201014918 九、發明說明： 【發明所屬之技術領域】 本發明係種低鉻高強度之鐵基高岐球頭合金，特 別是關於-種適用於锻造高爾夫木桿頭並可提升其機械強度 及延展性之低鉻高強度之鐵基高爾夫球頭合金。 【先前技術】 ❿ 目前在高目夫辆產紐術方面，高_夫球頭大致可以分 為三類，金屬木桿頭、鐵桿頭及推桿。在金屬木頭桿方面，使 用之材料有不鐘銅、銘合金、鈦合金及複合材料等。而在鐵桿 頭方面，仍以不鏽鋼材質為主，至於推桿基本亦與木桿頭、鐵 桿頭之使用材質相似’即不鏽鋼、鋅合金等合金現今，在金 屬木桿頭方面，其材料之發展亦仍以不錄鋼為主流，以利使球 頭具有更廣的設計空間。在造形上，金屬木桿頭的設計是朝向 〇 大型化(oversize)發展，其主要原因是如此之設計可擴大球頭在 打擊面的甜蜜區。現今產業的目標，在不鏽鋼材料期望金屬木 桿頭有200至230cc.之體積的目標；欽合金、銘合金則希望有 230至280cc.之體積的設計；長纖維複合材料則以3〇〇cc之體 積為目標。一般運用於木桿頭之材質需同時兼具高強度與高韌 性之特性，高強度將使擊球距離穩定，高韌性則可使控球性能 增加，必然可使高爾夫球桿頭之擊球效果發揮至最理想的狀 態’故強度與延伸率組合越高越好’以利於提高球頭之體積或 5 201014918 甜蜜區設計空間，其機械性質來講，木桿頭之性能需求：一般 以抗举強度為要求之標準，以160至220Ksi為要求範圍，而 延伸率則為6至8°/❶為基本訴需求。相對的鐵桿頭之要求：一 般則以90至lOOKsi為要求範圍，而延伸率以約25至30%為 需求’其強度和延伸率組合越高越好，以增加球頭體積或增加 擊球時間與操控性等設計之空間。 高爾夫球頭之素材設計與選用，必需具備相當耐钱性與高 強度，以及能夠在球頭加工組配成形後，施予強化處理。目前 主要以鐵系與鈦系為主，而鐵系由早期之431不鑛鋼發展至目 前17-4不鏽鋼’鈦系則是以6_4Ti的鈦合金(6〇/0鋁Α1+4%叙v， 其餘為鈦Ti)為主。至於高爾夫球頭之高強度素材上，亦不斷 被研究及開發，早期在開發與運用此系列材料，最典型為 17-4PH材料。為了使球頭增大，增大甜蜜區，在球頭重量固 定的限定下，陸續運用更高強度的材料，如：15_5PH， CUstom455，CUSt〇m465。近年來，更進一步運用更高合金含 量之Custom475材料等析出硬化型不鏽鋼，做為金屬木桿頭之 發展趨勢與制。請參照第丨_示，其揭示目前用以製作高 爾夫球頭製造t常用鐵基素材之機械性質比較表，於此列出， 以供做為參考。 再者，所謂的析出硬化型不鏽鋼，是指在鎳路系不鐵鋼中 添加-種或多種合金元素如銘、翻、銘、銅、銳、欽、叙等， 6 201014918 依序經固溶熱處理、淬火處理及時效處理，使其具有高強度、 高硬度和高耐钱性。一般析出硬化型不鏞鋼之類別與性質分析 如下所示： (-)> 17-4PH ：201014918 IX. Description of the invention: [Technical field to which the invention pertains] The present invention relates to a low-chromium and high-strength iron-based sorghum ball-end alloy, in particular to a type suitable for forging a golf club head and capable of improving its mechanical strength and ductility. Low chromium high strength iron based golf head alloy. [Prior Art] ❿ At present, in the high-cavity production, the high-go ball head can be roughly divided into three categories, metal wood heads, iron heads and putters. In the case of metal wood rods, the materials used are not copper, alloys, titanium alloys and composite materials. In terms of iron head, it is still mainly made of stainless steel. As for the putter, it is basically similar to the material used for wood head and iron head. That is, stainless steel, zinc alloy and other alloys. Nowadays, in the metal wood head, the development of its materials It is still based on the non-recorded steel, so that the ball head has a wider design space. In terms of shape, the design of the metal wood head is toward the oversize of the ,, the main reason is that the design can expand the sweet spot of the ball on the face. The goal of today's industry is to have a metal-wood head with a target of 200 to 230 cc. in stainless steel. Chin alloy and Ming alloy are expected to have a volume of 230 to 280 cc. For long-fiber composites, 3 cc. The volume is the target. Generally, the material used for the wood head needs to have both high strength and high toughness. The high strength will make the hitting distance stable, and the high toughness will increase the ball control performance, which will inevitably make the golf club head hit the ball. Play to the most ideal state 'so the combination of strength and elongation is better' to help increase the volume of the ball head or 5 201014918 sweet zone design space, its mechanical properties, the performance requirements of the wood head: generally anti-lift The strength is the required standard, with a range of 160 to 220 Ksi, and an elongation of 6 to 8 °/❶ is the basic requirement. Relative iron head requirements: generally 90 to lOOKsi is required, and elongation is about 25 to 30%. 'The combination of strength and elongation is as high as possible to increase the volume of the ball or increase the hitting time. Space with design such as handling. The design and selection of the material of the golf head must be very resistant to money and high strength, and it can be reinforced after the ball head processing is formed. At present, iron and titanium are the main ones, while iron is developed from the early 431 non-mineral steel to the current 17-4 stainless steel. Titanium is a 6_4Ti titanium alloy (6〇/0 aluminum Α1+4% The rest is dominated by titanium Ti). As for the high-strength material of the golf club, it has been continuously researched and developed. In the early development and application of this series of materials, the most typical material is 17-4PH. In order to increase the ball head and increase the sweet zone, higher strength materials such as 15_5PH, CUstom455, CUSt〇m465 are used successively under the fixed weight of the ball. In recent years, the use of a higher alloy content of Custom475 material and other precipitation hardened stainless steels has been used as a development trend and system for metal wood heads. Please refer to the 丨_, which reveals the comparison of the mechanical properties of the iron-based materials currently used in the manufacture of golf balls, which are listed here for reference. In addition, the so-called precipitation hardening type stainless steel refers to the addition of one or more alloying elements such as Ming, Turning, Ming, Copper, Rui, Qin, and Syria in the nickel road system without iron steel, 6 201014918 Heat treatment, quenching treatment and aging treatment make it have high strength, high hardness and high acid resistance. The classification and properties of general precipitation hardening type steels are as follows: (-)> 17-4PH:
❹ 17-4 PH不鏽鋼是麻田散鐵系不鏽鋼，含有約3%之鋼 (Cu)，其強化原理係由銅微粒之分散析出在麻田散鐵基地。 17-4PH不鏽鋼於i〇3(rc固溶處理後，其結構為M(麻田散鐵) 及少量的α(肥粒鐵），經480亡時效處理丨和3小時，於穿透 式電子顯微鏡(TEM)下並未發現析出物。時效處理16、24、你 及100小時後，皆可發現體心立方邮尤)晶體結構之富路固 溶體⑽析出，僅在100小時後發現有邮碳化物的析出 將時效溫度提高至赋後’於i至48小_可發現α 出，並且可發現少量之^析出。其主要合金成分範固 Fe- (16 至 18%)鉻 Cr_ (3 至 5%)鎳 Ni (3 至 * 5%)銅 至 0.45%)鈮 Nb。 (二）、15-5PH : 雄热上述 负良好的综合性能，但17~ 不鐵鋼之缺點是在組織中存有心肥粒鐵。反觀’⑸而 之設計原聰秋彳_全如_ H i7 4pH % 之缺點，因此湖降鉻(Cr)增加錦⑽)調整 粒鐵。在砸繊雜姆㈣Η儀的顯^ 201014918 有碳化鈮(NbC)和ΜΑ兩種碳化物被發現。時效硬化是析出 一種極細銅微粒的結構，不錄鋼在5〇〇t>c時效後，用傳統型穿 透式電子顯微鏡(TEM)和高解析電子顯微鏡(hrem)所觀察到 的疋9R結構的銅析出物組織^在5〇〇。〇時效128小時後，發 現Macs碳化物’大部分的MUG碳化物產生於麻田散鐵基地 和殘留沃細賴分祕。15_5PH不細献硬化時，強化 原因疋在時效期間析出一種極細銅的微粒。其主要合金成分範 圍為鐵 Fe- (14 至 15〇/〇)鉻 Cr- (3.5 至 5.5%)錄 Ni- (2.4 至 4.5%) 銅 Cu- (0.15 至 0.45%)銳 Nb。 (三)、13-8PH : 13·8ΡΗ不鏽鋼是低碳麻田散鐵析出硬化型不鏽鋼，其具有 高強度和高硬度，並有優良的抗腐蝕和抗應力腐蝕破裂能力 (SCC)。另外，此合金亦有好的延展性及韌性，在某些環境 條件下’其的機械性質優於17-4ΡΗ和15-5ΡΗ不鏽鋼。13-8ΡΗ 不鏽鋼從固溶熱處理的溫度淬火後，變態成體心立方^cc.) 晶體結構的板條狀麻田散鐵。在45〇〜575〇c下進行時效處理， 將導致沒-NiAl(万-銘鎳)球狀顆粒析出物，微細的均佈於基地 内。在高於525°C作時效時，可以發現有顯著數量的沃斯田鐵 回復，且沃斯田鐵顆粒快速變粗大。時效後合金的拉伸強度遠 高於只做固溶熱處理的合金，主妓因為有糾W顆粒從基 地析出。13-8PH不鏽鋼強化原因是析出一種B2有序的NiA1 201014918 相超晶格結構。此合金被發現在析出物與基地的交接處無鉬之 偏析現象，其主要合金成分範圍為鐵Fe- (12.25至13.25%)鉻 Ο (7.5 至 8.5%)鎳 Ni- (2 至 2.5%)鉬 Mo- (0.9 至 1.35%)鋁 A1。 (四） 、Custom465 :❹ 17-4 PH stainless steel is a granulated stainless steel containing about 3% of steel (Cu). The strengthening principle is based on the dispersion of copper particles in the granulated iron base. 17-4PH stainless steel after i 〇 3 (rc solution treatment, its structure is M (Massa loose iron) and a small amount of α (fertilizer iron), after aging for 480 丨 and 3 hours, in a transmission electron microscope (TEM) did not find precipitates. After aging treatment 16, 24, you and 100 hours later, you can find the body-centered cubicle) crystal structure of the solid road solid solution (10) precipitation, only found after 100 hours The precipitation of carbides raises the aging temperature to a post-emergence 'i to 48 small', and α is found, and a small amount of precipitates can be found. Its main alloy composition is Fe- (16 to 18%) chromium Cr_ (3 to 5%) nickel Ni (3 to * 5%) copper to 0.45%) 铌 Nb. (B), 15-5PH: The above-mentioned negative thermal comprehensive performance, but the disadvantage of 17~ non-ferrous steel is that there is a heart ferrite in the tissue. On the other hand, '(5) and the design of the original Congqiu _ _ _ H i7 4pH % of the shortcomings, so the lake chrome (Cr) increased Jin (10)) adjust the granular iron. In the 砸繊 姆 四 四 四 四 四 四 2010 2010 2010 2010 2010 2010 2010 149 149 149 149 149 149 149 2010 2010 2010 2010 2010 149 2010 2010 2010 Age hardening is a structure in which a very fine copper particle is precipitated, and the 疋9R structure observed by a conventional transmission electron microscope (TEM) and a high-resolution electron microscope (hrem) after aging at 5 〇〇t>c is not recorded. The copper precipitated structure ^ at 5〇〇. After 128 hours of aging, it was discovered that most of the MUG carbides from Macs were produced in the Ma Tian scattered iron base and the residual volcano. When 15_5PH is not carefully hardened, the reason for strengthening is to precipitate a very fine copper particle during aging. Its main alloy composition ranges from iron Fe- (14 to 15 〇/〇) chromium Cr- (3.5 to 5.5%) to Ni- (2.4 to 4.5%) copper Cu- (0.15 to 0.45%) sharp Nb. (3), 13-8PH: 13·8 ΡΗ stainless steel is a low-carbon ramification iron precipitation precipitation hardening stainless steel, which has high strength and high hardness, and has excellent corrosion resistance and stress corrosion cracking resistance (SCC). In addition, the alloy also has good ductility and toughness. Under certain environmental conditions, its mechanical properties are superior to those of 17-4ΡΗ and 15-5ΡΗ stainless steel. 13-8ΡΗ After quenching the temperature of the solid solution heat treatment, the stainless steel is transformed into a body-centered cubic ^cc.) crystal structure of the lath-like granulated iron. The aging treatment at 45 〇 to 575 〇 c results in the precipitation of spheroidal particles of no-NiAl (Wan-Ming Nickel), which are finely distributed in the base. When aging is higher than 525 ° C, a significant amount of Worthite iron recovery can be found, and the Worthfield iron particles rapidly become coarse. After aging, the tensile strength of the alloy is much higher than that of the alloy which is only subjected to solution heat treatment, and the main enthalpy is precipitated from the base due to the correction of W particles. The reason for the 13-8PH stainless steel strengthening is the precipitation of a B2 ordered NiA1 201014918 phase superlattice structure. This alloy was found to be free of molybdenum segregation at the junction of the precipitate and the base. The main alloy composition ranged from iron Fe- (12.25 to 13.25%) chrome (7.5 to 8.5%) nickel Ni- (2 to 2.5%). Molybdenum Mo- (0.9 to 1.35%) aluminum A1. (4), Custom465:
Custom465合金經980°C固溶處理與深冷處理後，其顯微結 構為板條狀麻田散鐵組織。在時效處理溫度55〇。(：以下，可觀 察到α’相析出’本合金的析出硬化主要是由於α，相的析出。 在時效處理溫度55(TC以上，可觀察到針狀Ni3Ti相與沃斯田 鐵相的形成，沃斯田鐵回復，使強度降低，延伸率提升。主要 合金為鐵 Fe- (11 至 12.5%)鉻 Cr_ (10.75 至 11.25%)鎳 Ni- (1.5 至 1.8%)鈦 Ti- (0.75 至 1.25%)鉬 Mo- 0.25%石夕 Si。 (五） 、Custom475 :After the solid solution treatment of the Custom465 alloy at 980 °C and cryogenic treatment, the microstructure of the 465 is a lath-like granulated iron structure. The aging treatment temperature is 55 〇. (: In the following, α' phase precipitation can be observed. 'The precipitation hardening of this alloy is mainly due to the precipitation of α and phase. At the aging treatment temperature of 55 (above TC, the formation of the needle-like Ni3Ti phase and the Worthite iron phase can be observed). , Worthite iron recovery, reduced strength, increased elongation. The main alloy is iron Fe- (11 to 12.5%) chromium Cr_ (10.75 to 11.25%) nickel Ni- (1.5 to 1.8%) titanium Ti- (0.75 to 1.25%) Molybdenum Mo- 0.25% Shi Xi Si. (5), Custom475:
Custom475合金經930°C固溶處理與深冷處理’其結構為體 心立方(B.C.C.)之麻田散鐵組織’進行450_550。〇時效處理後， 可發現除了麻田散鐵基地外，尚可觀察到B2(NiAl)及 U2(]%A1)之析出物產生。在65〇〇c時效處理後，除了麻田散 鐵結構外，亦可觀察到沃斯田鐵產生，且並未觀察到其他析出 物。其主要合金成分分別為鐵Fe_ (1〇 5至115%)鉻Cr__ (7 5 至 8.5%)鎳 Νι-(8 至 90/〇)鈷 c〇- (1 至 1.15%)鋁 A1- 〇.5〇/0石夕 Si- 0.5%猛 Μη 〇 由上可知，目前析出硬化型不鏽鋼應用於高爾夫木桿頭的 9 201014918 成分，皆在不鏽鋼裡加入了 10至18%之鉻Cr、3至12%之鎳The Custom 475 alloy was subjected to solution treatment at 930 ° C and cryogenic treatment, and its structure was a body-centered cubic (B.C.C.) granulated iron structure of 450 550. After the aging treatment, it was found that in addition to the Matian iron base, the precipitation of B2 (NiAl) and U2 (]% A1) was observed. After the aging treatment at 65 °c, in addition to the structure of the granulated iron structure, the production of Worth iron was observed, and no other precipitates were observed. Its main alloy composition is iron Fe_ (1〇5 to 115%) chromium Cr__ (75 to 8.5%) nickel Νι-(8 to 90/〇) cobalt c〇- (1 to 1.15%) aluminum A1- 〇. 5〇/0石夕 Si- 0.5% Μ Μ 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 目前 9 9 9 9 9 9 9 高尔夫 2010 2010 2010 % nickel
Ni ’以及其他微量元素如鈇Ti、銳灿、鉬M〇、銘ai等，藉 高溫熱加:η時產生析出物，__析出硬化及晶粒細化等效 果，從而提升機械強度。目前為止，上述商用化之析_匕型 不鏽鋼應用在高爾夫球頭上已經逐漸普遍化，隨著使用之球頭 數量增加，其需求量,純漸增加。但是，在Custom 465、Cust〇m 475 硬傾不鏽騎射，卻魏材料表面本身具有敲 ❹ *之現象產生。隨I目刖析出硬化不鏽鋼之合金發展，其合金 設計所添加之合金成分與微量元素有愈來愈高之趨勢。 综上所述’本發明者乃利用合金設計與製程處理之理念， ' 謂料㈣之健^強紅_夫_合金，其具有麻 ®散軸顯微結構之組織，加上具有絡元素及利用適當加工及 熱處理製程，而達喻㈣化之目的。S此她於傳統不鏽鋼 合金’本發明之鐵基合金更適合用以鍛造高爾夫木桿頭，並能 0 使該轉備更冑之強度、延伸率及抗雜等彡重優點。 【發明内容】 本發明之主要目的在於提供一種低鉻高強度之鐵基高爾夫 球頭合金’其包含4.5至5.5%鉻、3.5至4.5%錄、1.5至2.0 麵、1.0至1.5°/。欽、0 3至〇 4%銘及〇 15至0.2%碳，其餘比 例以鐵為齡。該合金之絡含量較低，且具有細散鐵相顯微 結構之組織’因而有利於降低高爾夫木桿頭之製造成本，並提 201014918 升高爾夫轉歡強度、耕率及抗雜。 本發明之- 人要目的在於提供一種低鉻冑強度之鐵基高爾夫 球頭合金’其利用適當加工及熱處理製程，使其合金成份之微 量讀’經由熱處理餘，將被熱處理的合金基地$，析出微 細且分佈均自之汹物，而達贿出強化，另搭配低含量之絡 兀素的強化效果，使其抗拉強度可達210至24〇ksi之間，降 伏強度可達195至220ksi之間，及延伸率介於6至8%之間， 因而有利於提升高爾夫球木桿頭之強度需求、防鏽性及鍛造加 工性。 為達上述之目的，本發明提供一種低鉻高強度之鐵基高爾 夫球頭合金’其包含4.5至5.5%鉻、3.5至4.5%鎳、1.5至2.0 翻、1.0至1.5%鈦、0.3至0.4%銘及0.15至0.2%碳，其餘比 例主要以鐵為基材。該合金具有麻田散鐵相顯微結構之組織， 加上具有鉻元素及利用適當加工及熱處理製程，而達到析出強 化之目的，故使得該合金適用於鍛造高爾夫木桿頭，以供提升 咼爾夫木桿頭之強度、延伸率及抗腐钱。 在本發明之一實施例中’該合金屬於麻田散鐵析出硬化型 不鏞鋼。 在本發明之一實施例中，該合金之抗拉強度介於210至 240ksi之間，降伏強度介於195至220ksi之間，及延伸率介於 6至8%之間。 201014918 在本發明之一實施例中，該合金另可選擇包含微量元素。 該微量元素較佳選自下列元素組成之族群：0.5至1.0%之石夕、 0.8至1.0%之錳及其組合。 根據本發明之低鉻高強度之鐵基高爾夫球頭合金，其係以 鐵基為主，並加入5%之絡，以防止生錄；加入3.5至4.5%之 銘’以改善韌性；以及另包含其他元素’如鎳、鉬、鈦等來增 加/析出強度；且摻雜有0.15至0.2%碳，以增加合金之焊接性。 本發明之合金成分範圍分別為4.5至5.5%鉻、3.5至4.5%錄、 1.5 至 2.0 鉬、1.0 至 1.5%鈦、〇.3 至 0.4%鋁、〇· 15 至 〇 2〇/〇碳、 0.5至1.0%破、〇.8至1.0%短。由於適當的設計材料合金元素 組合’可控制顯微結構為（麻田散鐵+沃斯田鐵），合金經由 適當之鍛造加工處理，施以ll〇(TC溫度固溶處理，使其材料 最终達到完整之麻田散鐵組織。若合金固溶處理後再經奶❹它 溫度之時效熱處理，可以由穿透式電子顯微鏡(Transmissi〇n Electron Microscope，tem)之分析’觀察查出其組織為體心立 方(B.C.C.)結構之α相；若合金固溶處理後再經55〇°c溫度之 時效熱處理，透過TEM分析與X-my分析，則可觀察到合金 在α基地上除了有富鉻固溶體（α，相)之存在，亦有一種具有 Β2有序的NiA1相超晶格與u2(Ni3A1)之析出物產生。當時效 溫度在55(rc以上時’可觀察到在晶界上有(M23C6)之麻田散鐵 碳化物產生，且此碳化物會隨著溫度之上升而有明顯的成長。 12 201014918 此碳化物之析$會S晶界附近失去耐#性，進巾導致粒間腐姓 的發生，使其合金之延性飾性降低。本發日臉由時效處理 後’其強切目是在時效綱㈣-種B2有相腦相超 晶格與面心立方體(Fc c )之U2(NMJ)析出物，故本發明除了 月b 乂夺效方式達到析出強化效果，其延伸率亦保持不錯之發展 範圍。 整體而言’本發明之合金經過適當的成份調配，以及適當 加工製程與祕理製程，可控繼當之臟結構組合。故使得 所發明之合金材料可達顺減度為21G至·b之間、降 伏強度為195 JL 220 ksi之間、延伸率為6至8%之最佳化強度、 咼防鏽性之南爾夫球頭木桿頭之設計目標。 【實施方式】 為了讓本發明之上述及其他目的、特徵、優點能更明顯易 懂’下文將特舉本發明較佳實施例，並配合所賴式，作詳細 說明如下。 一般而言’在不鏽鋼的基礎上發展起來之高強度不鏽鋼， 除了具有較㊅的抗拉缝，亦兼具味的耐雜性能^然而， 根據組織與強彳b機制的差異，其析出硬化型不_鋼大致可以分 為麻軸、祕斯w麟級化德鋼、麻 田散鐵時。本判發展& —種祕高強度之鐵基高爾 夫球頭合金，其成分主要包含鐵、絡(〇r)、鎳、鉬如。）、 13 201014918 鈦(Ti)、鋁(Al)，其中亦可摻雜或添加碳(〇、矽(si)及錳(Μη) 等微量元素，且該合金基本上屬於麻田散鐵系析出硬化型不錄 鋼合金。在本發明之一實施例中，該材料包含4.5至5.5%路、 3.5 至 4.5%鎳、1.5 至 2.0 鉬、1.0 至 1.5%鈦、〇.3 至 0·4〇/〇鋁及 0.15至0.2%碳，其餘比例主要為鐵。在本發明之另一實施例 中，該材料另包含至少一種微量元素，其中該微量元素較佳選 自下列元素組成之族群：0·5至1.0%之矽、0.8至10%之短及 其組合。上述比例皆為以重量百分比(wt%)計，合先敘明。 請參照第2圖所示’本發明之麻田散鐵析出硬化型合金在 鐵鉻鎳不鏽鋼合金系列之基本結構分佈圖中的分佈區域(如虛 線方框所示之區域），此類型合金主要通過麻田散鐵轉變產生 強化作用’並經時效處理析出彌散強化相（dispersi〇n strengthening phase)來進一步發揮強化作用。除了具有較佳之 耐大氣腐钮和財酸腐姓性能外’對氫脆（hydf〇gen embrittlement ’ HE)亦不敏感，且焊接性亦比麻田散鐵不鏽鋼 好。 凊參照第3圖所示，其揭示本發明之低鉻高強度之鐵基高 爾夫球頭合金之實施例與比較例之成分比例與機械性質之比 較表，其中編號1至8為本發明之成分鱗的實施例編號9 至12為比較例(相關數據為採樣1〇個試片之平均值）。由第3 圖可得知，鐵-5%鉻-4.5%鎳-L98%你U鈦_〇 32㈣2碳_〇 6 201014918 梦-0.91猛所組成之編號1實施例合金成份，經ii〇〇°c固溶處 理，再經由550°C時效熱處理後，其機械性質為抗拉強度平均 值為245.7ksi’降伏強度平均值為240.8ksi，延伸率則為8.1%， 且依此合金設計所製成之球頭經鹽霧試驗48小時及高爾夫球 砲擊3000次試驗均為合格。請參照附照1所示，其揭示本發 明編號1之實施例合金材料的金相圖，其顯示合金經ll〇〇«>C 固溶處理，再經由55(TC時效熱處理後之顯微結構組織。 請參照附照2及3所示，其揭示本發明編號1之實施例合 金材料經1100°C固溶處理後’再經由550。(：時效熱處理之明視 野圖與暗視野圖。