JPH05156369A - Manufacture of steel cord - Google Patents
Manufacture of steel cordInfo
- Publication number
- JPH05156369A JPH05156369A JP34770391A JP34770391A JPH05156369A JP H05156369 A JPH05156369 A JP H05156369A JP 34770391 A JP34770391 A JP 34770391A JP 34770391 A JP34770391 A JP 34770391A JP H05156369 A JPH05156369 A JP H05156369A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- less
- steel cord
- cooling
- mmφ
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Metal Extraction Processes (AREA)
Abstract
Description
【0001】[0001]
【産業上の利用分野】本発明はトラック、バス、乗用車
などのゴム製タイヤ、あるいは動力伝達用のベルトなど
の補強用に使用される高強度で高延性の極細線を撚り合
わせたスチールコードの製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel cord formed by twisting high-strength and high-ductility ultrafine wires used for reinforcing rubber tires of trucks, buses, passenger cars, etc., or belts for power transmission. It relates to a manufacturing method.
【0002】[0002]
【従来の技術】スチールコードは、熱間圧延後の調整冷
却によってパーライト組織とした後、伸線加工によって
30〜70%の加工を行い、パテンティング処理によっ
て加工の影響のないパーライト組織とし、さらに30〜
70%の加工を行い所定の線径のワイヤとし、最終湿式
伸線によって0.15〜0.35mmφのワイヤにし、
これを撚り合わせてスチールコードとして使用されてい
る。2. Description of the Related Art Steel cords are made into a pearlite structure by adjusting and cooling after hot rolling, and then 30 to 70% are processed by wire drawing, and a pearlite structure which is not affected by the processing by patenting treatment. 30 ~
The wire having a predetermined wire diameter is processed by 70%, and finally wet drawn to a wire having a diameter of 0.15 to 0.35 mmφ,
These are twisted together and used as a steel cord.
【0003】熱間圧延後の調整冷却によってパーライト
組織を得る方法としては、特公昭60−56215号公
報、特公昭60−7004号公報に記載された方法など
がある。特公昭60−56215号公報には、C:0.
2〜1.0wt%、Si:0.30wt%以下、Mn:
0.3〜0.9wt%からなる鋼を熱間圧延後にKNO
3 、NaNO3 塩浴中に焼き入れ、微細パーライト組織
の線材を得ることによって1〜5mmφのワイヤ製品を
直接製造する線材の熱処理法が記載されている。また、
特公昭60−7004号公報には、C:0.75〜1.
0wt%、Si:0.5〜1.5wt%、Mn:0.6
〜1.3wt%、Al:0.1wt%以下、必要により
Cr:0.3wt%以下を含有する鋼を熱間圧延後に8
50℃に冷却した後、その後の冷却速度を7℃/sとす
る伸線加工性のすぐれた鋼線材の製造方法が記載されて
いる。As a method for obtaining a pearlite structure by controlled cooling after hot rolling, there are methods described in JP-B-60-56215 and JP-B-60-7004. Japanese Examined Patent Publication No. 60-56215 discloses C: 0.
2 to 1.0 wt%, Si: 0.30 wt% or less, Mn:
KNO after hot rolling of steel consisting of 0.3 to 0.9 wt%
3 , a heat treatment method of a wire rod for directly producing a wire product having a diameter of 1 to 5 mm by quenching in a NaNO 3 salt bath to obtain a wire rod having a fine pearlite structure. Also,
In Japanese Examined Patent Publication No. 60-7004, C: 0.75-1.
0 wt%, Si: 0.5 to 1.5 wt%, Mn: 0.6
~ 1.3 wt%, Al: 0.1 wt% or less, and optionally Cr: 0.3 wt% or less after hot rolling 8
After cooling to 50 ° C., a method for producing a steel wire rod having excellent wire drawability is described in which the subsequent cooling rate is 7 ° C./s.
