JP6572783B2 - Plating steel wire, rubber composite using the same, and method for producing plated steel wire - Google Patents
Plating steel wire, rubber composite using the same, and method for producing plated steel wire Download PDFInfo
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- 238000007747 plating Methods 0.000 title claims description 211
- 229910000831 Steel Inorganic materials 0.000 title claims description 127
- 239000010959 steel Substances 0.000 title claims description 127
- 239000005060 rubber Substances 0.000 title claims description 67
- 239000002131 composite material Substances 0.000 title claims description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 18
- 229910001369 Brass Inorganic materials 0.000 claims description 122
- 239000010951 brass Substances 0.000 claims description 122
- 239000000203 mixture Substances 0.000 claims description 63
- 229910052802 copper Inorganic materials 0.000 claims description 37
- 229910052725 zinc Inorganic materials 0.000 claims description 24
- 229910052782 aluminium Inorganic materials 0.000 claims description 18
- 239000012535 impurity Substances 0.000 claims description 8
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 claims description 6
- 239000003795 chemical substances by application Substances 0.000 claims description 2
- 239000010410 layer Substances 0.000 description 126
- 239000010949 copper Substances 0.000 description 86
- 238000005491 wire drawing Methods 0.000 description 69
- 239000011701 zinc Substances 0.000 description 54
- 238000006243 chemical reaction Methods 0.000 description 23
- 230000006866 deterioration Effects 0.000 description 22
- 238000000034 method Methods 0.000 description 21
- 238000009792 diffusion process Methods 0.000 description 20
- 239000000853 adhesive Substances 0.000 description 17
- 230000001070 adhesive effect Effects 0.000 description 17
- 238000012360 testing method Methods 0.000 description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 16
- 238000010438 heat treatment Methods 0.000 description 16
- 238000004073 vulcanization Methods 0.000 description 13
- 229910007570 Zn-Al Inorganic materials 0.000 description 12
- 229910045601 alloy Inorganic materials 0.000 description 12
- 239000000956 alloy Substances 0.000 description 12
- 230000007423 decrease Effects 0.000 description 10
- 229910052717 sulfur Inorganic materials 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- 239000000463 material Substances 0.000 description 9
- ROOXNKNUYICQNP-UHFFFAOYSA-N ammonium persulfate Chemical compound [NH4+].[NH4+].[O-]S(=O)(=O)OOS([O-])(=O)=O ROOXNKNUYICQNP-UHFFFAOYSA-N 0.000 description 8
- 239000002245 particle Substances 0.000 description 8
- 230000008569 process Effects 0.000 description 8
- 239000012779 reinforcing material Substances 0.000 description 8
- 239000000243 solution Substances 0.000 description 8
- 230000005484 gravity Effects 0.000 description 7
- 229910052742 iron Inorganic materials 0.000 description 7
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 6
- 230000003014 reinforcing effect Effects 0.000 description 6
- 229910000730 Beta brass Inorganic materials 0.000 description 5
- 230000032683 aging Effects 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 238000009616 inductively coupled plasma Methods 0.000 description 5
- 239000012670 alkaline solution Substances 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- VSCWAEJMTAWNJL-UHFFFAOYSA-K aluminium trichloride Chemical compound Cl[Al](Cl)Cl VSCWAEJMTAWNJL-UHFFFAOYSA-K 0.000 description 4
- 229910001870 ammonium persulfate Inorganic materials 0.000 description 4
- 238000009713 electroplating Methods 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- HHVIBTZHLRERCL-UHFFFAOYSA-N sulfonyldimethane Chemical compound CS(C)(=O)=O HHVIBTZHLRERCL-UHFFFAOYSA-N 0.000 description 4
- 229910017773 Cu-Zn-Al Inorganic materials 0.000 description 3
- 229910021529 ammonia Inorganic materials 0.000 description 3
- 238000004458 analytical method Methods 0.000 description 3
- 239000010419 fine particle Substances 0.000 description 3
- 150000002500 ions Chemical class 0.000 description 3
- 239000000314 lubricant Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 239000011550 stock solution Substances 0.000 description 3
- NLXLAEXVIDQMFP-UHFFFAOYSA-N Ammonia chloride Chemical compound [NH4+].[Cl-] NLXLAEXVIDQMFP-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- XLOMVQKBTHCTTD-UHFFFAOYSA-N Zinc monoxide Chemical compound [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 239000012790 adhesive layer Substances 0.000 description 2
- 239000007864 aqueous solution Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005238 degreasing Methods 0.000 description 2
- PEVJCYPAFCUXEZ-UHFFFAOYSA-J dicopper;phosphonato phosphate Chemical compound [Cu+2].[Cu+2].[O-]P([O-])(=O)OP([O-])([O-])=O PEVJCYPAFCUXEZ-UHFFFAOYSA-J 0.000 description 2
- 238000004993 emission spectroscopy Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 125000000101 thioether group Chemical group 0.000 description 2
- JIAARYAFYJHUJI-UHFFFAOYSA-L zinc dichloride Chemical compound [Cl-].[Cl-].[Zn+2] JIAARYAFYJHUJI-UHFFFAOYSA-L 0.000 description 2
- NWONKYPBYAMBJT-UHFFFAOYSA-L zinc sulfate Chemical compound [Zn+2].[O-]S([O-])(=O)=O NWONKYPBYAMBJT-UHFFFAOYSA-L 0.000 description 2
- 229910000368 zinc sulfate Inorganic materials 0.000 description 2
- 229960001763 zinc sulfate Drugs 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 235000008733 Citrus aurantifolia Nutrition 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910017777 Cu—Al—Zn Inorganic materials 0.000 description 1
- 235000011941 Tilia x europaea Nutrition 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 235000019270 ammonium chloride Nutrition 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000002585 base Substances 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 239000006229 carbon black Substances 0.000 description 1
- 239000011362 coarse particle Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 229910000365 copper sulfate Inorganic materials 0.000 description 1
- ARUVKPQLZAKDPS-UHFFFAOYSA-L copper(II) sulfate Chemical compound [Cu+2].[O-][S+2]([O-])([O-])[O-] ARUVKPQLZAKDPS-UHFFFAOYSA-L 0.000 description 1
- 238000004132 cross linking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000012153 distilled water Substances 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000004571 lime Substances 0.000 description 1
- 230000005923 long-lasting effect Effects 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- QIQXTHQIDYTFRH-UHFFFAOYSA-N octadecanoic acid Chemical compound CCCCCCCCCCCCCCCCCC(O)=O QIQXTHQIDYTFRH-UHFFFAOYSA-N 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000009257 reactivity Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000011592 zinc chloride Substances 0.000 description 1
- 235000005074 zinc chloride Nutrition 0.000 description 1
- 239000011787 zinc oxide Substances 0.000 description 1
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- Ropes Or Cables (AREA)
- Tires In General (AREA)
- Metal Extraction Processes (AREA)
- Electroplating Methods And Accessories (AREA)
Description
本発明は、タイヤ用のスチールコードなど、各種ゴム製品の補強材に使用される、表面にめっきが施されたゴム組成物との接着性に優れためっき鋼線、及びそのめっき鋼線を用いたゴム複合体、並びにめっき鋼線の製造方法に関するものである。 The present invention uses a plated steel wire excellent in adhesion to a rubber composition having a surface plated, and a plated steel wire used as a reinforcing material for various rubber products such as steel cords for tires. The present invention relates to a conventional rubber composite and a method for producing a plated steel wire.
ゴム補強材、例えば、タイヤの補強材として使用されているスチールコードには、表面にＣｕとＺｎの合金であるブラスめっきが形成されている。このスチールコードを、未加硫ゴムに埋め込み、加硫処理することにより、ブラスメッキは、スチールコードとゴムとを接着させる作用を発揮する。 A steel cord used as a rubber reinforcing material, for example, a tire reinforcing material, is formed with brass plating, which is an alloy of Cu and Zn, on its surface. By embedding this steel cord in unvulcanized rubber and subjecting it to vulcanization treatment, the brass plating exhibits an effect of bonding the steel cord and rubber.
通常、スチールコード上のブラスめっきは、鋼線に電気Ｃｕめっきと電気Ｚｎめっきを連続して施し、層状とした後に、加熱してＣｕとＺｎを合金化することで形成する。 Usually, brass plating on a steel cord is formed by continuously applying electric Cu plating and electric Zn plating to a steel wire to form a layer, and then heating to alloy Cu and Zn.
ブラスめっき組成のＣｕ比率は、スチールコードとゴムの加硫処理直後の初期接着性を確保するとともに、タイヤ使用時の経年劣化による接着劣化を適正に制御するため、６２〜６５質量％程度の比較的狭い範囲に制御される。 The Cu ratio of the brass plating composition is about 62 to 65% by mass in order to ensure the initial adhesion immediately after vulcanization of the steel cord and rubber and to properly control the adhesion deterioration due to the aging deterioration at the time of tire use. Controlled within a narrow range.
