrolysis. At least one kind of 0.002 to 0.01% B, <=0.01% Ca and <=0.2% REM as hot workability improving elements and at least one kind of respectively <=0.5% V, Nb and Ti as corrosion resistance improving elements are incorporated at need into the above-mentioned steel.

Description

【発明の詳細な説明】[Detailed description of the invention]

【0001】0001

【産業上の利用分野】本発明は、電気材料用素材、特に
磁気記録媒体として使用されるフロッピーディスクセン
ターコア材としての用途に適合する素材としての、フェ
ライト系ステンレス鋼の製造方法に関するものである。
[Field of Industrial Application] The present invention relates to a method for producing ferritic stainless steel, which is suitable for use as a material for electrical materials, particularly as a center core material for floppy disks used as magnetic recording media. .

【0002】0002

【従来の技術】従来、磁気記録媒体として使用されるフ
ロッピーディスクには、読み取り振れを防止する目的で
ディスクの中央部に金属円板状のセンターコアと称する
ディスクが取付けられている。このセンターコア材とし
て必要な特性としては、■マグネットチャッキングに供
するため、強磁性であること、■駆動時の位置を決める
ツメが駆動初期においてセンターコアの表面を擦るため
、耐摩耗性に優れていること(Hv220以上) 、■
図1に示したような形状にセンターコアをプレス成形す
る際、割れ防止のため、素材の伸びが5%以上であるこ
と、■発銹に伴う金属粉が誤動作の原因となるため、S
US 430 並の耐食性を有すること、■二次加工性
に優れていること、などが要求される。また、近頃の趨
勢として、この種の材料は、耐摩耗性, 延性について
の要求が一層厳しくなるとともに、SUS 430 と
同程度もしくはそれ以下の低コストで製造できることが
不可欠である。
2. Description of the Related Art Conventionally, a floppy disk used as a magnetic recording medium has a metal disk-shaped center core attached to the center of the disk for the purpose of preventing reading shake. The properties necessary for this center core material are: ■ It must be ferromagnetic so that it can be used for magnetic chucking; ■ It has excellent wear resistance because the claws that determine the position during driving rub against the surface of the center core in the initial stage of driving. (Hv220 or higher),■
When press forming the center core into the shape shown in Figure 1, to prevent cracking, the elongation of the material must be at least 5%;
It is required to have corrosion resistance comparable to that of US 430, and (1) to have excellent secondary processability. In addition, as a recent trend, this type of material has become more demanding in terms of wear resistance and ductility, and it is essential that it can be manufactured at a cost as low as or lower than that of SUS 430.

【0003】上述のような特性が要求されているセンタ
ーコア材として、従来、SUS 430 に仕上げ冷間
圧延( 以下「ハード圧延」という)を施すことで硬質
にした、いわゆるハード圧延材が用いられてきた。しか
しながら、このハード圧延を施すだけの方法では、目標
水準の硬度を得るためには少なくとも20%以上の仕上
げ圧延を施す必要があり、延性低下に起因した加工時の
割れが問題となっていた。すなわち、SUS 430 
材を単にハード圧延しただけでの素材では、硬さと伸び
という相反する特性を両立させることが困難であり、実
際にこれらの材料を使用する部品メーカーでは、高い不
良率を出して問題となっている。このようなことから、
この種の材料について、延性とともに耐摩耗性にも優れ
た新しい素材の開発が望まれていた。
[0003] Conventionally, so-called hard-rolled materials, which are SUS 430 made hard by finishing cold rolling (hereinafter referred to as "hard rolling"), have been used as center core materials that are required to have the above-mentioned properties. It's here. However, with this method of just performing hard rolling, it is necessary to perform finish rolling of at least 20% or more in order to obtain the target level of hardness, and cracking during processing due to decreased ductility has been a problem. That is, SUS 430
It is difficult to achieve both the contradictory properties of hardness and elongation with materials that are simply hard-rolled, and parts manufacturers that actually use these materials are having problems with high defective rates. There is. From such a thing,
Regarding this type of material, there has been a desire to develop a new material that has excellent ductility and wear resistance.