再者，請參照附照4所示，其揭示本發明編 號1之實施例合金材料之擇區繞射圖(selected扯邱diftacti()n pattern ’ SADP) ’由此可觀察出在α基地上除了有富鉻固溶體 (α相)存在之外’亦有―種Β2有相NiA1相超晶格結構析 出。由於析出微細且均勻分佈之析出物，導致阻礙了差排的移 動，達到強化不鏽鋼之目的。另外，請參照第4圖所示，其揭 示本發明職1之實補合錄触由χ雕_琳繞射分 析，除了有Β2有序的麵相超晶格析出物出現之外，亦具 有面心立謂(F.CQ之L1_3A1)之糾物產生，故本發明之 不鏽鋼合錄料除了能㈣效方式達爾㈣化絲，其延伸 率亦保持不錯之發展範圍。 請再參照第3圖所示，編號χ至8之實施例合金材料的成 15 201014918 份皆在本發明之含量範疇内’合金材料經適當之加工製程與熱 處理後’其機械性質抗拉強度值介於210至245ksi之間，降 伏強度值則介於195至220ksi之間，延伸率可達6至go/。，且 經鹽霧試驗48小時及南爾夫球砲擊3000次試驗皆為合格。 請再參照第3圖所示，當合金材料的鉻含量低於本發明之 鉻含量範疇（例如編號9、10之比較例合金材料）時，由附照 5所示之比較例編號9的擇區繞射圖(SADP)則可觀察出，其芙 地除了有富鉻固溶體(α，相)之存在，並無其他析出物。再者， 由第3圖亦可發現編號9、10之比較例合金材料的延伸率低於 本發明的延伸率範疇且亦有發生生鏽之狀態。 另一方面，請再參照第3圖所示，當合金材料的鉻含量高 於本發明之鉻含量範疇（例如編號U、12之比較例合金材料） 時，由附照6及7所示之比較例編號12之明視野與擇區繞射 圖則可觀糾’經由ΤΕΜ分減在Baa界上有之麻田散 鐵碳化物產生’此碳化物之析出會讓晶界附近失去耐餘性，進 而導致粒_侧發生’使其合金之雜與她降低，且再由 第3圖發現其機械與延伸率皆低於本發_機械強度與 延伸率範》#，故_ n、12之比侧合金材齡了發生鏽姓 之外，其材質亦為脆性材質。 下文分別針對各種添加合金元素及微量元素之比例範圍及 其對於本㈣之低鉻高強度之鐵基高爾夫麵合金的合金性 16 201014918 質之影響逐一說明如下： 鉻(Cr):主要在增加合金材料之腐蝕氧化抵抗性，又可提 昇合金材料之硬化能及高溫強度’尤其是對於高碳鋼之耐磨耗 性更有極顯著之效果。而鉻基本上為體心立方毋c c)肥粒鐵 穩定相，當鉻含量過低時，將使該合金材料之抗錄抗腐蝕能力 降低，而當鉻含量過多時，則將大大提高該合金發生偏析的可 月b性。因此，為使合金材料於生產與設計過程中容易控制，以 展現最佳化高爾夫球頭性能’本發明之合金材料係將鉻含量控 制在4.5至5.5%之間。 鎳(Ni):主要考量在增加銲接性與韌性，在合金材料中添 加鎳時，不僅可增加合金材料的腐蝕及氧化抵抗性，還可提高 固溶強化及高淬透性之作用。細化肥粒鐵晶粒，在強度之相同 條件下，可提高鋼材的塑性和韌性，特別是低溫韌性。與鉻、 顧等聯合制’亦可提高輔的雜性與錢性。因此，為使 合金材料於生產與設計過程容易控制，以展現最佳化高爾夫球 頭性能，本發明之合金材料係將鎳含量控制在3 5至4 5%之 間。 钥(M〇):主要是控制Μ2Α的反應動力學。增加Cr/Ni不 鏽鋼中之辦#’可崎長轉產生敏狀咖。且亦可調整 材料之密，並使硬化觀人，防烟火躲，提昇合金材 料之高溫強度、潛變強度、及高溫硬度，當钥含量在i 5至3% 17 201014918 之間時，能增加耐蝕鋼抗有機酸及還原性介質腐蝕的能力，亦 即增加合金材料之抗孔钮性，並形成耐磨耗之碳化鉬粒子，且 有助於鋼液之流動性。唯，當鉬含量高於6.0%以上時會造成 過多之析出’使材料脆化。因此，本發明之合金材料係將鉬含 量控制在1.5至2.0%之間。 欽(Ti):添加鈦合金可降低合金密度，提升合金強度及抗姓 性且固溶強化作用極強’但同時降低固溶體之韌性。可提高鋼 材的回火穩定性’並有二次硬化作用，亦可提高耐熱鋼的抗氧 化性和熱強性。有防止和減輕不鏽鋼耐酸鋼晶和應力腐蝕的作 用。因此’本發明之合金材料係將鈦含量控制在1〇至15% 之間。 紹(A1):主要是用來脫氧和細化晶粒以及時效強化。不形 成碳化物’與氮及氧之親合力極強，其固溶強化作用大。在耐 熱合金中，與鎳形成γ ’相（NisAl)，而提高合金之強度。因 此’本發明之合金材料係將鋁含量控制在〇.2至〇 5%之間。 碳(C):碳元素基本上為一般鋼鐵材料不可或缺的元素，除 了為碳化物外，其亦是沃斯田鐵穩定相之元素，隨著碳含量增 加’肥粒鐵減少而沃斯田鐵愈穩定》惟，碳含量過高時，將不 利於合金材料的耐餘性。因此，本合金材料若能控制或添加碳 在0.2至0.3%之間’將有助於耐银性與沃斯田鐵相穩定。 矽(Si):在本發明之合金材料内摻雜或添加矽時，有利於防 18 201014918 止氣孔形成、增進辑収增加鋼嶋性 明之鐵基合金材料中，當 I本發 大於L0/°時，將不利於延伸 β @之合金若能添加G.5至1.G%之;^，將有助於 提高鑄造性質’以進行鑄件原料之製程。 、Ni ’ and other trace elements such as 鈇Ti, 锐灿, molybdenum M〇, Mingai, etc., by the addition of high temperature heat: η produces precipitates, __ precipitation hardening and grain refinement equivalent, thereby improving mechanical strength. So far, the above-mentioned commercialization of stainless steel has been gradually popularized on golf clubs, and as the number of ball heads used has increased, the demand has gradually increased. However, in Custom 465, Cust〇m 475 hard to shoot, but the surface of the Wei material itself has the phenomenon of knocking *. With the development of the alloy of hardened stainless steel, the alloy composition and trace elements added by the alloy design have an increasing trend. In summary, the inventor has utilized the concept of alloy design and process processing, 'the material of the material (4), the strong red _fu_alloy, which has the microstructure of the hemp-axis microstructure, plus the complex elements and Use appropriate processing and heat treatment processes to achieve the purpose of (four). S. This is in the traditional stainless steel alloy. The iron-based alloy of the present invention is more suitable for forging golf wood heads, and can make the transfer more advantageous in strength, elongation and resistance to impurities. SUMMARY OF THE INVENTION A primary object of the present invention is to provide a low chromium high strength iron-based golf ball alloy which contains 4.5 to 5.5% chromium, 3.5 to 4.5%, 1.5 to 2.0, and 1.0 to 1.5. Qin, 0 3 to 〇 4% Ming and 〇 15 to 0.2% carbon, the remaining proportion is iron. The alloy has a low content of the complex and has a microstructure of fine iron phase microstructures, which is advantageous for reducing the manufacturing cost of the golf club head, and the 201014918 liter golf turn strength, tillage rate and resistance. SUMMARY OF THE INVENTION The object of the present invention is to provide an iron-based golf ball alloy of low chrome strength, which utilizes a suitable processing and heat treatment process to cause a trace reading of the alloy composition to be heat treated by the heat treatment of the alloy base $, The precipitation is fine and the distribution is from the scorpion, and the bribe is strengthened, and the strengthening effect of the low content of lanolin is used, so that the tensile strength can reach between 210 and 24 〇ksi, and the lodging strength can reach 195 to 220 ksi. Between, and the elongation is between 6 and 8%, which is beneficial to improve the strength requirement, rust resistance and forging processability of the golf club head. To achieve the above object, the present invention provides a low chromium high strength iron-based golf club alloy which comprises 4.5 to 5.5% chromium, 3.5 to 4.5% nickel, 1.5 to 2.0 turns, 1.0 to 1.5% titanium, 0.3 to 0.4. % Ming and 0.15 to 0.2% carbon, the remaining proportion is mainly based on iron. The alloy has a microstructure of the microstructure of the granitic iron phase, plus the chromium element and the use of appropriate processing and heat treatment processes to achieve the purpose of precipitation strengthening, so that the alloy is suitable for forging golf club heads for upgrading Muir The strength, elongation and anti-corruption of the wood head. In an embodiment of the invention, the alloy is a granulated iron precipitation precipitation hardening type steel. In one embodiment of the invention, the alloy has a tensile strength between 210 and 240 ksi, a relief strength between 195 and 220 ksi, and an elongation between 6 and 8%. 