JPH05171276A - Production of carcass cord for passenger car tire - Google Patents
Production of carcass cord for passenger car tireInfo
- Publication number
- JPH05171276A JPH05171276A JP3263607A JP26360791A JPH05171276A JP H05171276 A JPH05171276 A JP H05171276A JP 3263607 A JP3263607 A JP 3263607A JP 26360791 A JP26360791 A JP 26360791A JP H05171276 A JPH05171276 A JP H05171276A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- less
- carcass cord
- treatment
- diameter
- 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
- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 238000000034 method Methods 0.000 claims abstract description 17
- 238000007747 plating Methods 0.000 claims abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 7
- 230000009466 transformation Effects 0.000 claims abstract description 5
- 229910001369 Brass Inorganic materials 0.000 claims abstract description 4
- 239000010951 brass Substances 0.000 claims abstract description 4
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 abstract description 24
- 239000010959 steel Substances 0.000 abstract description 24
- 238000005491 wire drawing Methods 0.000 abstract description 17
- 239000000203 mixture Substances 0.000 abstract description 5
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 239000000463 material Substances 0.000 description 9
- 229910001567 cementite Inorganic materials 0.000 description 8
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 8
- 229910000859 α-Fe Inorganic materials 0.000 description 7
- 238000012733 comparative method Methods 0.000 description 6
- 229910001562 pearlite Inorganic materials 0.000 description 6
- 239000004677 Nylon Substances 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 239000000835 fiber Substances 0.000 description 4
- 229920001778 nylon Polymers 0.000 description 4
- 229920000728 polyester Polymers 0.000 description 4
- 230000003014 reinforcing effect Effects 0.000 description 4
- 229910001563 bainite Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- 241000446313 Lamella Species 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000032798 delamination Effects 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 230000020169 heat generation Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Landscapes
- Tyre Moulding (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (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の補強用に使用される高強度、高延
性の極細線の製造方法に関するものであり、詳しくは、
伸線により直径０．０５mm以上０．０９mm以下であって
引張強さ４５００MPa 以上である高強度、高延性の乗用
車タイヤ用カーカスコードの製造方法に係る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an ultrafine wire of high strength and high ductility, which is used for reinforcing rubber tires of trucks, buses, passenger cars and the like.
The present invention relates to a method for producing a carcass cord for a passenger car tire having a high strength and a high ductility, which has a diameter of 0.05 mm or more and 0.09 mm or less and a tensile strength of 4500 MPa or more by drawing.
【０００２】[0002]
【従来の技術】トラック、バス、乗用車などのゴム製タ
イヤは、必要に応じて直径０．１５〜０．３５mmφのワ
イヤを撚り合わせて作られたスチールコードやナイロ
ン、ポリエステルなどの有機繊維を補強のため埋め込ん
で使用されている。これらゴム製タイヤに使用される補
強線は、線材製品協会、日本線材製品輸出組合編「線材
製品読本」に示されるように、使用される場所によって
大きく３つに分けられ、カーカス部、ブレーカ部、ビー
ド部に使用されている。そして、カーカス部に使用され
る補強線は、トラック、バスにおいてはスチールコード
が使用され、乗用車においては、ナイロン、ポリエステ
ルなどの有機繊維が使用されている。2. Description of the Related Art Rubber tires for trucks, buses, passenger cars, etc. are reinforced with steel cords made of twisted wires having diameters of 0.15 to 0.35 mm and organic fibers such as nylon and polyester as required. It is used because it is embedded. The reinforcing wires used for these rubber tires are roughly divided into three, depending on the place where they are used, as shown in "Wire Material Products Association", "Wire Material Products Association" edited by Japan Wire Material Products Association, carcass part and breaker part. Used in the bead area. The reinforcing wire used in the carcass part is made of steel cord in trucks and buses, and is made of organic fibers such as nylon and polyester in passenger cars.