【0004】このような問題を解決するため、従来、特
開昭64−19570 号公報、特開平1−25914
4号公報等では、SUS 430成分系の鋼のSi, 
Ni添加量を増すことで、合金組成の点から耐摩耗性お
よび延性を改善する試みがなされた。すなわち、Si添
加量の増加で素材そのものの硬度を上げるとともに、S
i添加により低下する靭性をNiを添加することにより
改善しようという考え方である。 しかしながらこの方法では、従来鋼のSUS 430 
に比べ高合金 (特にNi添加) になりコスト高にな
るとともに、仕上げ圧延により目的の硬度を得るために
は、通常のSUS 430 同様、ハード圧延を施す必
要があるため、相変わらず伸びが不足した。
[0004] In order to solve such problems, conventionally, Japanese Patent Application Laid-Open No. 19570/1983 and Japanese Patent Application Laid-open No. 1-25914 have been proposed.
In Publication No. 4 etc., Si of SUS 430 composition steel,
Attempts have been made to improve wear resistance and ductility from the viewpoint of alloy composition by increasing the amount of Ni added. In other words, increasing the amount of Si added increases the hardness of the material itself, and also increases the hardness of the material itself.
The idea is to improve the toughness, which decreases due to the addition of i, by adding Ni. However, with this method, conventional steel SUS 430
Compared to conventional SUS 430, it is a high-alloy material (particularly with the addition of Ni), which makes it more expensive, and in order to obtain the desired hardness through finish rolling, it is necessary to perform hard rolling like normal SUS 430, so it still lacks elongation.

【0005】このことから、延性とともに耐摩耗性にも
優れ、しかも安価なセンターコア材とするために、ハー
ド圧延を施さない方法が、特開昭63−14387 号
公報、特開昭63−169330〜169335号公報
で提案されている。これらの既知技術は、フェライトと
マルテンサイトの複合組織からなる高強度, 高延性ス
テンレス鋼であり、このものは、硬質なマルテンサイト
と軟質なフェライトとの全体の体積に占める割合を適当
に調製することにより、目的の硬度と延性を得ようとし
たものである。しかし、これらの複合組織ステンレス鋼
は、フェライト単相に比べると、たしかに硬質の割りに
延性が富むものにはなっているが、焼入れ焼鈍温度範囲
が狭いためその制御が難しく、しかも高合金化に伴い伸
びが低下し、通常のSUS 430 に比べ高価になる
という問題があった。
[0005] From this, in order to produce a center core material that has excellent ductility and wear resistance and is inexpensive, a method that does not involve hard rolling is disclosed in JP-A-63-14387 and JP-A-63-169330. -169335 are proposed. These known technologies are high-strength, high-ductility stainless steels consisting of a composite structure of ferrite and martensite, which is produced by adjusting the ratio of hard martensite and soft ferrite to the total volume appropriately. By doing so, the objective was to obtain the desired hardness and ductility. However, although these composite structure stainless steels are hard and ductile compared to single-phase ferrite, they are difficult to control due to the narrow quenching and annealing temperature range, and it is difficult to make them highly alloyed. As a result, the elongation is lowered and there is a problem that it is more expensive than ordinary SUS 430.

【0006】[0006]

【発明が解決しようとする課題】このようなことから、
最近では、延性および耐摩耗性に優れ、さらに耐銹性に
も優れる他、SUS 430 に比べて安価な素材への
さらなる要望があった。すなわち、本発明の目的は、今
まで以上に延性と耐摩耗性、耐銹性に優れた素材、具体
的には硬さHv≧250 , 伸びEl≧5%で、SU
S 430 並みの耐銹性を有するという条件を満たす
電気材料用素材、特に磁気ディスクフロッピーディスク
センターコア用フェライト系ステンレス鋼を提供する製
造技術を確立することにある。
[Problem to be solved by the invention] From the above,
Recently, there has been a growing demand for a material that has excellent ductility, wear resistance, and rust resistance, and is also less expensive than SUS 430. That is, the object of the present invention is to create a material with better ductility, wear resistance, and rust resistance than ever before, specifically, a material with hardness Hv≧250, elongation El≧5%, and SU
The object of the present invention is to establish a manufacturing technology that provides a material for electrical materials, particularly a ferritic stainless steel for magnetic disk floppy disk center cores, which satisfies the condition of having rust resistance comparable to that of S430.

【0007】[0007]

【課題を解決するための手段】本発明者らは、上記目的
を達成するために鋭意研究した結果、後述するような成
分系の素材に対し、10%以上のハード圧延後、 50
0〜750 ℃の温度範囲で10秒以上, 10分以下
の再加熱処理を施し、その後硝酸電解を施すといった製
造工程を経ることにより、安価でしかもSUS 430
 並の耐食性を有し、さらには延性,耐摩耗性に優れた
センターコア用素材として充分な特性を有するフェライ
ト系ステンレス鋼が得られることを知見し、本発明の構
成に想到したのである。
[Means for Solving the Problems] As a result of intensive research to achieve the above object, the present inventors found that after hard rolling of 10% or more, 50%
By going through the manufacturing process of reheating for 10 seconds or more and 10 minutes or less in the temperature range of 0 to 750 degrees Celsius, and then applying nitric acid electrolysis, it is inexpensive and can be made from SUS 430.
It was discovered that a ferritic stainless steel having moderate corrosion resistance, excellent ductility and wear resistance, and sufficient characteristics as a material for a center core can be obtained, and the structure of the present invention was conceived.