201014918 In an embodiment of the invention, the alloy may alternatively comprise trace elements. The trace element is preferably selected from the group consisting of 0.5 to 1.0% of stellite, 0.8 to 1.0% of manganese, and combinations thereof. The low-chromium high-strength iron-based golf ball alloy according to the present invention is mainly based on an iron base, and is added with 5% of a network to prevent bio-recording; 3.5 to 4.5% of the name is added to improve toughness; Other elements such as nickel, molybdenum, titanium, etc. are included to increase/precipitate strength; and 0.15 to 0.2% carbon is doped to increase the weldability of the alloy. The composition of the alloy of the present invention ranges from 4.5 to 5.5% chromium, 3.5 to 4.5%, 1.5 to 2.0 molybdenum, 1.0 to 1.5% titanium, 〇.3 to 0.4% aluminum, 〇·15 to 〇2〇/〇 carbon, 0.5 to 1.0% broken, 〇. 8 to 1.0% short. Due to the appropriate design material alloy element combination 'controllable microstructure is (Mata loose iron + Worthite iron), the alloy is processed through appropriate forging, applied ll 〇 (TC temperature solution treatment, the material finally reaches Complete granulated iron structure. If the alloy is solution treated and then subjected to aging heat treatment at the temperature of the milk, it can be observed by a transmission electron microscope (Transmissi〇n Electron Microscope, tem). The α phase of the cubic (BCC) structure; if the alloy is solution treated and then subjected to aging heat treatment at a temperature of 55 ° C, by TEM analysis and X-my analysis, it can be observed that the alloy has a chromium-rich solid solution on the α base. The existence of the body (α, phase) also has a NiA1 phase superlattice with Β2 order and the precipitation of u2(Ni3A1). When the temperature is 55 (above rc), it can be observed at the grain boundary. (M23C6) The production of the loose iron carbide in Ma Tian, and this carbide will grow significantly with the increase of temperature. 12 201014918 The analysis of this carbide will lose the resistance of the vicinity of the S grain boundary, and the towel will cause intergranularity. The occurrence of rot, making its alloy The ductility is reduced. After the aging treatment of the hair face, the strong cut is the U2 (NMJ) precipitate of the phase-effect superlattice and the face-centered cube (Fc c ) in the aging cycle (4) - B2 In addition to the monthly b 乂 effective method to achieve precipitation enhancement effect, its elongation rate also maintains a good development range. Overall, the alloy of the invention has been properly formulated, and the appropriate processing process and secret process are controllable. The combination of dirty structure, so that the alloy material invented can reach a cis-degree reduction of between 21G and · b, a relief strength of 195 JL 220 ksi, an elongation of 6 to 8%, and an anti-rust The above-mentioned and other objects, features and advantages of the present invention will become more apparent and obvious. The detailed description is as follows. Generally speaking, the high-strength stainless steel developed on the basis of stainless steel, in addition to having six tensile seams, also has a taste-resistant resistance. However, according to the organization and toughness b mechanism difference, its Precipitation hardening type steel can be roughly divided into hemp shaft, mysterious w-classified Degang, and Ma Tian loose iron. This judgment develops & a kind of high-strength iron-based golf head alloy, whose composition mainly contains iron. , (络r), nickel, molybdenum, etc.), 13 201014918 Titanium (Ti), aluminum (Al), which may also be doped or added with trace elements such as carbon (〇, 矽 (si) and manganese (Μη), And the alloy is basically a granitic iron-based precipitation hardening type unrecorded steel alloy. In one embodiment of the invention, the material comprises 4.5 to 5.5% road, 3.5 to 4.5% nickel, 1.5 to 2.0 molybdenum, 1.0 to 1.5. % Titanium, 〇.3 to 0. 