【０００３】スチールコードは、例えば、（１）放熱効
果が高く発熱が少ない、（２）カーカス部を薄くできる
のでタイヤが軽量化できる、などの長所があるため、ト
ラック、バスなどの大形タイヤにおいてはスチールコー
ドが使用されている。しかし、乗用車用のタイヤの場
合、従来のスチールコードを用いるとタイヤの重量が重
くなるためナイロン、ポリエステルなどの有機繊維が使
用されている。従来開発されているスチールコード用の
極細線として、例えば特開昭６０−２０４８６５号公報
には、Ｍｎ含有量を０．３％未満に規制して鉛パテンテ
ィング後の過冷組織の発生を抑え、Ｃ，Ｓｉ，Ｍｎ等の
元素量を規制することによって、撚り線時の断線が少な
く高強度および高靭延性の極細線およびスチールコード
用高炭素鋼線材が開示されており、また、特開昭６３−
２４０４６号公報には、Ｓｉ含有量を１．００％以上と
することによって鉛パテンティング材の引張強さを高く
して伸線加工率を小さくした高靭性高延性極細線用線材
が開示されている。Steel cords have advantages such as (1) high heat dissipation effect and low heat generation, and (2) tires can be made lighter because the carcass portion can be made thin, so that large-sized tires for trucks, buses, etc. Steel cord is used in. However, in the case of tires for passenger cars, the use of conventional steel cords increases the weight of the tire, so organic fibers such as nylon and polyester are used. As an ultrafine wire for a steel cord that has been conventionally developed, for example, in Japanese Patent Laid-Open No. 60-204865, the Mn content is restricted to less than 0.3% to suppress the generation of a supercooled structure after lead patenting. , C, Si, Mn, and the like, by controlling the amount of elements such as C, Si, Mn, etc., an ultrafine wire with high strength and high ductility and a high carbon steel wire material for steel cord with less breakage at the time of stranded wire are disclosed. 63-
No. 24046 discloses a wire material for high toughness and high ductility extra fine wire in which the tensile strength of the lead patenting material is increased by setting the Si content to be 1.00% or more to reduce the wire drawing work ratio. There is.
【０００４】[0004]
【発明が解決しようとする課題】乗用車に使用されるカ
ーカスコードは従来ナイロン、ポリエステルなどの有機
繊維であり、タイヤの軽量化のためにより高強度な補強
線の出現が期待されている。具体的にはタイヤの軽量
化、高性能化にあわせて、乗用車においてもカーカスコ
ードのスチール化が必要とされ、直径０．０９mm以下で
あって引張強さ４５００MPa 以上のカーカスコード用ワ
イヤの出現が要望されている。Carcass cords used in passenger cars have conventionally been made of organic fibers such as nylon and polyester, and it is expected that higher strength reinforcing wires will appear in order to reduce the weight of tires. Specifically, as the weight and performance of tires have increased, the carcass cord must be made steel for passenger cars as well, and the appearance of wires for carcass cords with a diameter of 0.09 mm or less and a tensile strength of 4500 MPa or more has emerged. Is requested.
【０００５】本発明はこのような要望を充足するカーカ
スコードの製造法を提供することを目的とする。It is an object of the present invention to provide a method for manufacturing a carcass cord that satisfies these needs.
【０００６】[0006]
【課題を解決するための手段】本発明は上記目的を達成
するために、以下の構成を要旨とする。すなわち重量％
で、Ｃ：０．９０％以上１．１０％以下、Ｓｉ：０．４
％以下、Ｍｎ：０．５％以下、Ｃｒ：０．１０％以上
０．３０％以下、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
する熱間圧延線材を用い、中間パテンティング処理を一
回以上挿入する引き抜き加工により線径を０．５０〜
０．９０mmφとし、その後、最終パテンティング処理に
おいて９００〜１０００℃の温度範囲でγ化処理を行な
い、直ちに５６０〜５９０℃の温度範囲で恒温変態処理
を施して引張強さ１４００〜１６００MPa のワイヤと
し、その後さらに１〜３μｍ厚のブラスメッキを行なっ
た後、最終湿式伸線を行ないワイヤ径を５０〜９０μｍ
のワイヤとし、引張強さ４５００MPa 以上のワイヤとす
ることを特徴とする乗用車タイヤ用カーカスコードの製
造方法である。また本発明は引き抜き加工に用いるダイ
スのアプローチ角を８〜１２°にすること、そしてこの
ような方法によって製造して得たカーカスコード用線を
２本以上撚り合わせて用いてもよい。In order to achieve the above object, the present invention has the following structures. Ie% by weight
C: 0.90% or more and 1.10% or less, Si: 0.4
%, Mn: 0.5% or less, Cr: 0.10% or more and 0.30% or less, and the balance iron and unavoidable impurities,
In addition, using a hot-rolled wire rod having an Al content of 0.003% or less, which is inevitable, the wire diameter is 0.50 to 0.50 by a drawing process in which an intermediate patenting treatment is inserted once or more.