【0008】すなわち本発明は、C:0.12wt%以
下、  Si:1.0 wt%以下、  Mn:1.0
 wt%以下、Cr:15〜20wt%、  Ni:1
.0 wt%以下、  Al:0.3 wt%以下、O
:0.003 wt%以下、  P:0.04wt%以
下、  S:0.03wt%以下、N:0.1 wt%
以下、さらに必要に応じて熱間加工性改善元素としてB
:0.002〜0.01wt%、Ca:0.01wt%
以下、REM:0.2 wt%以下、および耐食性改善
元素としてそれぞれ0.05wt%以下のV, Nbお
よびTiのうちから選ばれる少なくとも1種を含有し、
残部がFeおよび不可避的不純物からなる鋼を、仕上げ
焼鈍後、上記目的を達成するために上述したような成分
系の鋼に対し10%以上のハード圧延後、 500℃〜
750 ℃の温度範囲で10秒以上、10分以下の再加
熱処理を施した後、さらに硝酸電解を施すことを特徴と
する製造工程を経る方法であって、このような方法の実
施により、安価でSUS 430 並の耐食性を有し、
しかも延性, 耐摩耗性および耐銹性に優れた電気材料
用素材、特にフロッピーディスクセンターコア用素材と
して充分な特性を有するフェライト系ステンレス鋼の製
造方法である。
That is, the present invention provides C: 0.12 wt% or less, Si: 1.0 wt% or less, Mn: 1.0
wt% or less, Cr: 15-20 wt%, Ni: 1
.. 0 wt% or less, Al: 0.3 wt% or less, O
: 0.003 wt% or less, P: 0.04 wt% or less, S: 0.03 wt% or less, N: 0.1 wt%
Below, B is further added as an element for improving hot workability as necessary.
:0.002~0.01wt%, Ca:0.01wt%
The following contains REM: 0.2 wt% or less, and at least one selected from V, Nb, and Ti, each of which is 0.05 wt% or less as a corrosion resistance improving element,
After finish annealing the steel, the balance of which is Fe and unavoidable impurities, and after hard rolling of 10% or more of the steel with the above-mentioned composition to achieve the above purpose, the steel is heated at 500°C ~
This method involves a manufacturing process characterized by performing a reheating treatment in a temperature range of 750 °C for 10 seconds or more and 10 minutes or less, and then further performing nitric acid electrolysis. It has corrosion resistance comparable to SUS 430,
Moreover, it is a method for producing ferritic stainless steel, which has sufficient properties as a material for electrical materials, especially as a material for floppy disk center cores, with excellent ductility, wear resistance, and rust resistance.

【0009】本発明において、出発材料である鋼の組成
を上述のように限定した理由について、以下に説明する
。 C:Cは、少量で硬さを高め耐摩耗性を向上させる元素
である。しかしながら、このCの含有は、耐銹性を低下
させるとともに、また0.12wt%を超えると延性を
低下させ、2次加工性が劣化し硬質となり、プレス成形
性が阻害される。従って、本発明にあっては、C含有量
を0.12wt%以下とした。 Si:Siは、高温でフェライトを形成させる元素であ
り、脱酸剤として添加されるが、1.0 wt%を超え
て添加されると熱間圧延時に耳割れが生じ製品の歩留り
が悪くなるとともに靭性が低下するので、その含有量は
 1.0wt%以下とした。 Mn:Mnは、高温でオーステナイトを生成させる元素
であり、高温熱処理後の冷却( 焼入れ) によってマ
ルテンサイトを生成させる元素である。また、このMn
は1.0 wt%を超えて添加すると熱間加工性に有害
であるとともに、残留オーステナイトの出現を招くので
、その含有量を1.0 wt%以下とした。 Cr:Crは、SUS 430 並みの耐食性を確保す
るために最低限15wt%以上の添加が必要であり、一
方20wt%を超えて添加するとコスト高を招くととも
に硬質化し延性を低下させるため、その含有量の範囲を
15〜20wt%とした。 Ni:Niは、Mn同様にオーステナイトを形成させる
元素であり、耐食性向上に有効な元素であるが、1.0
 wt%を超えて添加すると、SUS 430 に比べ
コスト高となるため、その含有量を 1.0wt%以下
とした。
In the present invention, the reason why the composition of the steel as a starting material is limited as described above will be explained below. C: C is an element that increases hardness and wear resistance in a small amount. However, the content of C lowers rust resistance, and when it exceeds 0.12 wt%, it lowers ductility, resulting in poor secondary workability and hardness, which inhibits press formability. Therefore, in the present invention, the C content is set to 0.12 wt% or less. Si: Si is an element that forms ferrite at high temperatures and is added as a deoxidizing agent, but if it is added in excess of 1.0 wt%, it will cause edge cracking during hot rolling and reduce the yield of the product. Since the toughness decreases with the addition of C, its content was set to 1.0 wt% or less. Mn: Mn is an element that generates austenite at high temperatures, and is an element that generates martensite when cooled (quenched) after high-temperature heat treatment. Also, this Mn
If added in an amount exceeding 1.0 wt%, it is harmful to hot workability and causes the appearance of retained austenite, so the content is set to 1.0 wt% or less. Cr: It is necessary to add at least 15 wt% or more of Cr to ensure corrosion resistance comparable to that of SUS 430. On the other hand, adding more than 20 wt% will increase the cost, make it hard, and reduce ductility. The amount ranged from 15 to 20 wt%. Ni: Like Mn, Ni is an element that forms austenite and is an effective element for improving corrosion resistance.
If added in excess of wt%, the cost would be higher than SUS 430, so the content was set to 1.0 wt% or less.

