JP2000288134A - MANUFACTURE OF GOLF CLUB FACE MATERIAL MADE OF BETA- TYPE Ti ALLOY - Google Patents
MANUFACTURE OF GOLF CLUB FACE MATERIAL MADE OF BETA- TYPE Ti ALLOYInfo
- Publication number
- JP2000288134A JP2000288134A JP11096984A JP9698499A JP2000288134A JP 2000288134 A JP2000288134 A JP 2000288134A JP 11096984 A JP11096984 A JP 11096984A JP 9698499 A JP9698499 A JP 9698499A JP 2000288134 A JP2000288134 A JP 2000288134A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- score line
- type
- rolling
- face material
- 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.)
- Pending
Links
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 44
- 239000000463 material Substances 0.000 title claims abstract description 34
- 238000004519 manufacturing process Methods 0.000 title claims description 4
- 238000005096 rolling process Methods 0.000 claims abstract description 32
- 238000005097 cold rolling Methods 0.000 claims abstract description 20
- 230000032683 aging Effects 0.000 claims abstract description 8
- 230000015572 biosynthetic process Effects 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 8
- 239000000956 alloy Substances 0.000 claims description 7
- 238000012545 processing Methods 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 6
- 239000000203 mixture Substances 0.000 abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract description 2
- 238000003754 machining Methods 0.000 abstract 1
- 230000035939 shock Effects 0.000 abstract 1
- 238000005336 cracking Methods 0.000 description 8
- 230000035882 stress Effects 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 238000004080 punching Methods 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910000737 Duralumin Inorganic materials 0.000 description 2
- 238000003483 aging Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 102220253765 rs141230910 Human genes 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005422 blasting Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000002023 wood Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Golf Clubs (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、耐割れ性に優れた
Ｔｉ合金製ゴルフクラブフェース材の製法に関し、特に
β型Ｔｉ合金を対象とし、最終冷間圧延の圧延方向に対
するスコアラインの形成方向を調整することによって、
耐割れ性の高められたクラブフェース材を得るための方
法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a golf club face material made of a Ti alloy having excellent crack resistance, and more particularly to a β-type Ti alloy, in which a score line is formed in the direction of the final cold rolling. By adjusting
The present invention relates to a method for obtaining a club face material having enhanced crack resistance.
【０００２】[0002]
【従来の技術】Ｔｉ合金製のゴルフクラブフェース材と
して現在最も広く実用化されているのは、Ｔｉ−１５％
Ｖ−３％Ｃｒ−３％Ｓｎ−３％Ａｌ等に代表されるβ型
Ｔｉ合金であり、その製造に当たっては、適度の厚さま
で熱間圧延した後、最終製品厚さまで冷間圧延し、次い
で打抜き加工およびスコアラインの形成を含めたフェー
ス加工を施してから、高強度化のために時効処理する方
法が採用される。2. Description of the Related Art The most widely used Ti club alloy golf club face material is Ti-15%.
V-3% Cr-3% Sn-3% Al is a β-type Ti alloy typified by Al and the like. In producing the alloy, after hot rolling to an appropriate thickness, cold rolling to the final product thickness, A method of performing face processing including punching and formation of a score line, and then performing aging treatment for increasing strength is adopted.
【０００３】他方、上記方法によって製造されるβ型Ｔ
ｉ合金製のゴルフクラブフェース材は、当該β型Ｔｉ合
金の比強度がステンレス鋼やジュラルミン等のクラブフ
ェース材に比べて非常に高く卓越した反発係数を示すこ
とから、金属クラブフェース材の中でも格段に優れたも
のと認識されており、現にＴｉ合金製のクラブフェース
材は高級材としての地位が定着している。On the other hand, β-type T produced by the above method
Since the specific strength of the β-type Ti alloy is much higher than that of a club face material such as stainless steel or duralumin, the golf club face material made of an i-alloy has a remarkable coefficient of restitution, and is therefore a remarkable metal club face material. And the club face material made of Ti alloy has been established as a high-grade material.
【０００４】ところが、本発明者らがβ型Ｔｉ合金を対
象としてゴルフクラブフェース材の一層の改質を期して
研究を進めるうち、次の様な事実が明らかになってき
た。即ち、常法に従ってＴｉ合金素材を熱間圧延および
冷間圧延した後、最終製品としてスコアラインを形成し
たβ型Ｔｉ合金製のクラブフェース材では、打球時の衝
撃によってしばしばスコアラインに沿った割れを生じる
ことがあり、高級材としての品質安定性に重大な問題に
なることが確認された。However, as the inventors of the present invention proceeded with research aimed at further modifying the golf club face material for the β-type Ti alloy, the following facts have become apparent. That is, after the Ti alloy material is hot-rolled and cold-rolled according to a conventional method, a club face material made of a β-type Ti alloy in which a score line is formed as a final product often cracks along the score line due to impact at the time of hitting. In some cases, which is a serious problem in quality stability as a high-grade material.