0.90 mmφ, and then, in the final patenting treatment, a gamma treatment is performed in the temperature range of 900 to 1000 ° C, and immediately a constant temperature transformation treatment is performed in the temperature range of 560 to 590 ° C to obtain a wire having a tensile strength of 1400 to 1600 MPa. After that, brass plating having a thickness of 1 to 3 μm is further performed, and then final wet drawing is performed to set the wire diameter to 50 to 90 μm.
And a tensile strength of 4500 MPa or more. The method of manufacturing a carcass cord for a passenger car tire is characterized by the following: Further, in the present invention, the approach angle of the die used for drawing may be set to 8 to 12 °, and two or more carcass cord wires produced by such a method may be twisted and used.
【０００７】[0007]
【作用】以下に本発明を詳細に説明する。まず、本発明
の鋼組成を限定した理由は下記のとおりである。通常の
パテンティング処理においてはＣ含有量０．８％近傍の
共析成分においても旧オーステナイト粒界に添って初析
フェライトが析出すること、またこの初析フェライトが
伸線後の延性低下の原因となることを本発明者らは見い
だした。Ｃは経済的かつ有効な強化元素であるが、この
初析セメンタイトの析出量低下にも有効な元素である。
従って引張強さ３６０kgｆ／mm2 以上の極細線とし延性
を高めるためには、Ｃの添加量を０．９０％以上とする
ことが必要であり、高すぎると延性が低下し伸線性が劣
化するのでその上限を１．１０％とする。The present invention will be described in detail below. First, the reasons for limiting the steel composition of the present invention are as follows. In the usual patenting treatment, even in the eutectoid component having a C content of about 0.8%, pro-eutectoid ferrite is precipitated along the former austenite grain boundary, and this pro-eutectoid ferrite causes ductility after wire drawing. The present inventors have found that C is an economical and effective strengthening element, but is also an element effective in reducing the amount of proeutectoid cementite deposited.
Therefore, in order to obtain an ultrafine wire having a tensile strength of 360 kgf / mm 2 or more and to increase the ductility, it is necessary to add C in an amount of 0.90% or more. If it is too high, the ductility decreases and the wire drawability deteriorates. Therefore, the upper limit is set to 1.10%.
【０００８】Ｓｉは鋼の脱酸のために必要な元素であ
り、従ってその含有量があまりに少ない時、脱酸効果が
不十分となる。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０．４％以下とする。Si is an element necessary for deoxidizing steel, and therefore, when its content is too small, the deoxidizing effect becomes insufficient. In addition, Si dissolves in the ferrite phase in pearlite formed after heat treatment to increase the strength after patenting, but on the other hand, it reduces the ductility of ferrite and reduces the ductility of ultrafine wires after drawing, so 0.4% or less. And
【０００９】Ｍｎは鋼の焼き入れ性を確保するために小
量添加することが望ましい。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０．５％以下とする。It is desirable to add a small amount of Mn in order to secure the hardenability of steel. However, the addition of a large amount of Mn causes segregation, and bainite,
Since a supercooled structure called martensite is generated and the wire drawability thereafter is impaired, the content is made 0.5% or less.
【００１０】本発明のような過共析鋼の場合、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、かつ先に述べたようなセメ
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はこのよう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。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Ｃｒ添加量はその効
果が期待できる０．１０％以上とし、フェライト中の転
位密度を増加させ延性を害することの無い０．４０％以
下とする。従来の極細鋼線と同様に延性を確保するため
Ｓの含有量を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。In the case of the hyper-eutectoid steel as in the present invention, a cementite network is likely to occur in the microstructure after patenting, and a cementite having a thickness is likely to precipitate. In order to realize high strength and high ductility in this steel, it is necessary to make pearlite fine and to eliminate the cementite network and thick cementite as described above. Cr has the effect of suppressing the appearance of such abnormal portions of cementite and further refining pearlite. However, a large amount of addition increases the dislocation density in the ferrite after the heat treatment, and therefore significantly impairs the ductility of the ultrafine wire after drawing. Therefore, the addition amount of Cr is set to 0.10% or more, which is expected to be effective, and is set to 0.40% or less, which does not impair ductility by increasing dislocation density in ferrite. The content of S is set to 0.020% or less in order to secure the ductility similarly to the conventional ultra-fine steel wire, and P is also set to 0.020% or less because it also impairs the ductility of the wire rod like S. desirable.