【0010】B, Ca, REM:B,Ca, RE
Mは、いずれも熱間加工性改善元素である。とくにBは
、微量の添加であっても高温における強度と延性を著し
く増し、しかも熱間加工性改善に極めて有効な元素であ
る。しかしながら、その効果は 0.002wt%未満
ではほとんど無く、0.01wt%を超えると逆に脆性
を引き起こすとともに高温での耐酸化性が劣化してスケ
ール生成が多くなるといった問題点が生じるため、その
範囲を0.002 〜0.01wt%とした。また、C
aについては0.01wt%、REMについては 0.
2wt%を超えると、それぞれ却って熱間脆性を引き起
こして歩留りを著しく損なうので、これを上限として含
有させる。 V, Nb, Ti:V, Nb, Tiは、それぞれ
熱間加工性改善に有効であると共に、とりわけ耐食性改
善にも有効な元素である。ただし、これらの元素は、0
.05wt%をそれぞれ超えると、硬度制御が困難にな
るので、それぞれ0.05wt%を上限として含有させ
る。 Al:Alは、脱酸剤として添加されるが、 0.3w
t%を超えて添加した場合、介在物の散在によって二次
加工性が劣化するため、Al添加量は 0.3wt%以
下とした。 O:Oは、酸化物系の非金属介在物を形成し、鋼の清浄
度を低下させ、これに起因して加工割れを生じさせるの
で、その含有量上限を0.003 wt%とした。また
、その値は低い方が好ましいので下限は定めない。 P:Pは、その添加量が多いと靭性を低下させるため、
その添加量の上限を0.04wt%とした。 S:Sは、耐食性の低下を引き起こすため、この含有量
は少ないほうが好ましい。特に0.03wt%を超える
と耐食性劣化が著しいので、その含有量上限を0.03
wt%とした。 N:Nは、鋼の硬度を調整するために有効な元素である
が、その添加量が多いと硬質となり伸びが低下し、2次
加工性を劣化させ、硬質化してプレス成形性を低下させ
る。従って、本発明にあっては、N量を 0.1wt%
以下とした。
B, Ca, REM: B, Ca, RE
M is an element that improves hot workability. In particular, B is an element that significantly increases strength and ductility at high temperatures even when added in a small amount, and is extremely effective in improving hot workability. However, the effect is almost negligible below 0.002wt%, and when it exceeds 0.01wt%, it causes problems such as brittleness, deterioration of oxidation resistance at high temperatures, and increased scale formation. The range was 0.002 to 0.01 wt%. Also, C
0.01wt% for a, 0.01wt% for REM.
If it exceeds 2 wt%, hot embrittlement will occur and the yield will be significantly impaired, so this content should be set as the upper limit. V, Nb, Ti: V, Nb, and Ti are elements that are each effective in improving hot workability, and are particularly effective in improving corrosion resistance. However, these elements are 0
.. If each exceeds 0.05 wt%, hardness control becomes difficult, so the upper limit of each content is 0.05 wt%. Al: Al is added as a deoxidizing agent, but 0.3w
If Al is added in excess of t%, secondary workability deteriorates due to the scattering of inclusions, so the amount of Al added was set to 0.3 wt% or less. O: Since O forms oxide-based nonmetallic inclusions and reduces the cleanliness of steel, which causes processing cracks, the upper limit of its content was set at 0.003 wt%. Further, since it is preferable that the value be lower, no lower limit is set. P: P reduces toughness when added in a large amount, so
The upper limit of the amount added was set to 0.04 wt%. S: Since S causes a decrease in corrosion resistance, it is preferable that the content is small. In particular, if the content exceeds 0.03 wt%, the corrosion resistance deteriorates significantly, so the upper limit of the content should be set at 0.03 wt%.
It was set as wt%. N: N is an effective element for adjusting the hardness of steel, but if it is added in a large amount, it becomes hard, reduces elongation, deteriorates secondary workability, and becomes hard, reducing press formability. . Therefore, in the present invention, the amount of N is set to 0.1wt%.
The following was made.