加硫処理は、ゴム製品を製造する際の最終工程であり、１５０〜２００℃に２０〜４０分間加圧、加熱する工程である。加硫処理によって、ブラスめっきとゴムとの界面には接着層が形成され、スチールコードとゴムが直接接着する。この接着層は、ブラスめっきのＣｕおよびＺｎとゴムに含まれるＳ（硫黄）との反応によって形成された硫化物である。 The vulcanization process is a final process when manufacturing a rubber product, and is a process of pressurizing and heating at 150 to 200 ° C. for 20 to 40 minutes. By the vulcanization treatment, an adhesive layer is formed at the interface between the brass plating and the rubber, and the steel cord and the rubber are directly bonded. This adhesive layer is a sulfide formed by a reaction between Cu and Zn of brass plating and S (sulfur) contained in the rubber.
しかし、経年劣化とともにブラスめっき中のＣｕ、Ｚｎとゴム中のＳとの反応が進行して、硫化物層が厚く成長すると共に、硫化物層の組成が変化し、その結果、反応層の密度が低下して接着強度が低下する。そのために、初期接着強度の向上とともに、経年接着劣化を抑制することが望まれている。 However, the reaction between Cu and Zn in brass plating and S in rubber progresses with aging, and the sulfide layer grows thick and the composition of the sulfide layer changes. As a result, the density of the reaction layer Decreases and the adhesive strength decreases. For this purpose, it is desired to improve the initial adhesive strength and to suppress deterioration with time.
この接着劣化問題に対して、各種ブラスめっきが提案されており、Ｃｏを含んだ組成のブラスめっき（特許文献１）、Ｎｉを含む組成のブラスめっき（特許文献２）、また、ブラスめっき中のＣｕ比率を低下し、Ｚｎの犠牲防食を利用してスチールコードの耐食性を改善するもの（特許文献３）等、めっき組成に関して各種提案されている。しかし、ＣｕとＺｎからなるブラスめっきにＣｏ、Ｎｉを含むとめっき層が硬くなり伸線性を悪化させる問題がある。また、Ｃｕ比率を低下させるとブラスめっき層中の硬質なβブラスが増加し、伸線加工性が悪化する問題がある。
また、伸線性と接着性を改善するために、ＣｕとＺｎの組成比を深さ方向で異なるようにしためっき（特許文献４）も提案されている。しかし、複数回めっきを行う必要があり、製造コストに課題がある。
Various types of brass plating have been proposed for this adhesion deterioration problem. Brass plating having a composition containing Co (Patent Document 1), brass plating having a composition containing Ni (Patent Document 2), and brass plating. Various proposals have been made regarding plating compositions, such as those that reduce the Cu ratio and improve the corrosion resistance of steel cords using sacrificial corrosion protection of Zn (Patent Document 3). However, if Co and Ni are contained in brass plating made of Cu and Zn, there is a problem that the plated layer becomes hard and the wire drawing property is deteriorated. Further, when the Cu ratio is lowered, there is a problem that hard β brass in the brass plating layer is increased and wire drawing workability is deteriorated.
Further, in order to improve the drawability and adhesiveness, plating (Patent Document 4) is proposed in which the composition ratio of Cu and Zn is different in the depth direction. However, it is necessary to perform plating a plurality of times, and there is a problem in manufacturing cost.
本発明は、ゴム組成物との初期接着性に優れ、接着強度の経年劣化が少なく、かつ、伸線加工性の良好なめっき鋼線、そのめっき鋼線を用いたゴム複合体、および、めっき鋼線の製造方法を提供するものである。 The present invention is a plated steel wire that is excellent in initial adhesiveness with a rubber composition, has little deterioration over time in adhesive strength, and has good wire drawing workability, a rubber composite using the plated steel wire, and plating A method of manufacturing a steel wire is provided.
本発明者は、上記課題を解決するためのブラスめっき層の組成について鋭意検討した。その結果、ＣｕとＺｎからなる組成にさらにＡｌを加えることでめっき鋼線の伸線加工性を確保しつつ、ブラスめっき層とＳとの反応が抑制されることで、高い初期接着強度を確保でき、かつ、接着強度の経年劣化を抑制することが可能となることを見出して本発明を完成した。 The inventor has intensively studied the composition of the brass plating layer for solving the above-mentioned problems. As a result, the addition of Al to the composition consisting of Cu and Zn ensures high wire-drawing workability of the plated steel wire while suppressing the reaction between the brass plating layer and S, thereby ensuring high initial adhesive strength. The present invention was completed by finding out that it was possible to suppress deterioration with time of the adhesive strength.
本発明の要旨は以下のとおりである。
（１）表面にブラスめっき層を有するめっき鋼線において、前記ブラスめっき層はＣｕ、Ｚｎ、Ａｌおよび不可避的不純物からなり、線径が０．１〜０．３８ｍｍであることを特徴とするめっき鋼線。
（２）表面にブラスめっき層を有するめっき鋼線において、前記ブラスめっき層は、質量％で、Ｃｕ：６０〜７０％、Ａｌ：０．３〜５％を含有し、残部がＺｎ及び不可避的不純物からなり、前記ブラスめっき層の厚さが５０〜５００ｎｍであり、線径が０．１〜０．３８ｍｍであることを特徴とするめっき鋼線。
（３）加硫剤を含有するゴム組成物と（１）または（２）記載のめっき鋼線からなるゴム複合体において、前記めっき鋼線は前記ゴム組成物中に埋設し、前記めっき鋼線と前記ゴム組成物の界面に硫化物が存在することを特徴とするゴム複合体。
（４）表面にブラスめっき層を有するめっき鋼線を湿式伸線加工で製造する方法であって、前記ブラスめっき層はＣｕ、Ｚｎ、Ａｌおよび不可避的不純物からなり、前記湿式伸線加工は、引抜プーリーとめっき鋼線の間で滑りを発生させることなく、めっき鋼線に作用する逆張力を鋼線破断荷重の５〜２０％付与することを特徴とする、めっき鋼線の製造方法。
（５）前記ブラスめっき層の組成が、質量％で、Ｃｕ：６０〜７０％、Ａｌ：０．３〜５％を含有し、残部がＺｎ及び不可避的不純物からなり、前記ブラスめっき層の厚さが５０〜５００ｎｍである（４）記載のめっき鋼線の製造方法。
The gist of the present invention is as follows.
(1) In a plated steel wire having a brass plating layer on the surface, the brass plating layer is made of Cu, Zn, Al and unavoidable impurities, and has a wire diameter of 0.1 to 0.38 mm. Plated steel wire.
(2) In a plated steel wire having a brass plating layer on its surface, the brass plating layer contains, by mass%, Cu: 60 to 70%, Al: 0.3 to 5%, with the balance being Zn and inevitable A plated steel wire comprising impurities, wherein the brass plating layer has a thickness of 50 to 500 nm and a wire diameter of 0.1 to 0.38 mm.
(3) A rubber composite comprising a rubber composition containing a vulcanizing agent and the plated steel wire according to (1) or (2), wherein the plated steel wire is embedded in the rubber composition, and the plated steel wire A rubber composite characterized in that a sulfide is present at the interface between the rubber composition and the rubber composition.
(4) A method for producing a plated steel wire having a brass plating layer on the surface by wet wire drawing, wherein the brass plating layer is composed of Cu, Zn, Al and unavoidable impurities, A method for producing a plated steel wire, wherein reverse tension acting on the plated steel wire is applied 5 to 20% of the breaking load of the steel wire without causing slippage between the drawing pulley and the plated steel wire.
(5) The composition of the brass plating layer contains, by mass%, Cu: 60 to 70%, Al: 0.3 to 5%, the balance being made of Zn and inevitable impurities, and the thickness of the brass plating layer. The manufacturing method of the plated steel wire as described in (4) whose length is 50-500 nm.
本発明のめっき鋼線をタイヤ用のスチールコードとして使用した場合、スチールコードとゴム組成物との接着強度が、加硫直後から良好となり、かつ、タイヤ使用中に高温及び多湿の環境で時間が経過しても接着強度の劣化が小さい。よって、補強効果が高いタイヤを得ることができる。また、本発明のブラスめっき層を有するめっき鋼線を伸線加工する際には、ブラスめっき層表面に生成するＡｌ酸化物が潤滑性を向上させるため、伸線加工性が改善する。タイヤ以外のゴム複合体においても同様の効果が発揮される。 When the plated steel wire of the present invention is used as a steel cord for tires, the adhesive strength between the steel cord and the rubber composition is improved immediately after vulcanization, and time is kept in a high temperature and high humidity environment while using the tire. Even after elapse, the deterioration of the adhesive strength is small. Therefore, a tire having a high reinforcing effect can be obtained. Further, when the plated steel wire having the brass plating layer of the present invention is drawn, the Al oxide generated on the surface of the brass plating layer improves the lubricity, so that the drawing workability is improved. The same effect is exhibited also in rubber composites other than tires.