【0004】[0004]
【発明が解決しようとする課題】最近、エネルギー問題
から特に工業分野においては省エネルギーで製品を製造
することが必要とされており、鋼製品のように熱処理と
冷却を繰り返す工程においては、できるだけ熱処理工程
を省略する製造工程が必要とされている。スチールコー
ドの製造においても、熱間圧延後の伸線とパテンティン
グ処理を繰り返すことによって熱処理が行われている。
従って、できるだけ工程省略可能なスチールコードの製
造方法が期待されている。Recently, due to energy problems, it has been required to manufacture products with energy saving especially in the industrial field. In the process of repeating heat treatment and cooling like steel products, the heat treatment process should be performed as much as possible. There is a need for a manufacturing process that omits. Also in the production of steel cords, heat treatment is performed by repeating wire drawing after hot rolling and patenting treatment.
Therefore, a method of manufacturing a steel cord that is capable of omitting steps as much as possible is expected.
【0005】本発明は、4.5〜6.5mmφの熱間圧
延線材から伸線加工によってスチールコードを製造する
方法において、熱間圧延線材と最終ワイヤの間において
最低限必要な1回のパテンティング処理によってスチー
ルコードを製造する方法を提供する。The present invention is a method for producing a steel cord from a hot-rolled wire rod having a diameter of 4.5 to 6.5 mm by wire-drawing. A method of manufacturing a steel cord by a coating process is provided.
【0006】[0006]
【課題を解決するための手段】本発明の要旨は、重量%
で、C 0.80%以上0.90%以下、Si 0.
1%以上1.5%以下、Mn 0.1%以上1.0%以
下、必要によりCr 0.10%以上1.0%以下を含
有し、残部鉄及び不可避的不純物よりなり、かつ、不可
避的に入るAl含有量を0.003%以下とした4.5
〜6.5mmφの熱間圧延線材に、線材横断面に存在す
るアスペクト比が10以下であるセメンタイトの存在率
が75%以上となる調整冷却を行い、その後伸線加工に
より0.6〜1.3mmφのワイヤとし、その後最終パ
テンティング処理を行い、さらにブラスめっき処理を行
った後、最終湿式伸線加工により0.10〜0.3mm
φで引張強さ2800MPa以上のワイヤとし、その後
撚り合わせてコードとすることを特徴とするスチールコ
ードの製造方法である。前記調整冷却として、熱間圧延
終了後の線材を800℃以上1100℃以下の温度範囲
から50℃/s以上の冷却速度で450℃以上550℃
以下の温度に冷却した後450℃以上550℃以下の温
度範囲で変態を終了させ、さらに必要に応じて450℃
以上に120s以内保持し、室温まで冷却することは好
ましい。SUMMARY OF THE INVENTION The gist of the present invention is the weight%
, C 0.80% or more and 0.90% or less, Si 0.
1% or more and 1.5% or less, Mn 0.1% or more and 1.0% or less, and if necessary, Cr 0.10% or more and 1.0% or less, and the balance is iron and inevitable impurities, and is unavoidable. 4.5 with Al content of 0.003% or less
A hot-rolled wire rod having a diameter of ~ 6.5 mmφ is subjected to controlled cooling such that the abundance of cementite having an aspect ratio of 10 or less present in the cross section of the wire rod becomes 75% or more, and then 0.6-1. 3mmφ wire, then final patenting treatment, brass plating treatment, then final wet drawing 0.10-0.3mm
A steel cord manufacturing method is characterized in that a wire having a tensile strength of 2800 MPa or more at φ is formed and then twisted to form a cord. As the adjustment cooling, the wire rod after the hot rolling is finished is heated from 450 ° C to 550 ° C at a cooling rate of 50 ° C / s or more from a temperature range of 800 ° C to 1100 ° C.
After cooling to the temperature below, the transformation is completed within the temperature range of 450 ° C to 550 ° C, and if necessary, 450 ° C.
It is preferable to hold it for 120 s or more and cool it to room temperature.
【0007】[0007]
【作用】本発明の鋼組成の限定理由は下記のとおりであ
る。The reason for limiting the steel composition of the present invention is as follows.