4 〇 / 〇 aluminum and 0.15 to 0.2% carbon, the remaining proportion is mainly iron. In another embodiment of the present invention, the material further comprises at least one trace element, wherein the trace element is preferably selected from the group consisting of: 0.5 to 1.0%, 0.8 to 10%, and combination. The above ratios are all expressed in terms of weight percent (wt%), which are described in advance. Please refer to the distribution area of the basic structure distribution diagram of the ferritic iron precipitation precipitation hardening alloy in the iron-chromium-nickel stainless steel alloy series (such as the area shown by the dotted line) shown in Fig. 2, and this type of alloy mainly passes The transformation of the granulated iron in the Ma Tian produces a strengthening effect and further enhances the strengthening effect by disposing the dispersion phase (dispersi〇n strengthening phase). In addition to its better resistance to atmospheric corrosion and acid and acid rot, it is also insensitive to hydrogen embrittlement (HE) and has better weldability than 麻田散铁不锈钢. Referring to Fig. 3, there is shown a comparison table of the composition ratio and mechanical properties of the examples and comparative examples of the low chromium high strength iron-based golf club alloy of the present invention, wherein the numbers 1 to 8 are the components of the present invention. Examples of scales Nos. 9 to 12 are comparative examples (the relevant data is the average of 1 sample of samples). It can be seen from Fig. 3 that iron-5% chromium-4.5% nickel-L98% your U-titanium_〇32(four)2 carbon_〇6 201014918 dream-0.91 fierce composition number 1 embodiment alloy composition, by ii〇〇° c solution treatment, after aging treatment at 550 ° C, the mechanical properties of the tensile strength average of 245.7ksi 'the average strength of the relief strength is 240.8ksi, the elongation is 8.1%, and made according to the alloy design The ball head was tested for 48 hours by salt spray test and 3000 shots by golf ball. Referring to Attachment 1, which discloses a metallographic diagram of the alloy material of the example No. 1 of the present invention, which shows that the alloy is solution treated by ll〇〇«>C, and then passed through 55 (microscopically after TC aging heat treatment). Please refer to the attached drawings 2 and 3, which discloses that the alloy material of the example No. 1 of the present invention is subjected to a solution treatment at 1100 ° C and then passes through 550. (: A bright field view and a dark field view of the aging heat treatment. Furthermore, please refer to the attached photograph 4, which discloses a selected area diffraction pattern of the alloy material of the embodiment No. 1 of the present invention (selected leached difacti() n pattern 'SADP) ' thus can be observed on the α base In addition to the presence of a chromium-rich solid solution (α phase), there is also a precipitation of the NiA1 phase superlattice structure. Due to the precipitation of fine and uniformly distributed precipitates, the movement of the poor row is hindered and the strengthening is achieved. The purpose of stainless steel. In addition, please refer to Figure 4, which reveals that the actual complement recording of the job 1 of the present invention is analyzed by the χ _ _ ray diffraction, except for the 面 2 ordered surface superlattice precipitates appearing In addition, it also has the object of the face (F.CQ L1_3A1), so the invention In addition to the (four) effect of the Daer (four) silk, the elongation of the stainless steel recording material also maintains a good development range. Please refer to the figure 3, the number of the alloy materials of the example number χ8 to 15 201014918 are in this In the content range of the invention, after the appropriate processing and heat treatment, the mechanical properties of the alloy material are between 210 and 245 ksi, and the value of the lodging strength is between 195 and 220 ksi, and the elongation can reach 6 to Go/., and the salt spray test for 48 hours and the Nulff ball shot 3000 tests are all qualified. Please refer to Figure 3 again, when the chromium content of the alloy material is lower than the chromium content of the present invention (such as the number In the case of the comparative example alloy material of 9, 10, the selective area diffraction pattern (SADP) of Comparative Example No. 9 shown in Attachment 5 can be observed, except that it has a chromium-rich solid solution (α, phase). There is no other precipitate in the presence of the film. Further, it can be seen from Fig. 3 that the elongation of the alloy material of the comparative example Nos. 9 and 10 is lower than the elongation ratio of the present invention and the state of rust is also generated. On the one hand, please refer to Figure 3 again, when the alloy material When the chromium content is higher than the chromium content range of the present invention (for example, the alloy material of the comparative example numbered U and 12), the bright field of view and the selected area diffraction pattern of Comparative Example No. 12 shown in the attached drawings 6 and 7 can be corrected. The precipitation of the granulated iron in the Maba by the enthalpy is reduced. 