【0011】次に、本発明の製造方法において、上述の
如き組成の鋼は、常法に従って熱間圧延などの処理を経
て仕上げ焼鈍が施された後、10%以上の冷間圧延( 
ハード圧延) が施される。この仕上げ焼鈍後のハード
圧延において、その圧下率を10%以上とした理由は、
上記成分系で目的の硬度を得るためには少なくとも10
%以上の圧下率が必要だからである。
Next, in the manufacturing method of the present invention, the steel having the above-mentioned composition is subjected to finish annealing through treatments such as hot rolling according to a conventional method, and then cold rolled by 10% or more (
hard rolling). The reason why the rolling reduction ratio was set to 10% or more in hard rolling after final annealing is as follows.
In order to obtain the desired hardness with the above component system, at least 10
This is because a rolling reduction rate of % or more is required.

【0012】次に、上述のようなハード圧延を施した鋼
材は、引続き、できればアンモニア分解ガスあるいはア
ルゴン雰囲気中で再加熱処理が施される。この再加熱処
理における加熱の温度範囲を 500℃から750 ℃
の範囲とした理由は、 500℃以下では延性向上効果
が認められず、一方 750℃以上では延性向上に伴い
硬度が低下するため、この温度範囲に限定した。また、
この再加熱処理において、加熱温度への保持時間につい
ては、目的温度で10秒〜10分保持としたが、その理
由は、10秒未満ではその延性向上の効果が充分ではな
く、一方、10分以下では、 750℃を超える温度で
10分を超えた時間保持すると、延性向上に伴い硬度が
低下するとともに耐食性劣化が著しくなるからである。
Next, the hard-rolled steel material as described above is subsequently subjected to a reheating treatment, preferably in an ammonia decomposition gas or argon atmosphere. The heating temperature range for this reheating treatment is from 500℃ to 750℃.
The reason for this range is that at temperatures below 500°C, no ductility improvement effect is observed, while at temperatures above 750°C, hardness decreases as ductility improves, so this temperature range was selected. Also,
In this reheating treatment, the holding time at the heating temperature was set at the target temperature for 10 seconds to 10 minutes. In the following, this is because if the temperature exceeds 750°C for a time exceeding 10 minutes, the hardness decreases as the ductility improves, and the corrosion resistance deteriorates significantly.

【0013】上述のようなハード圧延と再加熱処理とを
施した鋼材については、さらにその後、硝酸電解処理が
施される。この硝酸電解処理の条件については、温度は
80℃以下、電気量は1〜50C/dm2, 硝酸濃度
1〜30%とするのが好ましい。すなわち、処理温度が
80℃を超えると硝酸の蒸発が著しいとともに槽に負荷
がかかるからである。また、電気量が1C/dm2未満
だと硝酸電解により充分表面の有害な酸化物皮膜を除去
することができず、また50C/dm2を超えると表面
が荒れてしまうためである。硝酸濃度については、1%
以下だと充分に硝酸電解が行われず、30%を超えると
表面の荒れが目立つためである。
[0013] The steel material that has been hard rolled and reheated as described above is then further subjected to nitric acid electrolytic treatment. Regarding the conditions for this nitric acid electrolytic treatment, it is preferable that the temperature be 80 DEG C. or less, the amount of electricity be 1 to 50 C/dm2, and the nitric acid concentration be 1 to 30%. That is, if the treatment temperature exceeds 80° C., nitric acid evaporates significantly and puts a load on the tank. Further, if the amount of electricity is less than 1 C/dm2, the harmful oxide film on the surface cannot be sufficiently removed by nitric acid electrolysis, and if it exceeds 50 C/dm2, the surface becomes rough. Regarding nitric acid concentration, 1%
This is because if it is less than 30%, nitric acid electrolysis will not be carried out sufficiently, and if it exceeds 30%, the surface will become noticeably rough.