めっき鋼線とゴム組成物との接着は、めっき鋼線表面のブラスめっき層に含まれるＣｕとゴム組成物に含まれるＳが加硫処理時に反応し、めっき／ゴム界面に主にＣｕ硫化物層を形成することにより発現する。接着強度は接着反応層のＣｕ硫化物の生成状況に依存する。接着反応層の密度が高い場合は接着反応層の組成がＣｕ2Ｓに近い組成となり、高い接着強度が得られるが、過剰に反応した場合は接着反応層が厚くなり、密度が低下すると共に、ＣｕＳに近い組成となり、接着強度は低下すると考えられている。 The adhesion between the plated steel wire and the rubber composition is such that Cu contained in the brass plating layer on the surface of the plated steel wire reacts with S contained in the rubber composition during the vulcanization treatment, and is mainly Cu sulfide at the plating / rubber interface. Expressed by forming a layer. The adhesive strength depends on the state of Cu sulfide formation in the adhesion reaction layer. When the density of the adhesion reaction layer is high, the composition of the adhesion reaction layer becomes a composition close to Cu 2 S, and high adhesion strength is obtained, but when it reacts excessively, the adhesion reaction layer becomes thick, the density decreases, It is considered that the composition becomes close to CuS and the adhesive strength is lowered.
本発明者らは、良好な伸線加工性を確保でき、かつ、ゴム組成物との接着強度の劣化が少ないめっき組成について検討を行い、ＣｕとＺｎからなるブラスめっきに、さらにＡｌを含有させることで、Ｃｕとゴム中のＳとの過剰な反応を制御するとともに、ブラスめっき層の硬さの上昇を抑制できること、さらには、ブラスめっき層表面に生成するＡｌ酸化物によりダイスによる伸線加工性を改善できることを知見した。 The inventors of the present invention have studied a plating composition that can ensure good wire drawing workability and have little deterioration in adhesive strength with a rubber composition, and further include Al in brass plating made of Cu and Zn. Therefore, it is possible to control an excessive reaction between Cu and S in the rubber, and to suppress an increase in the hardness of the brass plating layer, and to draw a wire with an aluminum oxide formed on the surface of the brass plating layer. It was found that the sex could be improved.
さらに詳細に検討を行った結果、ブラスめっき層の厚さ、ブラスめっき層中のＡｌ含有量を適正に制御することでＣｕとＳの過剰反応を効果的に抑制できるとともに、伸線加工性を一層改善できることがわかった。 As a result of further detailed investigations, it is possible to effectively suppress the excessive reaction between Cu and S by appropriately controlling the thickness of the brass plating layer and the Al content in the brass plating layer, and the wire drawing workability is also improved. It was found that it could be improved further.
また、ブラスめっき層にＡｌを含むめっき鋼線を、断線させること無く高速で安定して伸線加工するためには、伸線時にめっき鋼線に作用する引張り荷重を低減することが重要である。本発明者らは、引抜きプーリーとめっき鋼線間での滑りを抑制するためにプーリーとめっき鋼線間の滑りがないように制御したノンスリップ式の湿式伸線機を用い、伸線時の逆張力を適切に制御すること、およびダイス表面にＡｌ酸化物のコーテイング層を形成することで、ダイスとめっき鋼線の摩擦が低減され、より高速で高加工度の伸線が可能できることを知見し、本発明を完成するに至った。 Moreover, in order to stably wire-draw a plated steel wire containing Al in the brass plating layer at a high speed without breaking, it is important to reduce the tensile load acting on the plated steel wire during wire drawing. . The present inventors use a non-slip type wet wire drawing machine controlled so as not to slip between the pulley and the plated steel wire in order to suppress the slip between the drawing pulley and the plated steel wire. We found that by controlling the tension properly and forming a coating layer of Al oxide on the die surface, the friction between the die and the plated steel wire is reduced, and drawing at a higher speed and higher workability is possible. The present invention has been completed.
以下、本発明について、詳細に説明する。 Hereinafter, the present invention will be described in detail.
Ａｌの作用
めっき鋼線の製造工程において、ブラス合金化のための拡散処理は短時間で行う必要があり、その際、ＺｎとＣｕが相互拡散するようにＺｎが溶解する温度まで加熱する必要がある。
本発明の場合、Ｃｕめっき後に、ＺｎとＡｌをめっきするが、５％程度のＡｌを含むＺｎは共晶組成に近くなって純Ｚｎの融点より低下するため、低温加熱でブラス合金化反応が進行する好ましい組成である。
拡散合金化処理により本発明のブラスめっき層は、ほぼ均一なＣｕ−Ｚｎ−Ａｌ組成となる。ブラスめっき層中のＡｌは、Ｃｕの拡散を抑制して、Ｃｕがゴム中Ｓと過剰反応するのを防止するため、経時変化による接着劣化が小さくなる。
また、加熱によりブラスめっき層の表層のＡｌは一部酸化される。Ａｌ酸化物は伸線工程で、ダイス表面に付着して、伸線時の摩擦係数を低減し、伸線加工性を改善する。
Action of Al In the manufacturing process of the plated steel wire, the diffusion treatment for forming the brass alloy needs to be performed in a short time, and at that time, it is necessary to heat to a temperature at which Zn is dissolved so that Zn and Cu are interdiffused is there.
In the case of the present invention, Zn and Al are plated after Cu plating, but Zn containing about 5% Al is close to the eutectic composition and is lower than the melting point of pure Zn. Preferred composition to proceed.
By the diffusion alloying treatment, the brass plating layer of the present invention has a substantially uniform Cu—Zn—Al composition. Al in the brass plating layer suppresses the diffusion of Cu and prevents the Cu from excessively reacting with S in the rubber, so that the deterioration of adhesion due to aging is reduced.
Moreover, a part of Al on the surface of the brass plating layer is oxidized by heating. Al oxide adheres to the surface of the die during the wire drawing process, reduces the coefficient of friction during wire drawing, and improves the wire drawing workability.
線径：０．１〜０．４ｍｍ
めっき鋼線の線径は、しなやかさを得るために、０．４ｍｍ以下とする。これは、線径が０．４ｍｍより太くなり、しなやかさが低下すると、タイヤのゴム補強材に使用した場合に、自動車の乗り心地が低下するためである。また、線径が太くなると、伸線加工率が小さくなる結果、伸線材の強度が低くなり、十分な補強効果が得られない。したがって、めっき鋼線の線径は０．４ｍｍ以下が好ましい。一方、線径を細くすると、製造工程が長くなり、最終製品の生産性も低下するために製造に時間とコストがかかる。さらに、めっき鋼線の比表面積が増加し、ゴム組成物中のＳとブラスめっき層中のＣｕの反応が進行し、本発明のＣｕ−Ｚｎ−Ａｌブラスめっきでも反応を制御することが困難で、十分な接着性を確保できなくなるため、めっき鋼線の線径の下限を０．１ｍｍ以上とすることが好ましい。より好ましくは０．１７〜０．３４ｍｍである。
Wire diameter: 0.1-0.4mm
The diameter of the plated steel wire is set to 0.4 mm or less in order to obtain flexibility. This is because when the wire diameter is thicker than 0.4 mm and the flexibility is lowered, the ride comfort of the automobile is lowered when used as a rubber reinforcing material for a tire. In addition, when the wire diameter is increased, the wire drawing rate is reduced, and as a result, the strength of the wire drawing material is reduced and a sufficient reinforcing effect cannot be obtained. Accordingly, the diameter of the plated steel wire is preferably 0.4 mm or less. On the other hand, if the wire diameter is reduced, the manufacturing process becomes longer, and the productivity of the final product also decreases, so that manufacturing takes time and cost. Furthermore, the specific surface area of the plated steel wire is increased, the reaction between S in the rubber composition and Cu in the brass plating layer proceeds, and it is difficult to control the reaction even in the Cu-Zn-Al brass plating of the present invention. In order to ensure sufficient adhesion, it is preferable to set the lower limit of the diameter of the plated steel wire to 0.1 mm or more. More preferably, it is 0.17 to 0.34 mm.
めっき鋼線の強度は、補強効果を得るため、３２００ＭＰａ以上であることが好ましい。めっき鋼線の地鉄（被めっき鋼線）の成分は必ずしも限定はされないが、強度を確保するため、Ｃ含有量を、０．７〜１．２質量％とすることが好ましい。また、めっき鋼線の地鉄の金属組織は、パーライト組織の面積率が９５％以上で、粒界にフェライトやセメンタイトの析出を抑制することで伸線加工性が良好で高強度のめっき鋼線が製造可能となり、好ましい。 The strength of the plated steel wire is preferably 3200 MPa or more in order to obtain a reinforcing effect. Although the component of the ground iron (to-be-plated steel wire) of a plating steel wire is not necessarily limited, in order to ensure intensity | strength, it is preferable that C content shall be 0.7-1.2 mass%. In addition, the metal structure of the steel core of the plated steel wire has a pearlite structure with an area ratio of 95% or more, suppresses the precipitation of ferrite and cementite at the grain boundaries, and has high wire drawing workability and high strength. Can be manufactured, which is preferable.