【0008】一次伸線性が著しく低下するのはCの添加
量が0.8%以上のときであるため、下限を0.8%と
する。また、上限を中心偏析による影響のでない0.9
%以下とする。The primary drawability is remarkably lowered when the amount of C added is 0.8% or more, so the lower limit is made 0.8%. The upper limit is 0.9, which is not affected by center segregation.
% Or less.
【0009】Siは鋼の脱酸のために必要な元素であ
り、含有量が少なすぎると脱酸効果が不十分となるた
め、下限を0.1%とする。また、Siは熱処理後に形
成されるパーライト中のフェライト相に固溶してパテン
ティング後の強度を上げるが、反面フェライトの延性を
低下させ、伸線後の極細線の延性を低下させるため上限
を1.5%とする。Si is an element necessary for deoxidizing steel, and if the content is too small, the deoxidizing effect will be insufficient, so the lower limit is made 0.1%. Further, Si dissolves in the ferrite phase in pearlite formed after heat treatment to increase the strength after patenting, but on the other hand, it lowers the ductility of ferrite and lowers the ductility of ultrafine wires after drawing, so the upper limit is set. 1.5%.
【0010】Mnは鋼の焼き入れ性を確保するため下限
を0.1%とする。しかし、多量のMnの添加は偏析を
引き起こし、パテンティングの際にベイナイト、マルテ
ンサイトという過冷組織が発生し、その後の伸線性を害
するため上限を1.0%とする。The lower limit of Mn is 0.1% in order to secure the hardenability of steel. However, the addition of a large amount of Mn causes segregation, and a supercooled structure such as bainite and martensite is generated during patenting, which impairs the subsequent wire drawability, so the upper limit is made 1.0%.
【0011】過共析鋼の場合、パテンティング後の組織
においてセメンタイトのネットワークが発生しやすく、
セメンタイトの厚みのあるものが析出しやすい。この鋼
において高強度高延性を実現するためには、パーライト
を微細にし、かつセメンタイトネットワークや厚いセメ
ンタイトを無くす必要がある。Crはこの様なセメンタ
イトの異常部の出現を抑制し、さらにパーライトを微細
にする効果を持っているため必要により添加する。下限
はその効果の期待できる0.1%以上とする。しかし、
多量の添加は熱処理後のフェライト中の転位密度を上昇
させるため、引き抜き加工後の極細線の延性を著しく害
することになる。従って、上限を延性を害することのな
い1.0%以下とする。In the case of hyper-eutectoid steel, a cementite network is likely to occur in the structure after patenting,
Cementite with a large thickness easily precipitates. In order to achieve high strength and high ductility in this steel, it is necessary to make pearlite fine and to eliminate the cementite network and thick cementite. Cr suppresses the appearance of such an abnormal portion of cementite and further has the effect of refining pearlite, so Cr is added if necessary. The lower limit is set to 0.1% or more where the effect can be expected. But,
Addition of a large amount increases the dislocation density in the ferrite after heat treatment, and therefore significantly impairs the ductility of the ultrafine wire after drawing. Therefore, the upper limit is set to 1.0% or less, which does not impair the ductility.
【0012】従来の極細鋼線と同様に、延性を確保する
ためSの含有量は0.020%以下とし、PもSと同様
に線材の延性を害するのでその含有量を0.020%以
下とするのが望ましい。Similar to the conventional ultra-fine steel wire, the S content is 0.020% or less in order to secure the ductility, and P also impairs the ductility of the wire like S, so the content is 0.020% or less. Is desirable.
【0013】極細線の延性を低下させる原因として、A
l2 O3、MgO−Al2 O3 等のAl2 O3を主成分と
する非延性介在物の存在がある。従って、本発明におい
ては非延性介在物による延性低下を避けるために、Al
含有量を0.003%以下とする。As a cause of reducing the ductility of the ultrafine wire, A
There are non-ductile inclusions containing Al 2 O 3 as a main component, such as l 2 O 3 and MgO—Al 2 O 3 . Therefore, in the present invention, in order to avoid the decrease in ductility due to non-ductile inclusions, Al
The content is 0.003% or less.