【0014】以上説明したように、上述した鋼組成の素
材を、仕上げ焼鈍後ハード圧延を施し、再加熱処理をし
た後、硝酸電解を施して表面のスケールを除去すること
により、耐食性を劣化させることなく、延性, 耐摩耗
性および耐銹性に優れた電気酸洗槽用フェライト系ステ
ンレス鋼を製造することができる。すなわち、表1中の
鋼No.1鋼の、30%圧延材について90秒保持の再
加熱試験を行った結果を図2に示す。再加熱温度が 5
00℃以上になると、硬さの低下はみられず、延性の向
上が認められた。一方、 750℃を超えると硬度が著
しく低下し、250Hv を超える硬さ条件を満たすこ
とができなくなる。このことから、再加熱処理では 5
00〜750 ℃の温度で加熱すると、硬さと伸びとが
所期レベルになることがわかった。
As explained above, the material having the above-mentioned steel composition is subjected to final annealing, hard rolling, reheating treatment, and then subjected to nitric acid electrolysis to remove surface scale, thereby degrading the corrosion resistance. Ferritic stainless steel for electric pickling tanks with excellent ductility, wear resistance, and rust resistance can be produced without any corrosion. That is, steel No. in Table 1. Figure 2 shows the results of a reheating test held for 90 seconds on a 30% rolled material of No. 1 steel. Reheating temperature is 5
At temperatures above 00°C, no decrease in hardness was observed, and an improvement in ductility was observed. On the other hand, when the temperature exceeds 750°C, the hardness decreases significantly, making it impossible to satisfy the hardness condition exceeding 250Hv. From this, in reheating treatment, 5
It has been found that heating at temperatures between 00 and 750°C brings the hardness and elongation to the desired levels.

【0015】[0015]

【実施例】表1に示す組成の鋼を真空高周波炉で溶製し
て30kg小型鋼塊を得、この鋼塊を1250℃, 1
時間の加熱を施した後、4mm厚の熱延板とし、その後
、 800℃, 4時間の焼鈍を施してから、10℃/
hの速度で 700℃まで冷却し、その後大気放冷して
熱延焼鈍板とした。この熱延焼鈍板をショットブラスト
にかけたのちさらに酸洗して表面のスケールを除去後、
 0.3mm厚まで冷間圧延した。 その後その冷延板を850〜1100℃の温度範囲で3
0秒間の加熱を施してから空冷した。このようにして製
造した素材に対し、10%以上のハード圧延を施した後
、種々の温度範囲、保持時間で再加熱後、10C/dm
2の電気量、20℃10%硝酸溶液中で硝酸電解を行い
、硬度,伸び, 耐食性に及ぼすハード圧延条件、再加
熱条件についてそれぞれ調査した。また、このようにし
て作った仕上げ焼鈍板について、図1に示したような形
状にプレス成形加工を施し、その不良率とそれぞれの条
件について調査した。なお、伸びの評価はJIS 13
号B試験片を用いた引張試験により、また硬度はマイク
ロビッカースによる板面硬度測定( 荷重 500g)
から評価した。さらに耐銹性の評価は、実際にセンター
コア形状に一次加工した素材について塩水噴霧試験(3
5 ℃, 16時間噴霧, 8時間湿潤)を10サイク
ル施すことによりその発銹面積率を相対的に評価した。 表1表2−1および2−2、図2, 3にそれらの結果
をまとめて示す。
[Example] Steel with the composition shown in Table 1 was melted in a vacuum high-frequency furnace to obtain a 30 kg small steel ingot, and this steel ingot was heated at 1250°C for 1
After heating for several hours, it was made into a 4mm thick hot-rolled plate, then annealed at 800℃ for 4 hours, and then heated at 10℃/
The sample was cooled to 700° C. at a rate of 1 h, and then left to cool in the atmosphere to obtain a hot-rolled annealed plate. This hot rolled annealed plate was shot blasted and then pickled to remove surface scale.
It was cold rolled to a thickness of 0.3 mm. After that, the cold-rolled plate was heated in a temperature range of 850 to 1100℃ for 3
After heating for 0 seconds, it was air cooled. The material produced in this way is subjected to hard rolling of 10% or more, then reheated at various temperature ranges and holding times, and then heated to 10C/dm.
Nitric acid electrolysis was carried out in a 10% nitric acid solution at 20°C using the electricity amount of 2, and the effects of hard rolling conditions and reheating conditions on hardness, elongation, and corrosion resistance were investigated. Further, the finished annealed plate thus produced was press-formed into the shape shown in FIG. 1, and the defective rate and each condition were investigated. The elongation evaluation is based on JIS 13.
The hardness was measured by a tensile test using a No. B test piece, and the hardness was measured using a micro Vickers (load: 500 g).
It was evaluated from Furthermore, the rust resistance was evaluated using a salt spray test (3
The rusting area ratio was relatively evaluated by applying 10 cycles of 5°C, 16 hours of spraying, 8 hours of moistening. The results are summarized in Table 1 and Tables 2-1 and 2-2, and Figures 2 and 3.