本発明のめっき鋼線は、熱間圧延線材を伸線加工して熱処理とブラスめっきを行った後、更に伸線伸線加工を行い、所定の線径に仕上げることで製造される。例えば、線径が３〜５．５ｍｍの熱間圧延された線材を原材料として、これを線径１〜３ｍｍまで伸線加工する。次に、伸線した鋼線に、パテンティング熱処理を行い、引き続き電気めっきにより、Ｃｕめっき、ＺｎめっきおよびＡｌ単独めっき（めっきの順番はＣｕ、Ａｌ、Ｚｎでも可能である）を行う。めっきを行った後に、加熱温度４５０〜５５０℃で５〜１０ｓ加熱して合金化を行い、Ａｌを含むブラスめっき層を得ることが出来る。ここで、Ｃｕめっきはピロリン酸銅、硫酸銅等からなる水系のめっき液が使用可能で、Ｚｎめっきも硫酸亜鉛、塩化亜鉛等の水溶液からなるめっき浴が使用可能である。Ａｌ単独めっきをする場合、Ａｌは水溶液から析出させることができないため、溶剤系のジメチルスルホンと塩化アルミニウム溶液を用いて電気めっきする。 The plated steel wire of the present invention is manufactured by drawing a hot-rolled wire rod, performing heat treatment and brass plating, and further performing wire drawing and finishing to a predetermined wire diameter. For example, using a hot-rolled wire having a wire diameter of 3 to 5.5 mm as a raw material, this is drawn to a wire diameter of 1 to 3 mm. Next, a patenting heat treatment is performed on the drawn steel wire, and subsequently, Cu plating, Zn plating, and Al single plating (the order of plating can be Cu, Al, Zn) is performed by electroplating. After plating, the alloying is performed by heating at a heating temperature of 450 to 550 ° C. for 5 to 10 seconds to obtain a brass plating layer containing Al. Here, Cu plating can use an aqueous plating solution made of copper pyrophosphate, copper sulfate or the like, and Zn plating can also use a plating bath made of an aqueous solution of zinc sulfate, zinc chloride or the like. When Al alone plating is performed, since Al cannot be precipitated from an aqueous solution, electroplating is performed using a solvent-based dimethylsulfone and an aluminum chloride solution.
また、Ｃｕめっきした後、Ａｌ粉末を分散した浴中でＺｎめっきすることによりＺｎ−Ａｌ複合めっきを行い、最後に拡散熱処理する方法、あるいは液中プラズマによるＺｎ−Ａｌ合金めっきを行った後に加熱拡散処理を行うことで、Ａｌを含むブラスめっき層を得る方法も実施可能である。 In addition, after Cu plating, Zn-Al composite plating is performed by Zn plating in a bath in which Al powder is dispersed, and finally, diffusion heat treatment is performed, or heating is performed after performing Zn-Al alloy plating by submerged plasma. A method of obtaining a brass plating layer containing Al by performing a diffusion treatment is also possible.
さらに、Ｃｕめっき後に溶融Ｚｎ−Ａｌ合金めっきする方法もある。この方法では、めっきと同時に合金化されるために好ましい実施形態の一つである。この方法では、Ｃｕめっきの活性を高める必要があり、塩化Ｚｎあるいは塩化アンモニウムを主成分とするフラックス処理後に溶融Ｚｎ−Ａｌ合金めっきを行うことが好ましい。 Furthermore, there is a method of performing hot-dip Zn-Al alloy plating after Cu plating. This method is one of the preferred embodiments because it is alloyed simultaneously with plating. In this method, it is necessary to increase the activity of Cu plating, and it is preferable to perform hot dip Zn—Al alloy plating after the flux treatment mainly containing Zn chloride or ammonium chloride.
以上の方法で製造しためっき線は、更に湿式伸線により、線径が０．１〜０．４ｍｍになるように伸線加工を行う。めっき鋼線の引張り強さは、地鉄（被めっき鋼線）の成分と熱処理以降の伸線加工の加工度によって調整が可能である。 The plated wire produced by the above method is further drawn by wet drawing so that the wire diameter becomes 0.1 to 0.4 mm. The tensile strength of the plated steel wire can be adjusted depending on the composition of the base iron (plated steel wire) and the degree of wire drawing after the heat treatment.
本発明の拡散前のめっき層の構造は、例えば、図１に示すように、地鉄（被めっき鋼線）１の表面に、Ｃｕめっき層２、Ｚｎめっき層３、さらにその上にＡｌめっき層４を形成した３層めっき（ａ）、および地鉄５の表面に、Ｃｕめっき層６，Ａｌ粒子７を分散したＺｎめっき層８を形成した２層めっき（ｂ）であり、これを加熱拡散することで、図２に示す様にめっき層は合金化し、組成の均一なＡｌを含むブラスめっき層９が形成される。
Ａｌは非常に酸化されやすい元素であり、拡散加熱処理によりめっき表面にはＡｌ酸化層が生成されやすい。
The structure of the plating layer before diffusion of the present invention is, for example, as shown in FIG. 1, on the surface of a ground iron (steel wire to be plated) 1, a Cu plating layer 2, a Zn plating layer 3, and an Al plating thereon. The three-layer plating (a) in which the layer 4 is formed, and the two-layer plating (b) in which the Cu plating layer 6 and the Zn plating layer 8 in which the Al particles 7 are dispersed are formed on the surface of the ground iron 5. By diffusing, the plating layer is alloyed as shown in FIG. 2, and a brass plating layer 9 containing Al having a uniform composition is formed.
Al is an element that is very easily oxidized, and an Al oxide layer is easily formed on the plating surface by diffusion heat treatment.
本発明のＡｌを含むブラスめっき層は、加硫工程におけるＣｕとゴム組成物中Ｓの反応、および製品使用中のＣｕとＳの過剰反応を抑制する。また、ブラスめっき層表面のＡｌ酸化物は、伸線時のダイスとめっき鋼線間の摩擦を低減することで断線を防止し、さらに、高速伸線、高加工歪みでの伸線を可能にする。
以下、好ましいブラスめっき層の組成、形態について説明する。なお、ブラスめっき層の組成の「％」は、「質量％」を意味する。
The brass plating layer containing Al of the present invention suppresses the reaction between Cu and S in the rubber composition in the vulcanization process, and the excessive reaction between Cu and S during product use. In addition, the Al oxide on the surface of the brass plating layer prevents wire breakage by reducing the friction between the die and the plated steel wire during wire drawing, and enables wire drawing at high speed and high processing strain. To do.
Hereinafter, a preferable composition and form of the brass plating layer will be described. “%” In the composition of the brass plating layer means “mass%”.
ブラスめっき層中のＡｌ：０．３〜５％
ブラスめっき層中のＡｌは、めっき鋼線とゴム組成物との加硫接着時にＣｕとＳの反応を適正化し、かつ製品使用中の接着劣化を抑制する。また、伸線加工性を改善する。
これらの効果を得るために、ブラスめっき層中のＡｌは、０．３％以上であることが好ましい。一方、過剰なＡｌを含むとＣｕとＳの反応が著しく抑制され、十分な反応層が生成せず、加硫直後の初期接着強度が大きく低下するため、ブラスめっき層中のＡｌは５％以下であることが好ましい。ゴムとの初期接着と接着劣化を改善するには、Ａｌ含有量は０．５〜３％であることがより好ましい。
Al in brass plating layer: 0.3 to 5%
Al in the brass plating layer optimizes the reaction of Cu and S at the time of vulcanization adhesion between the plated steel wire and the rubber composition, and suppresses adhesion deterioration during product use. It also improves wire drawing workability.
In order to obtain these effects, Al in the brass plating layer is preferably 0.3% or more. On the other hand, if excessive Al is contained, the reaction between Cu and S is remarkably suppressed, a sufficient reaction layer is not formed, and the initial adhesive strength immediately after vulcanization is greatly reduced. Therefore, Al in the brass plating layer is 5% or less. It is preferable that In order to improve initial adhesion and adhesion deterioration with rubber, the Al content is more preferably 0.5 to 3%.
ブラスめっき層中のＣｕ：６０〜７０％
ブラスめっき層中のＣｕは、ゴム組成物中のＳと加硫処理時にＣｕ硫化物からなる接着反応層を形成し、接着強度を確保する。
ブラスめっき層中のＣｕが６０％未満では、加硫処理でゴム組成物中のＳとの反応量が減少して、十分な接着強を確保出来なくなる。また、ブラスめっき層中のＣｕが６０％未満では、拡散処理後のブラスめっき層中に硬質な結晶構造であるβブラス相が多く生成し、伸線加工性が低下する。よって、ブラスめっき層中のＣｕ比率は６０％以上であることが好ましい。
一方、ブラスめっき層中のＣｕが多くなるとβブラスの生成が抑制され、ブラスめっき層が柔らかくなるために伸線加工性は良好となるが、ゴム組成物中のＳとＣｕが過剰に反応しやすくなり、接着劣化が発生し易くなる。よって、Ｃｕ含有量は７０％以下が好ましい。
より好ましいＣｕ含有量は６３〜６７％である。
Cu in brass plating layer: 60 to 70%
Cu in the brass plating layer forms an adhesion reaction layer made of Cu sulfide at the time of vulcanization treatment with S in the rubber composition, and ensures adhesion strength.
When Cu in the brass plating layer is less than 60%, the amount of reaction with S in the rubber composition is reduced by vulcanization treatment, and sufficient adhesion strength cannot be secured. If the Cu in the brass plating layer is less than 60%, a lot of β brass phase having a hard crystal structure is generated in the brass plating layer after the diffusion treatment, and the wire drawing workability is lowered. Therefore, the Cu ratio in the brass plating layer is preferably 60% or more.