【0014】また、製造条件の限定理由は以下に述べる
とおりである。The reasons for limiting the manufacturing conditions are as described below.
【0015】調整冷却によってC含有量が0.82wt
%以上の鋼をパーライト組織とした場合、伸線性を向上
させるためにどのような組織としても、実用上の製造条
件においては、4.5〜6.5mmφの熱間圧延線材を
真ひずみで3.0以上に加工することは不可能であっ
た。これは、岡ら〔材料とプロセス、4(1991)2
042〕によって、パーライト組織とした場合、微細パ
ーライト組織とすれば加工硬化率が大きくなるため加工
性が低下し、粗いパーライト組織とすればセメンタイト
相の厚みが厚くなり加工性が低下するためとされてい
る。C content was 0.82 wt% by controlled cooling
% Steel having a pearlite structure, any structure for improving the wire drawability, under practical manufacturing conditions, a hot-rolled wire of 4.5 to 6.5 mmφ with a true strain of 3 It was impossible to process to more than 0.0. This is Oka et al. [Materials and Process, 4 (1991) 2
According to [042], when the pearlite structure is used, if the fine pearlite structure is used, the work hardening rate is increased and the workability is lowered, and if the coarse pearlite structure is used, the thickness of the cementite phase is increased and the workability is decreased. ing.
【0016】そこで、本発明者らは熱間圧延後に形成さ
れるセメンタイトの形状に着目し、線材の横断面内に観
察されるアスペクト比が10以下であるセメンタイトの
存在率が多くなるほど加工硬化率が低下し、加工性を向
上できることを見いだした。Therefore, the present inventors have paid attention to the shape of cementite formed after hot rolling, and the work hardening rate increases as the abundance of cementite having an aspect ratio of 10 or less observed in the cross section of the wire increases. It was found that the workability was improved and the workability was improved.
【0017】セメンタイトのアスペクト比を10以下と
するためには、例えば熱間圧延後の800℃以上110
0℃以下の温度範囲からの冷却速度をパーライト変態を
起こさないように50℃/s以上とする。恒温変態温度
は、変態温度が高くなるとセメンタイトが球状化しにく
いラメラー組織が発達するため、上限を550℃とす
る。また、変態温度が低くなると変態終了までの時間が
長くなり生産性を低下させるので、下限を450℃とす
る。In order to set the aspect ratio of cementite to 10 or less, for example, 800 ° C. or more after hot rolling and 110
The cooling rate from the temperature range of 0 ° C. or lower is set to 50 ° C./s or higher so as not to cause pearlite transformation. The isothermal transformation temperature has an upper limit of 550 ° C. because a lamellar structure in which cementite is hard to be spheroidized develops when the transformation temperature rises. Further, when the transformation temperature is low, the time until the transformation is completed is long and the productivity is lowered. Therefore, the lower limit is set to 450 ° C.
【0018】また、アスペクト比が10以下のセメンタ
イトの存在率を80%以上とするために、必要に応じ
て、変態終了後120s以内の範囲で変態温度以上に保
持することによってパーライト組織の球状化を促進する
ことができる。Further, in order to make the abundance of cementite having an aspect ratio of 10 or less 80% or more, if necessary, the pearlite structure is spheroidized by maintaining the temperature above the transformation temperature within 120 s after the transformation is completed. Can be promoted.
【0019】熱間圧延後の一次伸線における仕上げ線径
は、パーライト鋼に比べて差のでる1.3mmφ以下と
する。また、0.6mmφ未満に仕上げるとその後の加
工により得られるワイヤ特性が劣化するので0.6mm
φ以上とする。The finished wire diameter in the primary wire drawing after hot rolling is set to 1.3 mmφ or less, which is different from that of pearlite steel. Also, if the finish is less than 0.6 mmφ, the wire characteristics obtained by subsequent processing deteriorate, so 0.6 mm
φ or more.
【0020】[0020]
【実施例】表1に示す成分元素の鋼を用いて、表2に示
す製造条件に従ってスチールコードを製造した。EXAMPLES Steel cords were manufactured by using the steels having the constituent elements shown in Table 1 according to the manufacturing conditions shown in Table 2.