【0016】[0016]

【表1】[Table 1]

【0017】[0017]

【表2−1】[Table 2-1]

【0018】[0018]

【表2−2】[Table 2-2]

【0019】これらの結果に示すとおり、本発明の製造
条件に準拠して製造したフェライト系ステンレス鋼は、
電気材料用素材, 特にフロッピーディスクセンターコ
ア材としての要求特性を十分に満たすことが明白である
As shown in these results, the ferritic stainless steel manufactured according to the manufacturing conditions of the present invention has
It is clear that this material fully satisfies the required properties as a material for electrical materials, especially as a center core material for floppy disks.

【0016】[0016]

【発明の効果】以上説明したように本発明によれば、所
定の成分組成の鋼を、ハード圧延−再加熱処理−硝酸電
解と順次に処理するだけで、延性と耐摩耗性とに優れる
と共に、耐銹性にも優れる電気材料用フェライト系ステ
ンレス鋼を安価に製造することができる。
Effects of the Invention As explained above, according to the present invention, steel having a predetermined composition can be treated in sequence of hard rolling, reheating treatment, and nitric acid electrolysis, thereby achieving excellent ductility and wear resistance. , ferritic stainless steel for electrical materials, which also has excellent rust resistance, can be manufactured at low cost.

【図面の簡単な説明】[Brief explanation of drawings]

【図1】図1は、再加熱温度と硬さおよび伸びとの関係
を示すグラフ。
FIG. 1 is a graph showing the relationship between reheating temperature, hardness, and elongation.

【図2】図2は、圧下率と硬さとの関係を示すグラフ。FIG. 2 is a graph showing the relationship between rolling reduction and hardness.

【図3】図3は、圧下率と伸びとの関係を示すグラフ。FIG. 3 is a graph showing the relationship between rolling reduction and elongation.

Claims (2)

【特許請求の範囲】[Claims] 【請求項1】  C:0.12wt%以下、     
 Si:1.0 wt%以下、 Mn:1.0 wt%以下、      Cr:15〜
20wt%、Ni:1.0 wt%以下、      
Al:0.3 wt%以下、O:0.003 wt%以
下、    P:0.04wt%以下、S:0.03w
t%以下および  N:0.1 wt%以下を含有し、
残部がFeおよび不可避的不純物からなる鋼を、仕上げ
焼鈍後10%以上の冷間圧延を施し、その後 500℃
〜750 ℃の温度範囲で10秒以上、10分以下の再
加熱を施し、さらにその後硝酸電解を施すことを特徴と
する延性, 耐摩耗性および耐銹性に優れた電気材料用
フェライト系ステンレス鋼の製造方法。
[Claim 1] C: 0.12 wt% or less,
Si: 1.0 wt% or less, Mn: 1.0 wt% or less, Cr: 15~
20 wt%, Ni: 1.0 wt% or less,
Al: 0.3 wt% or less, O: 0.003 wt% or less, P: 0.04 wt% or less, S: 0.03w
t% or less and N: 0.1 wt% or less,
After final annealing, steel with the balance consisting of Fe and unavoidable impurities is subjected to cold rolling of 10% or more, and then heated to 500°C.
A ferritic stainless steel for electrical materials with excellent ductility, wear resistance, and rust resistance, which is characterized by being reheated in a temperature range of ~750°C for 10 seconds or more and 10 minutes or less, and then subjected to nitric acid electrolysis. manufacturing method.
【請求項2】  C:0.12wt%以下、     
 Si:1.0 wt%以下、 Mn:1.0 wt%以下、      Cr:15〜
20wt%、Ni:1.0 wt%以下、      
O:0.003 wt%以下、P:0.04wt%以下
、      S:0.03wt%以下およびNi:1
.0 wt%以下、      Al:0.3 wt%
以下、O:0.003 wt%以下、    P:0.
04wt%以下、S:0.03wt%以下および  N
:0.1 wt%以下を含有し、さらに熱間加工性改善
元素としてB:0.002 〜0.01wt%、Ca:
0.01wt%以下およびREM:0.2 wt%以下
の少なくとも1種、および耐食性改善元素としてそれぞ
れ0.05wt%以下のV, NbおよびTiのうちか
ら選ばれる少なくとも1種を含有し、残部がFeおよび
不可避的不純物からなる鋼を、仕上げ焼鈍後10%以上
の冷間圧延を施し、その後 500℃〜750 ℃の温
度範囲で10秒以上、10分以下の再加熱を施し、さら
にその後硝酸電解を施すことを特徴とする延性, 耐摩
耗性および耐銹性に優れた電気材料用フェライト系ステ
ンレス鋼の製造方法。
[Claim 2] C: 0.12 wt% or less,
Si: 1.0 wt% or less, Mn: 1.0 wt% or less, Cr: 15~
20 wt%, Ni: 1.0 wt% or less,
O: 0.003 wt% or less, P: 0.04 wt% or less, S: 0.03 wt% or less, and Ni: 1
.. 0 wt% or less, Al: 0.3 wt%
Below, O: 0.003 wt% or less, P: 0.
04wt% or less, S: 0.03wt% or less, and N
: 0.1 wt% or less, and as an element for improving hot workability, B: 0.002 to 0.01 wt%, Ca:
Contains at least one selected from 0.01 wt% or less and REM: 0.2 wt% or less, and at least one selected from V, Nb, and Ti each as a corrosion resistance improving element of 0.05 wt% or less, and the remainder is After final annealing, steel consisting of Fe and unavoidable impurities is subjected to cold rolling of 10% or more, then reheated at a temperature range of 500°C to 750°C for 10 seconds or more and 10 minutes or less, and then subjected to nitric acid electrolysis. A method for manufacturing ferritic stainless steel for electrical materials, which has excellent ductility, wear resistance, and rust resistance.
JP3174710A 1991-06-20 1991-06-20 Method for producing ferritic stainless steel for electrical materials with excellent ductility, wear resistance and rust resistance Expired - Fee Related JP2583694B2 (en)