On the other hand, when the amount of Cu in the brass plating layer increases, the formation of β brass is suppressed and the brass plating layer becomes soft, so that the wire drawing workability is improved. However, S and Cu in the rubber composition react excessively. It becomes easy to cause adhesion deterioration. Therefore, the Cu content is preferably 70% or less.
A more preferable Cu content is 63 to 67%.
なお、めっき鋼線のブラスめっき層中の組成は、以下の方法で分析できる。アンモニア原液に過硫酸アンモニウムを１０％混合したアルカリ溶液にめっき鋼線を浸漬してブラスめっき層を溶解し、溶解液中のＣｕ、Ｚｎ、Ａｌの元素をＩＣＰ（誘導結合プラズマ発光分光分析）あるいは原子吸光分析によりそれぞれの元素の溶液１ｌ当たりの重量から、Ｚｎ、Ａｌ、Ｃｕの全ブラスめっき層重量に対する質量％を求めることができる。 The composition of the plated steel wire in the brass plating layer can be analyzed by the following method. A plated steel wire is immersed in an alkaline solution in which ammonium persulfate is mixed with 10% ammonium persulfate in an ammonia stock solution to dissolve the brass plating layer, and elements of Cu, Zn, and Al in the solution are subjected to ICP (inductively coupled plasma emission spectroscopy) or atoms From the weight per 1 liter of the solution of each element, the mass% with respect to the total brass plating layer weight of Zn, Al, and Cu can be calculated | required by absorption analysis.
ブラスめっき層の厚さ：５０〜５００ｎｍ
Ａｌを含むブラスめっき層の厚さが薄すぎると、めっきを施す前の鋼線の表面の凹凸に起因して、めっき鋼線の表面に、局所的に地鉄が露出した部分（Ｆｅ露出部）が生じることがある。このＦｅ露出部では、めっき鋼線とゴム組成物が接着しないだけではなく、伸線時にダイスとめっき鋼線の直接接触による焼き付きが発生し、伸線材の著しい延性の低下、傷の発生、ダイスの割損によるトラブルとなる。したがって、ブラスめっき層の平均厚さは５０ｎｍ以上にすることが好ましい。一方、ブラスめっき層が厚い場合は、接着反応に関与するＣｕ量が増加し、時間の経過とともに、接着層の成長、接着反応層の密度低下、およびＣｕ硫化物の組成変化により、接着強度が低下することがある。したがって、めっき鋼線とゴム組成物との接着強度の経年劣化を抑制するためには、ブラスめっき層の平均厚さを５００ｎｍ以下にすることが好ましい。より好ましくは、ブラスめっき層の平均厚さは１５０〜３５０ｎｍである。
Brass plating layer thickness: 50-500 nm
When the thickness of the brass plating layer containing Al is too thin, due to the unevenness of the surface of the steel wire before plating, the portion where the ground iron is locally exposed on the surface of the plated steel wire (Fe exposed portion) ) May occur. In this Fe exposed area, not only does the plated steel wire and the rubber composition not adhere, but also seizure occurs due to direct contact between the die and the plated steel wire during wire drawing, resulting in a marked decrease in ductility of the wire drawing material, the occurrence of scratches, and the die. Troubles due to breakage of Therefore, the average thickness of the brass plating layer is preferably 50 nm or more. On the other hand, when the brass plating layer is thick, the amount of Cu involved in the adhesion reaction increases. May decrease. Therefore, in order to suppress the aging deterioration of the adhesive strength between the plated steel wire and the rubber composition, the average thickness of the brass plating layer is preferably set to 500 nm or less. More preferably, the average thickness of the brass plating layer is 150 to 350 nm.
めっき鋼線のブラスめっき層の平均厚さは、以下の方法で求めることができる。はじめに、アンモニア原液に過硫酸アンモニウムを１０％混合したアルカリ溶液にめっき鋼線を浸漬してブラスめっき層を溶解し、ブラスめっき層全質量（Ｗ）を求める。次に、溶解液中のＣｕ、Ｚｎ、Ａｌの元素濃度（Ｗｘ）をＩＣＰ（誘導結合プラズマ発光分光分析）あるいは原子吸光分析によりそれぞれ求め、各金属元素の濃度から、ブラスめっき層の平均比重ρを求める。そして、以下の式（１）でブラスめっき層の平均厚さを計算する。 The average thickness of the brass plating layer of the plated steel wire can be obtained by the following method. First, a plated steel wire is immersed in an alkaline solution in which 10% ammonium persulfate is mixed in an ammonia stock solution to dissolve the brass plating layer, and the total mass (W) of the brass plating layer is obtained. Next, the element concentration (Wx) of Cu, Zn, and Al in the solution is obtained by ICP (inductively coupled plasma emission spectroscopy) or atomic absorption analysis, respectively, and the average specific gravity ρ of the brass plating layer is determined from the concentration of each metal element. Ask for. And the average thickness of a brass plating layer is calculated by the following formula | equation (1).
ブラスめっき層の平均厚さｔ＝Ｗ／（Ａ×ρ） （１）
ただし、ｔ：ブラスめっき層の平均厚さ、Ｗ：単位長さのブラスめっき層の質量、Ａ：単位長さのブラスめっき層の表面積、ρ：ブラスめっき層の平均比重である。ブラスめっき層の平均比重ρは、下記式によって算出することができる。
ρ＝ρCu×ＷCu＋ρＺｎ×ＷＺｎ＋ρＡｌ×ＷＡｌ
ただし、ρCu：Ｃｕの比重、ρＺｎ：Ｚｎの比重、ρＡｌ：Ａｌの比重である。また、ＷCu：ブラスめっき層中Ｃｕの質量比、ＷＺｎ：ブラスめっき層中Ｚｎの質量比、ＷＡｌ：ブラスめっき層中Ａｌの質量比である。
Average thickness of brass plating layer t = W / (A × ρ) (1)
Where t: average thickness of the brass plating layer, W: mass of the brass plating layer of unit length, A: surface area of the brass plating layer of unit length, and ρ: average specific gravity of the brass plating layer. The average specific gravity ρ of the brass plating layer can be calculated by the following formula.
ρ = ρ Cu × W Cu + ρ Zn × W Zn + ρ Al × W Al
However, ρ Cu : specific gravity of Cu, ρ Zn : specific gravity of Zn, and ρ Al : specific gravity of Al. Further, W Cu is a mass ratio of Cu in the brass plating layer, W Zn is a mass ratio of Zn in the brass plating layer, and W Al is a mass ratio of Al in the brass plating layer.
Ａｌは非常に酸化し易い元素であり、めっき後、拡散処理および大気暴露によりブラスめっき層表面の一部のＡｌは酸化物となる。このＡｌ酸化物は伸線加工時にダイス表面と接触し、Ａｌ酸化物の被膜をダイス表面に形成し、めっき鋼線とダイス間の摩擦を低減する作用がある一方、表面のＡｌ酸化物は、加硫時にゴム組成物中のＳとブラスめっき層中のＣｕの反応による接着を抑制する。
よって、ブラスめっき層表面のＡｌ酸化層の生成比率が過度に少ないと、伸線加工性に改善効果が得られにくく逆に過度に多くなるとＣｕとゴム組成物中のＳとの反応が進まず、初期接着性が悪化することがある。
Al is an element that is very easily oxidized, and after plating, a part of Al on the surface of the brass plating layer becomes an oxide by diffusion treatment and exposure to the atmosphere. While this Al oxide is in contact with the die surface during wire drawing, an Al oxide film is formed on the die surface, reducing the friction between the plated steel wire and the die, while the surface Al oxide is Adhesion due to the reaction of S in the rubber composition and Cu in the brass plating layer is suppressed during vulcanization.
Therefore, if the generation ratio of the Al oxide layer on the surface of the brass plating layer is excessively small, it is difficult to obtain an improvement effect on the wire drawing workability, and conversely if excessively large, the reaction between Cu and S in the rubber composition does not proceed. The initial adhesiveness may be deteriorated.
次に、本発明のめっき鋼線の製造工程の例について説明する。図３の製造工程のブロック図に示すように、まず、熱間圧延によって製造した線径が３〜５．５ｍｍの熱間圧延線材を、デスケーリング（図３では省略）後、線径１〜３ｍｍまで伸線加工（乾式伸線）して、コイルに巻き取る。次に、コイルから繰り出した線径１〜３ｍｍの鋼線に、パテンティング熱処理を施し、加工の影響を除去することが好ましい。さらに、必要に応じて、酸洗によるデスケーリング、脱脂のめっき前処理を施し、連続してめっきを施す。 Next, the example of the manufacturing process of the plated steel wire of this invention is demonstrated. As shown in the block diagram of the manufacturing process in FIG. 3, first, a hot-rolled wire having a diameter of 3 to 5.5 mm manufactured by hot rolling is scaled (omitted in FIG. 3), The wire is drawn to 3 mm (dry wire drawing) and wound on a coil. Next, it is preferable to perform a patenting heat treatment on a steel wire with a wire diameter of 1 to 3 mm fed from a coil to remove the influence of processing. Furthermore, if necessary, descaling by pickling and degreasing pretreatment for plating are performed, and plating is continuously performed.