【0021】[0021]
【表1】 [Table 1]
【0022】[0022]
【表2】 [Table 2]
【0023】試料番号1〜10は本発明例用の試料で、
試料番号11〜14は比較例用の試料である。Sample Nos. 1 to 10 are samples for the examples of the present invention.
Sample numbers 11 to 14 are samples for comparative examples.
【0024】製造工程は図1に示す通りで、熱間圧延後
の調整冷却によって製造された4.5〜6.5mmφの
線材を伸線加工により最終パテンティング処理を行う線
径とした。このワイヤに最終パテンティング処理を行っ
た後、ブラスめっきを行い、さらに最終湿式伸線を行い
最終ワイヤとした。The manufacturing process is as shown in FIG. 1, and a wire diameter of 4.5 to 6.5 mmφ manufactured by controlled cooling after hot rolling was set to a wire diameter for final patenting treatment by wire drawing. After performing the final patenting treatment on this wire, brass plating was performed, and further final wet drawing was performed to obtain a final wire.
【0025】表2の組織率は、線材横断面に存在するセ
メンタイトにおいて、そのアスペクト比が10以下とな
るセメンタイトの存在率を示している。The microstructures shown in Table 2 indicate the abundance of cementite existing in the cross section of the wire rod and having an aspect ratio of 10 or less.
【0026】表2の一次伸線最終径実績は、伸線過程の
試料を取り出し、捻回試験においてデラミネーションの
発生しない限界のワイヤ試料径を示している。The actual final diameter of the primary wire drawing in Table 2 shows the diameter of the wire sample, which is the limit at which delamination does not occur in the twisting test after taking out the sample in the wire drawing process.
【0027】表2の撚り線時の断線数は、試料4000
mを2本撚りで撚り線加工した際の断線回数を示してい
る。The number of breaks in the stranded wire in Table 2 is 4000
The number of wire breakages when the twisted wire is processed by twisting m into two strands is shown.
【0028】本発明法に従って製造された試料番号1〜
10は、いずれも所定の線径で問題なく伸線が可能であ
り、撚り線加工においても断線を起こしていない。Sample Nos. 1 to 1 produced according to the method of the present invention
No. 10 is capable of wire drawing with a predetermined wire diameter without any problem, and has not been broken even in twisted wire processing.
【0029】試料番号11は恒温変態温度が低いため、
所定の組織率となってはいるが、圧延後の強度が高いた
め、一次伸線において目標の線径に到達する前にデラミ
ネーションが発生し、目標の線径まで到達できなかっ
た。Since the sample No. 11 has a low isothermal transformation temperature,
Although it has a predetermined microstructure rate, since the strength after rolling is high, delamination occurred before reaching the target wire diameter in the primary wire drawing, and the target wire diameter could not be reached.
【0030】試料番号12は恒温変態温度が高い水準で
変態温度が高いため層状構造が健全となり、120sの
保持においてもラメラー組織の球状化が促進されず、組
織率が30%と低い値となっている。このため、デラミ
ネーションが一次伸線の1.20mmφで発生し、目標
のワイヤ径まで到達できなかった。Sample No. 12 has a high isothermal transformation temperature and a high transformation temperature, so that the layered structure is sound, the spheroidization of the lamellar structure is not promoted even after 120 s is retained, and the structure ratio is as low as 30%. ing. Therefore, delamination occurred at the primary wire drawing of 1.20 mmφ and the target wire diameter could not be reached.
【0031】試料番号13は冷却速度が異なる水準で、
冷却速度が低いためパーライト組織が出現し、その後の
セメンタイトの分断が進んでいない。このため、デラミ
ネーションが一次伸線の1.20mmφで発生し、目標
の線径まで伸線加工はできたものの、ワイヤ内部に欠陥
を含んでいるため、強度と延性が低下している。Sample No. 13 has different cooling rates,
Since the cooling rate is low, a pearlite structure appears, and subsequent fragmentation of cementite has not progressed. For this reason, delamination occurred at the primary wire drawing of 1.20 mmφ, and although wire drawing could be performed up to the target wire diameter, since the wire contains defects, the strength and ductility are reduced.