【０００５】[0005]
【発明が解決しようとする課題】本発明は上記の様な事
情に着目してなされたものであって、その目的は、打球
時の衝撃によってスコアラインに生じる前記割れの発生
原因を追求すると共に、該割れの原因を解消し、高級品
としてのＴｉ合金製クラブフェース材の品質安定性を高
めようとするものである。SUMMARY OF THE INVENTION The present invention has been made in view of the above circumstances, and an object of the present invention is to pursue the cause of the occurrence of the cracks generated on the score line due to the impact at the time of hitting the ball. Another object of the present invention is to eliminate the cause of the cracks and enhance the quality stability of a Ti alloy club face material as a high-grade product.
【０００６】[0006]
【課題を解決するための手段】上記課題を解決すること
のできた本発明に係るＴｉ合金製ゴルフクラブフェース
材の製法とは、熱間圧延および冷間圧延されたβ型Ｔｉ
合金板を用いてゴルフクラブフェース材を製造するに当
たり、フェース加工におけるスコアラインの形成方向
を、最終冷間圧延の圧延方向に対し±５０°以上とする
ところに要旨を有している。Means for Solving the Problems A method of manufacturing a Ti alloy golf club face material according to the present invention which can solve the above-mentioned problems includes a hot-rolled and a cold-rolled β-type Ti.
In producing a golf club face material using an alloy plate, the gist is that the direction in which score lines are formed in face processing is ± 50 ° or more with respect to the rolling direction of final cold rolling.
【０００７】ここで使用されるβ型Ｔｉ合金の成分組成
などは特に制限されないが、ゴルフクラブフェース材と
して優れた加工性を有すると共に、時効処理後は高い強
度を示すものとして、Ｍｏ当量：１２〜１８質量％、Ａ
ｌ当量：３〜６質量％であるβ型Ｔｉ合金が好ましく用
いられる。また該β型Ｔｉ合金は、時効処理後の抗張力
で１４００ＭＰａ以上の強度特性を有するものが好まし
い。[0007] The composition of the β-type Ti alloy used here is not particularly limited, but it is considered to have excellent workability as a golf club face material and to show high strength after aging treatment. ~ 18% by mass, A
β-type Ti alloy having 1 equivalent: 3 to 6% by mass is preferably used. Further, it is preferable that the β-type Ti alloy has a strength characteristic of 1400 MPa or more in tensile strength after aging treatment.
【０００８】[0008]
【発明の実施の形態】本発明者らは前述した様な課題の
下で、まずスコアラインを形成したβ型Ｔｉ合金製クラ
ブフェース材に見られるスコアラインに沿った割れの発
生原因を明らかにすべく研究を行なった。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Under the above-mentioned problems, the present inventors first clarified the cause of the occurrence of cracks along the score lines in a β-type Ti alloy club face material having score lines. I did my research.
【０００９】その結果、上記Ｔｉ合金加工時の最終冷間
圧延方向に対するスコアラインの形成方向によって、割
れ発生頻度が著しく変わってくること、そして、上記ス
コアラインに沿った割れは、最終冷間圧延方向と同一方
向にスコアラインを形成したときに顕著に表われること
が確認された。その理由は次の様に考えられる。As a result, the frequency of occurrence of cracks changes significantly depending on the direction in which the score line is formed with respect to the final cold rolling direction during the processing of the Ti alloy. It was confirmed that when the score line was formed in the same direction as the direction, it was remarkably exhibited. The reason is considered as follows.
【００１０】即ち、β型Ｔｉ合金はそれなりに優れた加
工性を有しているとはいえ、通常の鉄鋼材料やジュラル
ミンの如きアルミニウム系合金等に比べると加工性が悪
く、特に冷間圧延時の圧下率が高くなるにつれて、特に
圧延方向に対し直交方法（圧延直交方向：通常Ｔ方向と
いう）の伸び率は急激に低下してくる。That is, although the β-type Ti alloy has excellent workability, it is inferior in workability to ordinary steel materials and aluminum alloys such as duralumin. As the rolling reduction becomes higher, the elongation in the method perpendicular to the rolling direction (the direction perpendicular to the rolling direction: usually referred to as the T direction) decreases sharply.