Priority Applications (1)

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JP3174710A JP2583694B2 (en) 1991-06-20 1991-06-20 Method for producing ferritic stainless steel for electrical materials with excellent ductility, wear resistance and rust resistance

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EP0625584A1 (en) * 1993-05-19 1994-11-23 Kawasaki Steel Corporation Ferritic stainless steel exhibiting excellent atmospheric corrosion resistance and crevice corrosion resistance
JP2007197837A (en) * 2001-09-27 2007-08-09 Hitachi Metals Ltd Oxidation resistant steel and component for solid-oxide type fuel cell obtained by using the same
JP2008088535A (en) * 2006-10-05 2008-04-17 Jfe Steel Kk Ferritic stainless hot rolled steel sheet for cold rolling and its production method
JP5652568B1 (en) * 2014-07-23 2015-01-14 Jfeスチール株式会社 Manufacturing method of ferritic stainless steel foil for solar cell substrate
JP5652567B1 (en) * 2014-07-23 2015-01-14 Jfeスチール株式会社 Manufacturing method of ferritic stainless steel foil for solar cell substrate
CN105821337A (en) * 2016-06-13 2016-08-03 苏州双金实业有限公司 Steel with fireproof performance
JP2017534761A (en) * 2014-10-22 2017-11-24 ポスコPosco High strength, high ductility ferritic stainless steel sheet and method for producing the same
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Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0625584A1 (en) * 1993-05-19 1994-11-23 Kawasaki Steel Corporation Ferritic stainless steel exhibiting excellent atmospheric corrosion resistance and crevice corrosion resistance
JP2007197837A (en) * 2001-09-27 2007-08-09 Hitachi Metals Ltd Oxidation resistant steel and component for solid-oxide type fuel cell obtained by using the same
JP4524760B2 (en) * 2001-09-27 2010-08-18 日立金属株式会社 Oxidation resistant steel and solid oxide fuel cell parts using the same
JP2008088535A (en) * 2006-10-05 2008-04-17 Jfe Steel Kk Ferritic stainless hot rolled steel sheet for cold rolling and its production method
JP5652568B1 (en) * 2014-07-23 2015-01-14 Jfeスチール株式会社 Manufacturing method of ferritic stainless steel foil for solar cell substrate
JP5652567B1 (en) * 2014-07-23 2015-01-14 Jfeスチール株式会社 Manufacturing method of ferritic stainless steel foil for solar cell substrate
JP2017534761A (en) * 2014-10-22 2017-11-24 ポスコPosco High strength, high ductility ferritic stainless steel sheet and method for producing the same
CN105821337A (en) * 2016-06-13 2016-08-03 苏州双金实业有限公司 Steel with fireproof performance
EP3851552A4 (en) * 2018-10-23 2021-11-03 Posco High-strength ferritic stainless steel for clamp and method for manufacturing same
JP2022505747A (en) * 2018-10-23 2022-01-14 ポスコ High-strength ferritic stainless steel for clamps and its manufacturing method

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