【0032】試料番号14は変態終了後の保持温度が4
50℃より低い水準で、変態後の保持温度が低いため、
組織率が低くなっている。このため、最終ワイヤまで製
造できてはいるが、撚り線加工における断線回数が多く
なっている。Sample No. 14 has a holding temperature of 4 after the transformation.
At a level lower than 50 ° C, the holding temperature after transformation is low, so
The organization rate is low. For this reason, although the final wire can be manufactured, the number of breaks in the twisted wire processing is large.
【0033】[0033]
【発明の効果】4.5〜6.5mmφの熱間圧延線材か
らの伸線加工によるスチールコードの製造において、熱
間圧延線材と最終ワイヤの間において最低限必要な1回
のパテンティング処理によって素線の引張強さが280
0MPa以上のスチールコードが製造可能となる。INDUSTRIAL APPLICABILITY In the production of a steel cord by wire drawing from a hot-rolled wire having a diameter of 4.5 to 6.5 mm, a minimum required one patenting treatment is performed between the hot-rolled wire and the final wire. The tensile strength of the wire is 280
A steel cord of 0 MPa or more can be manufactured.
【図1】本発明の製造工程を示す図である。FIG. 1 is a diagram showing a manufacturing process of the present invention.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.5 識別記号 庁内整理番号 FI 技術表示箇所 C22C 38/18 (72)発明者 落合 征雄 千葉県君津市君津1 新日本製鐵株式会社 君津製鐵所内─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 5 Identification number Internal reference number FI Technical display location C22C 38/18 (72) Inventor Masao Ochiai 1 Kimitsu, Kimitsu-shi, Chiba Nippon Steel Corporation Kimitsu Co., Ltd. Inside the ironworks
Claims (2)
不可避的に入るAl含有量を0.003%以下とした
4.5〜6.5mmφの熱間圧延線材に、線材横断面に
存在するアスペクト比が10以下であるセメンタイトの
存在率が75%以上となる調整冷却を行い、その後伸線
加工により0.6〜1.3mmφのワイヤとし、その後
最終パテンティング処理を行い、さらにブラスめっき処
理を行った後、最終湿式伸線加工により0.10〜0.
3mmφで引張強さ2800MPa以上のワイヤとし、
その後撚り合わせてコードとすることを特徴とするスチ
ールコードの製造方法。1. By weight%, C 0.80% or more and 0.90% or less, Si 0.1% or more and 1.5% or less, Mn 0.1% or more and 1.0% or less, and if necessary Cr 0. 10% or more and 1.0% or less, balance iron and inevitable impurities, and
The abundance of cementite having an aspect ratio of 10 or less in the cross section of the wire in a hot-rolled wire of 4.5 to 6.5 mmφ with an Al content of unavoidably 0.003% or less is 75% or more. After adjusting and cooling, a wire having a diameter of 0.6 to 1.3 mmφ is drawn by wire drawing, then a final patenting process is performed, and a brass plating process is further performed. 0.
Wire with 3 mmφ and tensile strength of 2800 MPa or more,
A method for manufacturing a steel cord, which is characterized by twisting the cords into cords thereafter.
線材を800℃以上1100℃以下の温度範囲から50
℃/s以上の冷却速度で450℃以上550℃以下の温
度に冷却した後450℃以上550℃以下の温度範囲で
変態を終了させ、さらに必要に応じて450℃以上に1
20s以内保持し、室温まで冷却することを特徴とする
請求項1記載のスチールコードの製造方法。2. As the conditioning cooling, the wire rod after the hot rolling is finished is heated in a temperature range from 800 ° C. to 1100 ° C.
After cooling to a temperature of 450 ° C. or higher and 550 ° C. or lower at a cooling rate of C ° C./s or higher, the transformation is completed within a temperature range of 450 ° C. or higher and 550 ° C.