従来のめっき工程は、Ｃｕめっき、Ｚｎめっきで層状めっきを形成した後、４５０〜５５０℃に５〜１０ｓ加熱して合金化処理を行い、ブラスめっき層としていた。一方、本発明では、（１）Ｃｕイオンが溶解しためっき浴中でのＣｕめっき、Ｚｎイオンが溶解しためっき浴中でのＺｎめっき、続いてジメチルスルホンと塩化アルミニウム浴中でのＡｌ電気めっき、（２）同様の方法で、Ｃｕ−Ａｌ−Ｚｎの順にめっき、（３）Ｃｕめっき後、Ｚｎイオンが溶解したＺｎめっき浴にＡｌ粉末を分散させてＺｎ−Ａｌ複合めっき、のいずれかを行った後、従来工程と同様に４５０〜５５０℃で、５〜１０ｓ加熱し、Ａｌを含むブラスめっき層とし、さらに湿式伸線加工を行い、極細のめっき鋼線を製造するものである。また、Ｃｕめっき後にＡｌを含むＺｎめっきを行う方法としては、液中プラズマを利用したＺｎ−Ａｌ合金めっきあるいは溶融Ｚｎ−Ａｌ合金めっきも適用可能であり、溶融めっきの場合は、めっきと同時にブラス合金処理も同時に行うことができる。 In the conventional plating process, after layered plating is formed by Cu plating and Zn plating, alloying treatment is performed by heating at 450 to 550 ° C. for 5 to 10 seconds to form a brass plating layer. On the other hand, in the present invention, (1) Cu plating in a plating bath in which Cu ions are dissolved, Zn plating in a plating bath in which Zn ions are dissolved, followed by Al electroplating in a dimethylsulfone and aluminum chloride bath, (2) In the same manner, either Cu-Al-Zn plating is performed, or (3) After Cu plating, Al powder is dispersed in a Zn plating bath in which Zn ions are dissolved, and Zn-Al composite plating is performed. After that, it is heated at 450 to 550 ° C. for 5 to 10 seconds in the same manner as in the conventional process to form a brass plating layer containing Al, and further wet-drawn to produce an extremely fine plated steel wire. In addition, as a method of performing Zn plating containing Al after Cu plating, Zn-Al alloy plating using molten plasma or hot-dip Zn-Al alloy plating can also be applied. Alloy processing can also be performed simultaneously.
ブラスめっき層の組成の制御は、３層めっきの場合は、ブラスめっき層の厚さで制御可能であり、Ｚｎ−Ａｌ複合めっきのＡｌ濃度はＡｌ分散粒子の濃度、電流密度で制御が可能である。
分散させるＡｌ粒子の大きさは特に限定はされないが、粗い粒子はブラスめっき層に分散する粒子がまだらとなり、合金化遅延となる可能性があり、微細粒子は均一分散性が困難で、微細粒子では凝集が発生し易くなるため、粒子径は０．１〜１μｍが好ましい。Ａｌ粒子は必ずしも球状である必要は無く、厚さが１μｍ以下の偏平粒子形状のものも使用可能である。
プラズマめっきおよび溶融めっきによるＺｎ−Ａｌ合金めっきの場合は合金めっき中のＡｌ濃度を制御することでブラスめっき層中のＡｌ濃度の制御を行うことが可能となる。
The composition of the brass plating layer can be controlled by the thickness of the brass plating layer in the case of three-layer plating, and the Al concentration of the Zn-Al composite plating can be controlled by the concentration of Al dispersed particles and the current density. is there.
The size of the Al particles to be dispersed is not particularly limited, but coarse particles may cause mottled particles dispersed in the brass plating layer, resulting in alloying delay, and fine particles are difficult to disperse uniformly. Then, since aggregation easily occurs, the particle diameter is preferably 0.1 to 1 μm. The Al particles do not necessarily have to be spherical, and flat particles having a thickness of 1 μm or less can be used.
In the case of Zn-Al alloy plating by plasma plating and hot dipping, it is possible to control the Al concentration in the brass plating layer by controlling the Al concentration in the alloy plating.
Ｃｕ−Ｚｎ−Ａｌめっき鋼線はめっき後湿式伸線により線径が０．１〜０．４ｍｍまで伸線することで、補強材として使用可能な極細のめっき鋼線とすることが出来る。ここで、湿式伸線時のめっき剥離を抑制するためには、伸線材表面の摩擦力を低減して伸線することが好ましい。具体的にはダイスと鋼線の間の潤滑性能を高めるために低摩擦係数となる湿式潤滑剤を使用し、引抜キャプスタンとめっき鋼線の間のスリップがないノンスリップ式伸線を行うことで伸線加工時のめっきの剥離が抑制される。従来のスリップ式伸線ではめっき剥離が大きく、ダイスへのＡｌ酸化物のコーテイング作用が得にくい。但し、後述する実施例に示されるように、めっき鋼線の線径、ブラスめっき層の組成、厚さが本発明の範囲内であれば, スリップ式の伸線方法でもゴム組成物との接着性に優れ、伸線加工性に優れためっき鋼線を得ることも可能である。 A Cu-Zn-Al plated steel wire can be made into an extremely fine plated steel wire that can be used as a reinforcing material by drawing the wire diameter to 0.1 to 0.4 mm by wet drawing after plating. Here, in order to suppress plating peeling at the time of wet wire drawing, it is preferable to perform wire drawing while reducing the frictional force on the surface of the wire drawing material. Specifically, in order to improve the lubrication performance between the die and the steel wire, a wet lubricant with a low friction coefficient is used, and non-slip type wire drawing without slip between the drawn capstan and the plated steel wire is performed. Plating peeling during wire drawing is suppressed. In conventional slip-type wire drawing, plating peeling is large, and it is difficult to obtain a coating action of Al oxide on the die. However, as shown in the examples described later, as long as the wire diameter of the plated steel wire, the composition of the brass plating layer, and the thickness are within the scope of the present invention, the slip-type wire drawing method can be bonded to the rubber composition. It is also possible to obtain a plated steel wire having excellent properties and wire drawing workability.
さらに、ノンスリップ式の伸線機を用いて伸線加工する際は、ダイス入り側におけるめっき鋼線の逆張力を制御することが好ましい。伸線材の破断荷重に対する割合（逆張力比）で、５％〜２０％の逆張力を負荷することで、ダイスとめっき鋼線の接触部での面圧が低下して摩擦係数が低下するため、伸線時の断線低減、高速伸線、強加工伸線が可能となり伸線加工性が大きく改善され好ましい。一方、逆張力比が２０％を越えると伸線材に鋼線にかかる負荷が大きくなり、断線が発生し易くなるとともに、ダイスとめっき鋼線間の面圧が低下し、Ａｌ酸化物による摩擦係数低減効果が小さくなり、伸線加工性の改善効果が小さくなる。このため、逆張力比は２０％を上限とすることが好ましい。より好ましい逆張力比は８〜１５％である。 Furthermore, when wire drawing is performed using a non-slip type wire drawing machine, it is preferable to control the reverse tension of the plated steel wire on the die entry side. By applying a reverse tension of 5% to 20% with respect to the breaking load of the wire drawing material (reverse tension ratio), the surface pressure at the contact portion between the die and the plated steel wire is reduced, and the friction coefficient is reduced. It is preferable because wire breakage can be reduced, high-speed wire drawing and strong wire drawing are possible, and wire drawing workability is greatly improved. On the other hand, if the reverse tension ratio exceeds 20%, the load applied to the steel wire on the wire drawing material increases, breakage is likely to occur, the surface pressure between the die and the plated steel wire decreases, and the friction coefficient due to the Al oxide The reduction effect is reduced, and the effect of improving the wire drawing workability is reduced. For this reason, it is preferable that the reverse tension ratio has an upper limit of 20%. A more preferable reverse tension ratio is 8 to 15%.
湿式伸線時の逆張力の制御方法は特に限定はされないが、ダンサー式あるいはモーターのトルク制御による逆張力の制御が可能である。特にダンサー式の逆張力の制御方法はリアルタイムに制御できるため、より高精度の逆張力制御が可能となり、好ましい伸線時の逆張力制御方法である。 The method for controlling the reverse tension at the time of wet drawing is not particularly limited, but the reverse tension can be controlled by a dancer type or motor torque control. In particular, since the dancer-type reverse tension control method can be controlled in real time, it is possible to perform reverse tension control with higher accuracy and is a preferable reverse tension control method during wire drawing.