【００１１】他方、ゴルフクラブフェースのスコアライ
ン形成部に打球時の衝撃が加わった場合、例えば図1に
示す如く、最初は打球による外力を受けてフェース面Ｆ
は図面左側の鎖線Ａ方向に変形し、その直後には弾性に
より図面右側の鎖線Ｂ方向に変形する。そして、該変形
に伴ってスコアラインＳには幅方向に押し縮められ（鎖
線Ａ）または押し広げられる（鎖線Ｂ）方向（即ち、ス
コアラインＳに対して直交方向）の力が作用することに
なり、この力はスコアラインＳの底面ＳLに集中する。On the other hand, when an impact at the time of hitting is applied to the score line forming portion of the golf club face, for example, as shown in FIG.
Is deformed in the direction of the dashed line A on the left side of the drawing, and immediately thereafter, is deformed by elasticity in the direction of the dashed line B on the right side of the drawing. Then, in the score line S, a force is applied to the score line S in the width direction (chain line A) or expanded (chain line B) (that is, the direction orthogonal to the score line S). now, this force is concentrated on the bottom surface S L of the score line S.
【００１２】即ち打球時に生じる外力によって最も応力
集中を起こし易いのは、スコアラインＳの底面ＳLで、
スコアラインＳに対し直交方向であり、従って当該底面
ＳLに沿った割れを抑えるには、スコアラインＳの形成
方向に対して直交方向の延性を高めることが有効と思わ
れる。[0012] That's likely to occur most stress concentration by an external force generated at the time of hitting is, the bottom surface S L of the score line S,
An orthogonal direction with respect to the score line S, thus suppressing cracks along the bottom surface S L, it is believed effective to increase the orthogonal direction of ductility for the formation direction of the score line S.
【００１３】一方、先に延べた様にβ型Ｔｉ合金は、冷
間圧延時の圧下率が高くなるにつれて、特に圧延方向に
対し直交方向（Ｔ方向）の伸び率が急激に低下してく
る。従って、上記スコアラインＳの形成方向が冷延チタ
ン合金板の圧延方向（Ｌ方向）と同一方向になるか、直
交方向となるかによって、割れの発生頻度は著しく変わ
ってくると考えられる。On the other hand, as described above, the elongation of the β-type Ti alloy, particularly in the direction perpendicular to the rolling direction (T direction), rapidly decreases as the rolling reduction during cold rolling increases. . Therefore, it is considered that the frequency of occurrence of cracks is significantly changed depending on whether the score line S is formed in the same direction as the rolling direction (L direction) of the cold-rolled titanium alloy sheet or in the orthogonal direction.
【００１４】ところが従来は、上記スコアライン部で生
じる割れの発生原因が明確にされていないこともあっ
て、特にスコアラインの形成方向を工夫するといったこ
とはなされたことがなく、そのため、該スコアラインＳ
の形成方向によっては割れが発生しなかったり或いは多
発し、安定性した品質が得られなかったものと考えられ
る。However, conventionally, the cause of the occurrence of cracks generated in the score line portion has not been clarified, and no particular effort has been made in the direction in which the score line is formed. Line S
It is considered that cracks did not occur or occurred frequently depending on the direction of formation of, and stable quality could not be obtained.
【００１５】本発明者らは上記知見、即ちスコアライン
底部に打球時の応力集中が起こり易く、また、フェース
素材として用いるＴｉ合金冷延板は圧延直交方向（Ｔ方
向）の伸び率が低くなる（逆に圧延方向、即ちＬ方向の
伸び率は低下し難い）、といった知見を活かし、スコア
ラインの形成方向を最終冷間圧延時の圧延方向に対して
適正な範囲に調整することにより、打球時の前記割れ現
象を確実に抑制できる様にしたものである。The present inventors have made the above findings, that is, stress concentration at the time of hitting is likely to occur at the bottom of the score line, and the cold rolled Ti alloy sheet used as the face material has a low elongation rate in the direction perpendicular to the rolling direction (T direction). (Conversely, the elongation percentage in the rolling direction, that is, the L direction is unlikely to decrease), and by adjusting the formation direction of the score line to an appropriate range with respect to the rolling direction in the final cold rolling, the hit ball The cracking phenomenon at the time can be surely suppressed.