The method for manufacturing a steel cord according to claim 1, wherein the steel cord is held for 20 seconds and cooled to room temperature.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3347703A JP2641081B2 (en) | 1991-12-04 | 1991-12-04 | Steel cord manufacturing method |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3347703A JP2641081B2 (en) | 1991-12-04 | 1991-12-04 | Steel cord manufacturing method |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH05156369A true JPH05156369A (en) | 1993-06-22 |
JP2641081B2 JP2641081B2 (en) | 1997-08-13 |
Family
ID=18392011
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP3347703A Expired - Lifetime JP2641081B2 (en) | 1991-12-04 | 1991-12-04 | Steel cord manufacturing method |
Country Status (1)
Country | Link |
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JP (1) | JP2641081B2 (en) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2006088019A1 (en) * | 2005-02-16 | 2006-08-24 | Nippon Steel Corporation | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
JP2006225701A (en) * | 2005-02-16 | 2006-08-31 | Nippon Steel Corp | Steel wire rod excellent in cold-forgeability after spheroidizing-treatment and producing method therefor |
JP2006316291A (en) * | 2005-05-10 | 2006-11-24 | Nippon Steel Corp | Steel wire superior in cold forgeability and manufacturing method therefor |
JP2008127589A (en) * | 2006-11-17 | 2008-06-05 | Kobe Steel Ltd | High-carbon steel wire and its manufacturing method |
JP2011196402A (en) * | 2010-03-17 | 2011-10-06 | Yokohama Rubber Co Ltd:The | Method of manufacturing rubber hose |
CN109972023A (en) * | 2019-05-16 | 2019-07-05 | 武汉科技大学 | A kind of bainitic steel and its preparation method and application with high strength and ductility |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5827926A (en) * | 1981-08-12 | 1983-02-18 | Nippon Steel Corp | Manufacture of wire rod having spheroidal structure |
JPH02263951A (en) * | 1988-12-28 | 1990-10-26 | Nippon Steel Corp | Manufacture of high strength high ductility steel wire rod and high strength high ductility extra thin steel wire |
-
1991
- 1991-12-04 JP JP3347703A patent/JP2641081B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5827926A (en) * | 1981-08-12 | 1983-02-18 | Nippon Steel Corp | Manufacture of wire rod having spheroidal structure |
JPH02263951A (en) * | 1988-12-28 | 1990-10-26 | Nippon Steel Corp | Manufacture of high strength high ductility steel wire rod and high strength high ductility extra thin steel wire |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2006088019A1 (en) * | 2005-02-16 | 2006-08-24 | Nippon Steel Corporation | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
JP2006225701A (en) * | 2005-02-16 | 2006-08-31 | Nippon Steel Corp | Steel wire rod excellent in cold-forgeability after spheroidizing-treatment and producing method therefor |
JP4669300B2 (en) * | 2005-02-16 | 2011-04-13 | 新日本製鐵株式会社 | Steel wire rod excellent in cold forgeability after spheroidizing treatment and method for producing the same |
JP2006316291A (en) * | 2005-05-10 | 2006-11-24 | Nippon Steel Corp | Steel wire superior in cold forgeability and manufacturing method therefor |
JP4669317B2 (en) * | 2005-05-10 | 2011-04-13 | 新日本製鐵株式会社 | Steel wire excellent in cold forgeability and manufacturing method thereof |
JP2008127589A (en) * | 2006-11-17 | 2008-06-05 | Kobe Steel Ltd | High-carbon steel wire and its manufacturing method |
JP4745941B2 (en) * | 2006-11-17 | 2011-08-10 | 株式会社神戸製鋼所 | High carbon steel wire and manufacturing method thereof |
JP2011196402A (en) * | 2010-03-17 | 2011-10-06 | Yokohama Rubber Co Ltd:The | Method of manufacturing rubber hose |
CN109972023A (en) * | 2019-05-16 | 2019-07-05 | 武汉科技大学 | A kind of bainitic steel and its preparation method and application with high strength and ductility |
Also Published As
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