'The precipitation of this carbide will cause the residual resistance to be lost near the grain boundary, which will cause the granule to occur, which will cause the alloy to be mixed with her, and then It is found from Fig. 3 that the mechanical and elongation ratios are lower than those of the hair _ mechanical strength and elongation rate #, so the ratio of the alloy material age to the rust is the brittle material. The following is a description of the ratio of various alloying elements and trace elements added and their alloying properties to the low-chromium high-strength iron-based golf surface alloys of this (4): Chromium (Cr): mainly in alloys The corrosion resistance of the material can also improve the hardening energy and high temperature strength of the alloy material, especially for the wear resistance of high carbon steel. The chromium is basically a body-centered cubic 毋cc) ferrite-iron stable phase. When the chromium content is too low, the anti-recording corrosion resistance of the alloy material is lowered, and when the chromium content is too high, the alloy is greatly improved. The segregation can occur in the monthly b-sex. Therefore, in order to make the alloy material easy to control during production and design to exhibit optimum golf head performance, the alloy material of the present invention controls the chromium content between 4.5 and 5.5%. Nickel (Ni): The main consideration is to increase the weldability and toughness. When nickel is added to the alloy material, it not only increases the corrosion and oxidation resistance of the alloy material, but also enhances the effects of solid solution strengthening and high hardenability. Refinement of ferrite grains and grains, under the same strength, can improve the plasticity and toughness of steel, especially low temperature toughness. Combined with chrome, Gu, etc. can also improve the hybridity and money. Therefore, in order to make the alloy material easy to control during the production and design process to exhibit optimum golf club head performance, the alloy material of the present invention controls the nickel content between 35 and 45%. Key (M〇): Mainly to control the reaction kinetics of Μ2Α. Increasing the Cr/Ni stainless steel in the office #' can be used to produce a sensitive coffee. It can also adjust the density of the material, and make it hard to observe people, prevent fire and smoke, and improve the high temperature strength, creep strength, and high temperature hardness of the alloy material. When the key content is between i 5 and 3% 17 201014918, it can increase. Corrosion resistant steel resists the corrosion of organic acids and reducing media, which increases the anti-porous properties of the alloy material and forms wear-resistant molybdenum carbide particles, which contribute to the fluidity of the molten steel. However, when the molybdenum content is more than 6.0% or more, excessive precipitation is caused to make the material embrittlement. Therefore, the alloy material of the present invention controls the molybdenum content to be between 1.5 and 2.0%. Chin (Ti): The addition of titanium alloy can reduce the density of the alloy, increase the strength and resistance of the alloy and the solid solution strengthening effect is strong, but at the same time reduce the toughness of the solid solution. It can improve the tempering stability of steel and has secondary hardening effect, and can also improve the oxidation resistance and heat strength of heat-resistant steel. It has the function of preventing and mitigating stainless steel acid-resistant steel and stress corrosion. Therefore, the alloy material of the present invention controls the titanium content between 1 Torr and 15%. Shao (A1): mainly used to deoxidize and refine grains and age strengthening. The formation of carbides has a strong affinity with nitrogen and oxygen, and its solid solution strengthening effect is large. In the heat resistant alloy, a γ' phase (NisAl) is formed with nickel to increase the strength of the alloy. Therefore, the alloy material of the present invention controls the aluminum content between 〇.2 and 〇5%. Carbon (C): Carbon is basically an indispensable element of general steel materials. In addition to being a carbide, it is also an element of the stable phase of the Worthite iron. As the carbon content increases, the ferrite iron decreases and Voss Tian Tie Yu is stable. However, when the carbon content is too high, it will be detrimental to the durability of the alloy material. Therefore, if the alloy material can control or add carbon between 0.2 and 0.3%, it will contribute to the silver resistance and the stability of the Worthite iron phase.矽(Si): When doping or adding bismuth in the alloy material of the present invention, it is advantageous to prevent the formation of the stomata and increase the collection of the steel-based alloy material, when I is larger than L0/° At the time, it will be unfavorable to extend the alloy of β @ if it can add G.5 to 1.G%; ^, will help to improve the casting properties' to carry out the process of casting raw materials. ,