【００１６】そして、許容範囲を含めて上記適正範囲を
明確にすべく更に研究を進めた結果、熱間圧延および冷
間圧延されたβ型Ｔｉ合金板を用いてゴルフクラブフェ
ース材を製造する際に、フェース加工におけるスコアラ
インの形成方向が、最終冷間圧延の圧延方向に対し±５
０°以上となる様に調整すれば、前述した衝撃割れが可
及的に抑えられ、品質の安定性したＴｉ合金製ゴルフク
ラブヘッド材が得られることを確認し、上記本発明に想
到したものである。As a result of further study to clarify the appropriate range including the allowable range, when a golf club face material is manufactured by using a hot-rolled and cold-rolled β-type Ti alloy sheet. In addition, the formation direction of the score line in the face processing is ± 5 with respect to the rolling direction of the final cold rolling.
If the angle is adjusted to 0 ° or more, it was confirmed that the above-described impact cracking was suppressed as much as possible, and a Ti alloy golf club head material having stable quality was obtained. It is.
【００１７】以下、図面を参照しつつスコアラインの形
成方向角度を定めた理由を詳細に説明する。図２は、Ｔ
ｉ冷延板の冷延方向に対する２つの典型的なヘッド材の
打抜き方向とスコアラインの形成方向を示した説明図で
あり、最終冷間圧延の圧延方向をＬ方向、圧延直交方向
をＴ方向で示し、打抜き加工材のフェース面Ｆに形成さ
れるスコアラインをＳで示している。Hereinafter, the reason why the score line forming direction angle is determined will be described in detail with reference to the drawings. FIG.
It is explanatory drawing which showed the punching direction of two typical head materials with respect to the cold rolling direction of i cold-rolled sheet, and the formation direction of a score line, The rolling direction of final cold rolling is L direction, and the orthogonal rolling direction is T direction. The score line formed on the face surface F of the punched material is indicated by S.
【００１８】図３は、スコアラインＳを圧延直交方向
(Ｔ方向)に形成した場合の拡大説明図（但し、説明の便
宜のためスコアラインＳの数は１つのみとしている）で
あり、この場合は、スコアラインＳの底部ＳLに打球時
の外力が作用したとき、スコアラインＳの底部ＳLに生
じる応力は、冷間圧延時の圧延方向（Ｌ方向）と同一方
向に作用することになり、底部ＳLに応力が集中して
も、圧延方向（Ｌ方向）の伸び率はそれほど低下してい
ないので、割れは発生し難い。FIG. 3 shows the score line S in the direction perpendicular to the rolling direction.
Enlarged view of a case of forming the (T direction) (However, the number of score lines S for convenience of explanation are only one) is, in this case, at the time of hitting the bottom S L of the score line S when an external force is applied, stress generated in the bottom S L of the score line S is made to act in the same direction as the rolling direction (L direction) of the cold rolling, even if stress is concentrated on the bottom S L, Since the elongation percentage in the rolling direction (L direction) has not decreased so much, cracking hardly occurs.
【００１９】これに対し図４は、スコアラインＳを圧延
方向(Ｌ方向)と同一方向に形成した場合の拡大説明図で
あり、この場合は、スコアラインＳの底部ＳLに打球時
の外力が作用したとき、スコアラインＳの底部ＳLにか
かる外力は該底部ＳLの形成方向（即ちスコアラインＳ
の形成方向）に対して直交する方向（即ち、冷間圧延時
に伸び率が著しく低下するＴ方向と同一方向）に作用す
ることになり、この部分に応力が集中し該底部ＳLに沿
って割れが発生し易くなる。[0019] In contrast Figure 4 is an enlarged view of a case of forming the same direction scorelines S to the rolling direction (L direction), in this case, the external force at the time of hitting the bottom S L of the score line S when is exerted, bottom S L external force exerted on the bottom portion S L formation direction (i.e. the score line S of the score line S
Direction of the perpendicular to the forming direction) (i.e., it acts on the T in the same direction) to decrease significantly constant elongation during cold rolling, stress in this portion is concentrated along the bottom portion S L Cracks easily occur.
【００２０】すなわち、図３に示す様な方向関係を満た
したときに衝撃割れは可及的に抑えられるが、図３，４
の例は、スコアラインＳの形成方向と圧延方向の典型的
な例を示したもので、該スコアラインＳの形成方向には
ある程度の許容範囲が存在する。そして該許容範囲の下
限は、図５に示す如く、また後記実施例でも明らかにす
る如く「±５０°」であり、即ちスコアラインＳの形成
方向を最終冷間圧延の圧延方向に対して±５０°以上、
より好ましくは±７０°以上とすれば、該スコアライン
Ｓの底部ＳLに生じる割れを可及的に抑制し得ることが
分かった。That is, when the directional relationship shown in FIG. 3 is satisfied, impact cracking can be suppressed as much as possible.