本発明のめっき鋼線を補強材としてタイヤに適用する場合は、タイヤの走行性能にあわせて適宜複数本撚り合わせ、スチールコードとしてゴムとカーボンブラック、硫黄、酸化亜鉛、その他各種添加剤を配合した原材料を練ったシート状ゴムに埋め込み、補強ベルト構造とする。その後、タイヤ構成部材を貼り合わせて加硫機にセットし、プレス、加熱し、ゴム組成物の強度を発現するための架橋と同時にゴム組成物とめっき鋼線との接着を行い、ゴム組成物とスチールコード（めっき鋼線）からなるゴム複合体を得ることができる。 When the plated steel wire of the present invention is applied to a tire as a reinforcing material, a plurality of wires are appropriately twisted according to the running performance of the tire, and rubber and carbon black, sulfur, zinc oxide, and other various additives are blended as a steel cord. The raw material is embedded in kneaded sheet-like rubber to form a reinforced belt structure. Thereafter, the tire constituent members are bonded together, set in a vulcanizer, pressed and heated, and the rubber composition and the plated steel wire are bonded simultaneously with crosslinking for expressing the strength of the rubber composition. A rubber composite made of steel cord (plated steel wire) can be obtained.
本発明のめっき鋼線の地鉄（被めっき鋼線）の成分は特に限定されないが、Ｃ：０．７〜１．２質量％、Ｓｉ：０．２〜０．５質量％、Ｍｎ：０．２〜０．６質量％、Ｐ：０．０１質量％以下、Ｓ：０．０１質量％以下、Ｃｒ：０．０１〜０．３５質量％の成分を有し、パーライト面積率が９５％以上で、粒界にフェライトやセメンタイトが析出していない組織を有する材料がめっき鋼線の強度、延性を確保し、ゴム複合体の補強効果を発揮させるのに好ましい。 Although the component of the ground iron (to-be-plated steel wire) of the plated steel wire of this invention is not specifically limited, C: 0.7-1.2 mass%, Si: 0.2-0.5 mass%, Mn: 0 0.2 to 0.6% by mass, P: 0.01% by mass or less, S: 0.01% by mass or less, Cr: 0.01 to 0.35% by mass, and pearlite area ratio is 95% As described above, a material having a structure in which ferrite and cementite are not precipitated at the grain boundaries is preferable for ensuring the strength and ductility of the plated steel wire and exhibiting the reinforcing effect of the rubber composite.
以下、本発明の実施例について説明する。なお、本実施例に記載の内容により本発明の内容は制限されない。 Examples of the present invention will be described below. In addition, the content of this invention is not restrict | limited by the content as described in a present Example.
表１に示す成分を有する鋼材を用いて図４に示す製造工程に従い、線径が５．５ｍｍの熱間圧延線材を原材料とし、熱間圧延線材を酸洗し、スケールを除去した後、石灰処理を行い、ステアリン酸Ｎａを主体とした乾式潤滑剤を用いて１．５ｍｍまで伸線加工した。この伸線材に熱処理として、１０００℃の加熱炉に導入し、４５ｓ保持し、金属組織をオーステナイトにした後、６００℃の鉛浴に７ｓ浸漬するパテンティング処理を行った。 In accordance with the manufacturing process shown in FIG. 4 using steel materials having the components shown in Table 1, a hot rolled wire having a wire diameter of 5.5 mm is used as a raw material, the hot rolled wire is pickled, scale is removed, and lime The treatment was performed and the wire was drawn to 1.5 mm using a dry lubricant mainly composed of Na stearate. As a heat treatment, the wire drawing material was introduced into a heating furnace at 1000 ° C., held for 45 s, the metal structure was made austenite, and then subjected to a patenting treatment immersed in a lead bath at 600 ° C. for 7 s.
パテンティング処理を行った鋼線に、硫酸による電解酸洗とアルカリ溶液による電解脱脂を施した。続いて、ピロリン酸銅めっき浴中で電気銅めっき行った後、硫酸亜鉛浴にＡｌ微粒子を分散させた溶液中でＺｎ−Ａｌ複合電気めっきを行い、Ｃｕ、Ａｌ微粒子分散Ｚｎめっきの２層めっきを得た。このめっき線を４８０℃で７ｓ加熱してブラス合金めっきとした。この時、ＣｕめっきとＺｎめっきの厚さを変えてＣｕ比を調整し、Ａｌ分散Ｚｎめっき溶液のＡｌ粉末濃度を変えてブラスめっき中のＡｌ濃度を調整した。
比較例の従来めっき鋼線は、ＣｕめっきとＺｎめっきを連続して行った後、４８０℃で７ｓ加熱し、拡散処理を行い、ＣｕとＺｎからなるブラスめっき鋼線とし、Ｃｕ濃度を５８％、６３％、７８％とした。通常のブラスめっき層中Ｃｕ濃度は６３％である。
The steel wire subjected to the patenting treatment was subjected to electrolytic pickling with sulfuric acid and electrolytic degreasing with an alkaline solution. Subsequently, after performing electrolytic copper plating in a copper pyrophosphate plating bath, Zn-Al composite electroplating is performed in a solution in which Al fine particles are dispersed in a zinc sulfate bath, and two-layer plating of Cu and Al fine particle dispersed Zn plating is performed. Got. This plated wire was heated at 480 ° C. for 7 s to obtain brass alloy plating. At this time, the Cu ratio was adjusted by changing the thickness of Cu plating and Zn plating, and the Al concentration in the brass plating was adjusted by changing the Al powder concentration of the Al-dispersed Zn plating solution.
The conventional plated steel wire of the comparative example is a brass-plated steel wire made of Cu and Zn by performing Cu treatment and Zn plating continuously, heating at 480 ° C. for 7 s, and performing diffusion treatment, with a Cu concentration of 58%. 63% and 78%. The Cu concentration in the normal brass plating layer is 63%.
めっき後の湿式伸線は、ノンスリップのダンサー式により逆張力を制御しつつエマルションタイプの湿式潤滑剤を用いて湿式伸線を行い、線径０．１〜０．４ｍｍの極細のめっき鋼線を製造した。また、一部実施例では、スリップ式湿式伸線によって極細のめっき鋼線を製造した。湿式伸線加工性は、断線発生率によって評価し、従来のめっき鋼線をスリップ式伸線機で伸線した表３の比較例Ｎｏ．１５の伸線で、伸線重量当たりの断線発生回数を基準とし、Ｎｏ．１５に対する断線回数を指数として極細のめっき鋼線の伸線加工性を評価した。伸線加工性が９０％以上であれば伸線加工性が良好であると判断し、８０％以上であれば合格とした。なお、同等以上の伸線加工性となった場合は伸線加工性指数を１００％とした。 Wet wire drawing after plating is performed using an emulsion-type wet lubricant while controlling reverse tension by a non-slip dancer type, and an ultra-fine plated steel wire with a wire diameter of 0.1 to 0.4 mm is obtained. Manufactured. Further, in some examples, an extremely fine plated steel wire was manufactured by slip-type wet wire drawing. The wet wire drawing workability was evaluated by the disconnection occurrence rate, and the conventional plated steel wire was drawn with a slip-type wire drawing machine in Comparative Example No. 3 in Table 3. No. 15 wire drawing, based on the number of wire breakage occurrence per wire drawing weight. The wire drawing workability of an extremely fine plated steel wire was evaluated using the number of breaks to 15 as an index. If the wire drawing workability was 90% or more, it was judged that the wire drawing workability was good. When the drawing workability was equal to or higher, the drawing workability index was set to 100%.
ブラスめっき層の組成は、伸線した極細のめっき鋼線から試料をサンプリングし、アンモニア原液に過硫酸アンモニウムを１０％混合したアルカリ溶液にめっき鋼線を浸漬し、ブラスめっき層を溶解し、溶解液をＩＣＰ分析することでＣｕ、Ｚｎ、Ａｌ濃度を求めて計算した。ブラスめっき層の厚さはブラスめっき層中のＣｕ、Ｚｎ、Ａｌ質量と比重から計算により、前記（１）式よりブラスめっき層の平均厚さを求めた。 The composition of the brass plating layer is obtained by sampling a sample from a drawn fine steel wire, immersing the plating steel wire in an alkaline solution in which 10% ammonium persulfate is mixed in an ammonia stock solution, dissolving the brass plating layer, and dissolving the solution. ICP analysis was performed to obtain Cu, Zn, and Al concentrations. The thickness of the brass plating layer was calculated from the mass and the specific gravity of Cu, Zn, and Al in the brass plating layer, and the average thickness of the brass plating layer was obtained from the above equation (1).
めっき鋼線とゴム組成物との接着性を評価するため、めっき鋼線４本を、５ｍｍのピッチで撚り合わせてコードとし、表２に示すゴム組成物に埋め込み、１６０℃で、１８分加熱するホットプレスにより加硫処理を行い、評価用試料を作成した。本試料のゴム組成物からコード引抜く際の荷重を測定し、最大引抜力を接着性の指標とした。初期の接着性（初期接着）は、加硫後２４ｈ以内の最大引抜力とした。また、接着強度の経年劣化は、ゴム組成物に埋設した試料を８０℃の蒸留水に３日間浸漬した後の最大引抜力で評価した。なお、初期接着は、比較例である試験Ｎｏ．１５のめっき鋼線をゴム組成物に埋設した初期接着の引抜き荷重を１００％とし、これに対する指数で評価した。初期接着は７５％以上であれば良好、７０〜７５％であれば合格とした。劣化処理後の接着性（劣化処理）は７０％以上であれば良好、６０〜７０％であれば合格とした。 In order to evaluate the adhesion between the plated steel wire and the rubber composition, four plated steel wires were twisted at a pitch of 5 mm to form a cord, embedded in the rubber composition shown in Table 2, and heated at 160 ° C. for 18 minutes. The sample for evaluation was prepared by vulcanizing with a hot press. The load when the cord was pulled out from the rubber composition of this sample was measured, and the maximum pulling force was used as an index of adhesiveness. The initial adhesion (initial adhesion) was the maximum pulling force within 24 hours after vulcanization. Further, the aging deterioration of the adhesive strength was evaluated by the maximum pulling force after the sample embedded in the rubber composition was immersed in distilled water at 80 ° C. for 3 days. In addition, initial adhesion is test No. which is a comparative example. The pulling load for initial adhesion in which 15 plated steel wires were embedded in the rubber composition was taken as 100%, and the index was evaluated with respect to this. If the initial adhesion was 75% or more, it was good, and if it was 70-75%, it was considered acceptable. The adhesiveness (deterioration treatment) after the deterioration treatment is good if it is 70% or more, and is acceptable if it is 60-70%.