猛陶：觀倾鐵胁，且齡_基合金材料中的氧 化物且有獅鋼之熱加卫，朗免絲^在本發明之合金材料 中威低於0.8%雖有比較好之延伸率，但抗拉#度相對偏 低’右猛耕1观雖有良好的抗㈣度，但其延伸率相對偏 低。因此’在本發明之合金材料中，若能添加0.8至1.0%之錳， 將有助於降低賊性、提冑硬倾域冑賊性質。 綜上所述’本發明之低鉻高強度之鐵基高爾夫球頭合金藉 由適當控制合金成分’脚適當調配鉻、鎳、翻、鈦、銘及碳 之含量，及適當摻雜添加矽及/或錳之元素，並可利用適當加 工及熱處理製程，使其合金成份之微量元素，經由熱處理製 程，將被熱處理的合金基地中，析出微細且分佈均勻之析出 物’而達到析出強化，另搭配低含量之鉻元素的強化效果，使 本發明設計之低鉻高強度之鐵基高爾夫球頭合金具備210至 240ksi之間的抗拉強度、195至22〇ksi之間的降伏強度及6至 8%之間的延伸率等極佳之機械性質。本發明之合金材料除了 具有低合金與高強度之特性，亦兼具良好之抗蝕性，符合了製 作高爾夫球木桿頭之強度需求、防鏽性佳與良好之加工性的要 19 201014918 求，實為製作高爾夫球木桿頭之最佳合金材料。在本發明中， 具備此機械性質之合金材料特別適用於鍛造製作高爾夫木桿 頭，以發揮高爾夫木桿頭的最佳性能。 雖然本發明已以較佳實施例揭露，然其並非用以限制本發 明，任何熟習此項技藝之人士，在不脫離本發明之精神和範圍 内’當可作各種更動與修飾’因此本發明之保護範圍當視後附 之申請專利範圍所界定者為準。 【圖式簡單說明】 第1圖：現有高爾夫球頭製造業常用鐵基素材之機械性質比較 表。 第2圖：鐵鉻鎳不銹鋼合金系列之基本結構分佈圖，其中利用 虛線方框繪示本發明之合金材料範圍。 第3圖：本發明之低絡高強度之鐵基高爾夫球頭合金之實施例 與比較例之成分比例與機械性質之比較表。 第4圖：本發明編號1之實施例合金材料(木桿頭鍛件)經11〇〇 °(：固溶處理，再經時效熱處理55(rC後之X光繞射曲線圖。 附照1 :本發明編號1之實施例合金材料經ll〇〇°C固溶處理 後’再經550°C時效熱處理的(500倍放大)金相圖。 附照2 :本發明編號1之實施例合金材料經11〇〇。(：固溶處理 後，再經550°C時效熱處理之(72000倍放大)明視野圖。 201014918 附照3 :本發明編號1之實施例合金材料經ll〇〇°C固溶處理 後，再經550°c時效熱處理之(72000倍放大)暗視野圖。 附照4 :本發明編號1之實施例合金材料經ll〇〇°C固溶處理 後，再經550°C時效熱處理之(61〇,〇〇〇,〇〇〇倍放大)擇區繞射圖 (SADP) 〇 附照5 :本發明編號9之比較例合金材料經固溶處理後，再經 550°C時效熱處理之(870,000,000倍放大)擇區繞射圖。 〇 附照6 :本發明編號12之比較例合金材料經固溶處理後，再 經550。(：時效熱處理之(55,〇〇〇倍放大)明視野圖。 附照7 :本發明編號12之比較例合金材料經固溶處理後，再 經550°C時效熱處理之(87〇,〇〇〇,〇〇〇倍放大)擇區繞射圖。 ❹ 21Meng Tao: Guan Ti iron threat, and the oxide in the age-based alloy material and the heat of the lion steel, the Lange wire ^ in the alloy material of the invention is less than 0.8%, although the better elongation However, the resistance is relatively low. Although the right cultivator has a good resistance (four degrees), its elongation is relatively low. Therefore, in the alloy material of the present invention, if 0.8 to 1.0% of manganese can be added, it will help to reduce the thief property and improve the nature of the hard thief. In summary, the low-chromium and high-strength iron-based golf ball alloy of the present invention appropriately mixes the contents of chromium, nickel, turn, titanium, indium and carbon by appropriately controlling the alloy composition, and appropriately doping and adding / or manganese element, and can use appropriate processing and heat treatment process, the trace elements of the alloy composition, through the heat treatment process, the finely-formed and uniformly distributed precipitates in the heat-treated alloy base to achieve precipitation strengthening, With the strengthening effect of low content of chromium element, the low chromium high strength iron-based golf club alloy designed by the invention has a tensile strength between 210 and 240 ksi, a strength between 195 and 22 〇 ksi, and 6 to Excellent mechanical properties such as elongation between 8%. The alloy material of the invention not only has low alloy and high strength characteristics, but also has good corrosion resistance, and meets the requirements for the strength of the golf club head, the rust prevention and the good workability. It is the best alloy material for making golf club heads. In the present invention, the alloy material having this mechanical property is particularly suitable for forging a golf wood head to give the best performance of the golf club head. The present invention has been disclosed in its preferred embodiments, and is not intended to limit the invention, and those skilled in the art will be able to make various modifications and modifications without departing from the spirit and scope of the invention. The scope of protection is subject to the definition of the scope of the patent application. [Simple description of the diagram] Figure 1: Comparison of mechanical properties of iron-based materials commonly used in golf head manufacturing. Fig. 2 is a view showing the basic structure of the iron-chromium-nickel stainless steel alloy series in which the range of the alloy material of the present invention is shown by a dotted line. Fig. 3 is a comparison table showing the composition ratio and mechanical properties of the low-strength high-strength iron-based golf club alloy of the present invention. Figure 4: The alloy material (wood head forging) of the example No. 1 of the present invention is subjected to 11 〇〇 ° (: solution treatment, followed by aging heat treatment 55 (X-ray diffraction curve after rC. Attachment 1 : The alloy material of the example No. 1 of the present invention is subjected to solution treatment at ll ° ° C and then subjected to (500 times magnification) metallographic diagram of aging treatment at 550 ° C. Attachment 2: alloy material of the example No. 1 of the present invention After 11 〇〇. (: after solution treatment, and then subjected to 550 ° C aging heat treatment (72000 times magnification) bright field view. 201014918 Attachment 3: The alloy material of the example No. 1 of the present invention is solidified by ll 〇〇 ° C After the solution treatment, the dark field view is further processed by aging at 550 ° C (72000 times magnification). Attachment 4: The alloy material of the example No. 1 of the present invention is solution treated at ll ° ° C, and then passed through 550 ° C. Aging heat treatment (61〇, 〇〇〇, 〇〇〇 magnification) Selective area diffraction pattern (SADP) 〇 Attachment 5: The alloy material of the comparative example No. 9 of the invention is solution treated and then passed through 550 ° C The aging heat treatment (870,000,000 times magnification) of the selected area diffraction pattern. 〇 Attachment 6: The alloy material of the comparative example No. 12 of the present invention is solution treated and then passed through 550. (: aging heat treatment (55, 〇〇〇 magnification) bright field view. Attachment 7: Comparative Example No. 12 of the invention alloy material after solution treatment, and then aging treatment at 550 ° C (87 〇, 〇 〇〇,〇〇〇倍放大) Select the area to diffract map. ❹ 21