Is a typical example of the direction in which the score line S is formed and the rolling direction. There is a certain tolerance in the direction in which the score line S is formed. The lower limit of the permissible range is “± 50 °” as shown in FIG. 5 and as will be clarified in the examples described later, that is, the direction in which the score line S is formed is ±± the rolling direction of the final cold rolling. 50 ° or more,
If more preferably ± 70 ° or more was found to be able to be suppressed as much as possible the cracking caused on the bottom S L of the score lines S.
【００２１】かくして本発明によれば、フェース加工に
おけるスコアラインの形成方向を、最終冷間圧延の圧延
方向に対し±５０°以上、より好ましくは±７０°以上
とすることにより、これまでしばしば生じていたスコア
ラインＳに沿った衝撃割れを確実に防止することがで
き、品質の安定したβ型Ｔｉ合金製ゴルフクラブフェー
ス材を提供し得ることになった。Thus, according to the present invention, the score line forming direction in the face processing is set to ± 50 ° or more, more preferably ± 70 ° or more with respect to the rolling direction of the final cold rolling, so that the score line is often generated. Thus, it is possible to reliably prevent impact cracking along the score line S, and to provide a β-Ti alloy golf club face material with stable quality.
【００２２】なお、こうしたスコアライン形成方向によ
る衝撃割れの発生は、異方性を有する冷延Ｔｉ合金板、
特に同一方向に熱間圧延および冷間圧延を行なったβ型
Ｔｉ合金板に共通する現象であり、従って本発明で用い
られるβ型Ｔｉ合金の種類は特に制限されず、Ti-15Mo-
5Zr-3Al、Ti-15Mo-5Zr-3Sn-3Al、13V-3.5Cr-3Sn-3.5Al-
1Moなど、様々の成分組成のβ型Ｔｉ合金に提供できる
が、高強度で高反発係数の求められるゴルフクラブ用フ
ェース材として特に好ましいのは、次に示す様な理由か
ら、Ｍｏ当量が１２〜１８質量％、Ａｌ当量が３〜６質
量％であるβ型Ｔｉ合金である。The occurrence of impact cracking due to the direction in which the score lines are formed can be caused by anisotropic cold-rolled Ti alloy sheets,
In particular, this phenomenon is common to β-type Ti alloy sheets that have been hot-rolled and cold-rolled in the same direction. Therefore, the type of β-type Ti alloy used in the present invention is not particularly limited, and Ti-15Mo-
5Zr-3Al, Ti-15Mo-5Zr-3Sn-3Al, 13V-3.5Cr-3Sn-3.5Al-
Although it can be provided for β-type Ti alloys having various component compositions such as 1Mo, it is particularly preferable as a face material for a golf club in which a high strength and a high coefficient of restitution are required. This is a β-type Ti alloy having 18% by mass and an Al equivalent of 3 to 6% by mass.
【００２３】Ｍｏ当量：１２〜１８質量％ Ｍｏは、最も代表的な全率固溶型β安定化元素で、β型
Ｔｉ合金として時効処理後の強度−延性バランスを高め
る上で極めて重要な元素であり、その効果を有効に発揮
させるには１２％以上、より好ましくは１３％以上含有
するものが望ましい。しかし、Ｍｏ量が多くなり過ぎる
と時効硬化性能が低下し高強度化の目的が達成できなく
なるので、１８％以下、より好ましくは１７％以下に抑
えるべきである。Mo equivalent: 12 to 18% by mass Mo is the most typical all-solution β-stabilizing element, and is an extremely important element for enhancing the strength-ductility balance after aging treatment as a β-type Ti alloy. In order to exhibit the effect effectively, it is desirable to contain 12% or more, more preferably 13% or more. However, if the Mo content is too large, the age hardening performance is reduced and the purpose of increasing the strength cannot be achieved, so the content should be suppressed to 18% or less, more preferably 17% or less.