【００１１】極細線の延性を低下させる原因としてＡｌ
2 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。Al is a cause of reducing the ductility of the ultrafine wire.
There are non-ductile inclusions containing Al 2 O 3 as a main component, such as 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.
【００１２】このように本発明における極細線用線材に
おいては、パテンティング処理後の強度増加のためＣ量
を増加し、これによる初析セメンタイトの出現とパーラ
イトラメラーの形状悪化をＣｒを添加することで抑制
し、パーライトの微細化による強度増加を実現した。ま
た、パーライトが微細化されることによりセメンタイト
層の延性が従来鋼並となった。さらにＣｒ，Ｓｉ，Ｍｎ
の添加量を低く抑えることでフェライト相の延性を従来
鋼と同程度に保ち、材料の延性増加を実現した。このよ
うな組織微細化のみによるパテンティング処理後の強度
増加を実現する成分設計により、パテンティング後の強
度と延性を従来鋼以上に高めることに成功した。従っ
て、パテンティング後の強度を高めているにもかかわら
ず、引き抜き加工率を上げて製造した極細線の延性劣化
が従来鋼並にとどまり、高強度と高延性が可能となっ
た。As described above, in the wire for ultrafine wire according to the present invention, the amount of C is increased due to the increase in strength after patenting treatment, and the addition of Cr causes the appearance of proeutectoid cementite and the deterioration of the shape of pearlite lamella. The increase in strength was realized by reducing the size of pearlite. In addition, the ductility of the cementite layer became comparable to that of conventional steel due to the refinement of pearlite. Furthermore, Cr, Si, Mn
By keeping the addition amount of Fe to a low level, the ductility of the ferrite phase was maintained at the same level as conventional steel, and the ductility of the material was increased. We succeeded in increasing the strength and ductility after patenting more than the conventional steel by designing the components that realize the increase in strength after patenting treatment only by the refinement of the structure. Therefore, although the strength after patenting is increased, the deterioration of ductility of the ultrafine wire produced by increasing the drawing rate is as low as that of conventional steel, and high strength and high ductility are possible.
【００１３】次に本発明の製造方法を限定した理由は以
下の通りである。最終パテンティング処理の際のワイヤ
の線径が０．５mmφ未満となった場合、０．０５以上
０．０９mmφ以下のワイヤにおいて４５００MPa 以上の
強度のワイヤを得ることができない。また、０．９０mm
φを越えた場合には５０〜８０μｍのワイヤとした場合
の強度が高くなりすぎ、ワイヤ延性が低下しデラミネー
ション（ワイヤの縦割れ）が起こりやすくなるので０．
９０mmφ以下とする。The reason why the manufacturing method of the present invention is limited is as follows. When the wire diameter of the wire during the final patenting treatment is less than 0.5 mmφ, a wire having a strength of 4500 MPa or more cannot be obtained from a wire having a diameter of 0.05 or more and 0.09 mmφ or less. Also, 0.90 mm
If it exceeds φ, the strength of a wire of 50 to 80 μm becomes too high, the wire ductility decreases, and delamination (longitudinal cracking of the wire) easily occurs.
90mmφ or less.
【００１４】直径０．０９mm以下であって引張強さ４５
００MPa 以上の強度を得るためには、最終パテンティン
グ処理の際の加熱温度は炭化物の再固溶が十分に進む９
００℃以上にし、またγ粒の成長が進み過ぎない１００
０℃以下で行なう必要がある。A diameter of 0.09 mm or less and a tensile strength of 45
In order to obtain a strength of 00 MPa or higher, the heating temperature during the final patenting treatment is such that the solid solution of carbides proceeds sufficiently 9
100 ° C or higher, and γ grain growth does not proceed too much 100
It must be performed at 0 ° C or lower.