なお、めっき鋼線の強度は、試験Ｎｏ．２４を除いて３２００ＭＰａ以上である。 In addition, the strength of the plated steel wire is determined according to Test No. Excluding 24, it is 3200 MPa or more.
表３に、めっき鋼線の性状とゴム組成物との接着性、伸線方法と伸線加工性の評価結果を示す。 Table 3 shows the evaluation results of the properties of the plated steel wire and the adhesion between the rubber composition, the wire drawing method and the wire drawing workability.
表３の試験Ｎｏ．１〜１４が本発明例である。試験Ｎｏ．１〜１４は本発明であり、めっき性状が好適範囲を具備しており、本発明のめっき鋼線はノンスリップ式伸線、スリップ式伸線のいずれでも、初期の接着性は良好で、劣化処理後の接着性とも、従来のめっき鋼線（比較例の試験Ｎｏ．１５）が評点４０％であるのに対して、いずれも６５％以上の接着強度があり、改善効果が明らかである。ノンスリップ式伸線で製造する場合はスリップ式伸線（試験Ｎｏ．３と１３）より良好な接着性と伸線加工性が得られる。 Test No. in Table 3 1-14 are examples of the present invention. Test No. 1 to 14 are the present invention, and the plating properties have a suitable range, and the plated steel wire of the present invention has good initial adhesiveness in both non-slip-type wire drawing and slip-type wire drawing, and is subjected to deterioration treatment. With respect to the later adhesiveness, the conventional plated steel wire (Test No. 15 in the comparative example) has a rating of 40%, but both have an adhesive strength of 65% or more, and the improvement effect is clear. In the case of producing by non-slip type wire drawing, better adhesion and wire drawing workability are obtained than slip type wire drawing (Test Nos. 3 and 13).
一方、比較例の試験Ｎｏ．１５は従来のプロセスで製造したＣｕとＺｎからなるブラスめっき鋼線をスリップ式湿式伸線機で伸線したもので、Ｃｕ比率が６３％で、接着性および伸線性の基準であるが、Ｃｕ、Ｚｎからなる拡散ブラスめっきのため、劣化処理後の接着性が低下する。 On the other hand, test No. of the comparative example. 15 is a brass-plated steel wire made of Cu and Zn manufactured by a conventional process and drawn with a slip-type wet wire drawing machine. The Cu ratio is 63%, which is a standard for adhesion and wire drawing. Due to diffusion brass plating made of Zn, the adhesiveness after the deterioration treatment is lowered.
試験Ｎｏ．１６はＣｕとＺｎからなるブラスめっきで、Ｃｕ比率が低く、初期の接着性が低下する。また、ブラスめっき層中のβブラス率が高くなってブラスめっき層が硬くなり、伸線加工性が悪化する。試験Ｎｏ．１７はブラスめっき層中のＣｕ比率が高く、ゴム組成物中のＳと過剰反応し、初期接着、劣化処理後の接着性とも悪化する。 Test No. No. 16 is brass plating made of Cu and Zn, and the Cu ratio is low and the initial adhesiveness is lowered. Further, the β brass ratio in the brass plating layer is increased, the brass plating layer is hardened, and the wire drawing workability is deteriorated. Test No. No. 17 has a high Cu ratio in the brass plating layer, excessively reacts with S in the rubber composition, and deteriorates both initial adhesion and adhesion after deterioration treatment.
試験Ｎｏ．１８はブラスめっき層中のＡｌが本発明の範囲より少なく、接着性改善効果が得られない。
試験Ｎｏ．１９はブラスめっき層中のＡｌが本発明の範囲より多く、初期接着性が悪化する。
Test No. No. 18 has less Al in the brass plating layer than the range of the present invention, and the effect of improving adhesion cannot be obtained.
Test No. No. 19 has more Al in the brass plating layer than the range of the present invention, and the initial adhesiveness deteriorates.
試験Ｎｏ．２０は、Ａｌ量は本発明の範囲であるが、ブラスめっき層が厚く、劣化処理により、ゴム組成物中のＳとブラスめっき層中のＣｕが過剰に反応し、接着反応層の密度低下とともにＣｕＳ組成となり、劣化処理後の接着性が低下する。
試験Ｎｏ．２１は、本発明の範囲よりブラスめっき厚が薄く、伸線加工により地鉄が露出し、伸線加工性が悪化するととともに、局部的にゴム組成物との接着性機能が失われ、接着性も低下する。
Test No. No. 20, Al amount is in the range of the present invention, but the brass plating layer is thick, and due to the deterioration treatment, S in the rubber composition and Cu in the brass plating layer react excessively, and the density of the adhesion reaction layer decreases. It becomes a CuS composition and the adhesiveness after a deterioration process falls.
Test No. No. 21, the brass plating thickness is thinner than the scope of the present invention, the steel is exposed by wire drawing, the wire drawing workability is deteriorated, and the adhesive function with the rubber composition is locally lost. Also decreases.
試験Ｎｏ．２２は線径が太く、引張り強度が３２００ＭＰａ未満となり、ゴム複合体としての補強効果が小さくなる。試験Ｎｏ．２３は最終線径が細く、高歪みの伸線加工になることで、伸線加工性が低下する。また、比表面積が増加し、ゴム組成物中のＳとの反応性が高くなるため、十分な接着強度が得られない。 Test No. No. 22 has a large wire diameter and a tensile strength of less than 3200 MPa, and the reinforcing effect as a rubber composite is reduced. Test No. No. 23 has a thin final wire diameter and is a highly strained wire drawing process, thereby reducing the wire drawing workability. Moreover, since the specific surface area increases and the reactivity with S in the rubber composition increases, sufficient adhesive strength cannot be obtained.
試験Ｎｏ．２４はブラスめっき層中にＡｌを含むものの、Ｃｕ比率が多く、劣化処理後の接着性が低下する。
試験Ｎｏ．２５はブラスめっき層中にＡｌを含むものの、Ｃｕ比率が少なく、βブラスが増加し、伸線加工性が低下する。
Test No. Although 24 contains Al in the brass plating layer, the Cu ratio is large and the adhesiveness after the deterioration treatment is lowered.
Test No. No. 25 contains Al in the brass plating layer, but the Cu ratio is small, β brass is increased, and wire drawing workability is lowered.
本発明のめっき鋼線は、ゴム組成物と強固に接着され、時間が経過してもその接着強度の低下が小さいため、ゴム複合体の補強材として好適に使用可能で、補強効果を長期間維持可能であり、タイヤコード及びビードワイヤだけでなく、ゴムホースやベルトの補強材として使用することが可能であり、産業上の利用可能性が極めて高い。 The plated steel wire of the present invention is firmly bonded to the rubber composition, and since the decrease in its adhesive strength is small over time, it can be suitably used as a reinforcing material for rubber composites and has a long-lasting reinforcing effect. It can be used as a reinforcing material for not only tire cords and bead wires, but also rubber hoses and belts.
１：地鉄（被めっき鋼材）
２：拡散処理前のＣｕめっき層
３：拡散処理前のＺｎめっき層
４：拡散処理前のＡｌめっき層
５：地鉄（被めっき鋼材）
６：拡散処理前のＣｕめっき層
７：拡散処理前のＺｎ−Ａｌ複合めっき層中のＡｌ粒子
８：拡散処理前のＺｎ−Ａｌ複合めっき層
９：拡散処理後のブラスめっき層
１０：被めっき線材
1: Steel (plated steel)
2: Cu plating layer before diffusion treatment 3: Zn plating layer before diffusion treatment 4: Al plating layer before diffusion treatment 5: Ground iron (steel material to be plated)
6: Cu plating layer before diffusion treatment 7: Al particles in Zn-Al composite plating layer before diffusion treatment 8: Zn-Al composite plating layer 9 before diffusion treatment 9: Brass plating layer 10 after diffusion treatment: Plated wire
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| EP3753749B1 (en) * | 2018-02-14 | 2024-08-14 | Sumitomo Electric Industries, Ltd. | Tire |
| KR102236874B1 (en) * | 2021-03-18 | 2021-04-06 | 넥센타이어 주식회사 | Steel Cord plated with alloy containing Cu and Al, Tire Belt comprising the steel cord and Tire comprising the tire belt |
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