【００２４】なお、Ｖ，Ｔａ，Ｎｂ等も全率固溶型β安
定化元素として上記Ｍｏと同様の効果を有しているの
で、これらを含有する場合は、これらを含めたＭｏ当量
として［Ｍｏ＋1/1.5・Ｖ＋1/5・Ｔａ＋1/3.6・Ｎｂ＋1.2
5Ｃｒ＋2.5Ｆｅ＋1.7Ｃｏ＋1.7Ｍｎ＋1.25Ｎｉ］が１２
〜１８質量％の範囲となる様に調整することが望まし
い。V, Ta, Nb and the like also have the same effect as Mo described above as a solid-solution β-stabilizing element. Therefore, when these are contained, the Mo equivalent including these is [ Mo + 1 / 1.5.V + 1 / 5.Ta + 1 / 3.6.Nb + 1.2
5Cr + 2.5Fe + 1.7Co + 1.7Mn + 1.25Ni] is 12
It is desirable to adjust so as to be in the range of １８18% by mass.
【００２５】Ａｌ当量：３〜６質量％ Ａｌは、α安定化元素として強度向上に寄与する元素で
あり、Ａｌ含有量が３％未満では満足な強度が得られ難
くなる。しかしＡｌ含有量が６％を超えると熱延処理後
の冷延性が極端に悪くなり、コイル化による連続生産が
困難になるばかりでなく、冷延材としての冷間加工性や
時効処理後の延性も不足気味になる。強度と延性の兼ね
合いを考慮してより好ましいＡｌ当量の下限は３．５
％、より好ましい上限は５．５％である。Al equivalent: 3 to 6% by mass Al is an element that contributes to strength improvement as an α-stabilizing element. If the Al content is less than 3%, it is difficult to obtain satisfactory strength. However, when the Al content exceeds 6%, the cold-rolling property after the hot-rolling treatment is extremely deteriorated, and not only continuous production by coiling becomes difficult, but also the cold-workability as a cold-rolled material and the aging treatment. The ductility also tends to be insufficient. Considering the balance between strength and ductility, the more preferable lower limit of the Al equivalent is 3.5.
%, And a more preferred upper limit is 5.5%.
【００２６】なお、ＳｎやＺｒもＡｌと同様にα安定化
元素としての作用を発揮するところから、それらの元素
を含有する場合は、それらの元素を含めて、Ａｌ当量と
して［Ａｌ＋1/3・Ｓｎ＋1/6・Ｚｒ］が３〜６質量％の範
囲となる様に調整することが望ましい。It should be noted that Sn and Zr also act as α-stabilizing elements in the same manner as Al. Therefore, when these elements are contained, the Al equivalent is calculated as [Al + 1/3 ·· [Sn + 1 / 6Zr] is desirably in the range of 3 to 6% by mass.
【００２７】本発明で使用するβ型Ｔｉ合金における好
ましい含有元素は上記の通りであり、残部は実質的にＴ
ｉであるが、次に示すような理由から更に他の元素とし
て少量のＣｕやＳｉなどを含有させることも有効であ
る。The preferred elements contained in the β-type Ti alloy used in the present invention are as described above, and the balance is substantially T
Although it is i, it is also effective to include a small amount of Cu or Si as another element for the following reasons.
【００２８】即ちＣｕはβ安定化元素の1種であり、一
般にＭｏ当量式には、含められないがＦｅ，Ｃｒなどと
同等の強度向上効果を発揮し、またＳｉは、β結晶の再
結晶を抑制する上で有効に作用する。That is, Cu is a kind of β-stabilizing element, and although generally not included in the Mo equivalence formula, exhibits the same strength improving effect as Fe, Cr and the like. It works effectively in suppressing.
【００２９】また本発明のＴｉ合金に許容される不可避
不純物元素としては、たとえばＯ，Ｎ，Ｈ，Ｓ等があり
これらの不可避不純物は、上記本発明の特性を阻害しな
い限り微量の含まれていても構わない。The unavoidable impurity elements permitted in the Ti alloy of the present invention include, for example, O, N, H, S and the like, and these unavoidable impurities are contained in trace amounts unless they impair the characteristics of the present invention. It does not matter.
【００３０】尚、本発明を実施する際におけるβ型Ｔｉ
合金の鋳造・鍛造・熱延条件、時効熱処理（焼鈍）条
件、脱スケール条件、冷間加工条件等は特に制限され
ず、公知のβ型Ｔｉ合金に適用される条件を本質的にそ
のまま、もしくは適当に変更を加えて実施すればよい。It should be noted that β-type Ti
The conditions for casting, forging, hot rolling, aging heat treatment (annealing), descaling, and cold working of the alloy are not particularly limited, and the conditions applied to known β-type Ti alloys are essentially unchanged or What is necessary is just to change and implement suitably.