【００１５】恒温変態温度はベイナイトの析出量が発生
しない５６０℃以上とし、必要以上に強度の低下しない
５９０℃以下とする。The isothermal transformation temperature is 560 ° C. or higher at which precipitation of bainite does not occur, and 590 ° C. or lower at which strength is not unnecessarily lowered.
【００１６】前述のようにしてパテンティング処理され
たパテンティング材の引張強さを少なくとも１４００MP
a 以上に調整する必要があり、最も強度の出やすい場合
でも１６００MPa 以下にしなければ、ベイナイト等の異
常部が出現し延性が低下する。The patenting material patented as described above has a tensile strength of at least 1400 MPa.
It is necessary to adjust it to a or more, and even if the strength is most likely to be obtained, unless it is set to 1600 MPa or less, an abnormal part such as bainite appears and ductility decreases.
【００１７】最終パテンティング処理後に行なうめっき
処理は、１μｍ未満の場合、伸線減面率が高いために、
伸線後のワイヤに十分なめっきが残存せずタイヤに埋め
込む際の密着性を著しく害するためめっき厚を１μｍ以
上とする。めっき厚さが３μｍを越えた場合、伸線加工
の際にめっき部が剥離されやすくなるので３μｍ以下と
する。When the plating treatment performed after the final patenting treatment is less than 1 μm, the area reduction ratio of the wire drawing is high.
The plating thickness is set to 1 μm or more, because sufficient plating does not remain on the drawn wire and adhesion to the tire is significantly impaired. If the plating thickness exceeds 3 μm, the plated portion is easily peeled off during wire drawing, so the thickness is set to 3 μm or less.
【００１８】乗用車用カーカスコードの場合、ワイヤ径
が０．０５mmφ未満となった場合、撚り線加工が著しく
困難になるので０．０５mmφ以上とする。また、ワイヤ
径が０．０９mmを越えた場合、４５００MPa 以上の強度
を得ることが困難になるので０．０９mmφ以下とする。In the case of a car cascode for passenger cars, if the wire diameter is less than 0.05 mmφ, it becomes extremely difficult to process the stranded wire, so the wire diameter is set to 0.05 mmφ or more. If the wire diameter exceeds 0.09 mm, it becomes difficult to obtain a strength of 4500 MPa or more, so the wire diameter is set to 0.09 mmφ or less.
【００１９】本発明法の場合、従来のスチールコードに
比べＣ添加量が高いため、伸線加工初期の加工性が低下
している。そこで、従来用いられているダイスのアプロ
ーチ角が１４°を基準にしたダイスではなく、アプロー
チ角が１０°を基準にして８°〜１２°の引き抜きダイ
スを用いるのが望ましい。これは、低角度のアプローチ
角を持つダイスを用いると伸線加工中の中心部に働く圧
縮応力成分が大きくなるため、より均一な加工となり、
伸線加工初期に発生しやすいマイクロクラックを抑える
ことができるためである。In the case of the method of the present invention, since the amount of C added is higher than that of the conventional steel cord, the workability at the initial stage of wire drawing is deteriorated. Therefore, it is desirable to use a drawing die having an approach angle of 8 ° to 12 ° with reference to an approach angle of 10 °, instead of the die having an approach angle of 14 ° used as a standard. This is because if a die with a low angle of approach is used, the compressive stress component acting on the center during wire drawing will increase, resulting in more uniform processing.
This is because it is possible to suppress microcracks that tend to occur in the initial stage of wire drawing.
【００２０】[0020]
【実施例】表１（化学成分）、および表２（加工条件お
よび特性）に示されるように、本発明法に基づく１〜１
０の製造方法と、比較のために製造方法１１〜１７を用
いてカーカスコードを製造した。製造工程は図１に示す
通りで、熱間圧延によって製造された５．５mmφの線材
を伸線加工とＬＰ処理により最終パテンティング処理を
行なう線径とする。このワイヤに最終パテンティング処
理を行なった後、ブラスメッキを行ない、さらに最終湿
式伸線を行ない最終ワイヤとした。その後、撚り線加工
を行ないカーカスコードとした。撚り線加工性は試料２
０kgを撚り線加工した際の断線回数が１回以内のものを
○で示し、２回以上断線した場合を×で表示した。EXAMPLES As shown in Table 1 (chemical components) and Table 2 (processing conditions and characteristics), 1 to 1 based on the method of the present invention.