【００３１】[0031]
【実施例】以下、実施例を挙げて本発明をより具体的に
説明するが、本発明はもとより下記実施例によって制限
を受ける訳ではなく、前・後記の趣旨に適合し得る範囲
で適当に変更して実施することも可能であり、それらは
いずれも本発明の技術的範囲に包含される。EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not necessarily limited by the following examples, and may be appropriately performed within a range that can conform to the purpose described above and below. Modifications can be made and all of them are included in the technical scope of the present invention.
【００３２】実施例 Ｔｉ−１５Ｍｏ−５Ｚｒ−３Ａｌのβ型Ｔｉ合金をイン
ダクトスカル溶解法によって溶製し、８０ｍｍt×１３
０ｍｍt×２６０ｍｍL（約１２ｋｇ）の鋳塊を得る。こ
れを８５０℃（β温度域）加熱で４０ｍｍtに鍛造した
後、脱スケールと疵取りを兼ねて周囲を約２ｍｍ切削す
ることにより熱間圧延素材とし、これを８５０℃に再加
熱してから熱間圧延することにより、厚さ４．４ｍｍの
熱延板を得た。EXAMPLE A β-type Ti alloy of Ti-15Mo-5Zr-3Al was melted by an inductoskull melting method, and was made 80 mm t × 13.
An ingot of 0 mm t × 260 mm L (about 12 kg) is obtained. After forging it to 40 mm t by heating at 850 ° C (β temperature range), the surroundings are cut by about 2 mm for both descaling and flaw removal to obtain a hot-rolled material, which is then reheated to 850 ° C. By hot rolling, a hot-rolled sheet having a thickness of 4.4 mm was obtained.
【００３３】得られた各熱延板をショットブラスト・酸
洗処理を施して厚さ４ｍｍまで脱スケールし、長手方向
冷延（４ｍｍ→２．７ｍｍ）を行なって、厚さ２．７ｍ
ｍの冷延焼鈍板を得た。得られた各冷延焼鈍板からゴル
フクラブヘッドのフェース材切り出し、フェース加工を
行なうと共に、各フェース材に最終圧延方向に対して０
°（圧延方向に平行方向）、４０°、４５°、５０°、
６０°および９０°（圧延方向に対して直交方向）の方
向にスコアライン（幅：約１ｍｍ、深さ：約０．５ｍ
ｍ、長さ：約２０ｍｍのＶ溝を９本）を形成してから５
００℃伐時間の時効硬化処理を行い、このフェース材を
用いてゴルフクラブ（一番ウッド）を作製した。Each of the obtained hot-rolled sheets is subjected to shot blasting and pickling, descaled to a thickness of 4 mm, and cold-rolled in the longitudinal direction (4 mm → 2.7 mm) to a thickness of 2.7 m.
m of cold-rolled annealed sheet was obtained. A face material of a golf club head is cut out from each of the obtained cold-rolled annealed plates, and face processing is performed.
° (parallel to the rolling direction), 40 °, 45 °, 50 °,
Score lines (width: about 1 mm, depth: about 0.5 m) in directions of 60 ° and 90 ° (perpendicular to the rolling direction)
m, length: 9 V-grooves of about 20 mm)
Age hardening treatment was performed for a cutting time of 00 ° C., and a golf club (first wood) was produced using this face material.
【００３４】得られた各クラブについて、ゴルフクラブ
性能試験用のロボットを用いて打球テストを行ない、１
０００発打球後のフェース外観を目視観察し、割れの有
無を調べた。結果は表１に一括して示す通りであり、最
終圧延方向に対するスコアラインの形成方向を５０°以
上としたものでは割れが全く認められないのに対し、該
形成方向を５０°以下としたものでは、フェース面に明
らかな割れが確認された。A hitting test is performed on each of the obtained clubs using a golf club performance testing robot.
The external appearance of the face after 000 hits was visually observed to check for cracks. The results are collectively shown in Table 1. When the formation direction of the score line with respect to the final rolling direction was set to 50 ° or more, no crack was observed, whereas the formation direction was set to 50 ° or less. In, a clear crack was confirmed on the face surface.
【００３５】[0035]
【表１】 [Table 1]
【００３６】[0036]
【発明の効果】本発明は以上の様に構成されており、β
型冷延Ｔｉ合金板を用いてゴルフクラブヘッドを作製す
る際に、フェース面に形成するスコアラインを最終冷延
の圧延方向に対し±５０°以上の角度で形成することに
より、打球時の衝撃による割れの発生を可及的に抑える
ことができ、高級Ｔｉ合金製クラブとしての品質安定性
を著しく高め得ることになった。The present invention is configured as described above,
When producing a golf club head using a cold-rolled Ti alloy plate, the score line formed on the face surface is formed at an angle of ± 50 ° or more with respect to the rolling direction of the final cold-rolling, so that the impact at the time of hitting the ball is achieved. The generation of cracks due to cracking can be suppressed as much as possible, and the quality stability as a high-grade Ti alloy club can be significantly improved.
【図１】本発明者らが確認した割れの発生原因の説明図
である。FIG. 1 is an explanatory diagram of the cause of the occurrence of cracks confirmed by the present inventors.
【図２】冷延Ｔｉ合金板からの典型的なフェース材の打
抜き例を示す見取り図である。FIG. 2 is a sketch drawing showing an example of punching a typical face material from a cold-rolled Ti alloy plate.
【図３】スコアラインを圧延直交方向に形成したときの
説明図である。FIG. 3 is an explanatory diagram when a score line is formed in a direction perpendicular to rolling.
【図４】スコアラインを圧延方向に形成したときの説明
図である。FIG. 4 is an explanatory diagram when a score line is formed in a rolling direction.
【図５】圧延方向に対するスコアライン形成方向の許容
限界角度を示す説明図である。FIG. 5 is an explanatory diagram showing an allowable limit angle of a score line forming direction with respect to a rolling direction.
Ｆ クラブフェース Ｓ スコアライン ＳL スコアライン底部 Ｌ方向 最終冷延の圧延方向 Ｔ方向 最終冷延の圧延直交方向F Club face S Score line S L Bottom of score line L direction Rolling direction of final cold rolling T direction Cross direction perpendicular to rolling of final cold rolling
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｆ 1/00 ６８５ Ｃ２２Ｆ 1/00 ６８５Ｚ ６８６ ６８６Ｚ 1/18 1/18 Ｈ ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) C22F 1/00 685 C22F 1/00 685Z 686 686Z 1/18 1/18 H
Claims (3)
合金板を用いてゴルフクラブフェース材を製造するに当
たり、フェース加工におけるスコアラインの形成方向
を、最終冷間圧延の圧延方向に対し±５０°以上とする
ことを特徴とするβ型Ｔｉ合金製ゴルフクラブフェース
材の製法。1. A hot-rolled and cold-rolled β-type Ti
In producing a golf club face material using an alloy plate, the direction of formation of score lines in face processing is set to ± 50 ° or more with respect to the rolling direction of final cold rolling. Manufacturing method of club face material.
質量％、Ａｌ当量：３〜６質量％である請求項１に記載
の製法。2. The method according to claim 1, wherein the β-type Ti alloy has a Mo equivalent of 12-18.
The method according to claim 1, wherein the Al equivalent is 3 to 6% by mass.
１４００ＭＰａ以上である請求項１または２に記載の製
法。3. The method according to claim 1, wherein the β-type Ti alloy has a tensile strength after aging treatment of 1400 MPa or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11096984A JP2000288134A (en) | 1999-04-02 | 1999-04-02 | MANUFACTURE OF GOLF CLUB FACE MATERIAL MADE OF BETA- TYPE Ti ALLOY |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11096984A JP2000288134A (en) | 1999-04-02 | 1999-04-02 | MANUFACTURE OF GOLF CLUB FACE MATERIAL MADE OF BETA- TYPE Ti ALLOY |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2000288134A true JP2000288134A (en) | 2000-10-17 |
Family
ID=14179489
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11096984A Pending JP2000288134A (en) | 1999-04-02 | 1999-04-02 | MANUFACTURE OF GOLF CLUB FACE MATERIAL MADE OF BETA- TYPE Ti ALLOY |
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| Country | Link |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004113829A (en) * | 2004-01-21 | 2004-04-15 | Bridgestone Sports Co Ltd | Golf club head |
| US8235833B2 (en) | 2004-04-21 | 2012-08-07 | Cobra Golf Incorporated | Transitioning hollow golf clubs |
-
1999
- 1999-04-02 JP JP11096984A patent/JP2000288134A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004113829A (en) * | 2004-01-21 | 2004-04-15 | Bridgestone Sports Co Ltd | Golf club head |
| US8235833B2 (en) | 2004-04-21 | 2012-08-07 | Cobra Golf Incorporated | Transitioning hollow golf clubs |
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