A carcass cord was manufactured using the manufacturing method of No. 0 and manufacturing methods 11 to 17 for comparison. The manufacturing process is as shown in FIG. 1, and the wire diameter of the 5.5 mmφ wire rod manufactured by hot rolling is the wire diameter for the final patenting treatment by wire drawing and LP treatment. After the final patenting treatment was performed on this wire, brass plating was performed and final wet drawing was performed to obtain a final wire. After that, a stranded wire was processed to obtain a carcass cord. Twisted wire processability is sample 2
When the number of wire breakages when 0 kg was twisted was less than once, it was indicated by ◯, and when it was broken twice or more, it is indicated by x.
【００２１】[0021]
【表１】 [Table 1]
【００２２】[0022]
【表２】 [Table 2]
【００２３】番号１〜１０は、表１および表２に示され
るように本発明法に従って製造されており、伸線加工に
おいては、表２に示すアプローチ角のダイスを使用して
伸線加工を行なった。これらの本発明鋼は、引張強さ、
絞り、撚り線加工性のいずれも優れた特性を示す。Nos. 1 to 10 are manufactured according to the method of the present invention as shown in Tables 1 and 2. In the wire drawing, the wire having the approach angle shown in Table 2 is used. I did. These invention steels have tensile strength,
Both drawability and stranded wire workability are excellent.
【００２４】比較法１１は本発明法と化学成分が異なる
鋼を用いた場合である。鋼成分が異なるため４５００MP
a 以上の強度が得られていない。比較法１２は本発明法
と最終パテンティングの際の線径が異なる場合である。
初線径が小さいため４５００MPa 以上の強度が得られて
いない。比較法１３は本発明法とγ化温度が異なる場合
である。γ化温度が低いため最終パテンティング後の強
度が１４００MPa 以上得られず、伸線後も４５００MPa
以上の強度が得られていない。また、撚り線加工特性も
悪くなっている。比較法１４は本発明法と最終パテンテ
ィングの際の恒温変態温度が異なる場合である。最終パ
テンティング処理後に１６００MPa 以上の強度が得ら
れ、伸線加工後に５１３０MPa の高強度が得られている
が撚り線加工性が低下している。比較法１５は本発明法
と最終パテンティング処理後のめっき厚が異なる場合で
ある。めっき厚が少ないため伸線時の加工発熱が高く材
料が脆化しているため、絞りが低下している。このた
め、撚り線加工性も悪くなっている。比較法１６は本発
明法と最終湿式伸線後の仕上げ線径が異なる場合であ
る。仕上げ線径が細いため伸線後のワイヤが脆化し、絞
りが低下し、撚り線加工性も悪くなっている。比較法１
７は本発明法と伸線加工の際に用いたダイスアプローチ
角が異なる場合である。伸線後のワイヤ強度は満足して
いるが、伸線加工時のアプローチ角が大きいため、マイ
クロクラックが内在し、撚り線加工特性が悪くなってい
る。Comparative method 11 is a case where a steel having a chemical composition different from that of the method of the present invention is used. 4500MP due to different steel composition
The strength above a is not obtained. Comparative method 12 is a case where the wire diameter at the time of final patenting is different from that of the method of the present invention.
Since the initial wire diameter is small, a strength of 4500 MPa or more has not been obtained. Comparative method 13 is different from the method of the present invention in the γ-forming temperature. Since the γ-forming temperature is low, the strength after final patenting was not 1400 MPa or more, and it was 4500 MPa even after wire drawing.
The above strength is not obtained. In addition, the twisted wire processing characteristics are also poor. Comparative method 14 is different from the method of the present invention in the isothermal transformation temperature at the time of final patenting. A strength of 1600 MPa or more was obtained after the final patenting treatment, and a high strength of 5130 MPa was obtained after the wire drawing, but the twistability was poor. Comparative method 15 is a case where the plating thickness after the final patenting treatment is different from the method of the present invention. Since the plating thickness is small, the heat generated during processing during wire drawing is high and the material becomes brittle, so the drawing is reduced. For this reason, the twisted wire processability is also poor. Comparative method 16 is different from the method of the present invention in the finished wire diameter after the final wet drawing. Since the finished wire diameter is small, the wire after drawing becomes brittle, the drawing is reduced, and the stranded wire workability is also poor. Comparison method 1
No. 7 is different from the method of the present invention in the die approach angle used in wire drawing. Although the wire strength after wire drawing is satisfactory, since the approach angle during wire drawing is large, microcracks are inherent and the twisted wire processing characteristics are poor.
【００２５】[0025]
【発明の効果】本発明の製造方法によると直径０．０５
mm以上０．０９mm以下であって引張強さ５０００MPa 以
上のカーカス用ワイヤおよび、これを撚り合わせて製造
されたカーカス用コードを得ることができる。According to the manufacturing method of the present invention, the diameter is 0.05.
It is possible to obtain a carcass wire having a tensile strength of 5000 MPa or more and a carcass cord manufactured by twisting the wires together, which has a tensile strength of 5000 MPa or more.
【図１】実施例の試料の製造工程を示す。FIG. 1 shows a manufacturing process of a sample of an example.
Claims (3)
入るＡｌ含有量を０．００３％以下とする熱間圧延線材
を用い、中間パテンティング処理を一回以上挿入する引
き抜き加工により線径を０．５０〜０．９０mmφとし、
その後、最終パテンティング処理において９００〜１０
００℃の温度範囲でγ化処理を行ない、直ちに５６０〜
５９０℃の温度範囲で恒温変態処理を施して引張強さ１
４００〜１６００MPa のワイヤとし、その後さらに１〜
３μｍ厚のブラスメッキを行なった後、最終湿式伸線を
行ないワイヤ径を５０〜９０μｍのワイヤとし、引張強
さ４５００MPa 以上のワイヤとすることを特徴とする乗
用車タイヤ用カーカスコードの製造方法。1. By weight%, C: 0.90% or more and 1.10% or less, Si: 0.4% or less, Mn: 0.5% or less, Cr: 0.10% or more and 0.30% or less, A hot-rolled wire rod consisting of the balance iron and unavoidable impurities and having an unavoidable Al content of 0.003% or less is used, and the wire diameter is reduced to 0 by performing an intermediate patenting treatment one or more times. .50-0.90 mmφ,
Then, in the final patenting process, 900 to 10
Gamma treatment is performed in the temperature range of 00 ° C, and immediately 560-
Tensile strength 1 by constant temperature transformation treatment in the temperature range of 590 ℃
400 ~ 1600MPa wire, then 1 ~
A method for producing a carcass cord for a passenger car tire, which comprises performing brass plating with a thickness of 3 μm, and then performing final wet drawing to obtain a wire having a wire diameter of 50 to 90 μm and a tensile strength of 4500 MPa or more.
１２°の引き抜きダイスを使用することを特徴とする請
求項１記載の乗用車タイヤ用カーカスコードの製造方
法。2. An approach angle of 8 to 8 during drawing.
The carcass cord manufacturing method for a passenger car tire according to claim 1, wherein a 12 ° drawing die is used.
カーカスコード用線を２本以上に撚り合わせたことを特
徴とする乗用車タイヤ用カーカスコードの製造方法。3. Produced according to claim 1 or 2,
A method for producing a carcass cord for passenger car tires, characterized in that two or more carcass cord wires are twisted together.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3263607A JP2996786B2 (en) | 1991-10-11 | 1991-10-11 | Manufacturing method of carcass cord for passenger car tire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3263607A JP2996786B2 (en) | 1991-10-11 | 1991-10-11 | Manufacturing method of carcass cord for passenger car tire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05171276A true JPH05171276A (en) | 1993-07-09 |
| JP2996786B2 JP2996786B2 (en) | 2000-01-11 |
Family
ID=17391894
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3263607A Expired - Fee Related JP2996786B2 (en) | 1991-10-11 | 1991-10-11 | Manufacturing method of carcass cord for passenger car tire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2996786B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013081982A (en) * | 2011-10-07 | 2013-05-09 | Nippon Steel & Sumitomo Metal Corp | Extra-fine steel wire having excellent delamination-resistance characteristics and method for manufacturing the same |
-
1991
- 1991-10-11 JP JP3263607A patent/JP2996786B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013081982A (en) * | 2011-10-07 | 2013-05-09 | Nippon Steel & Sumitomo Metal Corp | Extra-fine steel wire having excellent delamination-resistance characteristics and method for manufacturing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2996786B2 (en) | 2000-01-11 |
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